Reactions and Synthesis in Surfactant Systems (Surfactant Science Series)

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REACTIONS AND SYNTHESIS IN SURFACTANT SYSTEMS

edited by

John Texter Strider Research Corporation Rochester, New York

Marcel Dekker, Inc. TM

Copyright © 2001 by Taylor & Francis Group LLC

New York • Basel

Library of Congress Cataloging-in-Publication Data Reactions and synthesis in surfactant systems/edited by John Texter. p. cm.—(Surfactant science series ; 100) Includes index. ISBN 0-8247-0255-7 (acid-free paper) 1. Surface active agents. 2. Surface chemistry. I. Texter, J. (John) science series ; v. 100.

II. Surfactant

TP994 .R42 2001 668⬘.1—dc21 2001028628

This book is printed on acid-free paper. Headquarters Marcel Dekker, Inc. 270 Madison Avenue, New York, NY 10016 tel: 212-696-9000; fax: 212-685-4540 Eastern Hemisphere Distribution Marcel Dekker AG Hutgasse 4, Postfach 812, CH-4001 Basel, Switzerland tel: 41-61-261-8482; fax: 41-61-261-8896 World Wide Web http://www.dekker.com The publisher offers discounts on this book when ordered in bulk quantities. For more information, write to Special Sales/ Professional Marketing at the headquarters address above. Copyright 䉷 2001 by Marcel Dekker, Inc. All Rights Reserved. Neither this book nor any part may be reproduced or transmitted in any form or by any means, electronic or mechanical, including photocopying, microfilming, and recording, or by any information storage and retrieval system, without permission in writing from the publisher. Current printing (last digit): 10 9 8 7 6 5 4 3

2

1

PRINTED IN THE UNITED STATES OF AMERICA

SURFACTANT SCIENCE SERIES

FOUNDING EDITOR

MARTIN J. SCHICK 1918–1998 SERIES EDITOR

ARTHUR T. HUBBARD Santa Barbara Science Project Santa Barbara, California

ADVISORY BOARD

DANIEL BLANKSCHTEIN Department of Chemical Engineering Massachusetts Institute of Technology Cambridge, Massachusetts

ERIC W. KALER Department of Chemical Engineering University of Delaware Newark, Delaware

S. KARABORNI Shell International Petroleum Company Limited London, England

CLARENCE MILLER Department of Chemical Engineering Rice University Houston, Texas

LISA B. QUENCER The Dow Chemical Company Midland, Michigan

DON RUBINGH The Procter & Gamble Company Cincinnati, Ohio

JOHN F. SCAMEHORN Institute for Applied Surfactant Research University of Oklahoma Norman, Oklahoma

BEREND SMIT Shell International Oil Products B.V. Amsterdam, The Netherlands

P. SOMASUNDARAN Henry Krumb School of Mines Columbia University New York, New York

JOHN TEXTER Strider Research Corporation Rochester, New York

1. 2. 3. 4. 5. 6. 7. 8. 9. 10. 11. 12. 13. 14. 15. 16. 17. 18. 19. 20. 21. 22. 23. 24. 25. 26. 27. 28. 29. 30. 31. 32. 33. 34. 35. 36. 37. 38. 39. 40.

Nonionic Surfactants, edited by Martin J. Schick (see also Volumes 19, 23, and 60) Solvent Properties of Surfactant Solutions, edited by Kozo Shinoda (see Volume 55) Surfactant Biodegradation, R. D. Swisher (see Volume 18) Cationic Surfactants, edited by Eric Jungermann (see also Volumes 34, 37, and 53) Detergency: Theory and Test Methods (in three parts), edited by W. G. Cutler and R. C. Davis (see also Volume 20) Emulsions and Emulsion Technology (in three parts), edited by Kenneth J. Lissant Anionic Surfactants (in two parts), edited by Warner M. Linfield (see Volume 56) Anionic Surfactants: Chemical Analysis, edited by John Cross Stabilization of Colloidal Dispersions by Polymer Adsorption, Tatsuo Sato and Richard Ruch Anionic Surfactants: Biochemistry, Toxicology, Dermatology, edited by Christian Gloxhuber (see Volume 43) Anionic Surfactants: Physical Chemistry of Surfactant Action, edited by E. H. Lucassen-Reynders Amphoteric Surfactants, edited by B. R. Bluestein and Clifford L. Hilton (see Volume 59) Demulsification: Industrial Applications, Kenneth J. Lissant Surfactants in Textile Processing, Arved Datyner Electrical Phenomena at Interfaces: Fundamentals, Measurements, and Applications, edited by Ayao Kitahara and Akira Watanabe Surfactants in Cosmetics, edited by Martin M. Rieger (see Volume 68) Interfacial Phenomena: Equilibrium and Dynamic Effects, Clarence A. Miller and P. Neogi Surfactant Biodegradation: Second Edition, Revised and Expanded, R. D. Swisher Nonionic Surfactants: Chemical Analysis, edited by John Cross Detergency: Theory and Technology, edited by W. Gale Cutler and Erik Kissa Interfacial Phenomena in Apolar Media, edited by Hans-Friedrich Eicke and Geoffrey D. Parfitt Surfactant Solutions: New Methods of Investigation, edited by Raoul Zana Nonionic Surfactants: Physical Chemistry, edited by Martin J. Schick Microemulsion Systems, edited by Henri L. Rosano and Marc Clausse Biosurfactants and Biotechnology, edited by Naim Kosaric, W. L. Cairns, and Neil C. C. Gray Surfactants in Emerging Technologies, edited by Milton J. Rosen Reagents in Mineral Technology, edited by P. Somasundaran and Brij M. Moudgil Surfactants in Chemical/Process Engineering, edited by Darsh T. Wasan, Martin E. Ginn, and Dinesh O. Shah Thin Liquid Films, edited by I. B. Ivanov Microemulsions and Related Systems: Formulation, Solvency, and Physical Properties, edited by Maurice Bourrel and Robert S. Schechter Crystallization and Polymorphism of Fats and Fatty Acids, edited by Nissim Garti and Kiyotaka Sato Interfacial Phenomena in Coal Technology, edited by Gregory D. Botsaris and Yuli M. Glazman Surfactant-Based Separation Processes, edited by John F. Scamehorn and Jeffrey H. Harwell Cationic Surfactants: Organic Chemistry, edited by James M. Richmond Alkylene Oxides and Their Polymers, F. E. Bailey, Jr., and Joseph V. Koleske Interfacial Phenomena in Petroleum Recovery, edited by Norman R. Morrow Cationic Surfactants: Physical Chemistry, edited by Donn N. Rubingh and Paul M. Holland Kinetics and Catalysis in Microheterogeneous Systems, edited by M. Grätzel and K. Kalyanasundaram Interfacial Phenomena in Biological Systems, edited by Max Bender Analysis of Surfactants, Thomas M. Schmitt (see Volume 96)

41. Light Scattering by Liquid Surfaces and Complementary Techniques, edited by Dominique Langevin 42. Polymeric Surfactants, Irja Piirma 43. Anionic Surfactants: Biochemistry, Toxicology, Dermatology. Second Edition, Revised and Expanded, edited by Christian Gloxhuber and Klaus Künstler 44. Organized Solutions: Surfactants in Science and Technology, edited by Stig E. Friberg and Björn Lindman 45. Defoaming: Theory and Industrial Applications, edited by P. R. Garrett 46. Mixed Surfactant Systems, edited by Keizo Ogino and Masahiko Abe 47. Coagulation and Flocculation: Theory and Applications, edited by Bohuslav Dobiáð 48. Biosurfactants: Production · Properties · Applications, edited by Naim Kosaric 49. Wettability, edited by John C. Berg 50. Fluorinated Surfactants: Synthesis · Properties · Applications, Erik Kissa 51. Surface and Colloid Chemistry in Advanced Ceramics Processing, edited by Robert J. Pugh and Lennart Bergström 52. Technological Applications of Dispersions, edited by Robert B. McKay 53. Cationic Surfactants: Analytical and Biological Evaluation, edited by John Cross and Edward J. Singer 54. Surfactants in Agrochemicals, Tharwat F. Tadros 55. Solubilization in Surfactant Aggregates, edited by Sherril D. Christian and John F. Scamehorn 56. Anionic Surfactants: Organic Chemistry, edited by Helmut W. Stache 57. Foams: Theory, Measurements, and Applications, edited by Robert K. Prud'homme and Saad A. Khan 58. The Preparation of Dispersions in Liquids, H. N. Stein 59. Amphoteric Surfactants: Second Edition, edited by Eric G. Lomax 60. Nonionic Surfactants: Polyoxyalkylene Block Copolymers, edited by Vaughn M. Nace 61. Emulsions and Emulsion Stability, edited by Johan Sjöblom 62. Vesicles, edited by Morton Rosoff 63. Applied Surface Thermodynamics, edited by A. W. Neumann and Jan K. Spelt 64. Surfactants in Solution, edited by Arun K. Chattopadhyay and K. L. Mittal 65. Detergents in the Environment, edited by Milan Johann Schwuger 66. Industrial Applications of Microemulsions, edited by Conxita Solans and Hironobu Kunieda 67. Liquid Detergents, edited by Kuo-Yann Lai 68. Surfactants in Cosmetics: Second Edition, Revised and Expanded, edited by Martin M. Rieger and Linda D. Rhein 69. Enzymes in Detergency, edited by Jan H. van Ee, Onno Misset, and Erik J. Baas 70. Structure-Performance Relationships in Surfactants, edited by Kunio Esumi and Minoru Ueno 71. Powdered Detergents, edited by Michael S. Showell 72. Nonionic Surfactants: Organic Chemistry, edited by Nico M. van Os 73. Anionic Surfactants: Analytical Chemistry, Second Edition, Revised and Expanded, edited by John Cross 74. Novel Surfactants: Preparation, Applications, and Biodegradability, edited by Krister Holmberg 75. Biopolymers at Interfaces, edited by Martin Malmsten 76. Electrical Phenomena at Interfaces: Fundamentals, Measurements, and Applications, Second Edition, Revised and Expanded, edited by Hiroyuki Ohshima and Kunio Furusawa 77. Polymer-Surfactant Systems, edited by Jan C. T. Kwak 78. Surfaces of Nanoparticles and Porous Materials, edited by James A. Schwarz and Cristian I. Contescu 79. Surface Chemistry and Electrochemistry of Membranes, edited by Torben Smith Sørensen 80. Interfacial Phenomena in Chromatography, edited by Emile Pefferkorn

81. Solid–Liquid Dispersions, Bohuslav Dobiáð, Xueping Qiu, and Wolfgang von Rybinski 82. Handbook of Detergents, editor in chief: Uri Zoller Part A: Properties, edited by Guy Broze 83. Modern Characterization Methods of Surfactant Systems, edited by Bernard P. Binks 84. Dispersions: Characterization, Testing, and Measurement, Erik Kissa 85. Interfacial Forces and Fields: Theory and Applications, edited by Jyh-Ping Hsu 86. Silicone Surfactants, edited by Randal M. Hill 87. Surface Characterization Methods: Principles, Techniques, and Applications, edited by Andrew J. Milling 88. Interfacial Dynamics, edited by Nikola Kallay 89. Computational Methods in Surface and Colloid Science, edited by Maùgorzata Borówko 90. Adsorption on Silica Surfaces, edited by Eugène Papirer 91. Nonionic Surfactants: Alkyl Polyglucosides, edited by Dieter Balzer and Harald Lüders 92. Fine Particles: Synthesis, Characterization, and Mechanisms of Growth, edited by Tadao Sugimoto 93. Thermal Behavior of Dispersed Systems, edited by Nissim Garti 94. Surface Characteristics of Fibers and Textiles, edited by Christopher M. Pastore and Paul Kiekens 95. Liquid Interfaces in Chemical, Biological, and Pharmaceutical Applications, edited by Alexander G. Volkov 96. Analysis of Surfactants: Second Edition, Revised and Expanded, Thomas M. Schmitt 97. Fluorinated Surfactants and Repellents: Second Edition, Revised and Expanded, Erik Kissa 98. Detergency of Specialty Surfactants, edited by Floyd E. Friedli 99. Physical Chemistry of Polyelectrolytes, edited by Tsetska Radeva 100. Reactions and Synthesis in Surfactant Systems, edited by John Texter 101. Protein-Based Surfactants: Synthesis, Physicochemical Properties, and Applications, edited by Ifendu A. Nnanna and Jiding Xia 102. Chemical Properties of Material Surfaces, Marek Kosmulski 103. Oxide Surfaces, edited by James A. Wingrave 104. Polymers in Particulate Systems: Properties and Applications, edited by Vincent A. Hackley, P. Somasundaran, and Jennifer A. Lewis 105. Colloid and Surface Properties of Clays and Related Minerals, Rossman F. Giese and Carel J. van Oss 106. Interfacial Electrokinetics and Electrophoresis, edited by Ángel V. Delgado 107. Adsorption: Theory, Modeling, and Analysis, edited by József Tóth 108. Interfacial Applications in Environmental Engineering, edited by Mark A. Keane 109. Adsorption and Aggregation of Surfactants in Solution, edited by K. L. Mittal and Dinesh O. Shah 110. Biopolymers at Interfaces: Second Edition, Revised and Expanded, edited by Martin Malmsten 111. Biomolecular Films: Design, Function, and Applications, edited by James F. Rusling 112. Structure–Performance Relationships in Surfactants: Second Edition, Revised and Expanded, edited by Kunio Esumi and Minoru Ueno

ADDITIONAL VOLUMES IN PREPARATION

Liquid Interfacial Systems: Oscillations and Instability, Rudolph V. Birikh, Vladimir A. Briskman, Manuel G. Velarde, and Jean-Claude Legros

Novel Surfactants: Preparation, Applications, and Biodegradability: Second Edition, Revised and Expanded, edited by Krister Holmberg Colloidal Polymers: Preparation and Biomedical Applications, edited by Abdelhamid Elaissari

Preface

This book presents a review of extant applications of surfactant technology in chemical synthesis as well as chemical reactions and catalysis. The applications and utilization of surfactants in diverse chemistries, including many areas of organic, inorganic, colloidal, surface, and materials chemistry, cover a very wide gamut. With the possible exception of the journal Langmuir, no single journal or professional publication ties together all these areas. It is therefore hoped that this volume will help practitioners and students increase the breadth of their appreciation of surfactant systems in various synthetic and practical applications. The burgeoning arena of template synthesis and nanotechnology indicates that major advances in nanoelectronics will not be forthcoming from further miniaturization programs, but must rely on dramatic improvements in the sophistication with which we wield molecular design and synthesis of surfactants and amphiphiles. Self-assembly principles have been clearly delineated, and the time has come to put this technology to work in chemical synthesis and processing technologies. The success of such endeavors will require closer collaboration among synthetic and physical scientists and engineers, and greater appreciation among practitioners in one discipline for the opportunities and limitations of key related disciplines. The present volume is extremely wide in scope, covering a broad swath of organic, inorganic, surface, and colloidal chemistry and materials science united by the universal use of surfactant and amphiphile technology in each application. While the volume may seem too synthetic for some readers and too physical for others, it is intended to bring together many related areas and to facilitate closer collaboration between synthetic and physical practitioners in developing new applications and materials. The genesis of this broad arena is found in micellar catalysis, monolayer studies at the water–air interface, and inorganic particle precipitation. Although the general principles of monolayer formation at air–water interfaces and in self-assembled monolayers appear well defined, the controlled multilayer formation of composites, using surfactant templating and molecular recognition principles, is at an early stage in the development of practical applications and processes. Compartmentalization of reactants, as effected by self-organization in surfactant systems, is providing size and morphology control in synthesizing nanoparticulate inorganics and organics. These nanoparticulates are being incorporated into controlled arrays on mesoscales in furthering practical device development. While it was the editor’s intention to cover all major application areas, some areas will regrettably have been overlooked, and for these omissions the reader is extended an apology. It is hoped that this book will stimulate readers to invent new applications areas, as naturally occurs in the bridging of disciplines. The first of the five general parts of this volume comprises surfactant syntheses and electrochemical transformations. Part Two is basically physical–organic chemistry in surfactant systems. Included are micellar catalysis, reaction chemistry in microemulsions, electrocatalysis and electrosynthesis in various surfactant systems, and diverse applications involving emulsions, microemulsions, and vesicles. Parts Three and Four are focused on particle formation, organic and inorganic. Part Three addresses the role of surfactants in organic polymerizations and also provides a thorough review of polymerizable surfactants. Part Four examines particle formation and the role of iii

iv

Preface

surfactants in compartmentalizing precipitation chemistries, such as in reverse microemulsions and at surfactant interfaces. The precipitation of inorganic nanoparticles is not treated exhaustively, since an excellent recent volume edited by Tadao Sugimoto, Fine Particles: Synthesis, Characterization, and Mechanisms of Growth (Volume 92 of the Surfactant Science Series) treats this topic thoroughly. Part Five addresses syntheses and processing, via selfassembly, molecular recognition, and surfactant templating, on the supramolecular level. These categories cover a variety of themes, including: Organic chemistry as influenced by surfactants and surfactant assemblies, The production of organic particulates by chain polymerization in surfactant systems and by polymerizable surfactants, The synthesis of inorganic nanoparticles using compartmentalized reaction chemistry, The synthesis of supramolecular assemblies using surfactant assemblies as templates, The formation of multilayer composites using surfactants and other growth-directing materials. The interdisciplinary content presented bridges numerous areas of chemistry and materials science, including colloid and surface chemistry, organic synthesis and catalysis, inorganic synthesis and catalysis, electrochemical synthesis and electrocatalysis, inorganic–organic composites, and template-directed synthesis of mesoporous materials. This interconnected bridging makes this volume of interest to chemists and materials scientists of many persuasions. This volume is aimed at practicing industrial and academic scientists and engineers and at students involved in chemical and particle synthesis and processing. Nearly 100 contributors collaborated in producing the 40 diverse chapters of this volume. I thank each of the authors for their contributions and patience as the volume progressed. I also thank my acquisitions editor, Anita Lekhwani, for her cheerful collaboration, and our production editor, Joseph Stubenrauch, for steadfastly coaxing and urging the volume forward and onward to completion. John Texter

Contents

Preface iii Contributors ix Part One

Surfactant Synthesis and Transformations

1.

Industrial Surfactant Syntheses 1 Ansgar Behler, Manfred Biermann, Karlheinz Hill, Hans-Christian Raths, Marie-Esther Saint Victor, and Gu¨nter Uphues

2.

Cleavable Surfactants Krister Holmberg

3.

Gemini Surfactants and Surfactant Oligomers Martin In

4.

New Glycolipids Having Biological Activities: Key Role of Their Organization Armand Lattes, Isabelle Rico-Lattes, Emile Perez, and Muriel Blanzat

5.

Surfactants for Supercritical and Near-Critical Fluids 129 Terri Carson, Sharon L. Wells, and Joseph M. DeSimone

6.

Acid- and Oxidatively Labile Vinyl Ether Surfactants: Synthesis and Drug Delivery Applications Jong-Mok Kim and David H. Thompson

7.

Three Principles for Active Control of Interfacial Properties of Surfactant Solutions Jason Y. Shin, Lana I. Jong, Nihal Aydogan, and Nicholas L. Abbott

Part Two

45 59

145

155

Chemistry in Isotropic Phases and in Mesophases

8.

Reactivity Control by Aqueous Amphiphilic Self-Assembling Systems Gianfranco Savelli, Raimondo Germani, and Lucia Brinchi

9.

Diels-Alder Reactions in Micellar Media Sijbren Otto and Jan B. F. N. Engberts

10.

111

175

247

Interfacial Compositions of Surfactant Assemblies by Chemical Trapping with Arenediazonium Ions: Method and Applications 265 Laurence S. Romsted v

vi

Contents

11.

Electro-Organic Synthesis in Macro- and Microheterogeneous Solutions: Emulsions, Micelles, and Related Systems 295 Marc Thomalla

12.

Mediated Electro-Organic Synthesis in Microemulsions James F. Rusling

13.

Chemical Activation in Micelles, Pseudomicelles, and Microemulsions 337 Isabelle Rico-Lattes, Armand Lattes, Emile Perez, Ferdinand Gonzaga, and Andreea Ruxandra Schmitzer

14.

Reactions and Synthesis in Microemulsions and Emulsions in Carbon Dioxide 349 Keith P. Johnston, J. D. Holmes, G. B. Jacobson, C. T. Lee, G. Li, P. Psathas, and M. Z. Yates

15.

Reactions in Multiphase (Liquid/Liquid) Micellar Systems Turgut Battal and James F. Rathman

16.

Chemical Detoxification in Amphiphilic Systems Raymond A. Mackay

17.

Colloidal Chemistry of Lubricating Oils 385 Duncan C. Hone, Brian H. Robinson, Jane R. Galsworthy, and Roger W. Glyde

18.

Giant Vesicles as Microchemical Vessels Stephen J. Lee and Jason S. Keiper

19.

Electroless Plating of Organic Pigment Thin Films Using Surfactants with an Azobenzene Group Tetsuo Saji

20.

Kinetic and Thermodynamic Modeling of Micellar Autocatalysis Jean-Claude Micheau and R. Nagarajan

Part Three

323

359

373

395 407

413

Polymerization Chemistry

21.

Emulsion Polymerization Klaus Tauer

22.

Free Radical Polymerization in Microemulsions 455 Carlos C. Co, Renko de Vries, and Eric W. Kaler

23.

Heterophase Polymerization in Inverse Systems Katharina Landfester and Hans-Peter Hentze

24.

Vesicular Polymerization 501 Jutta Hotz and Wolfgang Meier

25.

The Use of Surfactant Self-Assembly in the Enzymatic Synthesis of Novel Polymers 515 Glen Irvin, Sukanta Banerjee, Ramannair Premachandran, Blake A. Simmons, Sichu Li, Vijay T. John, Gary McPherson, Joseph Akkara, David Kaplan, and Weilie Zhou

26.

Material Synthesis by Polymerization in Surfactant Mesophases Eric J. Paul and Robert K. Prud’homme

27.

Admicellar Polymerization 537 John O’Haver, Brian Grady, Jeffrey H. Harwell, and Edgar A. O’Rear

28.

Polymerizable and Polymeric Surfactants Alain Guyot and Klaus Tauer

Part Four 29.

429

Particle Precipitation

Organic Particle Precipitation John Texter

577

547

471

525

Contents

vii

30.

Synthesis of Inorganic and Organic Nanoparticles in Microemulsions L. Jeunieau, F. Debuigne, and Janos B.Nagy

31.

Colloidal Nanoparticles and Nanoparticulate Films Grown at the Air-Water Interface Janos H. Fendler

32.

Formation of Nanoparticles in Organized Amphiphilic Films Karen Grieve, Franz Grieser, and D. Neil Furlong

Part Five

609 633

639

Supramolecular Synthesis

33.

The Role of Steric Constraints and Intermolecular Interactions in the Formation of Surfactant Phases So¨nke Svenson

34.

Stereochemistry of Lipid Micelles and Vesicles That Survive Drying Ju¨rgen-Hinrich Fuhrhop

35.

Synthesis and Properties of Amphiphile-Based Gene Carriers Nily Dan

36.

Synthesis of Microporous Materials from Reverse Micelles Ramsharan Singh, Mario Castagnola, and Prabir K. Dutta

37.

Mesoscopic Films at Interfaces 761 Srinivas Manne, R. K. Workman, and J. L. Wolgemuth

38.

Synthesis of Mesoscopic Silica Films at Fluid-Fluid Interfaces Yoon Seob Lee and James F. Rathman

39.

Inorganic Nanostructure Design with Amphiphilic Block Copolymers Christine Go¨ltner

40.

The Role of Surfactants and Amphiphiles in the Synthesis of Porous Inorganic Solids Andreas Stein and Brian J. Melde

Index 853

715

729 737

779 797 819

667

Contributors

Nicholas L. Abbott Wisconsin Joseph Akkara* Nihal Aydogan

U.S. Army Soldier Systems Center, Natick, Massachusetts Department of Chemical Engineering, University of Wisconsin–Madison, Madison, Wisconsin

Sukanta Banerjee Turgut Battal

Department of Chemical Engineering, University of Wisconsin–Madison, Madison,

Department of Chemical Engineering, Tulane University, New Orleans, Louisiana

Department of Chemical Engineering, The Ohio State University, Columbus, Ohio

Ansgar Behler

Cognis Deutschland GmbH, Du¨sseldorf, Germany

Manfred Biermann

Cognis Corporation, Cincinnati, Ohio

Muriel Blanzat

Laboratoire IMRCP, UMR CNRS 5623, Universite´ Paul Sabatier, Toulouse, France

Janos B.Nagy Belgium

Laboratoire de Re´sonance Magne´tique Nucleáire, Universitaires Notre-Dame de la Paix, Namur,

Lucia Brinchi

Department of Chemistry, University of Perugia, Perugia, Italy

†

Terri Carson

Department of Chemistry, University of North Carolina at Chapel Hill, Chapel Hill, North Carolina

Mario Castagnola Carlos C. Co Nily Dan

Department of Chemistry, The Ohio State University, Columbus, Ohio

Department of Chemical Engineering, University of Delaware, Newark, Delaware

Department of Chemical Engineering, Drexel University, Philadelphia, Pennsylvania

Renko de Vries‡ F. Debuigne Belgium


Laboratoire de Re´sonance Magne´tique Nucleáire, Universitaires Notre-Dame de la Paix, Namur,

Current affiliation: *National Science Foundation, Arlington, Virginia. † Polyurethanes Research and Development, Dow Chemical Company, Freeport, Texas. ‡ Laboratory of Physical Chemistry and Colloid Science, Wageningen University, Wageningen, The Netherlands. ix

x

Contributors

Joseph M. DeSimone Department of Chemistry, University of North Carolina at Chapel Hill, Chapel Hill, and Department of Chemical Engineering, North Carolina State University, Raleigh, North Carolina Prabir K. Dutta


Jan B. F. N. Engberts The Netherlands Janos H. Fendler

Physical Organic Chemistry Unit, Stratingh Institute, University of Groningen, Groningen,

Department of Chemistry, Clarkson University, Potsdam, New York

Ju¨rgen-Hinrich Fuhrhop D. Neil Furlong

Institut fu¨r Organische Chemie (WE 2), Freien Universita¨t Berlin, Berlin, Germany

RMIT University, Bundoora, Victoria, Australia

Jane R. Galsworthy

Infineum UK Ltd., Abingdon, Oxfordshire, England

Raimondo Germani


Roger W. Glyde

Infineum UK Ltd., Abingdon, Oxfordshire, England

Christine Go¨ltner*

Max-Planck-Institute of Colloids and Interfaces, Golm, Germany

Ferdinand Gonzaga Brian Grady Oklahoma


School of Chemical Engineering and Materials Science, University of Oklahoma, Norman,

Franz Grieser

School of Chemistry, University of Melbourne, Parkville, Victoria, Australia

Karen Grieve

School of Chemistry, University of Melbourne, Parkville, Victoria, Australia

Alain Guyot

Laboratory for Polymerization Chemistry and Processes, CNRS, Villeurbanne, France

Jeffrey H. Harwell Institute of Applied Surfactant Research, and School of Chemical Engineering and Materials Science, University of Oklahoma, Norman, Oklahoma Hans-Peter Hentze Germany Karlheinz Hill


Krister Holmberg Sweden J. D. Holmes

Martin In

Department of Applied Surface Chemistry, Chalmers University of Technology, Go¨teborg,

Department of Chemical Engineering, University College, Cork, Ireland

Duncan C. Hone Jutta Hotz

Department of Colloid Chemistry, Max-Planck-Institute of Colloids and Interfaces, Golm,

School of Chemical Sciences, University of East Anglia, Norwich, Norfolk, England

Department of Physical Chemistry, University of Basel, Basel, Switzerland Complex Fluids Laboratory, CNRS-Rhodia, Cranbury, New Jersey

Glen Irvin

Chemical Engineering Department, Tulane University, New Orleans, Louisiana

G. B. Jacobson L. Jeunieau Belgium Vijay T. John

Los Alamos National Laboratory, Los Alamos, New Mexico

Laboratoire de Re´sonance Magne´tique Nucleáire, Universitaires Notre-Dame de la Paix, Namur, Department of Chemical Engineering, Tulane University, New Orleans, Louisiana

Keith P. Johnston

Department of Chemical Engineering, University of Texas, Austin, Texas

*Current affiliation: School of Chemistry, University of Bristol, Bristol, England.

Contributors

xi

Lana I. Jong*

Department of Chemical Engineering, University of Wisconsin–Madison, Madison, Wisconsin

Eric W. Kaler


David Kaplan

Department of Chemical Engineering, Tufts University, Medford, Massachusetts

Jason S. Keiper Jong-Mok Kim

Department of Chemistry, Emory University, Atlanta, Georgia Department of Chemistry, Purdue University, West Lafayette, Indiana

Katharina Landfester Germany Armand Lattes C. T. Lee

Department of Colloid Chemistry, Max-Planck-Institute of Colloids and Interfaces, Golm,



Stephen J. Lee

Chemical Sciences Division, U.S. Army Research Office, Research Triangle Park, North Carolina

Yoon Seob Lee


G. Li


Sichu Li


Raymond A. Mackay Srinivas Manne

Department of Physics, University of Arizona, Tucson, Arizona

Gary McPherson Wolfgang Meier Brian J. Melde

Department of Chemistry, Clarkson University, Potsdam, New York

Department of Chemical Engineering, Tulane University, New Orleans, Louisiana Department of Physical Chemistry, University of Basel, Basel, Switzerland

Department of Chemistry, University of Minnesota, Minneapolis, Minnesota

Jean-Claude Micheau


R. Nagarajan Pennsylvania

Department of Chemical Engineering, The Pennsylvania State University, University Park,

John O’Haver

Department of Chemical Engineering, University of Mississippi, University, Mississippi

Edgar A. O’Rear Institute of Applied Surfactant Research, and School of Chemical Engineering and Materials Science, University of Oklahoma, Norman, Oklahoma Sijbren Otto† Netherlands Eric J. Paul Emile Perez

Physical Organic Chemistry Unit, Stratingh Institute, University of Groningen, Groningen, The Department of Chemical Engineering, Princeton University, Princeton, New Jersey Laboratoire IMRCP, UMR CNRS 5623, Universite´ Paul Sabatier, Toulouse, France

Ramannair Premachandran Robert K. Prud’homme P. Psathas


Department of Chemical Engineering, Princeton University, Princeton, New Jersey


James F. Rathman


Hans-Christian Raths


Current affiliation: *Department of Chemical Engineering, University of California, Davis, Davis, California. † University Chemical Laboratory, University of Cambridge, Cambridge, England.

xii

Contributors

Isabelle Rico-Lattes Brian H. Robinson

Laboratoire IMRCP, UMR CNRS 5623, Universite´ Paul Sabatier, Toulouse, France School of Chemical Sciences, University of East Anglia, Norwich, Norfolk, England

Laurence S. Romsted New Jersey James F. Rusling

Department of Chemistry, Rutgers, The State University of New Jersey, New Brunswick,

Department of Chemistry, University of Connecticut, Storrs, Connecticut

Marie-Esther Saint Victor Tetsuo Saji


Department of Chemistry and Materials Science, Tokyo Institute of Technology, Tokyo, Japan

Gianfranco Savelli


Andreea Ruxandra Schmitzer France Jason Y. Shin

Laboratoire IMRCP, UMR CNRS 5623, Universite´ Paul Sabatier, Toulouse,

Department of Chemical Engineering, University of Wisconsin–Madison, Madison, Wisconsin

Blake A. Simmons


Ramsharan Singh


Andreas Stein So¨nke Svenson land, Michigan

Department of Chemistry, University of Minnesota, Minneapolis, Minnesota Corporate Research and Development–Chemical Sciences, The Dow Chemical Company, Mid-

Klaus Tauer


John Texter

Strider Research Corporation, Rochester, New York

Marc Thomalla

Universite´ Claude Bernard Lyon I, Villeurbanne, France

David H. Thompson Gu¨nter Uphues

Department of Chemistry, Purdue University, West Lafayette, Indiana


Sharon L. Wells Carolina

Department of Chemistry, University of North Carolina at Chapel Hill, Chapel Hill, North

J. L. Wolgemuth

Department of Physics, University of Arizona, Tucson, Arizona

R. K. Workman M. Z. Yates Weilie Zhou

Department of Materials Science and Engineering, University of Arizona, Tucson, Arizona

Los Alamos National Laboratory, Los Alamos, New Mexico Advanced Materials Research Institute, University of New Orleans, New Orleans, Louisiana

1 Industrial Surfactant Syntheses ANSGAR BEHLER


MANFRED BIERMANN


KARLHEINZ HILL and HANS-CHRISTIAN RATHS Germany MARIE-ESTHER SAINT VICTOR ¨ NTER UPHUES GU

I.

Cognis Deutschland GmbH, Du¨sseldorf,



INTRODUCTION

ether sulfates (AESs), aliphatic alcohols (AEs), alcohol sulfates (ASs), and soap. In the past decades, new surfactants have proliferated mainly as nonionic or nonsoap surfactants offering unique properties and features to both industrial and household markets. Nonsoap surfactants are widely used in diverse applications such as detergents, paints, and dyestuffs; as specialty surfactants in home and personal care; and in the cosmetics and pharmaceutical industries. Since the 1960s, biodegradability and a growing environmental awareness have been the driving forces for the introduction of new surfactants. These forces continue to grow and influence the surfactant market and production. A new class of surfactants, carbohydrate-based surfactants, has gained significant interest and increased market share. Consequently, sugar-based surfactants, such as alkyl polyglycoside (APG*), are used as a replacement for polyoxyethylene alkylphenols (APEs) where biodegradability is a concern. They represent a new concept in compatibility and care.

For over 2000 years, humankind has used surfactants or surface-active ingredients in various aspects of daily life, for washing, laundry, cosmetics, and housecleaning. In the United States alone, over 10 billion pounds of detergents are used annually. Anionic surfactants represent 70–75% of the detergent market. Natural soaps are the oldest anionic surfactants and are used mainly in personal care and in the detergent industries. However, the development of more economical processes for the manufacture of surfactants has contributed to an increased consumption of synthetic detergents. Nonsoaps or synthetic detergents account for 84% of the total detergent market. In 1996, over 5 billion pounds of nonsoap surfactants were produced. In the Asia-Pacific region, the total surfactant consumption grows at an annual rate of 3.9% with a projection of 5.8 million tons in 2010. From a global perspective, the consumption and proportion of surfactants exhibit a different pattern for the North American and Western European regions compared with the Asia-Pacific region or Japan in particular. However, the major surfactants common (with respect to detergent) to all regions are linear alkylbenzene sulfonates (LASs), alcohol

*APG is a registered trademark of Cognis Deutschland GmbH. 1

2

Nonetheless, over 35 different types of surfactants are produced and used commercially in the formulation of home care, personal care, and industrial products. Contrary to many textbooks that elaborate on surfactant physical properties or formulation guidelines, this chapter approaches the surfactant topic from both synthesis and manufacturing perspectives. It offers a comprehensive overview of the most commonly used industrial surfactants with respect to their synthesis and manufacturing processes; their reactions and applications; and their physical, ecological, and toxicological properties. A concise and thorough description of the most pertinent synthesis routes is presented for the major types of surfactants predominantly used in the home and personal care industry. These surfactants are primarily anionic, nonionic, cationic, and amphoteric. Also reviewed is the synthesis of surfactants derived from carboxylation, sulfation, and condensation of fatty acid and phosphoric acid derivatives. The most commonly used anionic surfactants are LASs, ASs, and AESs. Nonionic surfactants are produced mainly by alkoxylation technology, although amine oxides under alkaline conditions are also classified as nonionic. Section III discusses the synthesis, production, and applications of the most commonly used ethoxylated surfactants such as alcohol ethoxylates, nonyl phenol ethoxylates and fatty acid ethoxylates, fatty amine oxides (FAOs), and fatty alkanolamides (FAAs). Section IV is concerned with a class of biodegradable and highly compatible carbohydrate- or sugarbased surfactants such as sorbitan esters, sucrose esters, and glucose-derived esters. Their syntheses encompass a significant list of renewable raw materials, including sucrose from sugar beet or cane, glucose from starch, and sorbitol as the hydrogenated glucose derivative. The most commonly used sugar-based surfactants, such as APG and fatty acid glucamides (FAGs), are reviewed in depth. The syntheses of cationic and amphoteric surfactants are reviewed in Sections V and VI, respectively. Cationic surfactants contain exclusively a quaternary tetracoordinated nitrogen atom (quaternary ammonium compounds). They are widely used as textile softeners in laundry formulations and in flotation. Amphoteric surfactants (including betaines) exhibit a zwitterionic character, i.e., they possess both anionic and cationic structures in one molecule. Recent progress in the surfactant field focuses on polymeric, splittable, gemini, multifunctional, and biosurfactants.

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II.

ANIONIC SURFACTANTS

A.

Carboxylates

1. Soaps Soaps represent the oldest known class of surfactants. They have been known for at least 2300 years. In the period of the Roman Empire, the Celts produced soap from animal fats and plant ashes, which served as alkali. They gave this product the name ‘‘saipo’’ from which the word ‘‘soap’’ is derived [1]. The chemical nature of soaps, as alkali salts of long-chain fatty acids, was recognized many centuries later by Chevreul. He showed in 1823 that the process of saponification is a chemical process of splitting fat into the alkali salt of fatty acid and glycerine. The term soap is mainly applied to the water-soluble alkali metal salts of fatty acids, although ammonia or triethanol amine salts are also used as technical soaps. Salts of fatty acids with heavy metals or with alkaline earth metals are water insoluble and are termed ‘‘metallic soaps.’’ They possess no detergent or soaplike properties. Generally, three different processes are suitable for the large-scale production of soaps: 1.

The saponification of neutral oils (triglycerides)

2.

The saponification of the fatty acids obtained from fats and oils

3.

The saponification of the fatty acid methyl esters derived from fats and oils

The most important industrial process is the saponification of the neutral oils and of the fatty acids. Both processes may be run in either batch or continuous mode. All types of fats and oils can be used in this process. The most important ones are tallow and coconut oil. The main application of soap is in the personal care industry, followed by the detergent industry.

Industrial Surfactant Syntheses

3

For the preparation of high-grade soaps, the basic soap must be very pure and free of unpleasant odors. The color quality and the odor of the basic soap are determined by the content of by-products. These impurities are of different origins: 1.

2. 3.

Natural constituents of fats and oils (waxes, phosphatides, cerebrosides, sterols, fat-soluble vitamins, diol lipids, carotenoids, etc.) Substances generated by oxidation processes during storage of the raw materials Substances generated in the manufacturing process

By using special purification steps during the production process, these by-products are eliminated. 2. Ether Carboxylic Acids The sensitivity of soaps to water hardness is a big disadvantage for many applications. In contrast, the alkyl polyoxyethylene carobxylic or alkyl (poly-1-oxapropen) oxaalkene carboxylic acids, or short ether carboxylic acids, exhibit an extreme water hardness resistance combined with good water solubility. The starting material for ether carboxylic acids is fatty alcohol ethoxylates. Conversion to the ether carboxylic acid can be carried out by three different routes (Fig. 1). The fatty alcohol ethoxylates can be carboxymethylated by reaction with monochloroacetic acid in the presence of sodium hydroxide [2] or through terminal oxidation of the fatty alcohol ethoxylate [3–5]. The ether carboxylic acid can also be synthesized by the addition of a vinylic system, i.e., acrylonitrile, to an oxyethylated fatty alcohol and subsequent hydrolysis. Ether carboxylic acids are temperature stable and re-

FIG. 1

sistant to alkali and hydrolysis, even under strong acidic or alkaline conditions. Because of their advantageous ecological, toxicological, and physicochemical properties and good compatibility with representatives of all surfactant classes, ether carboxylic acids can be applied effectively in many fields. They are used in washing and cleaning agents as well as cosmetics. They are utilized as emulsifying and auxiliary agents in the textile, printing, paper, plastics, metalworking, and pharmaceutical industries [6]. The salts of ether carboxylic acids with a high degree of ethoxylation are considered to be very mild and skin-compatible surfactants. Therefore, they are particularly suitable for applications in cosmetics [7]. Ether carboxylic acids are also used for manual dishwashing detergents, carpet cleaners, and other household products [8]. In the plastics industry, ether carboxylic acids are employed as auxiliary agents for emulsion polymerization and as antistatic agents (or antistats). They also exert a good corrosion-inhibiting effect and, therefore, ether carboxylic acids are also used as emulsifiers in drilling, rolling, and cutting oil emulsions and cooling lubricants [9]. B.

Sulfonation Technology

The technology of sulfonation (C — S coupling reaction) and sulfation (C — O — S coupling reaction) can be realized by various processes. Only industrial processes that are of significant importance are discussed here. Those are sulfonation and sulfation or sulfoxidation and sulfochlorination (see Alkane Sulfonates).

Synthesis of ether carboxylic acids.

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(a) Sulfonation with Sulfur Trioxide. Sulfonation with SO3/air raised from sulfur has become the predominant technology for manufacturing sulfonation products [10–12]. The diluted SO3 gas is generated by burning sulfur, followed by catalytic oxidation of SO2 at a vanadium pentoxide contact (conversion). Alternative sources for gaseous SO3 are liquid SO3 and oleum (65%), which is not only hazardous in transport, handling, and storage but also more expensive. The sulfonation is done mostly in falling-film reactor with 3–5% SO3 in dry air (dew point < ⫺60⬚C). A falling–film reactor, such as the Ballestra SULFUREX F system (Fig. 2), is a bundle of about 6-m-long reaction tubes in a shell in which heat exchange takes place with cooling water. The organic raw material is fed to the top of the reactor and is distributed on the inner walls of the reaction tubes by identical annular slots. The contact time with SO3 is relatively short to prevent undesired colordeveloping side reactions. After removal of the exhaust gas with a gas-liquid separator, the sulfonic acid is generally transferred to a neutralization loop. In some cases in which aging of the raw sulfonic acid is necessary to achieve a high degree of sulfonation (LAS, estersulfonates), a residence time is achieved by using an aging vessel or loop. Falling-film reactors of different designs are now available on the market.

FIG. 2

Multitube sulfonation reactor.

(b) Sulfonation with Chlorosulfonic Acid [13]. Chlorosulfonic acid (CSA) is used in batch or continuous processes for the production of sulfates or ether sulfates on a relatively small scale: ROH ⫹ ClSO3H → ROSO3H ⫹ HCl The HCl must be removed by degassing and absorbing; the sulfonic acid ester can be neutralized with the desired bases. This chemistry requires glass-lined steel or glass equipment. In contrast to falling-film reactors, the sulfation equipment takes less space and investment. The costs and handling of CSA are disadvantageous compared with those of sulfur trioxide. (c) Sulfonation with Amidosulfonic Acid (‘‘Sulfamic Acid’’). Amidosulfonic acid is a relatively seldom used sulfation agent. It is used, for example, to sulfate alkylphenol derivatives to avoid ring sulfonation byproducts: C12H25 –C6H4 –(O–CH2 –CH2)6 –OH ⫹ H2NSO3H → C12H25 –C6H4 –(O–CH2 –CH2)6 –OSO3 NH4 Another example is the production of aliphatic ether sulfates [14]. 1. Alkylarylsulfonates [10–12,15,16] Linear alkylbenzene sulfonates (LABSs, LASs) or general alkylbenzene sulfonates (ABSs) have a long history, going back to the 1930s. Using a Friedel-Crafts reaction of olefins with benzene in the presence of either aluminum chloride or hydrogen fluoride made alkylbenzene an economically attractive raw material for the synthesis of this class of anionic surfactant, which developed into the ‘‘workhorse’’ of detergents. The first market product was tetrapropylenebenzenesulfonate (TPS) derived from ␣-dodecylene synthesized by tetramerization of propylene, giving a branched alkyl chain. Because of the insufficient biological degradability of the highly branched alkyl chain, which led to contamination of surface waters, TPS was replaced by the biologically more degradable LAS. The linear alkylbenzene is structurally a nonuniform product. The most common product has a carbon number range of the alkyl chain from C10 to C13 (Scheme 1). The phenyl isomer distribution occurring therein is determined by the choice of catalyst. With use of AlCl3, the content of 2-phenyl isomers is approximately 30% in mixture with 3-, 4-, 5-, and other phenyl isomers. In products of HF-catalyzed reaction, the content of 2phenyl isomers is significantly lower at about 20%.


5

SCHEME 1

The sulfonation of alkylbenzenes [17–21] can be handled with oleum, sulfuric acid, or gaseous sulfur trioxide. The sulfonate group is introduced into the benzene ring primarily in the p-position. The process may be operated as either a batch or continuous process. The industrial sulfonation of LAB is accomplished today frequently with SO3 in multitube fallingfilm reactors on a highly economical scale. The continuous sulfonation of alkylbenzene sulfonates is carried out at 40–50⬚C with a molar excess of 1–3% sulfur trioxide, diluted to 5–7 vol% in dry air. During the sulfonation step, the desired sulfonic acids are not the only products. Anhydrides, called pyrosulfonic acids, are also formed as by-products (Scheme 2). The content of alkylbenzenesulfonic acid can be increased with a postreaction (aging) step, which is necessary for a sufficient degree of sulfonation (Scheme 3). During aging, the pyrosulfonic acids can react with further alkylbenzene, sulfuric acid, or traces of water, increasing the content of alkylbenzenesulfonic acid. Another undesirable side reaction is the formation of sulfones, which are part of the ‘‘free oil’’ content of

LAS (Scheme 4). The reaction mixture is neutralized with sodium hydroxide solution. Aqueous pastes with up to 60% active substance content can be produced (Scheme 5). Other side reactions, for example, oxidation, whose chemistry is hard to state more precisely, give dark-colored by-products that can require bleaching of the aqueous LAS paste. Unlike other sulfonation or sulfation products, the crude alkylbenzenesulfonic acid, although very corrosive, can be stored in the acid form. The anhydrides are converted to alkylbenzenesulfonic acid by addition of 1–2% water at 80⬚C in order to stabilize the product. LAS is a good soluble anionic surfactant mainly for use in detergents [22]. It is moderately sensitive to water hardness. Most formulations contain surfactant mixtures in order to decrease sensitivity to water hardness and to enhance foam stability. The combinations are, for example, LAS with alkyl(ether) sulfates and/or noinionics. LAS is completely biodegradable under aerobic conditions, resulting in high environmental safety. Degradation under anaerobic conditions (the relevance of which has been controversial [23–31]) is, as for sulfonate structures, poor. As LAS is and will continue to be the major component of detergent systems because of its good price/efficiency ratio, more environmental data are available for it than for any other surfactant (European Center for Ecotoxicology and Toxicology of Chemicals, ECETOC Technical Report No. 51, Brussels, 1992). The processing of LAS toward compact detergent powders will have to be revised because of the sticky behavior of water-free products. Combinations of LAS

SCHEME 2

SCHEME 3

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Behler et al.

SCHEME 4

with alkyl sulfates are already employed because of the good crystallization of alkyl sulfates. Extension of the application of LAS to cosmetics was suggested by the use of the milder Mg salts [32]. 2.

Aliphatic Sulfonates

(a) Alkane Sulfonates. Sulfoxidation and sulfochlorination are the core technologies for the preparation of alkane sulfonates. Sulfoxidation, the older process, is more important than sulfochlorination. Sulfoxidation. Sulfoxidation [33–37] is a photochemically induced process starting with sulfur dioxide, oxygen, and an n-alkane, normally in the range C12 –C18 or C14 –C17. The radical chain reaction gives many isomers with mainly secondary sulfonate groups. The following sequence explains the reaction steps: h␯

SO2 ⫹ RH

→ R• ⫹ HSO2

R• ⫹ SO2

→ RSO2•

RSO2• ⫹ O2

→ RSO2OO•

RSO2OO• ⫹ RH

→ RSO2OOH ⫹ R•

UV

RSO2OOH ⫹ SO2 ⫹ OH2 → RSO3H ⫹ H2SO4 In practice, a paraffin-water mixture is contacted with SO2 gas and oxygen at 30–40⬚C under irradiation with ultraviolet (UV) lamps. The process is run with an excess of paraffin in order to avoid the formation of multisubstituted products. The excess of paraffin can be removed from the reaction mixture after cooling (with a separator) and can be recycled. Different work-up procedures have been established: the ‘‘Hoechst Light Water Technology’’ and the Hu¨ls process. Both processes have in common separation and recirculation of the paraffin from the crude reaction product by extraction. Also, the sulfur dioxide can be removed by degassing and washing in order to be recycled. The sulfuric acid can be separated by phase separation or extraction.

The final product has to be bleached and neutralized, giving a yellowish paste with about 65% active matter. Sulfochlorination. The sulfochlorination technology [37,38] is used for the conversion of paraffins or alkanes to alkane sulfonates. In a photochemically induced reaction, the paraffin is contacted by dry sulfur dioxide and chlorine: h␯ (>400 nm)

RH ⫹ SO2 ⫹ Cl2 → RSO Cl ⫹ HCl 2 20–40⬚C The resulting sulfochloride is a mixture of approximately 94% mono- and 6% disulfochloride. In a subsequent hydrolysis step with NaOH solution at 80⬚C, the sulfonates are formed: R — SO2Cl ⫹ 2NaOH → R — SO3Na ⫹ NaCl Alkane sulfonates are highly soluble surfactants and are preferably used in liquid products or concentrates. The trend to use renewable raw materials has reduced their use in household products to some extent. Typical applications are in detergents, personal care products, cleaners, and dishwashing detergents. As is common to all sulfonates, alkane sulfonates are easily biodegradable under aerobic conditions [39] but fail under anaerobic conditions. (b) Olefin Sulfonates. Alpha olefin sulfonates (AOSs) [40,41] are, in contrast to internal olefin sulfonates (IOSs), the most important products of this class. AOSs are mainly based on C12 –C18 alpha-olefins derived from ethylene oligomerization (Ziegler process). There is considerable interest in this class of surfactants today because they are derived from lowpriced raw materials coupled with an inexpensive sulfonation process. The most important sulfonation process works with SO3 (Fig. 3), which adds in the primary step to the double bond of the olefin, giving a ring-structured sultone intermediate. Through different reaction steps of sultone formation, elimination, rearrangements, transi-

SCHEME 5


7

FIG. 3

Sulfonation of ␣-olefins with gaseous SO3.

tions, and hydrolysis, a mixture of hydroxyalkane sulfonates and alkene sulfonates is obtained in a ratio of 30:70. As far as surfactant properties are concerned, the alkenyl sulfonate is the more desirable structure. In any event, bleaching of the final product is necessary because of oxidation side reactions. Because of the discussion of sultone intermediates [42], the use of AOS was limited. Through modern analytical methods, the sultones can be quantified, and the production process has been modified by adding a hydrolysis step, so that sultones need not be mentioned as a noteworthy component of AOS. The product can be regarded as safe for the consumer and the environment. AOS with a C14–16 alkyl chain is better foaming than C16–18 AOS. The sulfonate group gives high stability over a wide pH range. AOS is sensitive to water hardness. Typical applications are in detergents, shampoos, and cleansers [43–47].

␣-Sulfo fatty acid methyl esters (MESs). Starting materials for ␣-sulfo fatty acid esters are fatty acid methyl esters, which are available from the transesterification of natural oils and fats. This low refined oleochemical raw material is sulfonated with SO3/air. Ester sulfonates [48–59] are economically interesting surfac-

tants, showing good detergency for the C16 –C18 MES event at low temperatures. The sulfonation is quite a complex reaction (Scheme 6). Beside the desired ester sulfonate, MES contains methyl sulfate, ␣-sulfo fatty acids, and soap in amounts that depend on the manufacturing process. The first step is the insertion of SO3 into the ester linkage (Fig. 4). The primary reaction product, a mixed anhydride, can take up a second molecule of SO3 via its enol form. The anhydride carrying two SO3 units can lose one SO3, which can react with another molecule of methyl ester. This ‘‘storage’’ of SO3 is the reason for the necessary excess of SO3 in this sulfonation reaction. The whole reaction sequence takes more time than is available with a falling-film reactor. Therefore, in order to achieve a high degree of sulfonation, aging is necessary. During the subsequent neutralization, the inter-

SCHEME 6

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FIG. 4

Reaction mechanisms of the sulfonation of esters.

mediate anhydride of the ␣-sulfo acid is hydrolyzed to the disodium salt. To avoid this, hydrolysis of the ␣sulfo acid anhydride with methanol is carried out. To achieve good color, bleaching of the sulfonic acid with hydrogen peroxide is necessary. The color of MES is dependent on the ester raw material. Raw materials with low iodine values (1–100 mg/L). For wastewater bacteria, these substances are minimally toxic. According to their commercial importance, some toxicological data are presented for coco betaines, cocoamidopropyl betaines, and cocoamphoacetates [240– 242]. The results are summarized in Table 4. More detailed toxicological information for cocoamidopropyl betaine is published in Ref. 243. Whereas the ecological data indicate good environmental tolerance, the toxicological findings seem to reveal deficits with regard to skin and eye irritation values. These disadvantages, however, arise only at higher concentrations that do not conform to the practice. More important for a toxicological evaluation is the fact that amphoterics are usually combined with anionic surfactants, i.e., alkyl or alkyl ether sulfates. Besides other synergies, such blends have been found to be very mild to skin and mucous membranes [244– 246].

REFERENCES 1. 2.

3. 4. 5. 6. 7. 8. 9. 10. 11. 12. 13. 14. 15. 16. 17. 18. 19. 20.

J. Davidsohn et al., Soap Manufacture, Vol. 1, Interscience Publishers, New York, 1953, p. 1. K. Heyns and L. Basejewicz, Tetrahedron 9:67 (1960); K. Heyns and H. Paulsen, Angew. Chem. 69:600 (1957); H. Fiege and K. Wedemeyer, Angew. Chem. 93:812 (1981). H. A. Bruson, Org. Reactions 5:79 (1949). R. V. Christian and R. M. Hixon, J. Am. Chem. Soc. 70:1333 (1948). C. S. Hsia Chen, Org. Chem. 27:1920 (1962). G. Czichocki et al., Fat Sci. Technol. 94:66 (1992). A. Turowski, W. Skrypzak, A. K. Reng, and P. Ju¨rges, Parfum. Kosmet. 76:16 (1995). L. Leusink and C. Broer, Seifen Ole Fette Wachse 119: 810 (1993). H. Meijer, Chem. Ind. 40(4):58 (1988). W. H. de Groot, Kluwer Academic Publishers, Dordrecht, 1991. G. F. Moretti and I. Adami, Riv. Ital. Sostanze Grasse 75(3):143–153 (1998). D. W. Roberts, Org. Process Res. Dev. 2(3):194–202 (1998). F. J. Gohlke and H. Bergerhausen, Soap Chem. Spec. 43(10):47–49, 62, 113, 186 (1967). A. Zhu and W. Lin, Riyong Huaxue Gongye Issue 1: 13–15 (1997). K. S. Parasuram, Chem. Petrochem. J. 8(11):9–13 (1977). J. Falbe, Surfactants in Consumer Products, SpringerVerlag, Berlin, 1987. D. W. Roberts, R. S. Ward, and P. J. Hughes, J. Surfactants Deterg. 1(2):161–165 (1998). J. Jensen, Sci. Total Environ. 226(2,3):93–111 (1999). L. Cohen, Tenside Surfactants Deterg. 34:332–335 (1997). D. W. Roberts and J. O. Morley, Comun. J. Com. Esp. Deterg. 27:145–157 (1997).

40 21.

22. 23. 24. 25. 26.

27.

28. 29. 30. 31.

32. 33.

34. 35. 36. 37. 38. 39. 40. 41.

42.

43. 44. 45.

Behler et al. N. M. Rockwell and Y. K. Rao, Proc. World Conf. Lauric Oils: Sources, Process. Appl., 1994, pp. 138– 146. D. W. Roberts, Org. Process Res. Dev. 2(3):194–202 (1998). E. Gonzalez-Mazo, J. M. F. Pajares, and A. GomezParra, Environ. Sci. Technol. 32:1636–1641 (1998). F. Hirsinger, Chim. Oggi 16(10):62–66 (1998). U. Schoenkaes, Chim. Oggi 16(9):9–13 (1998). D. Prats, F. Ruiz, M. Rodriguez, P. Varo, and M. C. Garcia, Comun. J. Com. Esp. Deterg. 25:171–185 (1994). J. S. Leal, M. T. Garcia, R. Tomas, J. Ferrer, and C. Bengoechea, Tenside Surfactants Deterg. 31:253–256 (1994). P. Schoeberl, H. Klotz, R. Spiker, and L. Nitschke, Tenside Surfactants Deterg. 31:243–252 (1994). R. Fellows and F. W. Heywood, Spec. Publ. R. Soc. Chem. 107(Ind. Appl. Surfactants III):63–81 (1992). F. R. Schroeder, M. Schmitt, and U. Reichensperger, Waste Manage. (Oxf.) 19(2):125–131 (1999). D. C. McAvoy, S. D. Dyer, N. J. Fendinger, W. S. Eckhoff, D. L. Lawrence, and W. M. Begley, Environ. Toxicol. Chem. 17:1705–1711 (1998). L. Cohen, A. Moreno, and J. L. Berna, Tenside Surfactants Deterg. 35:265–269 (1998). I. Stanciu, L. Papahagi, R. Avram, C. Cristescu, I. Duta, and D. Savu, Rev. Chim. (Bucharest) 41:885– 888 (1990). J. M. Quack and M. Trautmann, Tenside Deterg. 22: 281–289 (1985). H. Ramloch and G. Taeuber, Chem. Unserer Zeit 13(5):157–162 (1979). C. Beermann, Eur. Chem. News Norm. Paraffins Suppl. 36–7:39–40 (1966). J. Perkowski and J. S. Miller, Pol. Przem. Chem. 66(1):9–13 (1987). H. I. Joschek, Chem. Ztg. Chem. Appar. 93:655–664 (1969). H. Berenbold and K. Kosswig, Tenside Surfactants Deterg. 32:152–154, 156 (1995). R. Stephan, Tenside Surfactants Deterg. 35:338–341 (1998). N. M. Van Os, R. Van Ginkel, A. Van Zon, F. W. Heywood, E. L. Berryman, and J. K. Borchardt, Surfactant Sci. Ser. 56(Anionic Surfactants):363–454 (1996). D. W. Roberts, J. G. Lawrence, I. A. Fairweather, C. J. Clemett, and C. D. Saul, Tenside Surfactants Deterg. 27:82–86 (1990). E. Spiess, Pollena Tluszcze Srodki Piorace Kosmet. 34(1–2):30–37 (1990). S. K. Friedman, G. Barker, and M. Mausner, Soap Cosmet. Chem. Spec. 59(9):35–36, 53 (1983). G. Schneider, Seifen Ole Fette Wachse 95:970–974 (1969).

46. 47. 48.

49. 50. 51. 52.

53. 54. 55.

56. 57. 58.

59.

60.

61. 62. 63. 64.

65. 66. 67. 68. 69. 70. 71.

S. K. Suri, M. S. Thakur, and S. Bhardwaj, J. Am. Oil Chem. Soc. 70(1):59–64 (1993). R. Stephan, Tenside Surfactants Deterg. 35:338–341 (1998). T. Ogushi, S. Matuura, S. Horie, and T. Maeda, Chuo Daigaku Rikogaku Kenkyusho Ronbunshu 3:49–58 (1998). M. Nakamura and K. Oba, Nihon Yukagakkaishi 46: 957–967 (1997). Y. K. Rao and B. Sajic, World Surfactants Congr. 4th 2:383–391 (1996). M. J. Schwuger and H. Lewandowski, Surfactant Sci. Ser. 74(Novel Surfactants):139–177 (1998). D. W. Roberts, C. J. Clemett, C. D. Saul, A. Allan, and R. A. Hodge, Comun. J. Com. Esp. Deterg. 26: 27–33 (1995). M. Fujiwara and T. Okano, Fragrance J. 23(4):81–86 (1995). T. Satsuki, K. Umehara, and Y. Yoneyama, J. Am. Oil Chem. Soc. 69:672–677 (1992). T. Inagaki, in Proc. World Conf. Oleochem. (T. H. Applewhite, ed.), AOCS, Champaign, IL, 1991, pp. 269–278. M. Nakamura and K. Oba, Nihon Yukagakkaishi 46: 957–967 (1997). H. Baumann, Fett. Wiss. Technol. 92(2):49–56 (1990). T. Satsuki, Annu. Surfactants Rev. 1(New Products and Applications in Surfactant Technology):132–155 (1998). J. Drozd, in Proc. World Conf. Oleochem. (T. H. Applewhite, ed.), AOCS, Champaign, IL, 1991, pp. 256–268. A. Domsch and B. Irrgang, in Anionic Surfactants (H. W. Stache, ed.), Surfactant Science Series, Vol. 56, Marcel Dekker, New York, 1995, p. 501. J. A. Milm, R. Soc. Chem. (Ind. Appl. Surf.) 77:76 (1990). A. J. O’Lenick, Jr. and W. C. Smith, Soap Cosmet. Chem. Spec. 64:36 (1988). T. Schoenberg, Cosmet. Toiletries 105:105 (1989). K. Lindner, in Tenside Textilhilfsmittel Waschrohstoffe, Vol. 1, Wissenschaftliche Verlagsgesellschaft, Stuttgart, 1964, p. 747. W. Ka¨stner and P. J. Frosch, Fette Seifen Anstrichm. 83:33 (1981). J. Valee´, Parfum. Cosmet. Savons 4:205 (1961). G. Gawalek, in Tenside, Akademie Verlag, Berlin, 1975, p. 232. X. Domingo, Surfactant Sci. Ser. 56(Anionic Surfactants):223–312 (1996). A. Syldath and K. H. Schmid, World Surfactants Congr. 4th 1:339–344 (1996). S. Tagata, A. Ishikawa, and H. Hayashi, Chim. Oggi 14(5):11–15 (1996). J. Steber, P. Gode, and W. Guhl, Fett Wiss. Technol. 90(1):32–38 (1988).

Industrial Surfactant Syntheses 72.

73. 74. 75. 76. 77.

78. 79. 80. 81. 82. 83. 84. 85. 86. 87. 88. 89. 90. 91. 92. 93. 94. 95. 96. 97. 98. 99.

100.

Cambridge, MA, USA. Report (1991), Issue ADLREF-65913-VOL-1-PT-3; Order No. PB91-214015, 110 pp. Avail. NTIS. From: Gov. Rep. Announce. Index (U.S.) 1991, 91(20), Abstr. No. 155,700. J. P. Sisley, Am. Dyestuff Rep. 43:741 (1954). J. Ross, U.S. Patent 2,693,479 to Colgate-Palmolive Company (1950). J. K. Fincke, U.S. Patent 2,634,287 to Monsanto (1948). F. W. Grag, U.S. Patent 2,979,521 to Colgate-Palmolive Company (1958). (a) G. Gawalek, in Tenside, Akademie-Verlag, Berlin, 1975, p. 171; (b) M. Linfield, ed., Anionic Surfactants, Surfactant Science Series, Vol. 7, Marcel Dekker, New York, 1976, p. 219. K. Yamashita et al., JP 50/70322 to Wako Pure Chemical Ind. (1975). M. Shinohara, JP 78/77014 to Riken Vitamin Oil (1975). H. Stu¨hler, EP 267,518 to Hoechst AG (1987). F. Ahmed et al., DE 3,831,446 to Colgate-Palmolive Company (1988). A. Behler et al., DE 4,038,477 to Henkel KGaA (1990). U. Zeidler, J. Soc. Cosmet. Chem. Jpn. 20:17 (1986). A. Straw et al., GB 2031455 to Colgate-Palmolive Company (1978). F. Ahmed, EP 318729 to Colgate-Palmolive Company (1989). H. Raaf et al., DE 2440802 to Blendax Werke Schneider (1974). W. J. King et al., U.S. Patent 3956478 to ColgatePalmolive Company (1975). R. Zimmerer and R. Berg, EO 18019 to Procter & Gamble Company (1979). A. Takahashi et al., JP 84/040940 to Lion Corp. (1984). Y. Yamazaki, JP 85/161920 to Lion Corp. (1990). I. D. Hill, U.S. Patent 4942034-A to Hill ID (1990). S. Mitsyama, JP 03,153,796 to Tamanohada Soap Co., Ltd. (1991). H. Takahashi et al., JP 85/269,578 to Sanyo Chem. Ind. Ltd. (1987). K. Tsubone, JP 90/28099 to Kaneboo KKK (1990). J. Shiomi, JP 93/95493 to Mandamu KK (1994). A. Behler et al., WO 95/06702 to Henkel KGaA (1993). W. Breitzke and A. Behler, DE 4328355 to Henkel KGaA (1993). W. Breitzke and A. Behler, DE 4406748 to Henkel KGaA (1994). J. K. Weil and A. J. Stirton, in Anionic Surfactants (W. M. Linfield, ed.), Surfactant Science Series, Vol. 7, Marcel Dekker, New York, 1976, pp. 224–230. R. G. Bistline, Jr., in Anionic Surfactants (H. Stache, ed.), Surfactant Science Series, Vol. 56, Marcel Dekker, New York, 1995, pp. 633–634.

41 101. 102.

103. 104. 105. 106. 107. 108. 109. 110.

111. 112.

113. 114. 115. 116. 117. 118. 119. 120. 121. 122. 123. 124. 125. 126.

127.

A. K. Reng, Parfuem. Kosmet. 61:87 (1980). (a) J. K. Weil, N. Parris, and A. J. Stirton, J. Am. Oil Chem. Soc. 47:91 (1970); (b) M. Fukuda and T. Tamura, JP 62001448 to Lion Corp. (1987). A. Fujio et al., JP 7070047 to Kao Corp. (1995). A. El-Sawy, S. A. Essawy, M. M. El-Sukkary, and A. M. F. Eissa, Hung J. Ind. Chem. 20:25 (1992). R. G. Bistline, Jr., W. R. Noble, F. D. Smith, and W. M. Linfield, J. Am. Oil Chem. Soc. 54:371 (1977). M. Yoshio, S. Etsuo, and H. Yasushi, JP 55149243 to Nippon Oils and Fats (1980). M. A. Podustov et al., SU 1051068 to Kharkov Polytechnic Institute (1983). M. A. Podustov et al., SU 1544769 to Kharkov Polytechnic Institute (1990). A. K. Reng and J. M. Quack, Seifen Ole Fette Wachse 102:307 (1976). (a) A. Turowski, W. Skrypzak, A. K. Reng, and P. Ju¨rges, Parfuem. Kosmet. 76:16 (1995); (b) J. Bohunek, G. Taüber, and H. Berghausen, DE 1815657 to Farbwerke Hoechst AG (1968). G. Crass, Tenside Surfactants Deterg. 30:408 (1993). (a) T. Konekiyo et al., JP 1016898 to Mitsubishi Petrochemical Co. (1989); (b) P. Goffinet and R. Canaguier, EP 189687 to Union Generale de Savonnerie (1986). F. Hironobu, K. Fumitaka, and M. Yoshio, JP 58015501 to Nippon Oils and Fats (1983). H. H. Friese, U. Ploog, and F. Pieper, DE 3419405 to Henkel KGaA (1985). R. Prather, U.S. Patent 4376088 to Upjohn Company (1983). G. D. Kudinova et al., SU 1151470 to Belorussian Technological Institute (1985). A. Yamamoto, Y. Arimoto, and M. Konno, BE 902736 to Chemical Works Company (1985). P. J. Petter, Int. J. Cosmet. Sci. 6(5):249–260 (1984). W. C. Allison and J. E. Neibaur, Household Pers. Prod. Ind. 32(5):92, 94, 96, 98, 100 (1995). J. H. Kim, T.-Y. Kim, M.-J. Ju, and K.-D. Nam, Kongop Hwahak 7(3):401–409 (1996). K. Miyazawa and U. Tamura, Cosmet. Toiletries 108(3):81–86 (1993). H. Xu, F. Chen, and S. Wang, Huadong Ligong Daxue Xuebao 23:720–724 (1997). L. Daradics and J. Palinkas, Tenside Surfactants Deterg. 31:308–313 (1994). M. M. A. El-Sukkary, M. A. Salama, and D. A. Ismail, Al-Azhar Bull. Sci. 3:619–624 (1992). J. J. Crudden and J. V. Lazzaro, Cosmet. Exhib. Conf. Conf. Proc., 1994, pp. 351–391. A. George, J. Modi, N. Jain, and P. Bahadur, Indian J. Chem. Sect. A Inorg., Bioinorg. Phys. Theor. Anal. Chem. 37A:985–992 (1998). B. Aha, M. Berger, B. Haase, J. Hermann, O. Keil, G. Machmu¨ller, S. Mu¨ller, C. Waldinger, and M. Schnei-

42

128. 129. 130. 131. 132.

133. 134. 135.

136. 137. 138.

139. 140. 141. 142. 143. 144. 145.

146. 147.

148. 149. 150.

Behler et al. der, Schriftenr. Bundesminist. Ernaehr. Landwirtsch. Forsten Reihe A: Angew. Wiss. (1997), Sonderh. (5. Symposium Nachwachsende Rohstoffe: Perspektiven fuer di Chemie, 1997), pp. 66–78. S. Y. Mhaskar, R. B. N. Prasad, and G. Lakshminarayana, J. Am. Oil Chem. Soc. 67:1015–1019 (1990). K. Scha¨fer, J. Wirsching, and H. Hocker, Fett/Lipid 99(6):217–222 (1997). D. B. R. T. Braun, Cosmet. Toiletries 104(9):87–89, 92–94, 96 (1989). C.-C. Kwan and S.-T. Lin, Sci. Conf. Asian Soc. Cosmet. Sci. 3rd, 1997, pp. 266–270. K. Berendes, S. Mu¨ller, and M. Schneider, Schriftenr. Nachwachsende Rohstoffe 10(Biokonversion nachwachsender Rohstoffe):246–252 (1998). H. Hensen and J. Kahre, Seifen Ole Fette Wachse J. 124:806, 808–810, 812, 814–815 (1998). A. Sander, E. Eilers, A. Heilemann, and E. Von Kries, Germany. Fett/Lipid 99(4):115–120 (1997). A. Behler, K.-H. Hill, A. Kusch, S. Podubrin, H.-C. Raths, and G. Uphues, in Nonionic Surfactants (N. M. van Os, ed.), Surfactant Science Series, Vol. 72, Marcel Dekker, New York, 1998, pp. 259 ff. W. Skrypzak, A. K. Reng, and J. M. Quack, Parfuem. Kosmet. 60:317 (1979). T. Kurosaki and A. Manbu, DE 3,047,378 to Kao Soap Company (1979). K. Sasse, in Methoden der Organischen Chemie (E. Mu¨ller, ed.), Thieme, Stuttgart, 1940, Vol. 12/2, p. 143. G. Uphues and U. Ploog, EP 0,272,568 to Henkel KGaA (1987). C. L. Edwards, Surfactant Sci. Ser. 72(Nonionic Surfactants):87–121 (1998). H.-C. Raths, Third CESIO International Surfactants Congress and Exhibition, London, June 1992. E. Santacesaria, M. Di Serio, and R. Garaffa, Ind. Eng. Chem. Res. 31:2413–2418 (1992). D. Schmedding and V. L. Tatum, Int. Environ. Conf. Exhib. Bk. 1:461–471 (1998). D. T. Bennie, Water Qual. Res. J. Can. 34(1):79–122 (1999). C.-D. Hager, UK Annu. Surfactants Rev. 1(New Products and Applications in Surfactant Technology):1–29 (1998). B. Fell, Tenside Surfactants Deterg. 35:326–337 (1998). I. Kirshenbaum and E. J. Inchalik, in Kirk-Othmer Encyclopedia of Chemical Technology, 3rd ed., Vol. 16 (M. Grayson and D. Eckroth, eds.), John Wiley & Sons, New York, 1981, pp. 637–653. P. I. Bhuva, Chem. Age India 38(3):101–109 (1987). P. H. Washecheck, ACS Symp. Ser. 159(Monohydric Alcohols):87–100 (1981). M. F. Gautreaux, W. T. Davis, and E. D. Travis, in Kirk-Othmer Encyclopedia of Chemical Technology,

151. 152. 153. 154. 155.

156. 157. 158. 159.

160. 161.

162. 163. 164. 165. 166.

167. 168. 169. 170. 171. 172. 173.

174. 175.

3rd ed., Vol. 1 (M. Grayson and D. Eckroth, eds.), John Wiley & Sons, New York, 1978, pp. 740–754. R. Aveyard, B. P. Binks, S. Clark, and P. D. Fletcher, J. Chem. Technol. Biotechnol. 48(2):161–171 (1990). J. Szymanowski, Tenside Surfactants Deterg. 26:198– 210 (1989). L. Marszall, Surfactant Sci. Ser. 23(Nonionic Surfactants):493–547 (1987). T. Foerster, Surfactant Sci. Ser. 68(Surfactants in Cosmetics (2nd Edition)):105–125 (1997). A. Wadle, H. Tesmann, M. Leonard, and T. Fo¨rster, Surfactant Sci. Ser. 68(Surfactants in Cosmetics (2nd Edition)):207–224 (1997). T. Balson and M. S. B. Felix, Biodegrad. Surfactants 204–230 (1995). M. Trautmann and P. Ju¨rges, Tenside Deterg. 21:57 (1984). D. N. Bhattacharyya, S. Krishnan, R. Y. Kelkar, and S. V. Chikale, J. Am. Oil Chem. Soc. 61:1925 (1984). T. C. Rao, Y. Sita Rama Sastry, R. Subbarao, and S. Lakshminarayana, J. Am. Oil Chem. Soc. 54:15 (1977). H. Grossmann, Tenside Surfactants Deterg. 12:16 (1975). K. Kosswig, in Nonionic Surfactants (N. M. van Os, ed.), Surfactant Science Series, Vol. 72, Marcel Dekker, New York, 1998, p. 123. G. Seipel, F. Wolf, and K. Lo¨ffler, Tenside Surfactants Deterg. 5:132 (1968). M. F. Cox and U. Weerasooriya, J. Surfactants Deterg. 1:11 (1998). I. Hama, H. Sasamoto, and T. Okamoto, J. Am. Oil Chem. Soc. 74:817 (1997). I. Hama, M. Sakaki, and H. Sasamoto, J. Am. Oil Chem. Soc. 74:829 (1997). A. Behler, B. Guckenbiehl, and H.-C. Raths, Proceedings of the 87th AOCS Annual Meeting, Indianapolis, AOCS, Champaign, IL, 1996, p. 79. A. Behler, B. Guckenbiehl, and H.-C. Raths, Tenside Surfactants Deterg. 33:64 (1996). I. Hama, T. Okamoto, E. Hidai, and K. Yamada, J. Am. Oil Chem. Soc. 74:19 (1997). I. Hama, M. Sakaki, and H. Sasamoto, J. Am. Oil Chem. Soc. 74:823 (1997). M. F. Cox and U. Weerasoorya, J. Am. Oil Chem. Soc. 74:847 (1997). I. Hama, H. Sasamoto, T. Tamura, T. Nakamura, and K. Miura, J. Surfactants Deterg. 1:93 (1998). K. Mu¨ller, Tenside Surfactants Deterg. 3:37 (1966). A. Domsch and C. Mo¨ller, Cosmetics Conference Proceedings 1997, Du¨sseldorf, Verlag fu¨r Chemische Industrie, H. Ziolkowsky GmbH, pp. 258–273. E. Santacesaria, M. Diserio, R. Garaffa, and G. Addino, Ind. Eng. Chem. Res. 31:2413 (1992). B. Bartha, L. Farkas, J. Morgos, P. Sallay, I. Rusznak, and G. Veress, J. Am. Oil Chem. Soc. 58:650 (1981).

Industrial Surfactant Syntheses 176. 177. 178.

179. 180. 181. 182. 183. 184. 185.

186.

187.

188.

189.

190. 191.

192.

M. Cuscurida and E. L. Yeakey, U.S. Patent 5,103,062 to Texaco Chemical Company (1992). J. F. Knifton and C. G. Naylor, U.S. Patent 5,344,984 to Texaco Chemical Company (1994). M. D. Hoey and J. F. Gadberry, in Surfactant Science Series, Vol. 72 (N. M. van Os, ed.), Marcel Dekker, New York, 1998, pp. 163–175. D. P. Bauer and T. K. Summerford, EP 0,320,694 to Ethyl Corp. (1989). K. S. Laurenzo and D. P. Bauer, U.S. Patent 4,889,954 to Ethyl Corp. (1989). K. S. Laurenzo, EP 0,356,918 to Ethyl Corp. (1990). K. S. Laurenzo and J. D. Sauer, U.S. Patent 4,942,260 to Ethyl Corp. (1990). H. Roerig and R. Stephan, Riv. Ital. Sostanze Grasse 68(6):317–321 (1991). Y. Hayashi, F. Shirai, T. Shimizu, Y. Nagano, and K. Teramura, J. Am. Oil Chem. Soc. 62:555 (1985). N. Baggett, in Comprehensive Organic Chemistry (J. F. Stoddart, ed.), Vol. 2, Pergamon Press, Oxford, 1979, p. 843. (a) J. Falbe, ed., Surfactants in Consumer Products— Theory, Technology and Application, Springer, Berlin, 1986; (b) H. Baumann and M. Biermann, in Nachwachsende Rohstoffe, Perspektiven fu¨r die Chemie (M. Eggersdorfer, S. Warwel, and G. Wulff, eds.), VCH, Weinheim, 1993, pp. 33–55. (a) P. Schulz, Chim. Oggi 33 (1992); (b) M. Biermann, K. Schmid, and P. Schulz, Starch/Starke 45:281 (1993); (c) W. Ruback and S. Schmidt, in Carbohydrates as Organic Raw Materials III (H. van Bekkum, H. Ro¨per, and A. G. J. Vorhagen, eds.), VCH, Weinheim, 1996, pp. 231–253; (d) B. Brancq, Seifen Ole Fette Wachse J. 118:905 (1992). (a) M. Biermann, F. Lange, R. Piorr, U. Ploog, H. Rutzen, J. Schindler, and R. Schmid, in Ref. 16, pp. 23–132; (b) S. Ropuszynski and E. Sczesna, Tenside Surfactants Deterg. 27:350 (1990); (c) S. Ropuszynski and E. Sczesna, Tenside Surfactants Deterg. 22:190 (1985). (a) N. B. Desai, Cosmet. Toiletries 105:99 (1990); (b) S. Nakamura, INFORM 8:866 (1997); (c) K. Hill, J. Falkowski, S. Biermann, and C. Brand, DE 4212155 (1992), Henkel KGaA, Zucker-Aktiengesellschaft Uelzen-Braunschweig in Uelzen, Chem. Abstr. 120: 194484 (1994). E. Fischer, Ber. Dtsch. Chem. Ges. 26:2400 (1893). (a) P. Ju¨rges and A. Turowski, in Perspektiven Nachwachsender Rohstoffe in der Chemie (H. Eierdanz, ed.), VCH, Weinheim, 1996, pp. 61–70; (b) H. Kelkenberg, Tenside Surfactants Deterg. 25:8 (1988). (a) K. Hill, W. von Rybinski, and G. Stoll, eds.), Alkyl Polyglycosides—Technology, Properties and Applications, VCH, Weinheim, 1997; (b) W. von Rybinski and K. Hill, in Novel Surfactants, Preparations, Applications, and Biodegradability (K. Holmberg, ed.), Mar-

43

193.

194.

195.

196.

197.

198. 199. 200. 201.

202.

203. 204. 205. 206.

cel Dekker, New York, 1998, pp. 31–85; (c) D. E. Koeltzow and A. D. Urfer, J. Am. Oil Chem. Soc. 61: 1651 (1984); (d) A. J. J. Straathof, H. van Bekkum, and A. P. G. Kieboom, Starch/Starke 40:438 (1988); (e) Th. Bo¨cker and J. Thiem, Tenside Surfactants Deterg. 26:318 (1989). (a) R. G. Laughlin, Y.-C. Fu, F. C. Wireko, J. J. Scheibel, and R. L. Munyon, in Novel surfactants, Preparations, Applications, and Biodegradability (K. Holmberg, ed.), Marcel Dekker, New York, 1998, pp. 1–30; (b) J. J. Scheibel, D. S. Connor, R. E. Shumate, and J. C. T. R. B. St. Laurent, EP-B 0558515, US-A 598462 (1990), Procter & Gamble, Chem. Abstr. 117: 114045 (1992). Colin A. Houston & Associates, Inc., Glucosamides: The challenge of a new sugar-based surfactant, 1993– 1998, June 1996. (a) W. Aulmann and W. Sterzel, in Ref. 192a, pp. 151– 160; (b) W. Matthies, B. Jackwaerth, and H.-U. Kraechter, in Ref. 192a, pp. 169–176; (c) J. Steber, W. Guhl, N. Stelter, and F. R. Schro¨der, in Ref. 192a, pp. 177–188; (d) M. Stalmans, E. Matthies, E. Weeg, and S. Morris, Seifen Ole Fette Wachse J. 119:794 (1993). (a) K. Schmid, in Perspektiven Nachwachsender Rohstoffe in der Chemie (H. Eierdanz, ed.), VCH, Weinheim, 1996, pp. 41–60; (b) H. Andree, J. F. Hessel, P. Krings, G. Meine, B. Middelhauve, and K. Schmid, in Ref. 192a, pp. 99–130. H. Tesmann, J. Kahre, H. Hensen, and B. A. Salka, in Ref. 192a, pp. 71–88; (a) H. Tesmann, J. Kahre, B. A. Salka, Cosmetics and Toiletries Manufacturing Worldwide (1996), pp. 21–33; (b) M. Weuthen, R. Kawa, K. Hill, and A. Ansmann, Fat. Sci. Technol. 97: 209 (1995). R. Garst, in Ref. 192a, pp. 131–138. O. Rhode, M. Weuthen, and D. Nickel, in Ref. 192a, pp. 139–149. Anonymous, Parfums Cosmet. Actual. 139(Feb–Mar): 44 (1998). (a) P. Bernardi, D. Fornara, L. Paglino, and T. Verzotti, The 1st Concise Surfactants Directory, Tekno Science, Milano, 1996, pp. 15–17; (b) Anonymous, Chem. Market. Rep. 17(June):23 (1996). A. Behler, K.-H. Hill, A. Kusch, S. Podubrin, H.-C. Raths, and G. Uphues, in Nonionic Surfactants (N. M. van Os, ed.), Surfactant Sciences Series, Vol. 72, Marcel Dekker, New York, 1998, pp. 273 ff. K. Yahagi, N. Hoshino, and H. Hirota, JFSCC Paper No., 1988, pp. 71 ff. M. Hofinger, H. Stu¨hler, S. Billenstein, H. Berenbold, and J. M. Quack, EP 0,284,036 to Hoechst AG (1987). W. Ruback and J. Schut, EP 0,295,385 to Hu¨ls AG (1987). S. Courdavault Duprat, L. Godefroy, P. Nivollet, D. Ray, Y. Storet, and J.-F. Vindret, EP 0,550,361 to Stepan Europe (1991).

44 207. 208. 209. 210. 211. 212. 213. 214. 215. 216. 217. 218. 219.

220. 221. 222. 223. 224.

225.

Behler et al. A. Domsch, P. Busch, and H. Hensen, Seifen Ole Fette Wachse 114:695 (1988). M. Saiki, Y. Imai, and M. Takagi, EP 0,240,622 to Takemoto Yushi Kabashiki Kaisha (1986). E. Ploetz and H. Ulrich, U.S. Patent 2,127,476 to I.G. Farbenindustrie AG (1938). E. Ploetz and H. Ulrich, U.S. Patent 2,173,069 to I.G. Farbenindustrie AG (1939). G. Demmering, DE 2,052,321 to Henkel KGaA (1970). J. Kolbe, W. Kortmann, and J. Pfeiffer, EP 0,075,770 to Bayer AG (1982). U. Ploog and M. Petzold, DE 3,032,216 to Henkel KGaA (1980). M. Hofinger, A. K. Renk, and J. M. Quack, DE 3,345,156 to Hoechst AG (1983). H. Rutzen, Fette Seifen Anstrichm. 84:87 (1982). O. Manzke, DE 1,618,026 to Wella AG (1967). R. Bimczok, E. D. Racky, and G. Lang, EP 0,747,468 to Wella AG (1995). J. R. Wechsler and M. Lane, U.S. Patent 4,370,272 to Stepan Chemical Company (1981). L. Edebo, B. Ahlstro¨m, S. Allenmark, M. Bertilsson, E. Jennische, S. Lange, M. Lindstedt, and R. A. Thompson, in Industrial Applications of Surfactants (D. R. Karsa, ed.), Royal Society of Chemistry, Cambridge, 1992, pp. 184 ff. S. F. Cancy, M. Thies, and H. Pardies, Chem. Commun. 2035 (1997). K. F. Gallagher, Cosmet. Toiletries Mag. 109(Dec):67 (1994). A. Shansky, Am. Perfum. Cosmet. 84:47 (1969). A. Behler, G. Uphues, and P. Neumann, DE 4,340,423 to Henkel KGaA (1993). C. Weitemeyer, W. Foitzik, H.-D. Ka¨seborn, U. Begoihn, and B. Gru¨ning, DE 4,207,386 to Th. Goldschmidt AG (1992). R. Ernst and E. J. Miller, in Amphoteric Surfactants (B. R. Bluestein and C. L. Hilton, eds.), Surfactant Science Series, Vol. 12, Marcel Dekker, New York, 1982, pp. 71 ff.

226. 227.

228. 229. 230. 231. 232.

233. 234. 235. 236. 237. 238. 239. 240. 241. 242. 243.

244. 245. 246.

V. Bade, EP 0,353,580 to Th. Goldschmidt AG (1989). F. B. Downing and F. W. Johnson, U.S. Patent 2,129,264 to E.I. du Pont de Nemours & Company (1938). P.-J. Derian, EP 0,736,521 to Rhone-Poulenc Chimie (1996). G. Uphues, Fett/Lipid 100:490 (1998). N. Parris, C. Pierce, and W. M. Linfield, J. Am. Oil Chem. Soc. 54:294 (1977). G. Braun, C.-J. Tschang, C. Vamvakiris, and K. Glaser, EP 0,282,908 to BASF AG (1987). M. Lindemann, R. Mayhene, A. O’Lenick, and R. Verdiccio, U.S. Patent 4,215,064 to Johnson & Johnson and Mona Industries Inc. (1978). J. Giersberg and H.-J. Kollmeier, DE 3,826,805 to Th. Goldschmidt AG (1988). H. Hein, H. J. Jaroschek, and W. Melloh, Fette Seifen Anstrichm. 80:448 (1978). G. Schwarz, P. Leenders, and U. Ploog, Fette Seifen Anstrichm. 81:154 (1979). F. D. Smith and W. M. Linfield, J. Am. Oil Chem. Soc. 55:741 (1978). A. F. Isbell, U.S. Patent 2,468,012 to General Mills Inc. (1945). R. G. Freese, U.S. Patent 2,810,752 to General Mills Inc. (1957). D. Aelony, U.S. Patent 2,814,643 to General Mills Inc. (1957). W. Koehl and W. Sterzel, Toxicological Evaluation, Henkel-TTB Report 9700144 (1997). W. Aulmann and W. Sterzel, Toxicological Evaluation, Henkel-TTB Report 9600144 (1996). HELLID data set for 61791-32-0, dated January 19, 1998, Henkel KGaA. Anonymous, Final report on the safety assessment of cocoamidopropyl betaine, J. Am. Coll. Toxicol. 10:33 (1991). K. Klein and O. Bator, Drug Cosmet. Ind. December: 38–42, 76–77 (1981). P. Alexander, Manuf. Chem. August:54–57 (1985). U. Zeidler and G. Reese, Arztliche Kosmetol. 13:39 (1983).

2 Cleavable Surfactants KRISTER HOLMBERG

I.

Chalmers University of Technology, Go¨teborg, Sweden

INTRODUCTION

percentage of the amount of carbon dioxide that could theoretically be produced, is the most important measure of biodegradation. It seems that for most surfactants containing easily cleavable bonds, the value for ultimate decomposition is higher than for the corresponding surfactants lacking the weak bond. Thus, the strong tend toward more environmentally benign products favors the cleavable surfactant approach on two accounts. A second incentive for the development of cleavable surfactants is to avoid complications such as foaming or formation of unwanted, stable emulsions after use of a surfactant formulation. Cleavable surfactants present the potential for elimination of some of these problems. If the weak bond is present between the polar and the nonpolar part of the molecule, cleavage will lead to one water-soluble and one water-insoluble product. Both moieties can usually be removed by standard work-up procedures. This approach has been of particular interest for surfactants used in preparative organic chemistry and in various biochemical applications. A third use of surfactants with limited stability is to have the cleavage product impart a new function. For instance, a surfactant used in personal care formulations may decompose on application to form products beneficial to the skin. Surfactants that impart a new function after cleavage are sometimes referred to as functional surfactants. Finally, surfactants that break down into nonsurfactant products in a controlled way may find use in specialized applications, e.g., in the biomedical field. For instance, cleavable surfactants that form vesicles or mi-

By tradition, surfactants are stable species. Among the surfactant workhorses are: anionics such as alkylbenzene sulfonates and alkyl sulfates, nonionics such as alcohol ethoxylates and alkylphenol ethoxylates, and cationics such as alkyl quats and dialkyl quats; only alkyl sulfates are not chemically stable under normal conditions. Through the years, the susceptibility of alkyl sulfates to acid-catalyzed hydrolysis has been seen as a considerable problem, particularly well known for the most prominent member of the class, sodium dodecyl sulfate (SDS). The general attitude has been that weak bonds in a surfactant may cause handling and storage problems and should therefore be avoided. More recently, the attitude toward easily cleavable surfactants has changed. Environmental concern has become one of the main driving forces for the development of new surfactants and rate of biodegradation has become a major issue. One of the main approaches taken to produce readily biodegradable surfactants is to build into the structure a bond with limited stability. For practical reasons the weak bond is usually the bridging unit between the polar headgroup and the hydrophobic tail of the surfactant, which means that degradation immediately leads to destruction of the surface activity of the molecule, an event usually referred to as the primary degradation of the surfactant. Biodegradation then proceeds along various routes depending on the type of primary degradation product. The ultimate decomposition of the surfactant, often expressed as amount of carbon dioxide evolved during 4 weeks exposure to appropriate microorganisms counted as a 45

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Holmberg

croemulsions can be of interest for drug delivery, provided the metabolites are nontoxic. Most cleavable surfactants contain a hydrolyzable bond. Chemical hydrolysis is either acid or alkali catalyzed, and many papers discuss the surfactant breakdown in terms of either of these mechanisms. In the environment, bonds susceptible to hydrolysis are often degraded by enzymatic catalysis but few papers dealing with cleavable surfactants have dealt with such processes in vitro. Other approaches that have been taken include incorporation of a bond that can be destroyed by ultraviolet (UV) irradiation or use of an ozonecleavable bond. This chapter is subdivided according to the type of weak linkage present in the surfactant. Emphasis is put on the development that has taken place in recent years.

II.

ALKALI-LABILE SURFACTANTS

A.

Normal Ester Quats

By the term ester quat one usually refers to surfaceactive quaternary ammonium compounds that have the general formula R4N⫹X⫺ and in which the long-chain alkyl moieties, R, are linked to the charged headgroup by an ester bond and with X⫺ being a counterion. With normal ester quats one means surfactants based on esters between one or more fatty acids and a quaternized amino alcohol. Figure 1 shows examples of three different ester quats, all containing two long-chain and two short substituents on the nitrogen atom. The figure also shows the ‘‘parent,’’ noncleavable quat. As can be seen, the ester-containing surfactants contain two carbon atoms between the ester bond and the nitrogen that carries the positive charge. Cleavage of the ester bonds of surfactants II–IV yields a fatty acid soap in addition to a highly water-soluble quaternary ammonium diol or triol. These degradation products exhibit low fish toxicity, and they are degraded further by established metabolic pathways. The overall ecological characteristics of ester quats are much superior to those of traditional quats as represented by compound I of Fig. 1. During the past decade the dialkylester quats have to a large extent replaced the stable dialkyl quats as rinse cycle softeners, which is the single largest application for quaternary ammonium compounds. The switch from stable dialkyl quats to dialkylester quats may represent the most dramatic change of product type in the history of surfactants, and it is entirely environment driven. Unlike stable quats, ester quats show excellent values for biodegradability and aquatic toxicity [1,2]. Ester quats have also fully or partially re-

FIG. 1 Structures of one conventional quaternary ammonium surfactant (I) and three ester quats (II–IV). R is a longchain alkyl, and X is Cl, Br, or CH3SO4.

placed traditional quats in other applications of cationics, such as hair care products and various industrial formulations [1]. The cationic charge close to the ester bond renders normal ester quats unusually stable to acid and labile to alkali. The strong pH dependence of the hydrolysis can be taken advantage of to induce rapid cleavage of the product. This phenomenon is even more pronounced for betaine esters, and the mechanism of hydrolysis is discussed in some detail in the following section. Figure 2 illustrates the pH dependence of hydrolysis of an ester quat. As can be seen, hydrolysis rate is at minimum at pH 3–4 and accelerates strongly above pH 5–6. Evidently, formulations containing ester quats must be maintained at low pH. Esters of choline have attracted special attention because the primary degradation products, choline and a fatty acid, are both natural metabolites in the body. Thus choline esters should constitute a group of very nontoxic cationic surfactants. A series of choline esters were synthesized and evaluated as disinfectants with controlled half-lives [3,4] (Fig. 3). Compounds with an alkyl group, R, of 9–13 carbons showed an excellent antimicrobial effect. The in vivo hydrolysis was rapid, presumably due to catalysis by butyrylcholinesterase,

Cleavable Surfactants

47

FIG. 3 Structure of a surface-active choline ester. R and X are the same as in Fig. 1.

FIG. 2 Influence of pH on the hydrolytic stability of dicetylester of bis(2-hydroxyethyl)ammonium chloride at 25⬚C. (From Ref. 1.)

which is present in human serum and mucosal membranes. B.

Betaine Esters

The rate of alkali-catalyzed ester hydrolysis is influenced by adjacent electron-withdrawing or electron-donating groups. A quaternary ammonium group is strongly electron withdrawing. The inductive effect leads to decreased electron density at the ester bond; hence, alkaline hydrolysis, which starts by a nucleophilic attack by hydroxyl ions at the ester carbonyl carbon, is favored. Compounds II–IV of Fig. 1 all have two carbon atoms between the ammonium nitrogen and the — O — oxygen of the ester bond. Such esters undergo alkaline hydrolysis at a faster rate than esters lacking the adjacent charge, but the difference is not very large. If, on the other hand, the charge is at the

FIG. 4

other side of the ester bond, the rate enhancement is much more pronounced. Such esters are extremely labile on the alkaline side but very stable even under strongly acidic conditions [5]. The large effect of the quaternary ammonium group on the alkaline and acid rates of hydrolysis is due to a stabilization/destabilization of the ground state, as illustrated in Fig. 4. The charge repulsion, involving the carbonyl carbon atom and the positive charge at the nitrogen atom, is relieved by hydroxide ion attack but augmented by protonation. The net result is that, compared with an ester lacking the cationic charge, the rate of alkaline hydrolysis is increased 200-fold whereas the rate of acid hydrolysis is decreased 2000-fold [6]. For surface-active betaine esters based on long-chain fatty alcohols, the rate of alkaline hydrolysis is further accelerated by micellar catalysis [7]. Presence of large, polarizable counterions, such as bromide, can completely outweigh the micellar catalysis, however [8]. The extreme pH dependence of surface-active betaine esters makes them interesting as cleavable cationic surfactants. Shelf life is long when they are stored under acidic conditions, and the hydrolysis rate will then depend on the pH at which they are used. Singlechain surfactants of this type have been suggested as ‘‘temporary bactericides’’ for use in hygiene products, for disinfection in the food industry, and in other instances where only a short-lived bactericidal action is wanted [7]. The patent literature also contains examples of betaine esters containing two long-chain alkyl groups [9–11]. Two examples are given in Fig. 5.

Mechanism for the acid- and base-catalyzed hydrolysis of betaine ester.

48

Holmberg

cleavage by F⫺ is extremely fast.) Single- and doubletailed cationic surfactants with the structures shown in Fig. 7 have been synthesized and tested with regard to degradation characteristics [13]. The route of preparation is relatively sophisticated, however, which means that such surfactants may be of limited practical value. E.

FIG. 5 Structures of two surface-active betaine esters. R and X are the same as in Fig. 1.

C.

Monoalkyl Carbonates

Alcohol ethoxylates with short polyoxyethylene chains are viscous oils. Their incorporation into powder detergents is a well-known problem. Carbonate salts of such surfactants have been used as labile derivatives from which the surfactant can be readily regenerated. Such derivatives could be called ‘‘prosurfactants’’ by analogy with the term prodrug in medicine. Reaction of an alcohol ethoxylate with carbon dioxide gives a solid carbonate salt that decomposes under the alkaline washing conditions to give the starting nonionic surfactant and carbonate, as illustrated in Fig. 6 [12]. (Strictly speaking, the prosurfactant is also a surfactant although it is not meant to serve as such in the application step.) Conversion of an alcohol ethoxylate into a solid carbonate enables the incorporation of high levels of this surfactant into granular detergents of high bulk density. D.

Surfactants Containing the Si — O Bond

The silicon-oxygen bond is susceptible to both alkaline and acid hydrolysis. In addition, the bond is specifically cleaved by fluoride ions at relatively neutral pH. (In nonaqueous media, where the ions are not hydrated, the

FIG. 6 Formation of a carbonate salt of a nonionic surfactant and subsequent regeneration of the starting surfactant during the washing step.

Surfactants Containing a Sulfone Group

An anionic and a cationic surfactant containing the ethylenesulfone moiety have been synthesized by oxidation of the corresponding sulfide [14]. These surfactants are stable in acid but break down to nonsurfactant products, a vinylsulfone and a phenol, in weak alkali, as shown in Fig. 8. The cleavage reaction is considerably faster for the cationic than for the anionic surfactant. This is mainly a micellar phenomenon: positively charged micelles are surrounded by a pseudophase of much higher hydroxyl ion activity than the bulk aqueous phase, and the reverse is true for negatively charged micelles. A comparative hydrolysis study with a nonsurfactant analogue of the anionic surfactant confirmed this view because the non-surface-active sulfone decomposed much faster than the surfactant. F.

Sugar Esters

Sugar esters have been receiving considerable attention, mainly because of developments in procedures for bio-organic synthesis. The main advantage of the biochemical route compared with conventional organic synthesis is the much higher regioselectivity obtained in the synthesis. A long reaction time is a typical disadvantage of the enzymatic process. Enzymatic synthesis of sugar esters has been thoroughly covered by Vulfson [15]. The topic will be briefly discussed in the following. In a systematic investigation of the effect of the number of condensed hexose units on surfactant properties, monododecyl esters of glucose, sucrose (two sugar units), raffinose (three units), and stachyose (four units) were prepared by organic synthesis followed by careful chromatographic purification [16]. As can be seen from Fig. 9, all compounds had the acyl substituent at the 6-position of a glucose ring; i.e., the ester

FIG. 7

Structure of a surfactant containing the Si — O bond.


FIG. 8

49

Alkaline hydrolysis of a sulfone-containing surfactant. X may be (CH3)3N⫹ or SO⫺ 3.

bond had the same environment in all four surfactants. The phase behavior and the surfactant properties of the compounds were studied. It was concluded that the self-assembly of the surfactants was governed primarily by geometric packing constraints, which, in turn, depended on the size of the polar headgroup. The phase behavior was practically independent of temperature and, as expected, none of the surfactants exhibited the clouding phenomenon characteristic of polyoxyethylene-based nonionic surfactants. Enzymatic synthesis of sugar esters can be run either in an organic solvent [17,18] or under solvent-free conditions at reduced pressure [19,20]. In the latter process a relatively hydrophobic sugar derivative, e.g., a glucoside or an isopropylidene derivative, is employed. An interesting new development is the use of a microemulsion as the reaction medium [21]. In order to avoid difficult work-up problems, the reaction product, i.e., the ester surfactant, was used as microemulsion surfactant. In a study aimed at optimizing the conditions of lipase-catalyzed sugar ester synthesis, several galactose and xylose esters were prepared by the solvent-free process starting from the isopropylidene derivative [22]. The monoester content was around 90% and the overall yield of the target ester ranged from 59 to 88%. Virtually no side products were formed, either in the course of the enzymatic reaction or in the subsequent removal of the isopropylidene group. This is very different from the complex product mixture obtained by organic synthesis, which is usually an acid- or basecatalyzed transesterification at elevated temperature. Fatty acid esters of unmodified sugars (or sugar alcohols) were prepared in an organic solvent using immobilized lipase as the catalyst. Condensation water was continuously removed by refluxing through a desiccant under reduced pressure. Starting materials were glucose, fructose, sorbitol, xylitol, and the three fatty acids lauric, oleic, and erucic [23]. Physicochemical characterization of the sugar esters gave the expected result with efficiency and effectiveness of the surfac-

tants mainly being dependent on the chain length of the fatty acid [24]. There was little difference in critical micelle concentration (cmc) between surfactants based on different sugars and the same fatty acid.

III.

ACID-LABILE SURFACTANTS

A.

Cyclic Acetals

Cyclic 1,3-dioxolane (five-membered ring) and 1,3-dioxane (six-membered ring) compounds, illustrated in Fig. 10, have been studied in depth by the groups of Burczyk, Takeda, and others as examples of acid-labile surfactants. They are typically synthesized from a longchain aldehyde by reaction with a diol or a higher polyol. Reaction with a vicinal diol gives the dioxolane [25–27] and 1,3-diols yield dioxanes [28,29]. If the diol contains an extra hydroxyl group, such as in glycerol, a hydroxy acetal is formed and the remaining hydroxyl group can subsequently be derivatized to give anionic or cationic surfactants, as illustrated in Fig. 11. It is claimed that glycerol gives ring closure to dioxolane, yielding a free, primary hydroxyl group, but it is likely that some dioxane with a free, secondary hydroxyl group is formed as well. The free hydroxyl group can be treated with SO3 and then neutralized to give the sulfate [30], it can be reacted with propane sultone to give the sulfonate [31], or it can be substituted by bromine or chloride and then reacted with dimethylamine to give a tertiary amine as polar group. Quaternization of the amine can be done in the usual manner, e.g., with methyl bromide [32]. An analogous reaction with pentaerythritol as diol yielded a 1,3-dioxane with two unreacted hydroxymethyl groups that can be reacted further, e.g., to give a dianionic surfactant [31]. The remaining hydroxyl group may also be ethoxylated, and such acetal surfactants have been commercialized [33]. The rate of decomposition in sewage plants of this class of nonionic surfactants is much higher than for normal ethoxylates [34].

50

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FIG. 9

Structures of surface-active sugar esters.

FIG. 10 Preparation of 1,3-dioxolane surfactant (a) and 1,3-dioxane surfactant (b) from a long-chain aldehyde and a 1,2- and a 1,3-diol, respectively.


FIG. 11

51

Examples of anionic (I) and cationic (II) 1,3-dioxolane surfactants.

Hydrolysis splits acetals into aldehydes, which are intermediates in the biochemical ␤-oxidation of hydrocarbon chains. Acid-catalyzed hydrolysis of unsubstituted acetals is generally facile and occurs at a reasonable rate at pH 4–5 at room temperature. Electron-withdrawing substituents such as hydroxyl, ether oxygen and halogens reduce the hydrolysis rate, however [35]. Anionic acetal surfactants are more labile than cationic ones [25], a fact that can be ascribed to the locally high oxonium ion activity around such micelles. The same effect can also be seen for surfactants forming vesicular aggregates, again undoubtedly due to differences in the oxonium ion activity in the pseudophase surrounding the vesicle. Acetal surfactants are stable at neutral and high pH. The advantage of using a cleavable acetal surfactant instead of a conventional amphiphile has been elegantly demonstrated in work by Bieniecki and Wilk [36]. A cationic 1,3-dioxolane derivative was used as surfactant in a microemulsion formulation that was employed as a reaction medium for an organic synthesis. When the reaction was complete, the surfactant was decomposed by addition of acid and the reaction product easily recovered from the resulting two-phase system. By this procedure, the problems of foaming and emulsion formation, frequently encountered with conventional surfactants, could be avoided. The 1,3-dioxolane ring has been found to correspond to approximately two oxyethylene units with regard to effect on cmc and adsorption characteristics [27]. Thus, surfactant type I in Fig. 11 should resemble ether sulfates of the general formula R — (OCH2CH2)2OSO3Na. This is interesting because the commercial alkyl ether sulfates contain two to three oxyethylene units. B.

pounds, but because the ring does not involve the two geminal hydroxyl groups of the aldehyde hydrate, they are included here in the category of acyclic acetals. Alkyl glucosides are by far the most important type of acetal surfactant. As this surfactant class has been the topic of several reviews [37–39], it will be only briefly outlined here. Alkyl glucosides are made either by direct condensation of glucose and a long-chain alcohol or by transacetalization of a short-chain alkyl glucoside, such as ethyl glucoside, with a long-chain alcohol, in both cases using an acid catalyst (Fig. 12). The procedure leads to some degree of sugar ring condensation, the extent of which can be governed by various means, e.g., the ratio of long-chain alcohol to sugar. The alkyl glucoside surfactants break down into glucose and long-chain alcohol under acidic conditions. On the alkaline side, even at very high pH, they are stable to hydrolysis. Their cleavage profile along with their relatively straightforward synthesis route makes these surfactants interesting candidates for various types of cleaning formulations.

Acyclic Acetals

Alkyl glucosides, often somewhat erroneously referred to as alkyl polyglucosides or APGs, are cyclic com-

FIG. 12 Two routes of preparation of alkyl glucosides. R is a long-chain alkyl.

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Holmberg

FIG. 13

Preparation of a cleavable surfactant containing two polyoxyethylene chains. R is a long-chain alkyl.

Polyoxyethylene-based cleavable surfactants have been synthesized by reacting end-capped poly(ethylene glycol) (PEG) with a long-chain aldehyde, as shown in Fig. 13 [40–42]. The physicochemical behavior of these surfactants resembles that of normal nonionics; for instance, they have the reverse solubility-temperature relationship and they exhibit a cloud point. Acid hydrolysis of the labile polyoxyethylene-based surfactants yields PEG-monomethyl ether and longchain aldehyde. It was found that the hydrolysis of these noncyclic acetal–linked surfactants was several orders of magnitude faster than that of cyclic acetal– linked surfactants [42]. This is important from a practical point of view because many applications of cleavable surfactants demand a rather high rate of breakdown. The hydrolytic reactivity increased as the hydrophobe chain length decreased if the hydrophiles were kept the same. This has been attributed to decreased hydrophobic shielding of the acetal linkage from oxonium ions. The structure of the hydrophobe, linear or branched, was not decisive of the hydrolysis

FIG. 14

rate, however, and neither was the size of the polar headgroup, i.e., the length of the PEG chains. Ono et al. [43,44] have synthesized series of noncyclic acetal surfactants—anionics, nonionics, cationics and amphoterics—from a common allyl chloride intermediate (Fig. 14). It was found that the cmc values of these surfactants were lower than those of conventional surfactants of the same alkyl chain length. Furthermore, the efficiency of the surfactants, expressed as the concentration required to produce a 20 mN/m reduction in surface tension, was higher for the cleavable surfactants. Evidently, the connecting moiety, i.e., the group connecting the hydrophobic tail and the polar headgroup, gives a hydrophobic contribution to the amphiphilic properties. A systematic study of hydrolysis rates was made with the four surfactant classes shown in Fig. 14. For a series of surfactants with the same hydrophobic tail and with the same connecting group, the time for complete decomposition was recorded. The results, shown in Table 1, constitute a nice illustration of the effect of

Schematic synthesis routes of noncyclic acetal surfactants.


53

TABLE 1 Times for Complete Decomposition of Four Acetal-Based Surfactants at 25⬚C and at Varying Conditionsa Surfactant type Anionic Cationic Nonionic Amphoteric

2% DCl

pD 1

pD 3

Immediately 48 h Immediately 3h

Immediately 1 week 15 min 24 h

30 min >2 weeks 90 h >1 week

a

Reactions were carried out in deuterated solvent to enable the hydrolysis reactions to be monitored by NMR. Source: Ref. 61.

the micelle surface on the hydrolysis rate. With negatively charged micelles the reaction is very fast, with positively charged micelles the process is sluggish, and with the noncharged (or zero net charged) micelles the rate is intermediate. C.

Ketals

Surfactants containing ketal bonds can be prepared from a long-chain ketone and a diol in analogy with the reaction schemes given in Figs. 10 and 11 for the preparation of acetal surfactants [45]. Ketal-based surfactants have also been prepared in good yields from esters of keto acids by either of two routes, as shown in Fig. 15 [46–48]. The biodegradation profiles of the dioxolane surfactants of Fig. 15 are shown in Fig. 16 [47]. As expected, the degradation rate is very dependent on the alkyl chain length. The process is markedly faster for the labile surfactants (and particularly for structure I, which contains an extra ether oxygen) than for the conventional carboxylate surfactant of the same alkyl chain

FIG. 15

length used as reference. Ketal surfactants are in general more labile than the corresponding acetal surfactants [49]. As an example, a ketal surfactant kept at pH 3.5 was cleaved to the same extent as an acetal surfactant of similar structure kept at pH 3.0 [50]. The relative lability of the ketal linkage is due to the greater stability of the carbocation formed during ketal hydrolysis compared with the carbocation formed during acetal hydrolysis. (It is noteworthy that biodegradation of an acetal surfactant has been found to be faster than that of a ketal surfactant of very similar structure [47]. Evidently, there is no strict correlation between ease of biodegradation and rate of chemical hydrolysis.) Jaeger has introduced the term ‘‘second-generation cleavable surfactant’’ for labile surfactants that on cleavage give another surfactant together with a small water-soluble species. The daughter surfactant generally has a higher cmc than the parent surfactant [51– 54]. Figure 17 shows a typical example of a secondgeneration cleavable surfactant. The concept has been applied to a variety of structures, including phospholipid analogues [54] and several applications of this specific type of cleavable surfactants have been proposed in the papers by Jaeger et al. Double-chain, double-headgroup second-generation surfactants have also been synthesized. The geometry of the molecules may be varied by the position of the link between the hydrocarbon tails. Both symmetrical and unsymmetrical cross-linkings with respect to the headgroups have been prepared [25,55,56]. These surfactants can be seen as examples of gemini surfactants, and in one approach labile gemini surfactants were synthesized that on acid treatment broke down into singlechain, single-headgroup surfactants [56]. They are of interest in model investigations, e.g., to study the morphology of aggregates. Their preparation is cumbersome, however, which means that their practical usefulness is limited.

Preparation of anionic 1,3-dioxolane surfactants from ethyl esters of keto acids.

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Holmberg

FIG. 16 Rate of biodegradation versus time for four ketal surfactants and for sodium decanoate as reference. I and II relate to the compounds of Fig. 6; (a) R = C12H25, n = 2; (b) R = C16H33, n = 2. (From Ref. 47.)

D.

Ortho Esters

Ortho esters are interesting candidates for acid-labile surfactants. They are easily prepared from triethyl orthoformate (or a homologue thereof) and alcohols, as illustrated in Fig. 18; they are stable in alkali; and they decompose in acid by the same general mechanism as acetals and ketals [57]. Hydrolysis gives 1 mole of alkyl formate along with 2 moles of alcohol, as also shown in Fig. 18. One or more of the starting alcohols can be an end-capped PEG, in which case a nonionic polyoxyethylene surfactant is obtained [58]. An interesting feature of ortho esters is that they are much more labile in acid than both acetals and ketals. For instance, an ortho ester based on monomethyl-PEG decomposes to about 50% at pH 6 and to almost 100% at pH 5 after 1 h at room temperature [58]. The ortho ester concept gives molecules with three branches that may be the same or different. Figure 19 shows two examples: a block copolymer with two

FIG. 17

chains of polyoxypropylene and one chain of polyoxyethylene and a triple-tailed nonionic surfactant connected in the polar headgroup [59]. Ortho ester surfactants have recently been commercialized. E.

Surfactants Containing the N — —C Bond

Jaeger et al. have synthesized surfactants consisting of two parts connected with a CONHN — —C moiety. Each part is a surfactant of its own with a hydrophobic tail and a polar headgroup, and the two headgroups are of different sign [60]. The structure is shown in Fig. 20. As can be seen, the two charges are far apart in the molecule; thus, the type is conceptually different from double-chain zwitterionic surfactants such as phosphatidylcholine. Instead, they may be viewed as a kind of heterogemini surfactant. Figure 20 also illustrates the acid-catalyzed breakdown of the surfactants. Hydrolysis into the cationic and the anionic surfactant parts occurs readily in weak

Acid-catalyzed hydrolysis of a second-generation cleavable surfactant.


FIG. 18

55

Synthesis and hydrolysis of ortho esters. R1, R2, and R3 are alkyl groups.

acid. The surfactant forms giant vesicles on sonication, and a suggested application is as entrapment and release devices that can be triggered by a change in pH from 7 to about 3. IV.

UV LABILE SURFACTANTS

The concept of triggering cleavage by UV light is attractive because it allows extremely fast breakdown of the surfactant to occur. An alkyl aryl ketone sulfonate, which bears some structural resemblance to alkylbenzene sulfonate surfactants, was synthesized [61]. This compound is photocleaved into a water-soluble aryl sulfonate and a mixture of two methyl-branched olefins, as shown in Fig. 21. The surfactant is of interest for solubilization of proteins because the work-up procedure is greatly facilitated by the instantaneous elimination of surfactant from the solution. The wavelength required for this type of photolysis, a so-called Norrish type II cleavage, is 300 nm and above. This low-energy radiation should be harmless to proteins. Another approach has been to incorporate the lightsensitive diazosulfonate group between the polar head-

FIG. 19

group and the tail of an anionic surfactant [62–64]. As can be seen from Fig. 22, these surfactants are also similar in structure to the commonly used alkylbenzene sulfonates. A comparison of cmc values for the diazosulfonate and the normal sulfonate surfactants with the same R substituent shows lower values for the former, indicating a contribution of hydrophobicity from the azo linkage. Photochemical cleavage yielded sulfate ion and the remaining diazonium compound, which was further photolyzed in a second step. An interesting use of photolabile surfactants is as emulsifiers in emulsion polymerization [65,66]. The use of a photolabile emulsifier opens the possibility to control the latex coagulation process simply by exposing the dispersion to UV irradiation. The ionic headgroup of the surfactant will be split off by photolysis leading to aggregation of the latex particles. Such latexes could be of interest for coating applications. A double-chain surfactant has been synthesized that contained Co(III) as complexing agent for two singlechain surfactants based on ethylenediamine in the polar headgroup. UV irradiation, or merely sunlight, causes reduction of Co(III) to Co(II). The latter gives a very

Two examples of surface-active ortho esters.

56

Holmberg

FIG. 20

Hydrolysis of a surfactant containing the N — —C bond. R is a long-chain alkyl.

labile complex, and the double-chain surfactant immediately degrades into two single-chain moieties [67].

V.

MISCELLANEOUS

Apart from the product classes already discussed, which include the most important types of cleavable surfactants, several more or less exotic examples of surfactants with limited half-lives have been reported. For instance, isethionate esters with a very high degree of alkali lability have been developed. These products, made by esterification of an alkyl polyoxyethylene carboxylic acid with the sodium salt of isethionic acid, have been claimed to be partially cleaved when applied to the skin [68]. Cleavable quaternary hydrazinium surfactants have been explored as amphiphiles containing a bond that splits very easily. The surfactants are cleaved by nitrous acid under extremely mild conditions [69]. Ozone-cleavable surfactants have been developed as examples of environmentally benign amphiphiles. These surfactants, which contain unsaturated bonds, break down easily during ozonization of water, which is a water purification process of growing importance [70]. Glucose-based surfactants having a disulfide linkage between the anomeric carbon of the sugar ring and the hydrophobic tail were synthesized and evaluated for

FIG. 21

use as solubilizing agents for membrane proteins [71]. Cleavage into nonsurfactant products was performed by addition of dithioerythritol, which is known to split disulfide linkages under physiological conditions. Surfactants with thermolabile bonds have been synthesized and evaluated as short-lived surfactants. Amino oxide surfactants with an ether oxygen in the 2-position are examples of such structures. They decompose at elevated temperature to the corresponding vinyl ether [72].

VI.

CONCLUDING REMARKS

Cleavable, or splittable, or chemodegradable surfactants are likely to become of increasing importance as the environmental concern with regard to surfactant formulations becomes even more widespread. The development that has occurred to this point has brought about a vitalization of the surfactants area in terms of new structures and synthesis strategies. The drive to make surfactants with bonds that break down in a controlled way to yield non-surface-active or less surfaceactive products has probably involved more creative thinking in terms of organic synthesis than any other area within the surfactant domain, possibly with the exception of the area of gemini surfactants. It will be interesting to monitor which of the many research av-

Photocleavage of a surface-active alkylaryl ketone.


FIG. 22

57

Preparation and light-induced degradation of a diazosulfonate surfactant.

enues employed to prepare cleavable surfactants will turn out to become important commercial processes in the future. REFERENCES 1.

2.

3.

4.

5. 6. 7.

8. 9.

10. 11. 12. 13.

G. Kru¨ger, D. Boltersdorf, and H. Lewandowski, in Novel Surfactants (K. Holmberg, ed.), Marcel Dekker, New York, 1998, pp. 115–138. J. Waters, H. H. Kleiser, M. J. How, M. D. Barratt, R. R. Birch, R. J. Fletcher, S. D. Haigh, S. G. Hales, S. J. Marshall, and T. C. Pestell, Tenside Surfactants Deterg. 28:460–468 (1991). M. Chelminska-Bertilsson, A. Edebo, R. A. Thompson, and L. Edebo, Scand. J. Gastroenterol. 30:670–674 (1995). B. Ahlstro¨m, M. Chelminska-Bertilsson, R. A. Thompson, and L. Edebo, Antimicrob. Agents Chemother. 39: 50–55 (1995). M. Robson Wright, J. Chem. Soc. B 707–710 (1969). R. P. Bell and F. J. Lindars, J. Chem. Soc. 1087–1098 (1954). M. Lindstedt, S. Allenmark, R. A. Thompson, and L. Edebo, Antimicrob. Agents Chemother. 34:1949–1954 (1990). R. A. Thompson and S. Allenmark, J. Colloid Interface Sci. 148:241–246 (1992). G. D. Lichtenwalter, L. E. Miller, C. Siram, and E. H. Wahl, PCT Int. Patent Appl. WO 9325648 A1 931223 (1993). L. M. Ilardi and S. A. Madison, U.S. Patent 5429755 A 950704 (1995). H. J. Weissen and N. Porta, Eur. Patent Appl. EP 638639 A1 950215 (1995). F. E. Hardy and A. D. Willey, PCT Patent Appl. WO 9525157 A1 950921 (1995). D. A. Jaeger, M. Darlene Ward, and A. K. Dutta, J. Org. Chem. 53:1577–1580 (1988).

14. 15. 16.

17. 18. 19. 20.

21. 22.

23. 24. 25. 26. 27. 28. 29. 30. 31.

D. A. Jaeger, C. T. Finley, M. R. Walter, and C. A. Martin, J. Org. Chem. 51:3956–3959 (1986). E. N. Vulfson, in Novel Surfactants (K. Holmberg, ed.), Marcel Dekker, New York, 1998, pp. 279–300. I. So¨derberg, C. J. Drummond, D. N. Furlong, S. Godkin, and B. Matthews, Colloids Surf. A 102:91–97 (1995). G. B. Oguntimein, H. Erdmann, and R. D. Schmid, Biotechnol. Lett. 15:175–180 (1993). A. Schlotterbeck, S. Lang, V. Wray, and F. Wagner, Biotechnol. Lett. 15:61–64 (1993). K. Adelhorst, F. Bjo¨rkling, S. E. Godtfredsen, and O. Kirk, Synthesis 2:112–115 (1990). L. Guillardeau, D. Montet, N. Khaled, M. Pina, and J. Graille, Tenside Surfactants Deterg. 25:342–344 (1992). P. Skagerlind, K. Larsson, M. Barfoed, and K. Hult, J. Am. Oil Chem. Soc. 74:39–45 (1997). G. Fregapane, D. B. Sarney, S. G. Greenberg, D. J. Knight, and E. N. Vulfson, J. Am. Oil Chem. Soc. 71: 87–91 (1994). A. Ducret, A. Giroux, M. Trani, and R. Lortie, Biotechnol. Bioeng. 48:214–221 (1995). A. Ducret, A. Giroux, M. Trani, and R. Lortie, J. Am. Oil Chem. Soc. 73:109–113 (1996). D. A. Jaeger, Supramol. Chem. 5:27–30 (1995). A. Bieniecki, K. A. Wilk, and J. Gapinski, J. Phys. Chem. B 101:871–875 (1997). A. Sokolowski, A. Bieniecki, K. A. Wilk, and B. Burczyk, Colloids Surf. A 98:73–82 (1995). G.-W. Wang, X.-Y. Yuan, Y.-C. Liu, X.-G. Lei, and Q.-X. Guo, J. Am. Oil Chem. Soc. 72:83–87 (1995). G.-W. Wang, Y.-C. Liu, X.-Y. Yuan, X.-G. Lei, and Q.-X. Guo, J. Colloid Interface Sci. 173:49–54 (1995). A. Sokolowski, A. Piasecki, and B. Burczyk, J. Am. Oil Chem. Soc. 69:633–638 (1992). G.-W. Wang, X.-Y. Yuan, Y.-C. Liu, and X.-G. Lei, J. Am. Oil Chem. Soc. 71:727–730 (1994).

58 32. 33. 34. 35. 36. 37. 38. 39. 40. 41. 42. 43. 44. 45. 46.

47.

48.

49. 50. 51. 52.

Holmberg K. A. Wilk, A. Bieniecki, B. Burczyk, and A. Sokolowski, J. Am. Oil Chem. Soc. 71:81–85 (1994). D. C. Galante and R. C. Hoy, Eur. Patent Appl. EP 0 742 177 A1 (1996). R. C. Hoy and A. F. Joseph, INFORM 7:428–429 (1996). A. Piasecki, J. Prakt. Chem. 327:731–738 (1985). A. Bieniecki and K. A. Wilk, J. Phys. Org. Chem. 8: 71–76 (1995). W. von Rybinski, Curr. Opin. Colloid Interface Sci. 1: 572–578 (1996). W. von Rybinski, in Alkyl Polyglycosides (K. Holmberg, ed.), Marcel Dekker, New York, 1998, pp. 31–85. D. Balzer, Tenside Surfactants Deterg. 33:102–110 (1996). B. Burczyk and A. Sokolowski, Tenside Surfactants Deterg. 15:68–71 (1978). A. Sokolowski and B. Burczyk, Tenside Surfactants Deterg. 18:199–201 (1981). C. Yue, J. M. Harris, P.-E. Hellberg, and K. Bergstro¨m, J. Am. Oil Chem. Soc. 73:841–845 (1996). D. Ono, A. Masuyama, and M. Okahara, J. Org. Chem. 55:4461–4464 (1990). D. Ono, A. Masuyama, T. Tanaka, and M. Okahara, Tenside Surfactants Deterg. 29:412–417 (1992). S. Yamamura, M. Nakamura, K. Kasai, H. Sato, and T. Takeda, J. Jpn. Oil Chem. Soc. 40:1002–1006 (1991). A. Masuyama, D. Ono, A. Yamamoto, T. Kida, Y. Nakatsuji, and T. Takeda, J. Jpn. Oil Chem. Soc. 44:446– 450 (1995). D. Ono, S. Yamamura, M. Nakamura, T. Takeda, A. Masuyama, and Y. Nakatsuji, J. Am. Oil Chem. Soc. 72:853–856 (1995). D. Ono, A. Masuyama, Y. Nakatsuji, M. Okahara, S. Yamamura, and T. Takeda, J. Am. Oil Chem. Soc. 70: 29–36 (1993). T. Kida, N. Morishima, A. Masuyama, and Y. Nakatsuji, J. Am. Oil Chem. Soc. 71:705–710 (1994). B.-K. Song and K. Wolf, DWI Rep. 114:549–554 (1995). D. A. Jaeger, M. D. Ward, and A. K. Dutta, J. Org. Chem. 53:1577–1580 (1988). D. A. Jaeger, Y. M. Sayed, and A. K. Dutta, Tetrahedron Lett. 31:449–450 (1990).

53. 54. 55. 56. 57. 58. 59. 60. 61. 62.

63.

64. 65. 66. 67. 68.

69. 70. 71. 72.

D. A. Jaeger and Y. M. Sayed, J. Org. Chem. 58:2619– 2627 (1993). J. Y. Wang, R. A. Uphaus, J. Wang, and D. A. Jaeger, Thin Solid Films 242:277–282 (1994). D. A. Jaeger and S. G. G. Russell, Tetrahedron Lett. 34:6985–6988 (1993). D. A. Jaeger, S. G. G. Russell, and H. Shinozaki, J. Org. Chem. 59:7544–7548 (1994). R. Eliason and M. M. Kreevoy, J. Am. Chem. Soc. 100: 7037–7041 (1978). K. Bergstro¨m and P.-E. Hellberg, Swedish Patent Appl. 9602617-4 (1996). K. Bergstro¨m and P.-E. Hellberg, Swedish Patent Appl. 9710241-3 (1997). D. A. Jaeger, B. Li, and T. Clark, Jr., Langmuir 121: 4314–4316 (1996). W. W. Epstein, D. S. Jones, E. Bruenger, and H. C. Rilling, Anal. Biochem. 119:304–312 (1982). I. R. Dunkin, A. Gittinger, D. C. Sherrington, and P. Whittaker, J. Chem. Soc. Chem. Commun. 2245–2246 (1994). I. R. Dunkin, A. Gittinger, D. C. Sherrington, and P. Whittaker, Synthesis J. Chem. Soc. Perkin Trans. 2 1837–1842 (1996). O. Nuyken, K. Meindl, A. Wokaun, and T. Mezger, J. Photochem. Photobiol. A Chem. 85:291–298 (1995). O. Nuyken, K. Meindl, A. Wokaun, and T. Mezger, Macromol. Rep. A32:447–457 (1995). T. Mezger, O. Nuyken, K. Meindl, and A. Wokaun, Polym. Mater. Sci. Eng. 73:153–155 (1995). D. A. Jaeger, V. B. Reddy, and D. S. Bohle, Tetrahedron Lett. 40:649–652 (1999). S. A. Madison, M. Massaro, G. B. Rattinger, and C. J. Wenzel, PCT Patent Appl. WO 9514661 A1 950601 (1995). D. A. Jaeger, J. Wettstein, and A. Zafar, Langmuir 14: 1940–1941 (1998). A. Masayama, C. Endo, S. Takeda, and M. Nojima, Chem. Commun. 18:2023–2024 (1998). J. Cuomo, J. H. Merrifield, and J. F. W. Keana, J. Org. Chem. 45:4216–4219 (1980). Y. Hayashi, F. Shirai, T. Shimizu, Y. Nagano, and K. Teramura, J. Am. Oil Chem. Soc. 62:555–557 (1985).

3 Gemini Surfactants and Surfactant Oligomers MARTIN IN

I.

CNRS-Rhodia, Cranbury, New Jersey

INTRODUCTION

importance of the length of the connecting chain between the headgroups, the ‘‘spacer,’’ in controlling the microstructure of the self-assemblies [22]. Menger and Littau raised the question of the micellar structure of surfactants, which could not aggregate without exposing hydrocarbon moieties to water [23]. Finally, Rosen pointed out the unexpected effectiveness of these surfactants in lowering surface tension and their enhanced synergistic effect in mixtures. He analyzed the effects on performance properties [4], which could make gemini the ‘‘new generation of surfactants.’’ The number of patents (which concern predominantly anionic and nonionic geminis) filed since then attests that this was rather convincing [24]. Gemini surfactants were considered the starting point for surfactant oligomers. Synthesis and physicochemical studies of surfactant trimers were reported [1,5]. Some surfactant oligomers have been synthesized and studied in other contexts. For instance, cationic lipids are mostly studied as carriers in the intracellular delivery of bioactive agents [25,26] and more specifically as nonviral transfecting agents [27]. Lipophilic di- and triamides have been used as ionophores for alkaline earth metal cations [28], and lipophilic cyclopolyamines are potential liquid membrane sensors for nucleosides [29]. The synthesis of higher homologues also provides an alternative path to the study of the transition from surfactant to polysoap behavior [30]. Gemini surfactants have shown many ‘‘unexpected properties,’’ which are a posteriori rather well understood, and concepts long known [31,32] explain at least qualitatively these observations. Surfactant self-assembly results from two opposing forces. Attraction be-

Covalent linking of several amphiphilic moieties at the headgroup level yields a ‘‘surfactant oligomer’’ (Fig. 1a). The surfactant oligomers we are going to deal with are higher homologues of the gemini surfactants (surfactant dimers) (Fig. 1c) [1]. They are distinguished from ‘‘oligomeric surfactants’’ (macrosurfactants), which consist of amphiphilic diblock copolymers (Fig. 1b), and are also currently the subject of active research [2]. In surfactant oligomers, the structural repeating unit is amphiphilic by itself. The chemical group that connects the amphiphilic moieties is of variable nature and length. Gemini surfactants have been synthesized and patented for more than 50 years [3], especially cationic ones. They have become topical again in the last two decades and their properties have been the subject of several reviews [1,4–13]. They are of industrial and academic interest for diverse reasons. Cationic geminis were first described [14–16] and claimed to be good textile softeners whose action resists laundering and dry cleaning operations [17,18] or as efficient bactericidal and fungicidal agents with good diffusion properties and skin compatibility [19,20]. More recently Devıńsky and colleagues, aiming to establish the relationship between biological activity and surfactant structure, synthesized and studied a large variety of cationic gemini surfactants [21]. Okahara and Ikeda have developed a new and easy synthetic route to oligo(ethylene glycol) diglycidyl ethers and described various types of derivatives including anionic gemini surfactants [6]. Zana and Talmon pointed out the 59

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The new parameters s and x have a strong influence on the surface activity and the packing at the interface of surfactant oligomers as well as on their self-assembling properties in the bulk. This is described in Sections III and IV. Like conventional surfactants, oligomers have been used in analytical and synthesis chemistry, as selective receptors, as hosting or templating agents, and also as reactants. This will be the subject of the last section.

FIG. 1 Surfactant oligomers (a) are distinguished from oligomeric surfactants (b) by the fact that the structural repeating unit is amphiphilic by itself. Surfactant oligomers are higher homologues of gemini surfactants (c). The structural repeating unit (d) corresponds to a conventional surfactant, which will be referred to as the ‘‘monomer.’’

tween the hydrophobic tails induces the aggregation, and repulsion between the hydrophilic headgroups ensures the existence of a large interfacial area [31]. Classical ways to modify the micellization, the shape of the micelles, or the lyotropic behavior consist of tuning these opposing forces by varying the length of the hydrophobic tail and the nature of the headgroup. The concept of surfactant oligomers provides new parameters to tune this balance of opposing forces. The degree of oligomerization x, i.e., the number of amphiphilic moieties in the surfactant, is a new variable parameter. The length of the spacer s can vary along with its hydrophobicity and rigidity. This makes it possible to achieve more direct and more efficient control of the optimal interfacial area per headgroup [32]. As in conventional surfactants, the length of the tail, m, and the chemical nature of the headgroup are possible chemical variables. These two variables are not specific to surfactant oligomers, but the study of their influence brings insight to the properties of surfactant oligomers. Gemini surfactants can also be nonsymmetric; i.e., both amphiphilic moieties can be different in terms of chain length and headgroup nature. A large variety of surfactant oligomers will be discussed in the next section, where their synthesis is reviewed. Following Zana, the cationic surfactant dimers with simple structure are referred to as m-s-m, 2X when the spacer consists of a — (CH2)s — chain and m-s/3-m, 2X when the spacer consist of s/3 ethylene oxide units. X is the counter ion. Using the same logic, trimers are referred to as m-s-m-s-m, 3X. Some anionic surfactants with simple structure are designated in the same way but the headgroup nature is precise.

II.

SYNTHESIS: STRUCTURE DIVERSITY

A.

Surfactant Dimers (Gemini)

1. Cationic Geminis Cationic surfactants are among the first gemini surfactants reported in the literature [3,14–20]. First claimed to be good fabric softeners or developed for their biological activity, they have also been studied for micellar catalysis. Easier to synthesize, they have been the materials of choice for fundamental studies. The influence of various parameters such as the length of the hydrophobic chains, their dyssymmetry, and the nature (hydrophilic or hydrophobic) and the length of the spacer has been studied. Some examples of cationic gemini surfactants are shown in Fig. 2. Synthetic methods for preparing diquaternary ammonium (Fig. 2a, c, e, and g) [14,21,33–42] and dipyridinium (Fig. 2d, f, and h) [19,43] geminis rely on the same reactions (quaternization of a tertiary amine with bromoalkane) as those used for their corresponding monomer, except for the use of difunctional reagents. Two routes can be distinguished. The first one proceeds by quaternization of a tertiary diamine (route 1) [14,21,33,38,42] as exemplified in Scheme 1 [14,20]. The second one couples two tertiary fatty amines with dibromoalkane (route 2) [36–39,41] as shown in Scheme 2 [38]. Two tertiary diamines can also be coupled with epichlorohydrin, giving a hydroxypropylene spacer [44,45]. Quaternary ammonium geminis with a hydrophilic spacer (Fig. 2b) have been synthesized using route 2 by reacting tertiary amines with ␣,␻-dibromo alcohols [46] or an ␣,␻-dibromo oligo(oxyethylene) [47–49] [the latter being synthesized via bromination of oligo(oxyethylene)glycol with phosphorus tribromide]. Other methods have been reported to produce diquaternary ammonium surfactants with oxyalkylene spacer [50].

Gemini Surfactants and Surfactant Oligomers

FIG. 2

61

Examples of cationic gemini surfactants.

2. Anionic Geminis A large variety of anionic gemini surfactants (see Fig. 3: sulfonate 3a, sulfate 3b, phosphate 3c, carboxylate 3d) with hydrophilic spacers have been prepared from the corresponding fatty diols according to the conven-

tional procedure used for classical surfactants [51–59] (Scheme 3, second step). Intermediate fatty diols have been prepared by the reaction of diglycidyl ethers (prepared according to Ref. 60) with the appropriate fatty alcohol, leading to gemini surfactants with a hydrophilic spacer (Scheme 3, first step). The intermediate fatty diols are nonionic gemini surfactants. They are not soluble in water, but their emulsifying properties

SCHEME 1

SCHEME 2

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In

FIG. 3

Examples of anionic gemini surfactants.

[57] and insoluble monolayers at the air-water interface have been studied [61]. Sulfation of the diols proceeds with chlorosulfonic acid in the presence of glacial acetic acid in dichloromethane at room temperature [51] or chloroform at 0⬚C [52], followed by neutralization with aqueous sodium carbonate or alcoholic sodium hydroxide (see Scheme 3).

Phosphatation is carried out with polyphosphoric acid in dry benzene at 50⬚C. Use of phosphorus pentoxide leads to some undesirable dehydration of the secondary alcohol, and phosphorus oxychloride leads to a complex reaction mixture [53]. Disodium sulfonates (Fig. 3a) are prepared from 1,3propanesultone in the presence of NaOH [51] or NaH in dry tetrahydrofuran (THF) at 60⬚C [51,54,55]. In all

SCHEME 3


cases, pure products are obtained after extraction and separation by silica gel column chromatography or by high-performance liquid chromatography (HPLC). The synthesis of dicarboxylate geminis (Fig. 3d) proceeds by reacting the diols with bromoacetic acid in t-BuOH under basic conditions, followed by esterification with methanol under acidic conditions. This ester is purified on a silica gel column and finally hydrolyzed by NaOH in methanol [59]. Taurine gemini surfactants (Fig. 3g) were synthesized by reaction of ethylene glycol diglycidyl ether with N-(alkyl)taurine in the presence of sodium carbonate in ethanol [56]. N-(Alkyl)taurines are prepared by reaction of the corresponding fatty amines with sodium 2-bromoethane-1-sulfonate. Anionic gemini surfactants with a hydrophilic spacer (Fig. 3e) were also synthesized by diesterification of polyethylene glycol with ␣-sulfonated fatty acids in carbon tetrachloride under reflux [62]. Esterification of polyethylene glycol with ␣-sulfonated acid (prepared as described in Ref. 63) yielded a monoester (about 50%), diester (about 25%), and unreacted PEG (25%); separation and purification of the components were carried out by reversed-phase chromatography [62]. The same types of sulfonate surfactants with a hydrophobic spacer has been synthesized by disulfonation of fatty diesters of adipic acid [64]. Another possible route to these compounds, coupling 2-hydroxy-1-alkanesulfonates with diacids, has proved unsuccessful [64]. The synthesis of other anionic gemini surfactants with a hydrophilic spacer of different lengths has been reported [65]. Dihydroxyl precursors such as tartaric acid have been used to prepare asymmetric anionic gemini surfactants [66]. Alkylphosphate geminis with a hydrophobic spacer (Fig. 3f) have been obtained by coupling alkyl phosphate tetramethylammonium salts with dibromoalkanes [67] or ␣,␣⬘-dibromoparaxylene [39] according to Bauman’s method [68]. This route relies on the fact that monoalkyl phosphates [ROP(O)O2]2⫺ are better nucleophiles than dialkyl phosphates [(RO)2P(O)O2]⫺. Alternatively, Eibl’s method [69] (phosphorylation of the diol using POCl3 in the presence of triethylamine) has been used to synthesize phosphate geminis with a — (CH2)s — spacer (Fig. 3f) [70] or a rigid hydrophobic spacer [39]. Gemini glycerophosphates with a long flexible hydrophobic spacer have also been synthesized as models for archaebacterial membrane lipids [71]. Sarcosine-type surfactant dimers have been synthesized from fatty acid and ethylenediaminediacetic acid via the mixed anhydride method [72]. Their efficiency as flotation agents is improved as compared with the

63

monomer, and strong synergistic effects have been observed on mixing with fatty amines. 3. Amino Acid Derivatives The use of amino acids to prepare gemini surfactants offers a large variety of headgroup structures. Moreover, it facilitates the synthesis of enantiomerically pure surfactants. Amino acid-based gemini surfactants have improved biocompatibility. Some of them have been shown to be less hemolytic and less irritating. They have also proved to be good immunoadjuvants for the formulation of vaccines. Some examples are presented in Fig. 4. Nonionic geminis (Fig. 4a) have been prepared by condensation of N ␣,N ␧-diacyl lysine with N,Nbis(methylpolyoxyethylene) amine [73]. Their structure is close to the structure of natural lecithin, and they do not rigorously correspond to surfactant dimers as defined in the introduction. The same type of compounds with alkyl chains of different lengths has been synthesized [74]. Gemini cationic surfactants with variable spacer lengths have been synthesized from arginine [75–78] (Fig. 4b). The synthesis proceeds in three steps: (1) protection of the guanido group of arginine with a nitro group, (2) coupling of two protected arginines via condensation of the ␣-carboxyl group to both primary amino groups of the ␣,␻-alkanediamine using benzotriole-1-yl-oxy-tris-(dimethylamino)-phosphonium hexafluorophosphate (BOP) in the presence of an activating base (DABCO), and (3) catalytic hydrogenation to unprotect the guanido group. Anionic gemini surfactants have also been synthesized from L-cysteine (Fig. 4c) [79]. A chemoenzymatic route for the preparation of a variety of amino acid– based gemini surfactants has been developed [80]. Immobilized lipases efficiently catalyze the formation of diester (respectively diamide) from N-protected amino acids and ␣,␻-alkane-diols (respectively ␣,␻-alkanediamine) with hydrocarbon spacers of different lengths. Tyrosine- (Fig. 4d) and serine-based geminis were then obtained by acylation and acyl chloride followed by removal of the carbobenzyloxy-protecting group by catalytic hydrogenation under standard conditions. For glutamic acid-based geminis, the carboxyl group of the residue was esterified prior to lipase action. For lysinebased geminis, the N-protected acylated amino acid turned out to be a better substrate for the lipase than the N-protected amino acid itself [80]. 4. Sugar Derivatives Carbohydrate-based gemini surfactants present the advantage of being derived from a renewable source. The

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FIG. 4

Examples of amino acid-based gemini surfactants.

presence of two sugar headgroups is expected to enhance intra- and intermolecular hydrogen bonding, but it was also hoped that the gemini structure could lower the Kraft temperature (a point that often limits the practical use of polyalkylglucosides) [81]. Examples are given in Fig. 5. The synthesis of the compound of Fig. 5b proceeds by reaction of carbohydrate lactone with a 2,2-dialkyl-

FIG. 5

propane-1,3-diamine in methanol [82,83]. The diamine was obtained by dialkylation of malonitrile with bromoalkane in dimethyl sulfoxide (DMSO), followed by reduction of the nitrile groups into primary amine groups by LiAlH4 in dry ether or with lithium in a liquid ammonia-ethanol mixture. Sugar-based surfactants with variable spacer lengths (Fig. 5a) have been prepared by catalytic hydrogena-

Examples of sugar-based gemini surfactants.


tion of D-glucose and the appropriate ␣,␻-alkanediamine [84]. At that step, a bola-amphiphile is obtained; it is acylated with fatty acid anhydride to get a gemini surfactant. Nonionic glucoside gemini surfactants with the two amphiphilic moieties linked at C-6 have been synthesized [85]. A large variety of xylose, glucose, galactose, and lactose (Fig. 5c) derived gemini surfactants, with different chain and spacer lengths, have been prepared from partially protected sugars (isopropylidene derivatives), using enzymes to introduce fatty acids regioselectively into carbohydrate moieties [86]. Both amphiphilic moieties were connected via different hydroxyl groups in the sugar molecule, and a heterodimer xylose-lactose (Fig. 6d) gemini was prepared [86].

65

phosphates (Fig. 7a) [91], carboxylates, and sulfates [66] as well as cationic headgroups [66]. Chiral cationic gemini surfactants have been synthesized from chiral biphenyl (Fig. 7b) [92]. 7.

Functional Gemini Surfactants

5. Surfactant Heterodimer Gemini surfactants can be nonsymmetric. This means that the two amphiphilic moieties can differ either in the length of the hydrophobic tail [87] or in the nature of the headgroup [88,89]. Some examples of surfactant heterodimers are presented in Fig. 6. Cationic gemini surfactants with two hydrophobic chains of different lengths (Fig. 6a) were obtained in two steps from the permethylated diamine as already described [87]. The intermediate alkyldimethyl [1-(2dimethylamino)ethyl] ammonium bromide is recrystallized in ether. Hybrid hydrocarbon-fluorocarbon cationic gemini surfactants have also been synthesized the same way [90]. The synthesis of gemini surfactants with two different hydrophilic headgroups (cationic-anionic, nonionicnonionic, anionic-nonionic) (Fig. 6b–d) involves more steps. For example, the compound of Fig. 6c was synthesized in three steps: An alkyl dimethyl amine reacts first with ethylbromoacetate and then with hydrazine to give the surfactant RMe2N⫹CH2CONHNH2Br⫺. The latter reacts with fatty keto acids, resulting in the surfactant of Fig. 6c. A 13C nuclear magnetic resonance (NMR) study revealed that it was obtained as the E isomer with respect to the carbon-nitrogen double bond [88]. This study also provides an example of a cleavable spacer gemini surfactant (see Section II.A.7). The chemoenzymatic route to sugar-based surfactants described earlier allows the synthesis of nonionic surfactant heterodimers (Fig. 6d) [86].

(a) Cleavable Surfactants. Several types of cleavable gemini surfactants have been synthesized based on disulfide- [93], hydrazine- [88], acetal- [94–96], or ozone-cleavable double bonds [97]. The synthesis of cationic surfactants containing a disulfide bond in the spacer has been achieved by condensation of an alkyldimethylamino betaine with cystine or cystamine via the mixed anhydride method [93]. The betaine is first converted to a mixed anhydride by reaction with isobutyl chloroformate. The second step is the aminolysis of the anhydride by the amino group of cystine dimethyl ester or cystamine. In aqueous solutions the disulfide surfactants obtained decompose at room temperature at pH > 8.0 but are stable even at a higher temperature (50⬚C) at lower pH. These surfactants have potential applications in the textile and cosmetic fields because the disulfide bond can also react with thiol groups (of reduced keratin, for instance) (thiol-disulfide interchange) [93]. Disulfide-based phospholipid dimers have been synthesized from functionalized monomer surfactant in the micellar state. This was done to study nearest neighbor recognition in membranes [98]. The simplest synthesis of gemini surfactants with an acetal (1,3-dioxalane) based spacer proceeds by acidcatalyzed condensation of diethyl tartrate with fatty ketones followed by alkaline hydrolysis [94]. The synthesis presented in Ref. 95 is more involved and does not strictly give a gemini surfactant because the linkage between the two amphiphilic moieties is not located at the headgroup but in the middle of the fatty chains. In that respect, these surfactants provide interesting intermediate structures between gemini and bolaform surfactants [7]. Anionic gemini surfactants with an ozone-cleavable spacer (bearing a carbon-carbon double bond) [97] have been synthesized with unsaturated diglycidyl ether by the same method as in Ref. 54. Their ozonolysis has been studied by proton NMR [97].

6. Chiral Gemini Surfactants Enantiomerically pure gemini surfactants derived from amino acids have already been mentioned. Other types of chiral surfactants have been synthesized from tartaric acid with anionic hydrophilic groups such as

(b) Miscellaneous. Ferrocenyl cationic geminis have been synthesized by the same procedure as the simple diquaternary ammonium gemini using bromoctylferrocene to quaternize permethylated propanediamine [99]. It was known that a variation of the oxidation state of the ferrocene moiety made it possible to control bulk

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FIG. 6

Examples of surfactant heterodimers.

as well as surface properties of ferrocenyl surfactant solutions (see Table 26) [100]. With gemini ferrocenyl surfactants the range of concentration for which this control is efficient is greatly extended [99] (see Chapter 7 in this volume). Finally, anionic gemini surfactants with azo groups in the spacer have been synthesized and used as initiators for radical polymerization (inisurfs) [101]. As with any inisurfs, they suffer from a poor radical yield. B.

Oligomers

A large variety of surfactant oligomers, mostly trimers, has been reported in the literature. Their structures are presented in Fig. 8. Some of them are obtained pure;

others consist of mixtures of surfactant oligomers with different oligomerization degrees. Triazine-derived trialkyltriquaternary ammonium surfactants have been synthesized by quaternization of trialkyl triazine with dimethyl sulfate and claimed to be efficient antibacterial, antifungal, and antiviral agents with weaker toxicity [102]. A trimer of DTAB with s = 3, 12-3-12-3-12, 3Br, was first synthesized in a multistep procedure described in Scheme 4 [103]. Since then, its synthesis has been improved starting with bis(aminopropylamine) as shown in Scheme 5 [104]. The first step (permethylation) is carried out in acidic aqueous solution with formaldehyde and sodium borohydride as reducing agent, as described in Ref. 105. The second step consists of the


FIG. 7

Examples of asymmetric gemini surfactants.

quaternization with bromododecane in acetonitrile at 80⬚C. The purification proceeds by recrystallization [104]. 8-3-8-3-8, 3Br, 16-3-16-3-16, 3Br (unpublished results), and the tetramer 12-3-12-4-12-3-12, 4Br (Fig. 8c) [104] have been synthesized in the same way. The preceding two-step procedure has been used to prepare m-6-m-6-m, 3Br (Fig. 8a) as well as triquaternary ammonium with a three-armed, star-shaped spacer (Fig. 8d) (unpublished results). For these surfactants with s ≠ 3, permethylation could be performed via the Eschweiler-Clarke reaction (with a C3 spacer, this reductive alkylation induces fragmentation of the tri-

FIG. 8

67

amine and yields the permethylated diamine [106]). The synthesis of 12-2-12-2-12, 3Br by the same route has been reported, but after the quaternization reaction, the trimer had to be purified from a mixture of dimer and trimer [107]. Another procedure to synthesize cationic surfactant trimers uses epichlorohydrin (Scheme 6) to produce cationic trimers with hydrophilic spacers (Fig. 8b) [108]. This route allows interesting variations in the structure. One can also obtain triquaternary ammonium surfactants with two fatty chains or diquaternary ammonium ones with three hydrophobic chains, depending on the nature of the amine that reacts with epichlorohydrin at the first step. The synthesis of diglycidyl ether from diol has been generalized to polyglycidyl ether from polyols [109] and opened the path to the synthesis of sulfonate surfactant trimers with a hydrophilic star-shaped spacer (Fig. 8e) [110,111]. Other surfactants with unequal numbers of ionic groups and hydrophobic chains, triple-chain, double ionic groups, were synthesized from alkylglyceroldiglycidyl ether [112]. Triple-chain surfactants with hydrophobic chains of different lengths were also obtained [112].

Examples of surfactant oligomers.

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SCHEME 4

Nonionic surfactants with three hydrophilic heads and two lipophilic tails have been patented [113]. As Tiloxapol (Fig. 8g) [114], they probably consist of a mixture of different oligomerization degrees. The chemoenzymatic route to sugar-based gemini surfactant described earlier was also used to prepare nonionic surfactant trimers [86].

III.

SURFACE ACTIVITY AND STRUCTURE AT INTERFACE

A.

Air-Water Interface

The surface activity of soluble surfactant oligomers in aqueous solution has been extensively studied by tensiometry to determine their critical micelle concentration (cmc), to address their packing at the air-water interface, and to determine their performance properties (see Appendix, Section VII, Tables 5, 9, 10, 13, 15–

22, 24–27, 29, 31–34, 36–46). The results of are often summarized by four parameters: C20, ␥cmc, ⌫m, and the cmc. The C20, which is the concentration needed to decrease the surface tension by 20 mN/m, characterizes the efficiency of a surfactant to lower surface tension. (The efficiency of the surfactant is actually often reported as pC20 = ⫺log C20.) The C20 value reflects the partitioning of the unmicellized surfactant between the bulk and the interface and is related to the standard free energy of adsorption at the air-water interface [115]. The surface tension at the cmc, ␥cmc, characterizes the effectiveness of a surfactant in lowering surface tension. It is related to the maximum film pressure a surfactant can build up at the air-water interface ⌸cmc, before self-assembling in the bulk is thermodynamically favorable. The ⌫m is the maximum excess surface concentration and is obtained from a ␥-c plot through the Gibbs equation: d␥ = nRT⌫d ln c

SCHEME 5

(1)


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SCHEME 6

These four parameters are related by the following equation [115]: ⌸cmc = 20 ⫹ k⌫m log(cmc/C20)

(2)

From ⌫m, the minimum surface area per molecule of surfactant Am, or per amphiphilic moiety am, has been determined. Nonionic and long hydrophobic chain ionic surfactant oligomers are insoluble in water. The diagram of state of the insoluble monolayers they form at the airwater interface has been established with the Langmuir film balance. The ⌸-A isotherms obtained are characterized by the liftoff area AL, the limiting surface area A⬁, and the collapse pressure ⌸c. AL corresponds to the highest surface area per molecule where a monolayer shows detectable resistance to compression. It is the inverse of the minimum surface concentration at which a surfactant builds up sensible pressure. A⬁ approximates the surface area per molecule at maximum compression and is obtained from the following relation: A⬁ = Ac ⫺ ⌸c (dA/d⌸)⌸c

(3)

where Ac is the area per molecule at ⌸c. 1. Efficiency in Lowering Surface Tension The efficiency of surfactant oligomers in lowering surface tension is greater than that of conventional surfactants (see Appendix, Section VII, Tables 16, 17, 20, 21, 25, 32–34, 39, 40, 42–46). Typical C20 values for m = 12 conventional surfactants lie in the millimolar range, and for m = 12 gemini surfactant C20 values are currently close to 10⫺4 M. This is, of course, correlated with the lower cmc. The lower C20 of gemini surfactants as compared with conventional ones means that the standard free energy of adsorption is more negative. This can result a priori from either an increase in the standard chemical potential of the surfactant in the bulk or a decrease in the standard chemical potential at the

interface. The observation that C20 decreases exponentially with the length of the alkyl chain in most of the gemini surfactants and with the same rate as it does for conventional surfactants suggests that the first hypothesis is the dominant factor. This is because the unfavorable contact between water and hydrocarbon for a gemini surfactant is twice that of the corresponding monomer. When the length of the alkyl chains m exceeds a certain value, which is about 16 but varies with physicochemical conditions, the m dependence of C20 is weaker than expected and can reverse (see Tables 17, 21) [23,39,46,116,117]. In a few cases, C20 has been observed to increase with m. For anionic surfactant trimers (the spacer being star shaped), the C20 increases with m from m = 10 to 14 (see Table 44) [110,111]. These rather surprising results have been observed with surfactant oligomers whose spacer contains heteroatoms or aromatic rings but not with — (CH2)s — spacers. They have been interpreted in terms of premicellization [39,46,116,117]. An alternative explanation could be that intramolecular association occurs between the long alkyl chains. Such intramolecular interactions have been suggested on the basis of volumetric measurements [118]. If the surfactant molecule limits the contact between hydrocarbon chain and water by intramolecular hydrophobic association without losing too much conformational entropy, its chemical potential in water will be reduced and so will its tendency to adsorb at the air-water interface. 2.

Effectiveness and Packing at the Air-Water Interface The effectiveness of surfactant oligomers in lowering surface tension is not very different from that of conventional surfactants. The ␥cmc values for most surfactant oligomers lie between 30 and 40 mN/m. The dependence of ␥cmc on the alkyl chain length has been extensively studied for cationic geminis [39,45,46,119]

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and appears to vary with the composition of the spacer. For — (CH2)s — spacers (hydrophoblic and flexible), ␥cmc decreases slightly when m increases (see Table 13), as observed in conventional surfactants. However, when a heteroatom is present in the spacer (either S, O, or N), the m dependence of ␥cmc is nonmonotonic (see Tables 18–22), and long alkyl chain gemini surfactants are significantly less effective in reducing surface tension [119]. Short-spacer gemini surfactants (s < 5) are more effective than their corresponding conventional surfactants. However, increasing s decreases significantly the effectiveness (increase in ␥cmc) [40,46,52–56,119–123] as illustrated in Fig. 9. This s dependence of ␥cmc is confirmed with trimers. Short-spacer cationic trimers are more effective than short-spacer cationic dimers [104,107], and long-spacer cationic trimers are less effective than long-spacer cationic dimers (Table 43) [104]. The minimum surface area occupied by a surfactant molecule at the air-water interface Am has been determined from the concentration dependence of the surface tension using the Gibbs equation. As already discussed [10], this is rigorously correct only when the surfactant is dissolved in brine because the prefactor n in the Gibbs equation is known (n = 1). In the absence of additional electrolyte, comparisons were made between analogous surfactants, taking n = x ⫹ 1. A neutron reflectivity study suggested that for the cationic gemini surfactant 12-s-12, 2Br, the correct value for n in the Gibbs equation is 2 instead of 3 [124]. Figure 10 shows that diquaternary ammonium geminis with a hydrophilic spacer — (EO)s/3 — are more densely packed at the air-water interface than their homologues with hydrophobic — (CH2)s — spacers. Note that Fig. 10 presents the surface area per amphiphilic moiety am, not per surfactant molecule. The am goes through a maximum between s = 10 and s = 12 in the case of hydrophobic spacers [121], whereas it increases monotonically for oxyethylene spacers [122]. The nonmonotonic behavior in the case of hydrophobic spacers was also observed with arginine-based cationic geminis (Fig. 4b) [77]. For the anionic gemini of Fig. 3d, the minimum surface area per molecule increases monotonically in the range of length studied (from one to four EO groups) (see Table 39) [59]. The nonmonotonic dependence of Am and the position of the maximum have been accounted for theoretically [125,126] by considering the competition between the spacer geometrical characteristics (length and flexibility) and the interactions between the amphiphilic moieties. Monte Carlo simulations [127] have

In

FIG. 9 ␥cmc versus spacer length, s, for 12 — (CH2)s — 12, 2Br (●) [121], 12 — CH2(EO)s/3CH2 — 12, 2Br (䡲) [122], and the compound of Fig. 3d, m = 10, Y = O(EO)s/3-1 [59] (䊱). For comparison, ␥cmc of DTAB is 39 mN/m.

reproduced the experimental observation that hydrophilic spacer geminis have a smaller specific surface area than hydrophobic spacer geminis. The possibility for hydrophilic spacers to buckle into water, where half of the space is forbidden for hydrophobic ones, explains these results. These simulations [127], however, did not reproduce the nonmonotonic dependence of Am upon s for hydrophobic spacers. The packing of an m = 18 cationic surfactant with a rigid phenyl spacer at the air-water interface has also been studied using the Langmuir film balance [39]. The high surface activity of geminis was readily observed in the pressure-area curve: AL = 2.40 nm2/molecule, a value that is close to the square of the molecule dimension in its all-anti conformation. Upon compression the monolayer collapsed at about 0.76 nm2/molecule. The same type of measurements done with succinimide surfactant monomers, dimers, and trimers

FIG. 10 Minimum surface area (at air/water interface) per amphiphilic moiety as a function of the spacer length for cationic dimers: 12 — (CH2)s — 12, 2Br — (䊱) [121]; 12 — (EO)s/3 — 12, 2Br — (●) [122]; arginine-based surfactant (䡲) [77]. DTAB and the arginine monomer have the same specific surface area, which is represented by the dotted line.


[128] showed that AL increases as the degree of oligomerization increases: 0.7, 1.3, and 1.7 nm2/molecule for the C18 monomer, dimer, and trimer, respectively; A⬁ is 0.56, 0.96, and 1.22 nm2/molecule, respectively. For the dimers and the trimers A⬁ was less sensitive to the alkyl chain length (comparison between m = 8, 12, and 18) than for the monomer and was determined by the structure of the headgroup. The ⌸-A curve has been established for glycerophosphate geminis with m = s/2 [71] and amphiphilic phtalocyanines, which can be considered as surfactant oligomers with a cyclic headgroup structure [129]. Neutron reflectivity studies of nonionic sugar derivative geminis [130] and cationic geminis [124] have been reported. 3. Foaming Ability and Foam Stability Gemini surfactants have good foaming properties. Cationic gemini surfactants with short spacers have shown good foamability (with foam volume 10 times that obtained with DTAC) associated with good stability of the foam after 30 min for m = 12 and 14 [45]. The structure of the spacer does not influence the foamability to a large extent but seems to be an important parameter for the stability [45]. The same trends have been observed with anionic gemini surfactants studied by Okahara’s group. With sulfate geminis (Fig. 3b), foamability and foam stability decrease as the spacer length increases [51,52]. Phosphate geminis (Fig. 3c) have shown very good foam stability for Y = (EO)1 or (EO)2 [53]. Sulfonate geminis (Fig. 3a) with m = 12 and short spacers produce about 30% more foam than the corresponding surfactant monomers. They still show good foamability for all spacer lengths, but foam stability is lost when the spacer contains more than two EO groups [54]. The foam stability can be improved by varying the composition of the spacer. For instance, sulfonate geminis with a sulfone group (see the structure in Table 32) in the spacer from very stable foams [57]. With carboxylate geminis (Fig. 3d), larger (35%) volumes of foam can be obtained as compared with the conventional carboxylate surfactant, but its stability is not greatly improved [59]. ␣-Sulfonated fatty acid oligoethylene glycol diester (Fig. 3e) showed some improvement in foam stability but not in foamability (Fig. 11) [62]. The foaming properties of surfactants containing an unequal number of hydrophobic chains and headgroups have also been studied [55,108,112]. The stability of soap films produced from dilute and semidilute cationic gemini surfactant 12-2-12, 2Br solutions have been studied with a thin-film balance [131]. Stable common black films can be produced

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FIG. 11 Foaming properties of the gemini surfactants of Fig. 3e (squares) and of their corresponding monomers (circles). Filled symbols: volume of foam obtained right after shaking (foam ability). Empty symbols: the fraction of foam volume remaining after 30 min standing (foam stability) [62].

from 12-2-12, 2Br solutions at the cmc, but it is impossible to form stable films with the corresponding monomer (DTAB). Only longer chain cationic surfactants can produce stable films by themselves, and the formation of a stable film from DTAB solutions requires addition of a cosurfactant or salt [131,132]. Moreover, upon addition of salt, the 12-2-12, Br soap films undergo a sharp thickness transition from common black films to Newton black films 5–6 nm thick. DLVO theory accounts well for the thickness dependence of the disjoining pressure. It also suggests that the apparent charge density on 12-2-12 2Br films is one order of magnitude lower than on DTAB films (0.0047 C/m2 instead of 0.046 C/m2 for DTAB). This low charge density, in conjunction with a decrease in the hydration due to the spacer between the headgroups, explains the possible transition to Newton black films with 12-2-12. However, it does not explain the difference in film stability, which may be related to the high viscosity of 12-2-12 semidulute solutions. Correlation between foam stability and bulk viscosity has also been pointed out in Ref. [57]. B.

Solid-Water Interface

1. Adsorption Isotherms Multistep adsorption processes have been seen with several cationic gemini surfactants adsorbing onto silica (40 ␮m, washed several times with hydrochloric acid, specific surface area 29 m2/g) [133]. The amount of surfactant adsorbed; the sodium, bromide, and proton concentration in the supernatant; and the electrophoretic mobility of the silica particles were measured along the binding isotherm. The first step consists of a

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rapid but small increase of the surfactant amount adsorbed, followed by a plateau that starts at the point of zero charge. It corresponds essentially to an exchange of the residual sodium ions bound to the silica. After the first adsorption plateau, whose broadness decreases as s increases, a second rapid increase in the amount adsorbed corresponds to the formation of surfactant aggregates at the interface. These aggregates (admicelles) bind bromide ions less than the corresponding bulk micelles (contrary to what has been observed with DTAB). Their positive charges induce a reduction of the pKa of the silanol groups of the silica surface, as evidenced by the sharp drop of the pH (particularly with the short spacer gemini 12-2-12, 2Br) associated with the second step. At saturation, the amount of adsorbed surfactant is inversely proportional to the spacer length, s. It was suggested that for short-spacer gemini surfactants, the first step may involve charge redistribution at the silica interface. In a subsequent study, the same authors compared the adsorption isotherms of DTAB and 12-2-12, 2Br onto the same silica particles treated differently (with and without HCl wash) [134]. The adsorption mechanism of the monomer and the dimer on the unwashed and on the washed silica is qualitatively the same. However, the variation in the state of the surface induces quantitative differences: the amount of surfactant adsorbed at the point of zero charge and at saturation is larger with the unwashed silica. This makes the multistep mechanism difficult to observe with unwashed silica and may explain the results of other studies [104,135]. The adsorption of 12-2-12, 2Br starts at a much lower concentration than for the corresponding monomer DTAB, and the point of zero charge (PZC) of the particles is reached at a much lower concentration for 12-2-12, 2Br. However, the maximum amount differs only a little. Both surfactants keep on adsorbing at the silica surface even after their micellization in the supernatant, saturation being reached at an equilibrium concentration of about 1.5 times the cmc. These results have been confirmed by force balance measurements and direct imaging with atomic free microscopy (AFM) [136]. The charges of the mica surface are neutralized (suppression of the repulsive doublelayer force) at a bulk concentration of 1 to 5 ␮M of surfactant. As the concentration of surfactant increases, hydrophobicity of the surfaces increases (high pull-off force) and discrete surfactant monolayer patches grow and eventually merge. A further increase in concentration (5 ␮M to 0.1 mM) decreases the pull-off force, steadily increases the electrostatic repulsive force, and increases the compressed layer thickness, suggesting

In

the formation of a bilayer. This step was observed directly by AFM to occur also by growth of patches. At a concentration of 2 mM, a full bilayer is formed. The force profile at 0.8 mM presents an extra repulsive force attributed to further adsorption on top of the bilayer. This interpretation is supported by AFM measurement of the surface roughness. The authors pointed out the time dependence of the force profiles obtained and concluded that there was a slow process of adsorption [136]. Adsorption isotherms of DTAB, 12-2-12, 2Br, and 12-2-12-2-12, 3Br on silica (0.3 ␮m and specific surface area 16.7 m2/g) in 10⫺2 M NaBr have been established [135]. Electrophoretic mobility along the isotherm suggests that bilayers are formed with all surfactants, but a two-step adsorption process was observed only for the DTAB. The amount of surfactant adsorbed at saturation decreases from 57 to 48 ␮mol/g from the monomer to the dimer and down to 30 ␮mol/g for the trimer. A higher concentration of salt increases the amount of surfactant adsorbed at saturation, and no addition of salt reveals the two-step adsorption process for 12-2-12, 2Br has been observed only in the absence of salt [137]. The same studies have been carried out on laponite [138] and on titanium dioxide (bare or hydrophobically modified) [139]. The adsorption of cationic trimers of the same type with longer spacers (s = 3 and 6) onto silica has also been reported [104]. 2.

Interfacial Packing and Aggregate Geometry From the amount of surfactant adsorbed at saturation, and knowing the specific surface area of the solid substrate, an average limiting surface area per surfactant molecule is readily obtained. For comparison, because the maximum amount of adsorbed surfactant depends on the state of the substrate surface, the surface area per amphiphilic moiety in gemini surfactants A2 is normalized by the surface area of the corresponding monomer A1 measured in the same series of experiments. For the cationic surfactant 12-s-12, 2Br, the normalized surface area increases linearly with the spacer length (Fig. 12) [133]. The average surface area occupied by an amphiphilic moiety is larger than that for DTAB except for s = 2. This spacer dependence is amplified with higher degrees of oligomerization (Fig. 13). For short spacers (s = 2 [135] and s = 3 [104]), the area per amphiphilic moiety slightly decreases with the degree of oligomerization. This means that each amphiphilic moiety is more densely packed in layers of surfactant oligomers with short spacers. However, for long spacers (s = 6), the surface area increases almost lin-


FIG. 12 Normalized limiting surface area (at silica/water interface) per amphiphilic moiety in 12-s-12, 2Br gemini surfactants as a function of the spacer chain length, s [133]. Normalization is done with respect to the limiting surface area of DTAB, A1, measured in the same series of experiments; ‘‘s = 0’’ corresponds to DDAB [140].

early with the degree of oligomerization [104]. For comparison, results obtained for C12 multiple-chain surfactants with one cationic headgroup [140] have also been reported (Fig. 13). This illustrates the fine-tuning of the packing that can be achieved with surfactant oligomers by playing with the spacer length and the degree of oligomerization. By AFM, using the precontact repulsive force (within the electrical double layer) [141,142], Manne et al. observed directly the aggregates formed by the cationic gemini surfactants 12-s-12, 2Br on the cleavage plane of mica [143]. The gemini surfactant with the shortest spacer, s = 2, which gives wormlike micelle in bulk solution, forms bilayers on mica surfaces. Bilayers were also observed with the double-chain sur-

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factant DDAB, known to form vesicles in dilute solutions. Parallel cylinders are obtained when adsorbing the 12-4-12, 2Br surfactant and DTAB. These surfactants form spherical micelles in dilute solutions, which can slightly elongate at high enough concentration for the surfactant dimer. With the single-chain divalent surfactant, referred to as 12-2-1, 2Br, spherical admicelles form. From these observations, the authors concluded that the dimensionless packing parameter as defined in Ref. 32 to explain the morphology of micelles in the bulk determines the shape of the interfacial aggregates as well. However, the mica surface playing the role of a huge ‘‘counterion,’’ the curvature of the aggregate at the interface can be (and most often is) lower than the curvature of the aggregate in the bulk. IV.

STRUCTURE AND PROPERTIES OF SURFACTANT OLIGOMERS SELF-ASSEMBLIES

A.

Critical Micelle Concentration

The cmc of surfactant oligomers has been measured by tensiometry, conductimetry, dye solubilization measurements. Gemini surfactants are characterized by a cmc that is 10 to 100 times lower than that of the corresponding conventional surfactant (monomer), the reduction factor being essentially determined by the cmc of the monomer. Cmc values are reported in the tables of the Appendix. It can be seen that different methods can yield very different values. Some difficulties in determining the cmc have been reported rather often for geminis and surfactant oligomers. In conductivity measurements, ion pairing can sometimes interfere with micellization, especially with short-chain surfactants [144]. Slow adsorption at the interface may sometimes mask the cmc in surface tension measurements. This has already been discussed [1]. 1.

FIG. 13 Normalized limiting surface area (at silica/water interface) per amphiphilic moiety as a function of the degree of oligomerization x [104]; s = 3 (●); s = 6 (䊱); surfactant tetramer of Fig. 8c (䡲); multiple chain surfactants, ‘‘s = 0’’ (⽧) [140].

Alkyl Chain Length Dependence of the Cmc—Comparison with Monomers The hydrophobic chain length m is not a variable specific to surfactant oligomers. However, the study of its influence on the cmc yields good insight into the micellization properties of surfactant oligomers. In most cases, the m dependence of the cmc is classical, meaning that the cmc decreases exponentially as the alkyl chain length increases (see Tables 14–24) [145,146]: ln cmc = A ⫺ Bmm

(4)

Figure 14 shows that the Bm factor is nearly inde-

74

In

cmcx = x.(cmc1)x

FIG. 14 Cmc versus alkyl chain length, m, in gemini and monomeric homologues: m-2-m, 2Br (●) [146]; m-6-m, 2Br (䊱) [145]; monomer (䡲) [155].

pendent of the spacer length and rather close (but not equal) to that obtained for conventional surfactants. The same has been observed for the compounds of Fig. 2e when compared with their monomer (see Table 23) [42] and for the anionic gemini of Fig. 3e (see Table 30) [62]. This means that the free energy of transfer of one CH2 from water into the micelle core, ⌬Gtr (CH2), is close in both types of surfactants [38,42,63]. This provides an important clue to understanding the low cmc values of surfactant oligomers. Gemini surfactants have lower cmc values than conventional ones because each molecule contains more methylene groups, which water does not like to solvate. The slope Bm is actually not equal for both types of surfactant, and the two straight lines in Fig. 14 become farther apart when m increases. (Bm is 1 for geminis and 0.7 for monomers, but for a correct comparison the Bm value of 1 should be divided by 2, because m corresponds to only half the number of methylene groups in geminis.) This means that the ratio cmc(monomer)/cmc(dimer) increases with m. Thus, when going from the monomer to the dimer, the cmc is decreased by a factor that is related to the cmc of the monomer. This suggests that the standard free energy of micellization per amphiphilic moiety ⌬G⬚M is equal in both types of surfactants. This can be better understood by considering the micellization equilibrium, NSx S [Sx]N, for an nonionic oligomer surfactant Sx which form micelles with aggregation number N (in number of surfactant molecules). The mass action model allows to relate the cmc (expressed in mole of amphiphilic moiety per liter) to the free energy of micellization per mole of amphiphilic moiety, as follows: ⌬G⬚M = RT(1/x)ln(cmcx) ⫺ (1/x)RT ln x

(5)

Assuming ⌬G⬚M to be independent of x leads to the following relation:

(6)

where cmcx is the cmc of the oligomer and cmc1 the cmc of the corresponding monomer. Equation (6) shows that the cmc of a surfactant dimer is twice the square of the cmc of the corresponding monomer. Thus, if we can assume that the free energy of micellization of an amphiphilic moiety does not depend on the structure of the surfactant it belongs to, then the reduction in cmc when going from the monomer to the dimer is half the cmc of the monomer. ⌬G⬚M for cationic oligomers has been proved to be approximately independent of x and equal to ⫺20 kJ per mol of amphiphilic moiety [104], using the following relation [147]: ⌬G⬚M = RT(1/x ⫹ ␤)ln cmc ⫺ (1/x)RT ln x,

(7)

where ␤ = 1 ⫺ ␣ is the degree of association of the counterions to the micelles, and where the cmc is expressed in mole of amphiphilic moiety per liter. Considering ⌬G⬚M independent of x is a very good first approximation. We can however notice small differences (see later Fig. 23) that are going to be discussed in Section II.A.3. Ion pairing and intramolecular interaction between the hydrophobic tails of the surfactant oligomer are among the factors that would decrease the absolute value of ⌬G⬚M and increase the cmc. In establishing Eqs. (5) and (7), a mixing entropic term (common to any aggregation phenomenon) has been neglected. Indeed, Eqs. (5) and (7) are obtained by neglecting the molar micelle concentration 兩[Sx]N兩. This is reasonably close to the cmc and when N is large. However when x increases, we can expect N to tend to 1. (This supposes that the aggregation number n, expressed in number of alkyl chain, is independent of x and equal to Nx. This has been shown for cationic oligomers.) In other words, micellization of a surfactant oligomer is entropically more favored than micellization of the corresponding monomer, because part of the mixing entropy has already been lost at the synthesis step. The importance of this contribution largely depends on m and on the nature of the head group (charge and valence of the counter ions). The smaller m is, the more important is this contribution, because 兩⌬G⬚M兩 and n = Nx decrease when m decreases. For the cationic oligomers with m = 12 and bromide counter-ion, this contribution is not significant when x < 5. If x eventually increases enough to make the contribution of the mixing entropy of the amphiphlic moiety significant, a thermodynamic description of the micellization will become a polyelectrolytes problem


where ion condensation and conformational entropy of the head group backbone have to be taken into account. In Fig. 15, the cmc is plotted against x ⫻ m, the total number of methylene groups belonging to the hydrophobic tails. It can be seen that, to get the same cmc with a dimer as with an m = 16 conventional surfactant, the surfactant dimer must contain 24 methylene groups in its hydrophobic chains. This may sound like a waste and is due to the fact that the additional methylene groups in gemini surfactants come with an additional headgroup. Thus, many of the methylene groups are close to a hydropholic charged group and do not trigger micellization. There is, however, an interesting benefit of this apparent waste. The vertical dotted lines in Fig. 15 correspond approximately to the maximum number of methylene groups a surfactant can contain to be soluble in water (meaning neither crystals nor mesophases) at room temperature. It is below 16 for monomers and above 32 for dimers and reaches at least 36 for trimers. Hence, the benefit of surfactant oligomers may not be as much to with reducing the cmc as compared with conventional surfactants. It is certainly to allow cmc values that could never be reached by increasing the length of a conventional surfactant because this would have induced a phase separation [108]. In cationic surfactant heterodimers, m-2-m⬘, 2Br, the cmc depends not on the difference (m ⫺ m⬘) but on the total number of methylene groups in the surfactant [87]. The m dependence of the cmc values sometimes deviates from the exponential behavior described before when the alkyl chain becomes longer than a certain length (Fig. 16) and can sometime reverse (Table 16). This has been observed when the spacer contains either aromatic rings or oxygen atoms (oxyethylene or hydroxypropylene spacers) [23,39,46,116,117]. The onset

FIG. 15 Cmc versus number of methylene groups per surfactant molecule for cationic monomers (䡲), dimers (●), trimer (䊱), and tetramer (⽧).

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FIG. 16 Deviation from the classical exponential m dependence of the cmc of cationic gemini surfactant of Fig. 2c in 0.01 M NaCl (䡲), and 0.1 M NaCl (●) at 50⬚C [116].

length of this unusual behavior decreases with increasing ionic strength [116,117]. With the star-shaped anionic trimer (Fig. 8e), the cmc increases with m [110,111] (Fig. 17). This unusual behavior is necessarily related to hydrophobic interactions. The formation of premicellar aggregates has been proposed to explain it [39]. Equilibrium constants for the formation of premicellar aggregates have been calculated from the difference between the experimental ␥ –log C plots and virtual plots established by extrapolating to high m values results obtained at low m values [46,116]. Alternative hypotheses should be considered with more attention. An increase of the cmc means a decrease in the absolute value of the free energy of micellization. This can result either from a decrease of the chemical potential of the free (unmicellized) surfactant ␮ ⬚s or from an increase of the chemical potential of the surfactant in the micelles ␮ m⬚ . In the same way, the unusual m dependence of the C20 mentioned earlier can result either from a decrease of ␮ s⬚ or from an increase of the chemical potential of the surfactant adsorbed at

FIG. 17 Inverted m dependence of the cmc in anionic trimers with hydrophilic star-shaped spacers (see structure, Table 44) [110,111].

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the air-water interface ␮ ⬚A/W. Premicellization indeed reduces the chemical potential in the bulk and explains lower surface activity and higher cmc. But an alternative, which would be less expensive in terms of mixing entropy, would involve intramolecular association between the alkyl chains of a surfactant oligomer. This hypothesis has been suggested by experimental observations of the change in enthalpy and in volume upon micellization [118]. Intramolecular association would decrease the hydrophobic hydration shell and thus decrease ␮ s⬚ and increase the cmc as well as C20. The other alternative corresponds to an increase of ␮ m⬚ and could result, for instance, from the formation of micelles in which the hydrocarbon moieties would largely remain in contact with water. This would achieve Menger’s initial goal [23] but would probably not lead to an increase in C20. A convincing explanation for the unusual m dependence of the cmc is still to be found. NMR conformational studies of the long-chain geminis such as the one carried out on m = 8 cationic surfactants with o-, m-, and p-phenylenedimethylene spacers [148] could be helpful. For this system, a neutron scattering study supports the formation of premicelles [149]. Also, an accurate determination of the Kraft temperature as done for 16-s-16, 2Br surfactants [150] would clarify the situation. Finally, Monte Carlo simulations, in which the cmc is defined as the surfactant concentration at which half of the surfactants have at least one surfactant as nearest neighbor [127,151], also yield an increase of the cmc as m increases.

In

FIG. 18 Cmc versus spacer chain length for carboxylate (Fig. 3d) (●), phosphate (Fig. 3c) (䡲), sulfonate (Fig. 3a) (⽧), and sulfate (Fig. 3b) (䊱) disodium gemini with m = 10 [59].

linear scale. The same holds for anionic gemini surfactants (Table 35). For the series m = 12, s has been varied up to high values [38,153]. The decreasing part of the curve has been explained by the increasing hydrophobicity of the surfactant. For s larger than or equal to 10, the cmc

2.

Headgroup Nature Dependence of the Cmc As mentioned before, the cmc of gemini surfactants is essentially determined by the cmc of the corresponding monomer. Hence the influence of the headgroup, and the dependence of the cmc on the nature of the headgroup, is the same as in the conventional surfactant. Figure 18 shows that for a given s/3, the cmc of anionic gemini surfactants varies with the headgroup nature as COONa > OPO(OH)(ONa) > O(CH2)3SO3Na > OSO3Na [59]. 3.

Spacer Chain Length Dependence of the Cmc The cmc of cationic surfactants m-s-m, 2Br varies nonmonotonically with s when the spacer is hydrophobic (Fig. 19) (Tables 3–7). It increases for short spacers up to four or five methylene groups, then decreases. This has been observed for m = 8 [148], 10 [152], 12 [38], and 16 [41]. Note that the comparison is done on a

FIG. 19 Spacer length dependence of the cmc for cationic gemini m-s-m, 2Br: m = 8 (⽧) [148]; m = 10 (䡲) [152]; m = 12 (●) [38]; m = 16 (䊱) [41].


77

depends on s in the same way as it depends on m [38,153]: ln cmc = A ⫺ Bss

(8)

The factor Bs = 0.3 is smaller than Bm/2 = 0.5. When long enough, the hydrophobic spacer group can buckle into the micelle core. However, this is apparently not so easy considering the low value obtained for Bs , which is even smaller than that found for bolaform surfactants [154] (Fig. 20). The data of Fig. 20 suggest that the impediment to the spacer being inserted into the hydrophobic core of the micelle results from the combined effect of electrostatic interaction, loss of conformational entropy (as in a bolaform surfactant), and steric hindrance (as in double-chain surfactants). The increase of the cmc with s when s < 5 (Fig. 19) is probably related to electrostatic interactions between the headgroups. When the spacer is short, part of the work against electrostatic repulsion necessary to bring the surfactants together upon micellization has already been done at the synthesis step as discussed in Ref. 99. This hypothesis is supported by several arguments. First, the cmc increases with s up to s = 4–5, which corresponds to the length of the spacer at which the interfacial surface area per amphiphilic moiety is equal in gemini and in conventional surfactants. The second argument relies upon Monte Carlo simulations. With ionic gemini surfactants, nonmonotonic variation of the cmc is observed, whereas the cmc of nonionic gemini surfactants increases monotonically with s [127]. This small electrostatic effect is clearly pointed out by considering the free energy of micellization per amphiphilic moiety. ⌬GM is slightly more negative for

FIG. 20 Influence on the cmc of increasing the number of methylene groups n in the hydrophobic tail of a conventional surfactant [CnH2n⫹1N(CH3)3, Br] (●), in a bolaform surfactant [(CH3)3NCnH2nN(CH3)3, 2Br] (⽧), in a double-chain surfactant [C12H25CnH2n⫹1N(CH3)2, Br] (䡲), and in the spacer of a gemini surfactant [C12H25(CH3)2N(CH2)nN(CH3)2 C12H25, 2Br] (䊱).

FIG. 21 Ratio of cmc of the cationic geminis 12-s-12, 2Br (cmc2) over the cmc of the corresponding monomer C12H25 ⭈ Cs/2Hs⫹1N(CH3)2, Br (cmc2/cmc1) (●) and standard free energy of micellization per amphiphilic moiety ⌬GM (䡲) versus spacer length s.

short spacers than for long spacers (see Fig. 21) [104,152]. The differences in ⌬GM are not large but they are systematic, and the trend is confirmed with surfactant trimers and tetramers [104]. ⌬GM decreases with the degree of oligomerization for s = 3, whereas it is constant for s = 6 (see Fig. 23). To understand the s dependence of the cmc, it is useful to compare the cmc of geminis 12-s-12, 2Br with the cmc of double-chain surfactants C12H25Cs/2Hs⫹1N ⭈ (CH3)2, Br [155,156]. The latter correspond closely to the monomers in the sense that they have the same number of methylene groups per headgroup. Figure 21 shows that the reduction factor of the cmc, going from the monomer to the dimer, increases as the spacer increases. This increase is not regular and closely related to the variation of ⌬GM. Note that only for s = 10 and 12 is ⌬GM less negative than ⌬GM of DTAB.* With hydrophilic oligo(oxyethylene) spacers, the cmc increases with s for cationic (see Tables 10 and 11) [47,48,49] as well as for anionic surfactants (see Table 30 and Fig. 18). A slightly lower cmc has been observed for cationic geminis of Fig. 2b with very large oxyethylene spacers (Table 11) [47]. When hydrophilic spacers become very large, gemini surfactants look like telechelic hydrophobicvally modified polymers, which are known to micellize at fairly low concentrations to *This observation has to be related to the structure of the micelles, in which the spacer has been shown to remain largely in contact with water [167]. This might correspond to the situation Menger was expecting [23] and is actually unfavorable for micellization.

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form flowerlike micelles [157]. This has, however, not been observed with anionic gemini surfactants of Fig. 3e with spacers consisting of up to 35 EO groups [62] (Table 30). The chemical nature of the spacer influences the cmc value in a way that is sometimes difficult to rationalize. For intermediate spacer lengths, the cmc is lower when the spacer is hydrophilic than when the spacer is hydrophobic (see Tables 13 and 16). The cationic surfactant trimer with hydroxypropylene spacer 12-3*-12-3*12, 3Cl (Fig. 8b) has a cmc of 9.6 mM, whereas 12-3-12-3-12, 3Cl has a cmc of 160 mM. Devıńsky et al. observed slight changes in the cmc of cationic gemini surfactants with different spacers of the type — CH2CH2 — X — CH2CH2 — , with X = CH2, NCH3, O, or S [119]. In this study, the lipophilicity of the spacer seems to be the determining parameter. The ionization degree of the micelles is independent of s for m = 8 (Table 3) but increases with s for m = 10 and 12 (Tables 4 and 5). 4. Oligomerization Degree Figure 22 shows the decrease of the cmc as the degree of oligomerization x increases for an m = 12, s = 3 series of cationic surfactants [104]. The cmc appears to vary as a power law of the oligomerization degree for this series with s = 3, and the same is observed with s = 2 [107] and s = 6 [104] up to the trimer. The cmc of the cationic tetramer is 2.5 orders of magnitude lower than that of DTAB. The ionization degree of the micelle at the cmc, ␣, is independent of x and is essentially determined by m and s (see Tables 3–5) [104]. With bromide counterions and for m = 12, ␣ = 0.2 for s = 3 and ␣ = 0.3 for s = 6, independent of x. The free energy of micellization decreases (becomes more negative) for short spacers but is constant for long spacers (Fig. 23). B.

FIG. 22 Cmc versus oligomerization degree for cationic surfactant oligomers m = 12, s = 3 [104].

havior has been obtained for the corresponding monomer, m-s/2 [158]. Micropolarity does not change with spacer length in cationic gemini 16-(EO)s/3-16, 2Br [48]. The micropolarity of cationic surfactant oligomers does not depend on x [104,158] but slightly decreases with x in nonionic surfactant oligomers of Fig. 8g [114]. The solubilization capacity for transazobenzene, as expressed by the ratio of solubilizate concentration over surfactant concentration, increases monotonically with m in cationic geminis as with conventional surfactants (see Table 14) [159]. It varies nonmonotonically with s, going through a maximum at s = 6, where it is about twice that of s = 2 and five times that of s = 12 (Table 4). The solubilization of toluene or n-hexane by cationic gemini surfactants is more efficient than by cationic surfactant monomers [40]. Cationic geminis have higher selectivity for toluene than for hexane [40]. Solubilization of ␤-naphthol in short spacer cationic surfactant dimers and trimers adsorbed to silica [135,137], titanium oxide [139], and laponite [138] increases with x. This is true when expressed as the molar ratio of ␤naphthol adsolubilized to the adsorbed surfactants.

Micelle Properties

1.

Micropolarity, Solubilization Capacity, and Emulsification The micropolarity of cationic surfactant oligomers has been characterized by the value of the fluorescence intensity ratio I1/I3 of the first and third vibronic peaks in the emission spectra of micelle-solubilized pyrene [48,92,158]. It depends on the composition of the pyrene solubilization site, i.e., near the micelle-water interface. For cationic geminis with hydrophobic — (CH2)s — spacers, the micropolarity varies nonmonotonically with the spacer chain length, going through a maximum at about s = 6 [158]. Similar be-

FIG. 23 Standard free energy of micellization per cationic amphiphilic moiety versus degree of oligomerization x for s = 3 (●) and s = 6, m = 12 (䡲) [104].


However, as pointed out in Ref. 135, the solubilization capacity decreases with x when expressed per dodecyl chain. This has been interpreted as a result of the increasing packing density as x increases. The emulsification efficiency of cationic geminis was determined by comparing the rate of drop coalescence between heptane/water emulsions prepared from cationic geminis and their monomeric homologues. The drop coalescence was characterized by an exponential decay of the number of drops. The lifetime of the drops was found to be 1.7 times longer with the geminis [43]. The emulsification properties of nonionic diol geminis has also been studied [57]. The phase behavior of ternary water/styrene/C12 cationic gemini surfactants with hydrophobic [160] and hydrophilic [122] spacers of different lengths has been reported. The extension of the single-phase region that lies in the water corner of the phase diagram triangle depends strongly on the spacer chain length for hydrophobic — (CH2)s — spacers and more weakly for hydrophilic — (EO)s/3 — spacers. The extension of the single-phase region is strongly temperature dependent with — (EO)s/3 — spacer but weakly with — (CH2)s — spacers. At a fixed concentration of surfactant, between 5 and 20 wt%, only the 12-2-12, 2Br surfactant had poorer solubilization capacity than DTAB (expressed as the molar ratio of solubilized styrene over surfactant). With hydrophobic spacers, the solubilization capacity increases with s and is maximum for s = 12, at which it is six times higher than for DTAB. With hydrophilic spacers, it is maximum for spacers consisting of one or two EO groups. The influence of temperature, spacer rigidity, and oil size on the oil-water-geminis ternary phase diagram has also been studied by Monte Carlo simulation [161]. 2. Microviscosity The microviscosity of gemini surfactant micelles decreases when the spacer goes from 2 to 12 in a 16-s16, 2Br series when the spacer is hydrophilic [41] but not much when it is hydrophobic [48,70,114,158]. The microviscosity depends, however, almost linearly on the degree of oligomerization x and is about 6 to 10 times (depending on the temperature) higher for the cationic tetramer than for the monomer [104,158]. This has also been observed for nonionic oligomer micelles, in which the dipyrenylpropane excimer lifetime is three to four times larger [114]. Microviscosity of admicelles on silica determined from the order parameter of a paramagnetic probe varies with the oligomerization degree in the order dimer > trimer > monomer [135] and increases with added salt [137].

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C.

Morphology of the Aggregates

The size and the shape of surfactant oligomer micelles have been studied by small-angle neutron scattering (SANS) [41,48,152,162–165] and directly observed by transmission electron microscopy at cryogenic temperature (cryo-TEM) [22,166,167]. Micellar shape can also be inferred from solubilization studies [159] or from the concentration dependence of the aggregation number determined by fluorescence quenching measurements [103,166]. The spacer length is a key parameter of the micelle morphology [22,166], as could have been deduced from the s dependence of the surface area. Hydrophobic short spacers (4 ⱖ s) reduce the preferred curvature of the micelles as compared with conventional surfactant micelles. With cationic geminis, wormlike micelles are obtained when m = 12. Spacers of intermediate length (5 ⱖ s ⱖ 12) favor the formation of spherical micelles. Interestingly, the spherical shape is preserved up to very high concentrations for s = 10 and 12 [168]. Thus, increasing s can be seen as releasing the spacer constraint for lower intermediate spacers but actually corresponds to a strong constraint for upper intermediate spacers. For long spacers (s ⱖ 16) vesicles are obtained as in the corresponding surfactant monomer (double chain) [22,166,167]. The trend is confirmed by SANS of 16-s-16, 2Br surfactants [164,165]. Because of electrostatic interactions, the scattered intensity presents a maximum at a finite wave vector q*, which is inversely proportional to the distance between the micelles. At low enough concentration, the distance between the micelles reflects the size of the micelles. At a fixed low concentration (between 10 and 50 mM) of 16-s-16, 2Br surfactants, q* increases as s increases from 5 to 12, suggesting that the aggregation number of the micelles decreases as s becomes larger. The scattered intensity 16-3-16, 2Br varies as q⫺2. This has been interpreted as the signature of the formation of disks, but cryo-TEM micrographs showed vesicles and bilayer membrane fragments coexisting with wormlike micelles [166] (and this is consistent with I ⬀ q⫺2). The same results have been obtained with m = 16 phosphate geminis of Fig. 3f [70]. For s = 2, the scattered intensity varies as q⫺2, which indicates zero curvature objects (disks or vesicles). For s = 4 wormlike micelles and for s = 6 or 10 prolate ellipsoids are formed. With hydrophilic spacers (EO), the aggregation number of the micelles also depends on the length of the spacer. But even with the shortest spacer (one EO), the growth of the micelle is limited and the influence

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of the spacer length on the size of the micelles is less pronounced with hydrophilic spacers than with hydrophobic ones [41,48]. Nonionic sugar-based geminis of Fig. 5a, with m = 14, form cylindrical micelles when s = 6 and 8 and vesicles when s = 10 [84]. Nonionic sugar-based geminis of Fig. 5b form anisotropic micelles, cylindrical for 7 ⱖ m ⱖ 5 and discoidal for m = 8 [163]. 1.

Wormlike Micelles of Cationic Surfactant Oligomers

(a) Micellar Growth. Cationic surfactant oligomers with short spacers are among the few systems in which the transition from spherical to very long wormlike micelles occurs at low concentration (below 10 wt%) and does not require addition of salt or cosurfactants or the presence of hydrophobic counterions. The formation of long wormlike micelles was directly observed by cryoTEM in the 12-s-12, 2Br series [166,167]. However, the micellar growth can be described more quantitatively by looking at the concentration dependence of the aggregation number N(c), which is obtained by SANS [152,162] or fluorescence quenching measurements [103,167]. The concentration dependence of the zero shear viscosity also gives information on micellar growth [169–171]. The N(c) has been analyzed with the ladder model [172], which describes a prolate micelle as a cylinder capped at each end by hemispherical micelles. The concentration dependence of N is then expressed as N = N0 ⫹ 2K 1/2(c-cmc)1/2

(9)

where N0 is the aggregation number at the cmc and c and cmc are mole fractions here. K = exp(Ec /kT)

TABLE 1 Characteristic Parameters of the Micellar Growth of 10-s-10, 2Br Geminis [152,162] s

N0

Ec /kT

2 3 4 6 8 10 12

25 23 24 22 17 18 13

15 12 10 7 5 5 6

N0 is the aggregation number at the cmc; Ec is the end-cap energy.

the differences in end cap energy it yields are not pronounced in view of the large differences in viscosity observed at higher concentrations. Fluorescence quenching and SANS can provide information on the elongated micelle sizes only at low concentration. In this concentration range, the micelles are charged and not screened, and their growth is hindered by electrostatic repulsion [173]. Their growth rate results not only from the end-cap energy but also from an electrostatic contribution that favors the breaking of the micelles. This contribution decreases with increasing concentration. Three growth regimes have been distinguished [173]: at low enough concentrations, such that the Debye screening length is larger than the micelle size, the concentration dependence of the size is weak and the micelles are nearly monodisperse. As the concentration increases, a sharp crossover to a rapid

(10)

where Ec is the end-cap energy, i.e., the excess chemical potential of a surfactant in the end caps compared with the chemical potential of a surfactant residing in the central cylindrical portion. This equation describes well the SANS results obtained for 10-2-10, 2Br geminis [152,162]. The parameters deduced from such an analysis are presented in Table 1. The end-cap energy decreases as the spacer length increases. When applied to the data obtained by fluorescence quenching for the m = 12 series of cationic surfactant oligomers [103,167], the ladder model yields an endcap energy of 11 kT for the 12-5-12, 2Br, 13 kT for the 12-3-12, 2Br, and 17 kT for the trimer 12-3-12-312, 3Br. Data in Fig. 24 show that when the tendency of the micelles to grow is strong, the ladder model applies only for the lowest concentrations. Moreover,

FIG. 24 Aggregation number of cationic surfactant oligomers: 12-5-12, 2Br (䡲); 12-3-12, 2Br (●); 12-3-12-3-12, 3Br (⽧) [103,166] analyzed with the ladder model; c, the surfactant concentration, and the cmc are expressed in mole fraction.


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growth regime occurs (when the Debye length equals the micelle size). The crossover concentration coincides with the concentration c* at which the micelles begin to interact with each other (semidilute regime). As in the case of neutral micelles, the size distribution is large (exponential), but the characteristic size, N, grows faster than c1/2 governing the growth of neutral micelles [Eq. (9)]. Its concentration dependence reads N ⬇ 2c1/2 exp[E/2kBT ⫺ lB a␯2/2c]

(11)

where lB is the Bjerrum length, a is the diameter of the micelle, c is the volume fraction and ␯ is an apparent charge density of the micelle. At higher concentration, the electrostatic contribution that tends to break the micelles results essentially from the entropy of the counterions near the end caps, where they are less tightly bound. The growth may be characterized by an effective power law: N ⬀ c(⌳⫹1)/2

(12)

where ⌳ is related to the net charge on an end cap and depends only logarithmically on c [173]. The crossover concentration c* from the slow to the fast growth regime is observed in the concentration dependence of zero shear viscosity [169,174]. For low concentration, the viscosity of surfactant oligomer solutions is not significantly higher than the viscosity of water. But at c > c*, the viscosity increases very rapidly (Fig. 25). According to Mackintosh et al. [173], c* ⬀ E⫺1/2 and c this allows a comparison of the end-cap energy among various surfactant oligomers. In Table 2 we reported the values of c* and 10/兹c*, which is proportional to Ec, for various cationic surfactant oligomers. When m = 12, decreasing s from 3 to 2 doubles the end-cap energy. The same result is obtained by going from the dimer to the trimer, keeping s = 3 constant [170]. The rheology of heterodimers m-2-m⬘, 2Br has been studied by Oda et al. [171]. Differences in alkyl chain length markedly affect the end-cap energy (see 12-2-12, 102-14, and 8-2-16 in Table 2). End-cap energy values can be estimated rather indirectly from the dynamical properties of the systems (rheology or diffusion coefficient). For instance, in the plateau region of the relaxation spectrum, the storage modulus G⬘ = G0 is nearly independent of the frequency and the loss modulus G⬙ goes through a minimum. The ratio G0/G⬙min is related to the ratio of the length of the micelles to the mesh size of the entanglement network. The latter depends essentially on the concentration, whereas the temperature strongly determines the micelle length. The temperature dependence

FIG. 25 Concentration dependence of the zero shear viscosity of aqueous solutions of 12-2-12, 2Br (⽧), 12-3-12, 2Br (●), 12-3-12-3-12, 3Br (䡲), and 12-3-12-4-12-3-12, 4Br (䊱). (From Ref. 104, with permission. Copyright (2000) American Chemical Society.)

of the ratio G0/G⬙min gives an end-cap energy of about 50 kT for 12-2-12, 2Br at 4% but lower values as the concentration increases (down to 30 kT at 10%) [169]. For the trimer 12-3-12-3-12, 3Br, the same analysis also leads to a decrease of the end-cap energy from 80 to 10 kT as the concentration increases from 4 to 10%

TABLE 2 Crossover Concentration from Slow to Fast Micellar Growth Regime c* for Cationic Surfactant Oligomers Surfactant 12-2-12 14-2-14 16-2-16 12-3-12 8-2-16 10-2-14 12-2-16 14-2-18 12-3-12-3-12 12-3-12-4-12-3-12

c* (wt%)

10/兹c*

1 0.08 0.015 4 6 3 0.15 0.07 1 0.5

10 35 82 5 4 6 28 38 10 14

c* is determined from viscosity measurements, as the concentration at which the viscosity is twice the viscosity of the water; 10/兹c* is directly proportional to the end-cap energy.

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(unpublished results). The accuracy of such an analysis is, however, questionable and would require a better understanding of the relaxation mechanism to be proved. Diffusion coefficient measurements by fluorescence recovery after photobleaching (FRAP) [175], interpreted assuming that the Cates model [176] holds in the concentration range studied, yields about 30 kT for 12-2-12, 2Br, 12-3-12, 2Br, and 16-4-16, 2Br, inconsistent with the differences observed in c* [175]. The end-cap energy can also be estimated by fitting the concentration dependence of the zero shear viscosity in the fast growth regime [169]. This supposes assuming a relation between the viscosity, the length of the micelles L (proportional to N), and the concentration c and introducing it in the growth law for charged micelles [Eq. (11)]. This has been done for the 12-312, 2Br and 12-3-12-3-12, 3Br surfactants [170], assuming the Fuoss law:

␩0 = Lc1/2

(13)

leading to Ec = 40 and 80 kT, respectively. Fuoss’ law has been assumed, rather than the relations proposed in Ref. 169, because the micelles were probably not fully entangled in the concentration range in which the viscosity increases rapidly (see next section) [170]. According to the values of 10/兹c* and the estimated values of Ec for m = 12 surfactants, surfactants with a longer chain length (16-2-16, 2Br, for example) would have very high end-cap energies of several hundreds of kT. These are unreasonable values and show that large m surfactant oligomer solutions have been most often studied in a metastable state [171,177], and at equilibrium they exist as two-phase systems. (The Kraft temperature of 16-2-16, 2Br is 45⬚C [150].) In those conditions, the increase in viscosity probably does not reflect the growth of wormlike micelles. Addition of DTAB to 12-2-12, 2Br decreases the size of the micelles, but DTAB does not concentrate in the end cap [178]. (b) Rheology. Cationic surfactant oligomers provide systems of charged and unscreened wormlike micelles, and many aspects remain to be understood in the dynamics of these polyelectrolyte type of living polymers [179]. For instance, as the concentration increases, ␩0 goes through a maximum at a concentration c** and then decreases (Fig. 25) [169,170,171]. The same is observed for relaxation time as well as for the diffusion coefficient [175]. This decrease has been attributed to a shortening of the micelles due to a theoretically pre-

dicted increase in ionization degree [169]. However, a decrease in the relaxation time and in the viscosity is also observed upon addition of salt [169,174], which is expected to increase the length of the micelles. [Upon further addition of salt, 12-2-12, 2Br solutions phase separate, leading to the coexistence of a dilute micellar phase and a lamellar phase [180]. Addition of salt to 12-3-12, 2Br solutions yields phase separation, but in this case a hexagonal phase is formed (unpublished results).] It has been proposed that, in the concentration range where the viscosity increases rapidly, the systems were not fully entangled [170]. This is suggested by the strong concentration dependence of the elasticity at low concentration (Fig. 26). The crossover to a fully entangled regime seems to be reached at maximum viscosity concentration, c**. For fully entangled systems, the elasticity is expected to vary as c2, as observed for the dimer 12-3-12, 2Br system at c > 10 wt% (Fig. 26). The existence of a concentration regime of overlapping yet not fully entangled micelles may be a clue to understanding the nonmonotonic behavior of the viscosity. It also provides a simple explanation for the increase of the elastic plateau modulus upon addition of salt observed in 12-2-12, 2Br [181] and 12-3-12, 2Br solutions (unpublished results). It may also explain why the temperature dependence of viscosity for concentrations close the maximum in viscosity does not follow the Arrhenius law [169]. The extension of the concentration range where the micelles overlap and are yet not entangled (expressed as c**/c*) would reflect the rate at which they grow [170] and could provide a more reliable method to estimate Ec.

FIG. 26 Concentration dependence of the elasticity (inverse of the recoverable compliance) of 12-3-12, 2Br (●) and 12-3-12-3-12, 3Br (䡲) aqueous solutions [170].


The nonlinear rheology of 12-2-12, 2Br solutions has been subject to several studies. As in other wormlike micelle systems, shearing solutions of 12-2-12, 2Br close to c* induces thickening [182–184]. The shear rate inducing thickening decreases with the concentration and increases with temperature [184]. Shear thickening is associated with anisotropy in neutron scattering [182] as well as in refractive index and conductivity [183]. Cryo-TEM micrographs of sheared samples [184] have shown that a phase separation occurs between surfactant-rich and surfactant-poor regions. (c) Branched and Closed-Looped Wormlike Micelles. In trimer 12-3-12-3-12, 3Br solutions the extension of the overlapped yet unentangled regime is as broad as in the 12-3-12, 2Br system, although the c* values suggest that the micelles are growing faster [170]. This could be good confirmation for the presence of branches that have been observed by cryo-TEM [104,185]. In the fully entangled regime, the elasticity of 12-3-12-3-12, 3Br solutions is enhanced as compared with 12-3-12, Br solutions (Fig. 26). This may also result from branching [170]. The formation of branched wormlike micelles has also been observed by cryo-TEM in 12-2-12, 2Br solutions [184] and has been obtained in molecular dynamics simulations [186]. Formation of a dominant population of closed loops in wormlike micellar systems, theoretically considered for a long time [32,187], has been achieved with the cationic surfactant tetramer 12-3-12-4-12-3-12, 4Br [188] (Fig. 27). The contour length distribution N(L) of the closed-looped micelles has been determined from cryo-TEM micrographs (Fig. 28). At large contour lengths, the distribution observed scales as N(L) ⬀ L⫺5/2, as expected from ring-chain equilibrium polymerization theory [187]. At small contour lengths, the ring closure probability depends on the rigidity of the micelles, and the maximum of the distribution at L = 150 nm corresponds to twice the persistence length [188]. 2.

Vesicles and Other Low-Curvature Aggregates of Surfactant Oligomers The formation of vesicles from gemini surfactants has been specifically reviewed [189]. Vesicles are obtained with m = 12 and s > 16 but also for m = 16 and s < 4 gemini surfactants. This is true for diquaternary ammonium [22,166,167] as well as diphosphates [67]. Vesicle formation has also been observed from nonionic sugar-based geminis such as in Fig. 5a (14-1014) [84]. The cleavable heterodimer surfactant of Fig. 6c [88] forms vesicles that can be destroyed by acid catalysis under milder conditions (pH 3) than many

83

FIG. 27 Cryo-TEM micrographs of a vitrified 1% aqueous solution of 12-3-12-4-12-3-12 showing many closed loops coexisting with open wormlike micelles. (From Ref. 188, with permission. Copyright (1999) American Chemical Society.)

other cleavable surfactants, a property that could find application in drug vectorization [88]. Other cleavable gemini surfactants have been shown to yield small unilamellar vesicles [96] having transition temperatures that are pH dependent. An interesting result concerns the stereodependence of the fusion of vesicles [91]. Upon addition of Ca2⫹, vesicles formed from (S, S) and (R, R) stereoisomers of surfactants in Fig. 7a undergo fusion whereas (R, S) isomer vesicles undergo fission. This observation has been correlated with the monolayer isotherms at the airwater interface. The surface area per headgroup is smaller for the meso compound than for the (S, S) isomer and decreases when Ca2⫹ ions are added whereas it increases for the (S, S) isomer [91].

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FIG. 28 Loop size distribution in 1% aqueous solution of 12-3-12-4-12-3-12, 4Br. The mode of the distribution corresponds to twice the persistence length (lp = 75 nm). The decreasing part of the distribution scales as L⫺5/2 as expected from the ring closure probability for Gaussian polymers. (From Ref. 188, with permission. Copyright (1999) American Chemical Society.)

Vesicles of diphosphate geminis 12-18-12, 2Na and 12-24-12, 2Na are characterized by a noncooperative phase transition observed by differential scanning calorimetry (DSC) and fluorescence depolarization, the midpoint of the transition range being about 45⬚C [67]. The transition is accompanied by a line broadening of the 1H and 31P NMR signals. X-ray diffraction suggests that the spacer hydrocarbon chain is membrane spanning in the 12-24-12, 2Na surfactant vesicles. This was previously observed with glycerophosphate gemini surfactants of the type n/2-n-n/2, 2Na [71]. The temperature transition is structure dependent and decreases as the pH increases. The authors pointed out that, for an equivalent thickness, the transition temperature was higher in membrane-spanning spacer gemini vesicles than in classical phosphoglyceride bilayer lipid membranes [71]. This could explain, from the evolutionary standpoint, why such lipids have been found in bacteria living under extreme thermal conditions [71]. As with conventional surfactants, mixtures of cationic and anionic surfactants can yield vesicles [190,191]. Bromide counterions of cationic geminis have been replaced by palmitate ions. The vesicles obtained have a higher transition temperature as expected with ‘‘catanionic’’ systems, but the interesting result is that this transition temperature decreases from 74 to 39⬚C when the spacer goes from 2 to 12. Large spacer surfactants also form vesicles that are more permeable to hydroxyl anions. Other catanionic systems involving

In

geminis have been studied. For instance, addition of an anionic gemini to CTAB solutions induces a line broadening of the NMR signal of the methyl proton of CTAB, which has been interpreted as the formation of a network of cross-linked micelles [192]. This interpretation has, however, been contradicted by a cryoTEM study that revealed the presence of vesicles and other large aggregates, suggesting that the system was close to precipitation [193]. Vesicles have also been obtained from asymmetric phosphate gemini surfactants mixed with L-histidinebased surfactants having two long alkyl chains [194]. The histidine surfactant is not soluble by itself. When mixed with (R, S) surfactant of Fig. 7a, at pH 6.5, large vesicles (150 to 750 nm in diameter) are obtained. With the (R, R) surfactant, ill-defined tubular structures are obtained. When added to the (S, S) isomer of the surfactant of Fig. 7a, 40-nm-wide right-handed helical ribbons are obtained with pitch of 90 nm rather independent of the composition. Similar helical ribbons are obtained with cationic 16-2-16 having L-tartrate or Dtartrate as counterion [195]. But in that case, the width and the pitch of the ribbons can be tuned by adjusting the enantiomeric excess, (cL ⫺ cD)/(cL ⫹ cD) or by adding an excess of chiral counterion. It is worth mentioning that these geminis with a chiral counterion have the ability to gel halogenate organic solvents in the presence of a small amount of water [196]. Several factors seem necessary to gel the organic solvent: the short spacer, the chirality of the counterion, and its ability to hydrogen-bond. Other cationic geminis (m = 16, and 2,3-dimethoxybutane spacer) have shown the ability to self-assemble in chloroform in the presence of a small amount of water [197]. The vesicle-micelle transition has been studied by adding spherical micelle–forming surfactants such as DTAB and 12-10-12, 2Br to a vesicle-forming gemini surfactant 12-20-12, 2Br [198]. No wormlike micelle intermediate state has been observed. The vesicle-micelle transition can also be triggered by increasing the temperature of 16-3-16, 2Br solutions [199]. Addition of hexanol to solutions of 12-2-12, 2Br induces a transition from wormlike micelles to vesicles [177]. This transition has been studied by rheology and cryo-TEM observation. When the molar ratio, r, of hexanol to gemini increases, the viscosity and the size of the micelles first increase up to r = 1/8. Increasing r further (up to 1/3) leads to the formation of highly branched micelles coexisting with small vesicles of about 100 nm diameter. In this regime the viscosity decreases. Increasing r then induces the growth of the vesicles and eventually leads to phase separation [177].


D.

Liquid Crystalline Phases

1. Lyotropic Behavior Cationic gemini surfactants 12-s-12, 2Br (with 16 ⱖ s ⱖ 4) form lyotropic mesophases stable from room temperature up to temperatures of 150–200⬚C [168]. The concentration range of stability of the micellar solutions broadens on increasing s and spans almost the entire phase diagram (up to 90%, where it starts to coexist with crystals) when s = 10 and 12. This has been interpreted as being due to a maximum mismatch between the length of the spacer and the length of the alkyl chains. For long spacers the range of the micellar phase narrows again, and with 12-16-12, 2Br surfactant, lyotropic mesophases are obtained at 30% [168]. The concentration range of stability of the lyotropic mesophases is widest for 12-8-12, 2Br. The mesomorphic behavior of 16-s-16, 2Br [200,201] has also been studied with emphasis on short spacers (s = 1, 2, 3, and 6). The Kraft boundary of the mesophases decreases with increasing s because of a disruption of the crystal packing. All these surfactants form a long rod nematic phase at the micellar (L1)/hexagonal (H1) boundary except for s = 6. For s = 2 and 3 the formation of an intermediate phase (Int) (noncubic liquid crystals with curvature intermediate between hexagonal and lamellar) is observed, but not for s = 6. Cubic bicontinuous (V1) and lamellar (L␣) phases are obtained for all surfactants but require high temperatures (54⬚C and 76⬚C, respectively) for s = 6. The succession of phases of cationic surfactant dimers and trimers with m = 12, s = 3 and 6 and various counterions has been surveyed using cross-polarized light microscopy and the water penetration technique (M. In and G. G. Warr, in preparation). Intermediate and bicontinuous cubic phases are confirmed for short spacers. More strongly binding counterions have a similar effect as a reduction in spacer length or an increase in oligomerization degree. This study again illustrates the fine tuning one can achieve by varying parameters specific to surfactant oligomers, namely the spacer length and the degree of oligomerization. Lyotropic behavior of cationic gemini surfactants with hydrophilic (EO) spacers (Fig. 2b) has also been studied [49]. The concentration range of the L1 phase broadens as s/3 increases as in hydrophobic spacer geminis. The lyotropic behavior of the nonionic gemini of Fig. 5b with m = 6 was studied by polarized light microscopy and deuterium NMR spectroscopy [81]. At 27⬚C, as the concentration decreases, the succession of phases is S-L␣ (89%), L␣-V1 (75%), V1-H1 (71%), H1-

85

VB (62%), VB-L1 (50%), where S stands for solid phase and VB for viscous birefringent phase. From 2H NMR spectra it appears that L␣ and H1 phases always coexist with an isotropic phase (V1 for L␣ and L1 for H1). The VB phase was identified later as a biphasic region [163]. This sugar-based surfactant does not exhibit any cloud point in the range of temperature studied (0–100⬚C). The study has been completed for other chain lengths [163]. For m = 5, the viscous birefringent phase no longer appears. For m = 7 an upper critical solution temperature exists between 0.5 and 10%. The V1 phase region is no longer seen but is supposed to exist in a very narrow range of concentration. For m = 8, the phase boundaries are less sensitive to temperature. The isotropic L1 phase exists up to 0.8% and then coexists with an unidentified phase of optical texture resembling an L␣ phase. A pure L␣ phase is formed at 48%. The surfactant of Fig. 5b with m = 9 is insoluble in water up to 100⬚C [163]. 2. Thermotropic Behavior The thermotropic behavior of 16-s-16, 2Br surfactants has been reported [200,201]. DSC experiments show a main transition around 100⬚C corresponding to an S → VN (viscous neat phase) transition, with further small transitions at higher temperature. Optical microscopy shows that for short spacers (s = 1 and 2) the VN phase transforms into an isotropic phase at about 200⬚C (precise temperature transitions are difficult to obtain as a result of the progressive decomposition of the material). For longer spacers (s = 3 and 6), the system goes across to a smectic A phase at about 200–230⬚C. The transition at 100⬚C has an unexpectedly low enthalpy, which suggests that either the solid is not well ordered or the VN phase has significant conformational restrictions. X-ray diffraction in the VN phase indicates a tilted bilayer structure with disordered alkyl chains filling the space between ordered headgroup layers including the spacer. The degree of order in the headgroup layer depends on the spacer length (higher with a short spacer) and for longer spacers varies with the temperature. Thermotropic behavior was observed with cationic m = 12 gemini with (EO)s/3 space [49] but not with their homologues with (CH2)s spacer [168]. V.

CHEMISTRY WITH GEMINI SURFACTANTS

A.

Analytical Chemistry

1. Micellar Electrokinetic Chromatography Micellar electrokinetic chromatography (MEKC) allows the separation of neutral compounds by electro-

86

In

phoresis on the basis of their differential partition between micelles and the solution. The cmc and the hydrophobicity of the micelles are critical parameters for the efficiency of this technique. Sulfonate gemini surfactants of Fig. 3a (Y = O) were able to separate various substituted naphthalene and benzene derivatives at concentrations as low as 7.5 mM [202]. Using sodium dodecyl sulfate (SDS) would have required 50 mM for the same resolution. The surfactant of Fig. 3a and SDS were also shown to have remarkably different selectivities. The separation of chlorophenols has also been carried out with the same type of surfactants [203]. Cationic surfactants have been used to separate ergot alkaloids by MEKC [204]. With all types of gemini surfactants, the retention factor increases linearly with surfactant concentration as expected [203,204]. Micellar-enhanced ultrafiltration, another micelle-based separation technique could also take advantage of the various morphologies observed in surfactant oligomer micelles, but as far as we know, no data have been reported in the literature. 2. Specific Electrodes Di- and triamide surfactant dimers and trimers of the type shown in Fig. 29 have been synthesized in an attempt to prepare membrane systems having high selectivity for alkaline earth metal cations (Mg2⫹ and Ca2⫹). Some of them have shown enough selectivity to allow measurements of Mg2⫹ activities in the millimolar range at physiological pH without interference by H3O⫹ ions [28]. The selectivity of these ionophores for Mg2⫹ over monovalent cations has been studied in detail [205,206] and the conditions for their use in membrane electrodes for application to human blood serum optimized [207]. The synthesis of lipophilic receptors has been reported [208] and is an active field of research. The synthesis of lipocyclopolyamines as potential adenosine mono-, di-, and triphosphates has already been mentioned [29]. More recently, the interfacial behavior of a new amphiphilic cage molecule [tetra-(N-2-tetra-decylcarboxamideoethyl)-tetraazacyclotetradecane] showing selective complexation of copper ions has been studied [209]. The use of this compound for liquid-liquid extraction has been demonstrated in the case of chlorinated solvents. B.

Micellar Catalysis

Bunton and coworkers, noticing the higher catalytic activity of polyelectrolytes compared with micelles, were interested in surfactants that would ‘‘combine some

features of polyelectrolytes and detergents.’’ They studied the catalytic activity of gemini surfactants 16-s-16, 2Br (s = 2, 4, and 6) for the reaction of hydroxide ion with chloro- and fluoro-2,4-dinitrobenzene and hydroxide and fluoride ion with p-nitrophenyl diphenyl phosphate [34]. Surfactants with s = 4 and 6 have shown much higher catalytic activity than CTAB for all the reactions studied. A short spacer (s = 2) or a rigid space (2,3-butinediyl) did not show any catalytic activity for reactions involving hydroxide ions. Cyclization of 2(3-bromopropyloxy) and 2-(3-bromododecyloxy)phenoxide ion in micelles of cationic geminis (m = 16, spacer = butanediyl or 2,3-dimethoxybutanediyl) has been studied [197]. Intramolecular reactions are better suited to address the catalytic activity of micelles because they are independent of the reaction volume. The observed rate constant kobs is three times higher with the butanediyl spacer gemini than with the 2,3-dimethoxybutanediyl spacer. The surfactant concentration dependence of kobs showed a plateau, followed by an increase associated with the formation of larger aggregates. Under preparative conditions, i.e., with a large ratio of substrate to surfactant, only the product of intramolecular reaction was obtained [197]. C.

Chemistry Hosted or Templated by Surfactant Oligomer Self-Assemblies

1. Synthesis of Colloidal Metallic Particles A nonionic surfactant gemini known as Surfynol 465 has been used to synthesize gold [210,211] and silver [212] colloidal particles. The amphiphilic moieties in this surfactant consist of a branched alkyl chain with an oxyethylene headgroup. They are linked by an acetylenic spacer. The physicochemical properties of Surfynol 465 have been studied in detail by tensiometry, densitometry, osmometry, calorimetry, and UV and NMR spectroscopy [213–215]. The main properties are the following: cmc ranges from 10 to 16 mol/g, ␥cmc = 26 mN/m, Aa/w = 0.64 nm2 per molecule, cloud point at about 40⬚C, N0 = 13. Mixing Surfynol 465 with chloroauric acid (HAuCl4) or silver perchlorate (AgClO4) leads to the formation of metallic particles in higher yield than with other synthesis methods. The mechanism has been studied by UV-visible and Raman scattering [212,216,217]. The particles form by successive first-order reduction reactions, where the acetylenic group of the surfactant acts as the reducing agent. The surfactant then adsorbs at the particle interface and stabilizes the colloidal solution. Anisotropic colloidal gold particles have been obtained by UV photolysis of HAuCl4 in solutions of 12-2-12, 2Cl cationic gemini


FIG. 29

87

Surfactant dimers and trimers used as alkaline earth metal cation ionophores [28].

surfactant [218]. The concentration necessary to produce these particles was 15 times lower than with CTAC. An excess of surfactant is necessary to disperse the insoluble complex 12-2-12, 2AuCl4 and allow efficient UV radiation, but if the surfactant/Au ratio is too high, polyhedral isotropic particles are obtained. 2. Emulsion Polymerization The ␥-radiation polymerization of styrene microemulsions described in Section IV.B.1 led to spherical latex particles whose size range could be controlled by the monomer/surfactant ratio but also depends on the spacer length of the gemini surfactant involved [122,160]. With — (CH2)s — spacers and in the absence of cross-linker, the latex particle size goes through a maximum at s = 10, but it goes through a minimum at s = 6 in the presence of cross-linker. The optimal microemulsion formulations leading to both small particles and high molecular weight are obtained with s = 6 geminis [160]. In such conditions, the molecular weight is four times that obtained in CTAB microemulsions. With — (EO)s/3 — hydrophilic spacers, the same type of behavior is observed. The spacer length leading to the maximum molecular weight

(which in this case corresponds to the maximum particles size) is s/3 = 3 [122]. These observations led the authors to conclude that the polymerization behavior of ternary microemulsions with cationic geminis is rather independent of the chemical nature of the spacer provided that the flexibility of the interface is sufficient [122]. 3.

Gemini Surfactants as Templating Agents for Mesoporous Material Tailoring the porosity of inorganic material is an issue for applications such as molecular sieving or selective catalysis. It has become a very active field of research since the pioneering work of scientists at Mobil Oil Research and Development, who used the cooperative self-assembling of silicate polyanions and cationic surfactant micelles to produce mesoporous silica [219] (see Chapter 40 in this volume). A large variety of surfactants have now been used, including cationic gemini surfactants [220–222]. The greatest advantage of using gemini surfactants for templating the formation of mesoporous material may be that they provide a new parameter, s, to control the structure, independently of m, which is the determining variable for the average pore

88

In

size. However, the quality of the material obtained is also sensitive to s [220]. Typical syntheses proceed by mixing m-s-m, 2Br surfactants with tetraethyl orthosilicate (TEOS) in water (in molar proportions 0.06:1: 150) under basic or acidic conditions at room temperature or/and under hydrothermal conditions for one or several days [221]. The crystallinity of the precipitate obtained is improved by subsequent hydrothermal treatment in fresh water. Most often, the structure of the ordered organic/inorganic composite material obtained is determined by the lyotropic behavior of the surfactant. Hence, short spacers favor lamellar phases (MCM-50) and intermediate spacers favor hexagonal phases (MCM-41) for s < 10. The 12-12-12, 2Br yields MCM-41 at room temperature [221], and a cubic structure (MCM-48) is obtained with 16-12-16, 2Br under hydrothermal conditions [220]. The use of gemini surfactants has been shown to reduce the synthesis time of high quality (in terms of crystallinity and pore size distribution) cubic mesoporous silica [220]. VI.

CONCLUSIONS

The large variety of surfactant oligomer structures of interest today has been demonstrated. Their synthesis is sometimes involved but does not necessarily require new chemistry and can often rely upon well-known procedures. Surfactant oligomers have been shown to exhibit good surface activity. Their efficiency in lowering surface tension relies upon an adsorption triggered by several hydrophobic chains and interfacial interactions that take place at lower concentration because of their larger size. The cmc depends strongly on the degree of oligomerization and slightly on the spacer length. These two parameters, specific to surfactant oligomers, also determine the optimal area per headgroup and hence the morphology of the micelles as well as the mesoscopic behavior. Original structures, as compared with conventional monomeric surfactant, are obtained essentially for short spacers. Surfactant solutions behaving as polymers can be obtained and their viscosity controlled by the structure of the surfactant and not only through formulation. The stability of vesicles can also be controlled by varying the spacer characteristics. The answer to the question ‘‘Is it worth going to higher oligomerization degree?’’ varies depending on the point of view. From the point of view of general applications, the answer is probably negative. The biggest gain is made from the monomer to the dimer, and the benefits of having higher degrees of oligomeriza-

tion may not be worth the synthesis effort. For specialized surfactant applications and fundamental properties, it is the hope of the author that the reader’s answer will be positive. ACKNOWLEDGMENTS I would like to take this opportunity to thank Vesna Vukov and Sharon Krauss, whose help in gathering the references, and sometime in translating them, has been invaluable. I am also thankful to Corine Ge´rardin and Amit Kulkarni for their comments on the manuscript. Last, many thanks are also extended to Dave Tracy and Raoul Zana for sharing their immense knowledge in the field of surfactant oligomers. VII.

APPENDIX

Notation: Cmc: critical micelle concentration. ␣: ionization degree of the micelles at the cmc. ␥cmc: surface tension at the cmc. pC20: logarithm of the inverse of the surfactant concentration necessary to decrease the surface tension by 20 mN/m. A: surface area per molecule at the air-water interface. In the absence of swamping electrolyte, the values reported in the following tables are obtained by taking n = x ⫹ 1 in the Gibbs equation [Eq. (9)]. k: number of solubilized dye molecules per surfactant molecule above the cmc. KT: Kraft temperature. A.

Cationic Gemini Surfactants

1. Variable Spacer (a) Hydrophobic Spacer TABLE 3 s 3 4 5 6

a

8-s-8, 2Br cmc (M)

␣a

10⫺2 10⫺2 10⫺2 10⫺2

0.70 0.67 0.69 0.67

2.5 ⫻ 10⫺2

0.54

2.3 ⫻ 10⫺2

0.62

2.4 ⫻ 10⫺2

0.62

1.4 2.6 2.6 2.5

⫻ ⫻ ⫻ ⫻

Conductimetry at 25⬚C [148].

Gemini Surfactants and Surfactant Oligomers TABLE 4

89

10-s-10, 2Br cmca (M)

s 2c 3 4 5 6 8 10 12

6.0 6.4 9.0 9.2 8.7 6.8 4.7 3.7

⫻ ⫻ ⫻ ⫻ ⫻ ⫻ ⫻ ⫻

10⫺3 10⫺3 10⫺3 10⫺3 10⫺3 10⫺3 10⫺3 10⫺3

ka

cmcb (M)

␣b

99 106 121 147 212 186 160 43

6.2 ⫻ 10⫺3 6.5 ⫻ 10⫺3 8.7 ⫻ 10⫺3 — 9.2 ⫻ 10⫺3 7.5 ⫻ 10⫺3 4.2 ⫻ 10⫺3 2.2 ⫻ 10⫺3

0.15 0.22 0.28 — 0.29 0.32 0.37 0.39

a

Dye solubilization (trans-azobenzene) at 20⬚C [159]. Conductimetry at 25⬚C [152,162]. c Surface tension measurement by the maximum bubble pressure at 25⬚C gives cmc = 6.5 ⫻ 10⫺3 M and ␥cmc = 32 mN/m [40]. b

TABLE 5

12-s-12, 2Br

s

cmca (M) 2 3 4 5 6 8

10 12 14 16

8.4 (1.5 9.6 1.2 (1.4 1.1 1.0 (1.1 8.3 (7.0 6.3 3.7 2.0 1.2 (1.0

⫻ ⫻ ⫻ ⫻ ⫻ ⫻ ⫻ ⫻ ⫻ ⫻ ⫻ ⫻ ⫻ ⫻ ⫻

10⫺4 10⫺2) 10⫺4 10⫺3 10⫺2) 10⫺3 10⫺3 10⫺2) 10⫺4 10⫺3) 10⫺4 10⫺4 10⫺4 10⫺4 10⫺3)

␣a

cmcb (M)

␥cmcb (mN/m)

˚ 2) Ab (A

0.22 (0.24) 0.22 0.28 (0.28) 0.29 0.32 (0.32) 0.45 (0.44) 0.54 0.62 — 0.67 (0.62)

8.1 ⫻ 10⫺4 c

30c

69c

9.1 ⫻ 10⫺4 1.0 ⫻ 10⫺3

35.0 39.8

105 116

— 1.1 ⫻ 10⫺3

— 42.5

— 143

8.9 ⫻ 10⫺4

42.8

176

10⫺4 10⫺4 10⫺4 10⫺4

43.0 41.5 39.5 39.4

220 226 200 154

3.2 2.8 1.8 1.4

⫻ ⫻ ⫻ ⫻

a

Conductimetry at 25⬚C [38]. Values in parentheses are for the corresponding monomer surfactant ms/2, Br [155]. b Surface tension (ring method) at 25⬚C [121] unless otherwise specified. c Surface tension (Wilhelmy plate open frame version) at 22⬚C [131].

TABLE 6

12-s-12, 2Cl

s 2 3 4 6 10 20 Source: Ref. 153.

cmc (M) 1.3 1.8 1.3 1.3 6.3 7.0

⫻ ⫻ ⫻ ⫻ ⫻ ⫻

10⫺3 10⫺3 10⫺3 10⫺3 10⫺4 10⫺5

90

In TABLE 7

a

cmc (M)

b

cmc (M)

␣

1.4 ⫻ 10⫺5 — 3.2 ⫻ 10⫺5 — 6.5 ⫻ 10⫺5 — — —

2.1 ⫻ 10⫺5 2.6 ⫻ 10⫺5 2.7 ⫻ 10⫺5 — 4.3 ⫻ 10⫺5 3.3 ⫻ 10⫺5 —

0.60 0.35 0.56 — 0.43 0.60

s 2 3 4 5 6 8 10 12

16-s-16, 2Br b

c

cmc (M) 2.5 2.7 3.6 4.3 3.3 2.7 2.0

⫻ ⫻ ⫻ ⫻ ⫻ ⫻ ⫻

10⫺5 10⫺5 10⫺5 10⫺5 10⫺5 10⫺5 10⫺5

KT d (⬚C)

cmce (M)

45

3.4 ⫻ 10⫺5

34

4.4 ⫻ 10⫺5

41

4.7 ⫻ 10⫺5

a

Surface tension (ring method) at 25⬚C [34]. Conductimetry at 25⬚C [38]. c Fluorescence spectroscopy at 30⬚C [41]. d Conductimetry [150]. e Conductimetry at 46.5⬚C [150]. b

TABLE 8

s cmc (M)

2

4

6

8

10

12

3.2 ⫻ 10⫺3

3.2 ⫻ 10⫺3

3.1 ⫻ 10⫺3

2.6 ⫻ 10⫺3

2.3 ⫻ 10⫺3

1.6 ⫻ 10⫺3

Note: Dye solubilization [145].

TABLE 9

s 8 9 10 11 12

cmc (M) 4.0 6.3 1.6 3.0 3.0

⫻ ⫻ ⫻ ⫻ ⫻

10⫺4 10⫺5 10⫺4 10⫺4 10⫺5

␥cmc (mN/m)

˚ 2) A (A

45 43 44 50 34

314 444 381 335 189

Note: Surface tension (du Nouy ring) at 25⬚C [43].

cmc (M) 1.0 8.3 9.1 5.0 7.9

⫻ ⫻ ⫻ ⫻ ⫻

10⫺2 10⫺4 10⫺3 10⫺4 10⫺3

␥cmc (mN/m)

˚ 2) A (A

42 50 37 47 37

208 150 178 153 113


91

(b) Hydrophilic Spacer

TABLE 10

s

cmc (M) 8.0 9.2 8.6 9.0 1.2

1 2 3 4 5

⫻ ⫻ ⫻ ⫻ ⫻

␥cmc (mN/m)

10⫺4 10⫺4 10⫺4 10⫺4 10⫺3

38.2 41.0 40.8 42.1 42.0

Note: Surface tension (Wilhelmy plate) at 25⬚C [122].

TABLE 11

s-m

cmc1a (M)

cmc2a (M)

cmcb (M)

KT c (⬚C)

1-12 1-14 1-16 2-16 3-16 7-16 1-18 3-18 7-18 1-22 3-22 7-22 20-22

— 5.0 ⫻ 10⫺5 3.4 ⫻ 10⫺5

— 2.5 ⫻ 10⫺4 1.5 ⫻ 10⫺4

4.8 ⫻ 10⫺4 — 3.8 ⫻ 10⫺5

— — 28.8

10⫺5 10⫺3 10⫺5 10⫺5 10⫺4 10⫺5 10⫺5 10⫺4 10⫺4

6.5 ⫻ 10⫺5 1.6 ⫻ 10⫺4

12.4 100 >100 28.7 7.0 18.0 7.0 1.8

0.08 0.6 >212.9 >195.4 53.1 12.3 26.5 9.8 2.4

0.003 0.02 >100 >100 15.2 2.2 5.0 1.6 0.5

0.004 0.02 >212.9 >195.4 28.1 3.8 7.4 2.3 0.6

ICn, Concentrations inhibiting the growth of Aspergillus fumigatus by 50% (n = 50) and 90% (n = 90).

New Glycolipids Having Biological Activities

FIG. 5

Chemical structure of galactosyl ceramide (Galcer).

show very good activity of such bolaforms against HIV-1 gp120. The median inhibitory concentration (IC50) for binding is, in some cases, less than half (0.4 ␮M) that of suramin (0.9 ␮M). VII. A.

NEW CATANIONIC GLYCOLIPIDS Gemini Catanionics

Catanionic surfactant mixtures, such as two chains [37] or geminis, showing various aggregate microstructures (micelles, vesicles, and lamellar phases) have received increased attention [38]. Their mode of synthesis, achieved by mixing two oppositely charged surfactants, could be an alternative technique for easily preparing new two-chain or gemini glycolipids. Analogues of Galcer having these structures require multistep synthesis and purification; to overcome this drawback, we intended to synthesize catanionic analogues of galactosylceramide. Although various two-chain glycolipids have been described in the literature [40], very few examples of gemini glycolipids have been reported [40,41]. B.

123

FIG. 7 Chemical structure of soluble analogue of Galcer (CA 52).

The catanionic monomeric species were characterized by mass spectrometry. The electrospray mass spectrometry technique is a useful method for characterizing molecules that form noncovalent complexes in solution [43] or in the gas phase [44]. Thus we have been able, for the first time, to observe directly monomeric species of catanionic surfactants. C.

Surface tension measurements confirm the formation of micelles with bichain and gemini compounds when they are hydrophobic enough. Above the cmc, all compounds form mesophases in concentrated water solution at room temperature. With polarized light microscopy we observe lamellar phases, which indicate the possibility of vesicle formation. Dynamic light scattering studies confirm the spontaneous formation of vesicles in a concentration range of 1 to 4 mM, and transmission electron microscopy (TEM) showed the aggregate morphology of vesicles. D.

Synthesis

We synthesized new analogues of Galcer, replacing the amide covalent bond by an amine-acid ionic bond (Scheme 7). N-Alkylamino-1-deoxylactitol and carboxylic acids stoichiometrically gave salts upon stirring in water, forming an ionic amine-acid bond. We thus obtained new catanionic glycolipids in high yields (96% in two steps from unprotected lactose) [42].

FIG. 6

Self-Association Properties

Anti–HIV-1 Activities

Catanionic analogues showed interesting anti–HIV-1 activities (Table 9). The gemini compound with n = 15 and m = 12 is particularly interesting, providing both high anti-HIV activity (median effective concentration EC50 = 0.5 ␮M) and low toxicity (CC50 > 100 ␮M). In fact, it is more active and less toxic than previously studied Galcer analogues. Indeed, as previously ob-

Carbon-linked galactosphingolipid analogue (C. R. Bertozzi, Ref. 33).

124

Synthetic scheme of N-substituted-1,8-naphthalimide derivatives.

Lattes et al.

SCHEME 6

New Glycolipids Having Biological Activities

Synthetic scheme for preparation of catanionic compounds.

125

SCHEME 7

126

Lattes et al.

TABLE 9 Compound 6a 6b 6c 6d 7a 7b CA 52

10.

Catanionic Anti-HIV Activities EC50 (␮M)

CC50 (␮M)

IS

Log P

>1000 100 16 0.9 500 0.5 50

>1000 >100 38 2.5 600 >100 220

— >1 2.3 2.7 1.1 >200 4.5

1.7 3.3 4.9 6.5 2.1 8.4 4.5

11.

12. 13. 14. 15.

16.

served, the monomeric forms appear to be the most active, as the EC50 values are below the respective cmc. The last results provide good reasons to use these easily synthesized catanionic compounds to prepare spontaneous surfactants with interesting properties, not only in therapeutic applications but also for encapsulation and vectorization.

17. 18. 19. 20. 21.

VIII.

CONCLUSIONS

In summary synthetic glycolipids are of interest for their biological applications. Therefore, depending on their structures, these new series of glycolipids have applications as mimics of natural ligands of proteins. An interesting new strategy concerns the formation of gemini catanionic glycolipids. With this simplified synthesis we are now able to test many self-assembled entities offering considerable advantages over stepwise bond formation in the construction of active molecules.

22.

23. 24. 25.

26.

REFERENCES 27. 1. 2. 3. 4. 5. 6. 7. 8. 9.

B. Brancq, L’Act Chim (AS-I) 2–3:63–65 (1996). M. Von Itzstein et al., Nature 363:418–423 (1993). L. A. Lasky, Science 258:964–969 (1992). J. S. Lazo and D. E. de Quinn, Anal. Biochem. 102: 68–70 (1980). G. W. Stubbs, H. G. Smith, and B. Litman, Biochim. Biophys. Acta 425:46–50 (1976). P. Latge, I. Rico, R. Garelli, and A. Lattes, J. Dispersion Sci. Technol. 12:227–237 (1991). P. Latge, I. Rico, A. Lattes, and L. Godefroy, French Patent 9005338 (1990). F. Costes, M. El Ghoul, M. Bon, I. Rico-Lattes, and A. Lattes, Langmuir 11:3644–3647 (1995). M. El Ghoul, P. Latge, I. Rico, A. Lattes, and L. Godefroy, EP 924014038 (1992).

28. 29.

30. 31.

32.

P. Latge, M. Bon, I. Rico, and A. Lattes, New J. Chem. 16:387 (1992). I. Rico-Lattes, J. C. Garrigues, E. Perez, C. Andre´-Barre`s, C. Madelaine-Dupuich, and A. Lattes, New J. Chem. 19:341–344 (1995). C. Andre´-Barre`s, C. Madelaine-Dupuich, and I. RicoLattes, New J. Chem. 19:345–347 (1995). R. Garelli-Calvet, F. Brisset, I. Rico, and A. Lattes, Synth. Commun. 23:35–44 (1993). R. Garelli-Calvet, F. Briset, I. Rico-Lattes, A. Lattes, and L. Godedroy, French Patent 91128511 (1991). J. Fantini, D. Hammache, O. Delezay, N. Yahi, C. Andre´-Barre`s, I. Rico-Lattes, and A. Lattes, J. Biol. Chem. 11:7245–7252 (1997). C. Cupuy, X. Auvray, C. Petipas, R. Anthore, F. Costes, I. Rico-Lattes, and A. Lattes, Langmuir 12:3162–3172 (1996). I. Rico-Lattes and A. Lattes, Colloids Surf. A 123–124: 37–48 (1997). C. Dupuy, X. Auvray, C. Petipas, R. Anthore, I. RicoLattes, and A. Lattes, Langmuir 14:91–98 (1998). F. Brisset, R. Garelli-Calvet, C. Chebli, I. Rico-Lattes, and A. Lattes, New J. Chem. 20:595–605 (1996). C. Dupuy, X. Auvray, C. Petipas, I. Rico-Lattes, and A. Lattes, Langmuir 13:3965–3967 (1997). R. Garelli-Calvet, P. Latge, I. Rico, A. Lattes, and A. Puget, Biochim. Biophys. Acta 1109:55–58 (1992). (a) A. Dolev, W. W. K. Rohwedder, T. L. Munts, and H. J. Putton, Lipids 2:33–38 (1967); (b) W. Grosh, F. Weber, and K. M. Fisher, Ann. Technol. Agric. 26:133– 137 (1977). X. Auvray, C. Petipas, R. Anthore, I. Rico-Lattes, and A. Lattes, Langmuir 11:433–439 (1995). A. Lattes and I. Rico, Pour la Science 137:44–50 (1992). (a) M. J. Gibian and P. Vandenberg, Anal. Biochem. 163:343–346 (1987); (b) B. Axelrod, T. M. Cheeselbrough, and S. Laakso, Methods Enzymol. 71:441 (1981). C. B. Moore, D. Law, and D. W. Denning, J. Antimicrob. Chemother. 322:831–836 (1993). M. H. Villas-Boas, H. Egge, G. Pohlentz, R. Hartmann, and E. Barreto-Bergter, Chem. Phys. Lipds 70:11–19 (1994). D. D. Manning, L. E. Strong, Xin Hu, P. J. Beck, and L. L. Kiessling, Tetrahedron 53:11937–11952 (1997). J. C. Garrigues, E. Perez, M. D. Linas, I. Rico-Lattes, J. P. Seguela, and A. Lattes, J. Mycol. Med. 6:111–117 (1996). J. C. Garrigues, I. Rico-Lattes, E. Perez, and A. Lattes, Langmuir 14:5968–5971 (1998). J. M. Harouse, S. Bhat, S. L. Spitalnik, M. A. Laughlin, K. Stefano, D. H. Silberg, and F. Gonzalez-Scarano, Science 253:320 (1991). J. Fantini, D. G. Cook, N. Nathanson, S. L. Spitalnik, and F. Gonzalez-Scarano, Proc. Natl. Acad. Sci. U. S. A. 90:2700–2704 (1993).

New Glycolipids Having Biological Activities 33.

34.

35.

36.

37.

38.

C. R. Bertozzi, D. G. Cook, W. R. Kobertz, F. Gonzalez-Scarano, and M. D. Bernadski, J. Am. Chem. Soc. 14:10639–10641 (1992). B. Guidetti, C. Andre´-Barres, I. Rico-Lattes, and A. Lattes, Perspect. Drug Discov. Des. 5:2234–2422 (1996). J. Fantini, D. Hammache, O. Delezay, N. Yahi, C. Andre´-Barre`s, I. Rico-Lattes, and A. Lattes, J. Biol. Chem. 272:7245–7252 (1997). D. Rideout, R. Schinazy, C. D. Pauza, K. Lovelace, L. C. Chiang, T. Calogeropoupole, M. MacCarthy, and J. M. Elder, J. Cell. Biochem. 51:446 (1993). (a) H. Fukuda, K. Kawata, and H. Okuda, J. Am. Chem. Soc. 112:1635 (1990); (b) R. Zana and H. Levy, Langmuir 13:402–408 (1997). L. L. Brasher and E. W. Kaler, Langmuir 12:6270– 6276 (1996).

127 39. 40. 41.

42. 43.

44.

O. Lockhoff, Angew Chem. Int. Ed. Engl. 30:1611 (1991). M. J. L. Castro, K. Kovensky, and A. Fernandez-Cirelli, Tetrahedron Lett. 38:3995–3997 (1997). J. M. Pestman, K. R. Jerpstra, M. C. A. Stuart, H. A. Van Doren, A. Brisson, R. M. Kellog, and J. B. F. N. Engberts, Langmuir 13:6857–6862 (1997). M. Blanzat, E. Perez, I. Rico-Lattes, D. Prome´, J. C. Prome´, and A. Lattes, Langmuir 15:6163–6169 (1999). (a) B. L. Schwartz, K. J. Light, and R. D. Smith, J. Am. Soc. Mass Spectrom. 5:201–204 (1994); (b) G. Pocsfawi, G. Di Landa, P. Ferranti, A. Ritieni, G. Randazzo, and A. Malomi, Rapid Commun. Mass Spectrom. 11:265–272 (1997). (a) J. A. Loo, Mass Spectrom. Rev. 16:1–23 (1997); (b) R. L. Winston and M. C. Fitzgerald, Mass Spectrom. Rev. 16:165–179 (1997).

5 Surfactants for Supercritical and Near-Critical Fluids TERRI CARSON* and SHARON L. WELLS Chapel Hill, North Carolina

University of North Carolina at Chapel Hill,

JOSEPH M. DESIMONE University of North Carolina at Chapel Hill, Chapel Hill, and North Carolina State University, Raleigh, North Carolina

I.

INTRODUCTION

water and organic solvents, CO2-based processes offer the potential for significant energy savings. This would be especially true for water-intensive industries such as coatings, pulp and paper, textile dyeing, and polymer manufacturing. Although such uses of CO2 are advantageous, their full development in other industrial processes, organic synthesis, and polymerizations has not been realized. However, with increased research efforts from both academic and industrial sectors, the use of dense CO2 will show its value in the years to come. The unique solvent characteristics of supercritical fluids were discovered over 100 years ago [3]. Common gases such as CO2 and ethylene were pressurized and found to dissolve complex organic compounds. A fluid is defined as supercritical when its temperature and pressure are higher than their critical-point value (Tc, Pc). The solvent strength (dielectric constant) is highly tunable by changes in the temperature or pressure of the system. The fluid exists as a single phase possessing properties of both a liquid and a gas. Its density can be similar to that of liquids while it simultaneously has gaslike viscosities. Among the research studies conducted using supercritical fluids, CO2 has been the solvent of choice for many applications for a number of reasons. It is relatively nontoxic, nonflammable, easily recycled, inex-

Over the past century, scientists have developed considerable interest in liquid and supercritical CO2. In part, this interest has been sparked by environmental concerns involving the emission of volatile organic compounds (VOCs), the use of chlorofluorocarbons (CFCs) in polymer manufacturing and coating industries, and the enormous amounts of water used in numerous industrial processes. The use of liquid and supercritical CO2 (scCO2) as an alternative solvent choice is attractive because of the unique properties related to solvent strength. The solvent power of these fluids can often approach, and occasionally exceed, those of organic solvents without placing the environment at risk. An example where this idea has been employed is in the coffee industry. Supercritical CO2 is used in the decaffeination process of coffee where dichloromethane was previously used [1,2]. In addition to the pollution prevention opportunities provided through the utilization of CO2, increased energy efficiency is an important opportunity associated with CO2 use. Because CO2 has a very low heat of vaporization relative to *Current affiliation: Dow Chemical Company, Freeport, Texas. 129

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pensive, and readily available. CO2 can be obtained from natural sources and isolated from exhaust streams of power plants and industrial plants that produce ethanol, ammonia, hydrogen, and ethylene oxide [4]. The one-component phase diagram of CO2 is shown in Fig. 1. From this diagram it can be seen that the critical point of CO2 is easily accessible (Tc = 31.1⬚C, Pc = 73.8 bar) in comparison with other supercritical solvents such as water (Tc = 374⬚C, Pc = 218 atm). Products formed in CO2 are often isolated as dry powders upon CO2 removal, thus eliminating energy-intensive drying processes or contamination of aqueous waste. Some companies have recognized these benefits and implemented CO2-based processes. For example, Ford Motor Company uses Union Carbide’s CO2-based Unicarb process to deposit coatings onto bumpers as opposed to using more hazardous solvent-based paints and primers [5]. Dupont has begun work on a $40 million test plant where poly(tetrafluoroethylene) (Teflon) will be synthesized in CO2, replacing chlorofluorocarbon solvents that are harmful to the earth’s atmosphere [6]. However, despite the numerous attractive features and widespread applications, significant advances using CO2 are hindered because of the low solubility of most hydrophilic compounds and polymers in CO2. The solubility characteristics of CO2 are very similar to those

FIG. 1

of perfluorohexane and represent a relatively low dielectric medium. The dielectric constant ranges from 1.01 to 1.45 for gaseous CO2 and 1.60 to 1.67 for liquid CO2 [7]. Some polar molecules such as methanol are able to dissolve in CO2 because of its strong quadrupole moment, but others such as amides, ureas, urethanes, and azo dyes demonstrate poor solubility [8,9]. The solubility properties of a number of small molecules have been reviewed elsewhere [10,11]. High-molar-mass polymers generally have limited solubilities in CO2 [12]. A number of researchers have focused their efforts on explaining this phenomenon, and some insight can be found in examining lattice fluid theory. According to this theory, three major factors govern the solubility of amorphous polymers in CO2: (1) solutesolute interactions, (2) solute-solvent interactions, and (3) solvent-solvent interactions [13]. Johnston and coworkers conducted an extensive study quantitatively modeling experimental cloud point curves for various amorphous poly(alkylene oxide), poly(alkyl acrylate), and poly(dimethylsiloxane) homopolymers [14]. It was found that solubility is dependent upon polymer-polymer interactions and that polymer-CO2 interactions play a secondary role. The only classes of polymers that have appreciable solubility in CO2 at mild conditions (T < 100⬚C, P < 350 bar) are fluoropolymers and silicones [15–18]. We reported the synthesis of poly-

One-component CO2 phase diagram.

Surfactants for Supercritical Fluids

(1,1-dihydroperfluorooctyl acrylate) [poly(FOA)] using CO2 as a continuous phase that yielded homogeneous solutions throughout the course of the reaction [18– 21]. Krukonis and coworkers have demonstrated the solubility of poly(perfluoropropylene oxide) in CO2 [22]. Barton and Kiran have reported on the high solubility of polydimethyl siloxane (PDMS) in CO2 at approximately 450 bar [23–25]. Despite the inability of CO2 to dissolve most polar or polymeric compounds, its solvency can be enhanced by the addition of surfactants that can drastically strengthen its effective solvating power for such substances. This chapter focuses on the efforts made toward the design and synthesis of surfactants for supercritical CO2. These surfactants have been categorized into sections according to the ‘‘CO2-philic’’ segment contained in the polymer (e.g., perfluoropolyethers, PDMS). A range of architectures have been explored, including homopolymers, block and graft copolymers, dendrimers, and small-molecule surfactants. Most often these materials were synthesized for the purpose of stabilizing hydrophilic or lipophilic compounds in CO2 for such applications as cleaning, separations, or polymerizations.

II.

FLUOROPOLYMER SURFACTANTS

A.

Synthesis and Characterization in scCO2

In 1992 our laboratory reported the homogeneous synthesis of a high molar mass amorphous fluoropolymer, poly(1,1⬘-dihydroperfluorooctyl acrylate) (PFOA) in CO2 [18]. The reaction scheme is shown in Scheme 1. Polymerizations were extended to include the synthesis of statistical copolymers whereby FOA was copolymerized with monomers such as methyl methacrylate (MMA), styrene, ethylene, and butyl acrylate (BA). These copolymerizations proceeded homogeneously even with the addition of high concentrations of the comonomer (Table 1). Other fluorinated acrylate polymers have been synthesized in a similar manner, including poly[2-(N-methylperfluorooctane-sulfonamido)]ethyl acrylate, poly[2-(N-ethylperfluorooctane-sulfonamido)ethyl acrylate, and poly[2-(N-methylperfluorooctanesulfonamido)ethyl methacrylate [26]. Along with this investigation, decomposition rates and efficiency factors were measured for azobisisobutyronitrile (AIBN) in CO2 and comparisons were drawn with conventional liquid solvents. It was found that AIBN decomposes at a rate 2.5 times slower in CO2 than in benzene but with greater efficiency. This phenomenon

131

SCHEME 1 Synthesis of PFOA in scCO2. The fluoroalkyl tail in PFOA contains about 25%—CF3 branches.

can be explained in terms of a decreased solvent cage effect that exists in a low-viscosity supercritical medium. Hence, CO2 can be considered an ideal solvent for free radical polymerizations with no chain transfer to solvent side reactions. Solution properties of PFOA in CO2 were studied using small-angle neutron scattering (SANS) [27]. McClain et al. demonstrated that SANS, after providing sufficient polymer-solvent contrast, was a viable technique to study homopolymer solutions in CO2. SANS data were generated for a concentration series of both a high- and a low-molecular-weight PFOA in CO2, Mw = 1.4 ⫻ 106 g/mol and 1.1 ⫻ 105 g/mol, respectively. Samples were measured in dilute solution [0.005 < C (g/mL) < 0.008] over a range of temperatures and pressures. The results of the SANS measurements are summarized in Table 2. The molecular weights measured by SANS were consistent with values expected from the synthetic conditions. The values for the radius of gyration (Rg) as a function of Mw were found to follow the function Rg = (0.10 ⫾ 0.02)M1/2, where M is the molecular weight. This was the first study confirming that CO2 is a thermodynamically good solvent for PFOA, as indicated by the measurement of positive values for the second virial coefficient A2. In comparison, Martino et al. have shown that other CO2-soluble polymers, poly(hexafluoropropylene oxide) (Krytox) and PDMS, have A2 values that are zero and negative, respectively, at similar conditions [28]. Studies have also indicated that A2 of PFOA not only is positive but

132

Carson et al. Statistical Copolymers Containing FOA and Vinyl Monomersa

TABLE 1 Copolymer

Feed ratio

Incorporated

Intrinsic viscosity (dL/g)

0.47 0.48 0.53 0.35

0.57 0.58 0.57 —

0.10 0.15 0.45 0.14

Poly(FOA-co-MMA) Poly(FOA-co-styrene) Poly(FOA-co-BA) Poly(FOA-co-ethylene)

Polymerizations were performed at 59.4 ⫾ 0.1⬚C and 345 ⫾ 0.5 bar for 48 h in CO2. Intrinsic viscosity determinations were conducted in 1,1,2-trifluorotrichloroethane (Freon-113) at 30⬚C.

a

ventional solvents. Both SAXS and SANS have proved to be powerful techniques for obtaining structural information about aggregated systems in solution. The SAXS study by Fulton et al. was the first of many subsequent scattering experiments performed on aggregated amphiphilic polymeric systems in CO2. The PFOA-g-PEO polymer synthesized with 5 kg/ mol PEO grafts was studied by SAXS. The experiments were performed at 60⬚C and three different pressures (470, 300, and 255 bar) in CO2 in the presence of water. The water-to-surfactant ratio was 0.32. The data are shown in Fig. 2. As the pressure of the system was decreased, there was an increase in the scattered intensity. The increase is a result of not only the greater particle-solvent contrast at lower CO2 densities but also the small increase in the size of the particles as pressure was decreased, as evidenced by the shift in the scattering peaks at lower scattering vectors (q). The oscillatory nature of the scattering curves is indicative of spherical core-shell structures. A depiction of the spherical micelle of PFOA-g-PEO with the collapsed PEO chains and water molecules within the core is shown in Fig. 3. A core-shell model was used to fit the SAXS data at low q. From the fits, the outer radii of the ag˚ with gregates were found to be approximately 125 A relatively low polydispersities. The radii of the particles

also is increased as the density of the CO2 increases (S. Wells, M. Adam, M. Rubenstein, and J. M. DeSimone, in preparation). DeSimone and coworkers also studied the synthesis of a CO2-philic/hydrophilic amphiphilic graft copolymer [29]. Using the macromonomer technique, poly(FOA-g-PEO) copolymers were made and found to be completely soluble in CO2 at 238 bar and 60⬚C (10 wt%). The microenvironment of these solutions was studied using solvatochromic characterization. Methyl orange (MO), a water-soluble dye that is insoluble in CO2, was added to the CO2 system in a solution with water. It was found that the PEO grafts enabled the solubility of the dye in CO2, yielding bright orange solutions. This phenomenon was further confirmed by ultraviolet (UV) spectroscopy data that yielded a ␭max of 418 nm for the colored solution (MO(aq) has a ␭max of 464 nm). This blue shift is a result of decreasing solvent polarity, which has been observed by Zhu and Scheely [30]. The discovery of uptake of both methyl orange and water into the scCO2 continuous phase by the PFOAg-PEO graft copolymer led to studies using small-angle x-ray scattering (SAXS) [31]. Many copolymers molecularly designed for CO2 applications are difficult to characterize because of their limited solubility in con-

TABLE 2

SANS Results for Concentration Series of Poly(FOA) in CO2 at Various Conditions

Poly(FOA) sample

P (bar)

T (⬚C)

␳a (g cm⫺3)

Low Mw High Mw High Mw High Mw

395 340 395 340

60 65 60 40

0.888 0.842 0.888 0.934

a

Density of pure CO2 at these conditions. Source: Adapted from Ref. 27.

˚) Rg (A 35 120 100 114

⫾ ⫾ ⫾ ⫾

0.15 13 6 9

A2 (⫻105 cm3 mol g⫺2) 9.5 1.9 4.1 2.5

⫾ ⫾ ⫾ ⫾

0.5 0.4 0.8 0.3

Mw (⫻10⫺6 g mol⫺1) 0.113 1.5 1.2 1.6

⫾ ⫾ ⫾ ⫾

0.006 0.4 0.3 0.3


133

FIG. 2 Small-angle x-ray scattering spectra for 1.9% (w/w) PFOA-g-PEO in supercritical CO2 at 60⬚C and three different pressures, 255, 300, and 470 bar. (Adapted from Ref. 30.)

FIG. 3 Proposed structure of a PFOA-g-PEO graft copolymer micelle in supercritical CO2. (Adapted from Ref. 30.)

increased when either the concentration was reduced or the pressure was decreased. The radius of the core was ˚ at the higher pressures and 125 estimated to be 105 A ˚ at lower pressures. The number of PEO segments in A the core was estimated to be about 600 based on the measured volume of the micelle core and PEO bulk density. In attempts to mimic and further study the PFOAg-PEO system, Chillura-Martino et al. performed SANS experiments on the same sample [28]. By taking advantage of the contrast differences between H2O and D2O, more conclusive data were obtained. The data showed not only that the micelles were swollen in the core but also that the shell was slightly swollen, suggesting that PEO segments also penetrate the shell. Measurements were also performed on the polymer in the absence of water and showed that the micelle dimensions were smaller. Figure 4 shows the differences in the SANS data when H2O and D2O were present versus when there was no added water. The radius of gyration taken from a core-shell fit increased from ˚ (no added water) to 86 A ˚ (H2O swollen) and ⬃56 A ˚ (D2O swollen). 136 A

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FIG. 4 The differential cross section per unit sample volume (d ⌺/d⍀(Q)) versus Q for PFOA-g-PEO graft copolymer in CO2 before and after swelling with H2O and D2O. (Adapted from Ref. 28.)

B.

Application in Heterogeneous Polymerizations

Materials useful as stabilizers in colloidal dispersions of lipophilic or hydrophilic polymers usually employ amphiphilic molecules. They contain anchoring segments that have an affinity for the polymer particles, most likely by physical adsorption, and a segment that is highly soluble in the continuous phase. DeSimone et al. demonstrated the amphiphilicity of PFOA and carried out the first successful dispersion polymerization in scCO2 [32,33]. The polymerization of methyl methacrylate was carried out in a 10-mL high-pressure reaction view cell at 65⬚C and 204 bar using AIBN or a fluorinated derivative of AIBN as the initiator. Polymerizations conducted in the absence of stabilizer produced polymers in low yield. In remarkable contrast, the reactions with added stabilizer produced free-flowing powders in high yields upon removal of CO2. Scanning electron micrographs displayed micrometer-sized particles with spherical morphologies and a relatively narrow size distribution (Fig. 5). Indeed, the amphiphilicity of PFOA contributed to the success of particle formation. DeSimone et al. have also reported the successful dispersion polymerization of styrene in scCO2 using amphiphilic diblock copolymers containing poly(styrene) (PS) and PFOA segments [34]. These materials were prepared via a controlled free radical method known as the iniferter technique. The detailed synthesis has been described by Guan and DeSimone and is illustrated in Scheme 2 [35]. With such block copolymers, polydisperse submicrometer-sized PS particles were produced by dispersion polymerization with spherical morphologies. It was also found that as the

FIG. 5 Scanning electron micrograph of PMMA particles produced by a dispersion polymerization in scCO2 using PFOA as stabilizer.

length of the stabilizing moiety increased, the particle size distribution decreased. The PS-b-PFOA surfactants were further characterized by small-angle neutron scattering studies and found to self-assemble in solution to form multimolecular micelles [36]. Both SAXS and SANS measurements were performed on the samples at 65⬚C and 338 bar. The scattering curves confirm that spherical micelles are formed in solution. As with the PFOA-g-PEO samples, a core-shell model was used to fit the data (Fig. 6). Table 3 shows the polymer dimensions as well as the results from the fits. As the PFOA block length increases, as expected the thickness of the shell and size of the overall micelle increase. A core-shell model could not be applied to the 4K-b-245k copolymer because of the large asymmetry, which was expected to give rise to a different morphology. The form factor for an f-arm star polymer was applied to the data and gave ˚ and f ⬃ 7.7 arms) consistent with results (Rg ⬃ 200 A those for other diblock copolymer samples. After confirmation of micelle formation, the PS-bPFOA surfactants were used to emulsify CO2-insoluble PS oligomer [27]. SANS characterization of micelles of PS-b-PFOA surfactants in CO2 (65⬚C, 340 bar) with


135 TABLE 3 Size of Core-Shell Micellar Aggregates for PS-b-PFOA in scCO2 at 65⬚C and 338 bar as a Function of Shell (Corona) Block Length Copolymer (PS-b-PFOA) 4k-b-17k 4k-b-40k 4k-b-61k 4k-b245k

Aggregation no.

R1 ˚) (A

R2 ˚) (A

6.6 7.1 6.9 99% of the added oligomer into the core of the micelle. The micellar core volume increased with added oligomer as a function of oligomer concentration as can be seen in Fig. 7. There was an approximately eightfold increase in the volume of the micelle core with the addition of up to 20% (w/w) oligomer. SAXS and SANS experiments provided conclusive data on the size and shape of micelles formed from PSb-PFOA block copolymers in CO2. However, to understand completely the CO2-polymer interactions, complementary high-pressure, high-resolution (HPHR) nuclear magnetic resonance (NMR) spectroscopy experiments were conducted over a range of densities at a fixed temperature [37]. Figure 8 shows HPHR 1H NMR spectra of the PFOA-b-PS recorded at 65⬚C and CO2 densities between 0.26 and 0.85 g/cm3. At low and intermediate CO2 densities, the NMR detected only the

FIG. 7 Swelling of 3.7k-b-39.8k surfactant micelles in CO2 (65⬚C, 340 bar) with PS oligomers. Surfactant concentration = 4% (w/v). (Adapted from Ref. 27.)

136

FIG. 8 High-pressure H NMR spectra of PS-b-PFOA in CO2 at T = 66.6⬚C and CO2 densities between 0.26 g/cm3 (bottom trace) and 0.85 g/cm3 (top trace). The shaded field indicates the region where signals from the PS block are expected for the spectra taken at low densities. (Adapted from Ref. 36.)

PFOA block. The aromatic signals for polystyrene remain undetected up to high CO2 densities, indicating that the polystyrene was completely immobilized on the NMR time scale. This suggests that the PS is in the core and is neither solubilized nor plasticized by CO2 in low and intermediate density ranges. In the highdensity range, PS peaks appeared with intensities corresponding to about 35% of the total protons, indicating that a fraction of the micelle core became plasticized (Fig. 9). In an effort to produce stable latexes of poly(vinyl acetate) (PVAc) and ethylene-vinyl acetate (EVA) in CO2, DeSimone and coworkers have synthesized fluorinated and siloxane-based stabilizers including homopolymers, block copolymers, and reactive macromono-

Carson et al.

mers [38]. The surfactants containing fluorinated acrylate segments were synthesized similarly to the PScontaining materials utilizing the iniferter technique. Polymerizations with these materials resulted in stable latexes at high conversion even in the absence of stirring. No apparent trend was observed in the results when the chemical composition of the stabilizers was varied. All reactions proceeded to high conversions and by visual observation produced white, opaque, and stable latexes. The solid latex particles could not be examined by electron microscopy because of the low Tg of PVAc, but the latex was characterized by turbidimetry. Polymerizations conducted in the presence of the fluorinated acrylate surfactants were found to be most turbid after 1 h and the surfactant with the longest blocks (PVAc: Mn = 3.1 ⫻ 104 g/mol; PFOA: Mn = 5.4 ⫻ 104 g/mol) produced the smallest diameter polymer particles. The synthesis of highly cross-linked polymeric microspheres using scCO2 as the solvent medium was reported [39]. These experiments were carried out with and without the addition of block copolymers of methyl methacrylate and perfluoroalkyl methacrylates that were prepared using screened anionic polymerizations. Polymerizations were conducted whereby divinylbenzene and ethylvinylbenzene were copolymerized at 65⬚C and 310 bar using AIBN as an initiator. In the absence of stabilizer and under certain specific conditions, relatively uniform, nonporous microspheres were produced with diameters ranging from 1 to 5 ␮m. Experimental variables such as the cross-linker ratio, monomer concentration, cross-linker structure, and mechanical agitation were examined. In an effort to produce particles under nonspecific conditions, the polymerizations were conducted in the presence of surfactant (0.25–3 wt%). At lower concentrations of surfactant, the microspheres showed a high degree of ag-

FIG. 9 Schematic representation of the solubilization of the PFOA-b-PS block copolymer in supercritical CO2. After the CO2 density was increased above the critical value, PS units at the core-shell interphase became mobilized. (Adapted from Ref. 36.)


gregation and a broad particle size distribution. Only when 3 wt% surfactant was used did the microspheres become more uniform and less aggregated. Furthermore, the particle sizes were much smaller ( Na⫹ > K⫹ > Ca⫹. The fluoroether carboxylate salts also extracted thymol blue from an aqueous solution in CO2. Fluorinated polyether surfactants have been prepared for CO2-based applications such as heavy metal extraction, dispersion polymerizations, and protein extraction [49]. In the case of heavy metal extraction, a perfluoropolyether containing a dithiol end group has been synthesized and found to extract as much as 98% of mercury from contaminated soil in laboratory-scale CO2 extractions. It was determined that over 90% of the total extraction occurred during the first hour. The dispersion polymerization of MMA has also been carried out in CO2 using a graft copolymer stabilizer, poly(MMA-co-hydroxyethyl methacrylate)-g-Krytox [50]. Factors such as the graft chain length and the graft

density were varied in order to determine their effect on the PMMA colloid. It was found that increasing the graft density resulted in efficient stabilization, and a change in the graft length produced varied results depending on the backbone length. Perfluoropolyethers derivatized with sorbitol ester, sulfate, and sulfonate groups have been synthesized to facilitate the extraction of proteins and polar molecules in CO2 [49]. Emulsion studies were conducted with this surfactant system and the formation of three phase transitions was observed: emulsion in the continuous water phase (WI), emulsion in the continuous CO2 (WII), and emulsion at the water-CO2 interface (WIII). Furthermore, an investigation of the pressure effect on emulsion behavior revealed that the high compressibility of CO2 allows WI → WIII → WII phase transitions that closely resemble those found with increased electrolyte concentrations. Beckman et al. have reported the synthesis of biotinfunctionalized fluoroether surfactants used in the extraction of avidin into CO2 [51]. Extraction occurred by both inverse and three-phase emulsions but was twice as high for the three-phase system.

V.

NONPOLYMERIC AMPHIPHILES IN CO2

The formation of reverse micelles in supercritical alkanes was reported by researchers at the University of Texas at Austin and Battelle’s Pacific Northwest Laboratories in the late 1980s [52–54]. The surfactants employed in this study were commercially available ionic amphiphiles with hydrocarbon tails, and they dramatically increased the solubility of amino acids, watersoluble polymers, proteins, and metal-containing compounds [53]. However, extension of the use of these


139

surfactants in CO2 had limited success because of the poor to negligible solubility of the surfactants. To address this issue of solubility, new surfactants have been synthesized containing fluorocarbon tails. Fulton et al. studied reverse micelles formed from F(CF2)6–10CH2CH2O(CH2OCH2O)3 or (FSO-100) in CO2 using SAXS [31]. These studies indicated that the nonionic surfactant completely dissolved at high pressures and 65⬚C. The small PEO units and broad molecular weight distributions of the samples promoted the formation of polydisperse micelles of the order of ˚ . Johnston and coworkers also demonstrated the 84 A use of a hybrid fluorocarbon-hydrocarbon surfactant C7F15CH(OSO⫺3 Na⫹)C7H15 for the purpose of creating water in carbon dioxide microemulsions [55]. The water-to-surfactant ratio in a single-phase microemulsion was found to be as high as 32 at 25⬚C and 231 bar. Over 150 surfactants were studied in scCO2 microemulsion systems and none were shown to take up more than a few water molecules per surfactant molecule [56–58]. Subsequent work by this group employed an ammonium carboxylate perfluoropolyether surfactant, [(OCF2CF(CF3))n(OCF2)m]OCF2COO⫺NH⫹4 , in the formation of aqueous microemulsion droplets in CO2. Indeed, the incorporation of CO2 functional groups facilitates high solubility of water in these systems [59]. Further work concerning microemulsion formation in nonpolar supercritical fluids has been published in two reviews [60,61]. VI.

DENDRITIC SURFACTANTS

Cooper et al. showed that dendrimers with fluorinated shells not only are soluble in CO2 but also are powerful aids in transporting CO2-insoluble molecules into the solvent [62]. Extending the methods developed by Meijer, a forth-generation hydrophilic dendrimer, DAB-denr-(NH2, )32, was functionalized by a heptamer acid fluoride of hexafluoropropylene oxide, CF3CF2 ⭈ CF2(OCF(CF3)CF2)5-OCF(CF3C(O)F (Scheme 3) [63]. This generated a well-defined, unimolecular dendritic ‘‘micelle’’ with a CO2-philic shell and a hydrophilic core. The functionalized dendrimer was insoluble in water and most common organic solvents but soluble in CO2 at very moderate conditions (room temperature and 76 bar). However, the unfunctionalized dendrimer was insoluble in CO2 under the same conditions. The radius of gyration and mass of the dendrimer measured ˚ and in CO2 at 25⬚C and 340 bar by SANS were 30.0 A 3.35 ⫻ 103 g/mol, respectively. Spectroscopic analysis and extraction studies (Fig. 11) demonstrate that the dendritic micelle can transfer

SCHEME 3 celle.

Synthesis of the unimolecular dendritic mi-


141

FIG. 12 SANS scattering curve for PVAc-b-PFOA in CO2 as a function of pressure (Mn,PVAc = 10.3 kg/mol; Mn,PFOA = 63.1 kg/mol).

behavior of polymeric surfactants in CO2 [65]. Aided by high-power lasers, static and dynamic light scattering (DLS) methods have also proved to be powerful, reliable, and readily assessable techniques for studying the characteristics of polymers in CO2. Very detailed studies of PVAc-bPFOA and PVAc-b-poly(1,1,2-tetrahydroperfluorooctyl acrylate) PTAN copolymers, both of which exhibited the CMD transition, have been reported [66]. Figure 13 shows the hydrodynamic size plotted against CO2 density for a PVAc-b-PTAN (PVAc: Mn = 10.3 kg/mol/ PTAN: Mn = 60.4 kg/mol) solution. As predicted by SANS data, in the low-density range there are 15-nm spherical micelles. As the density was increased, the CMD transition region appeared leading into the 3- to 4-nm unimer region. In addition to showing the CMD, DLS data were used to show the coexistence of unimers and micelles in the transition region. This coexistence prompted the construction of a copolymer surfactant–CO2 binary phase diagram. The concentration (ranging from 0.0001 to 1 g/cm3) versus carbon dioxide density phase diagram for the PVAc-b-PTAN surfactant at 45⬚C is shown in Fig. 14. Three regions on the phase diagram can be identified: a two-phase region at CO2 densities below 0.82 g/cm3 where the polymer was insoluble and phase separated into polymer-rich and solvent-rich phases, a region of spherical micelles at intermediate CO2 densities, and a unimer region at high densities. The coexistence line connecting the micelle and unimer phases indicates not only the CMD at constant copolymer concentrations but also the critical micelle concentration at constant CO2 density. The CMD phenomenon implicates reversible control of self-assembly of polymeric surfactant in CO2. To

FIG. 13 Effect of the CO2 density on the hydrodynamic radius for a copolymer concentration: (a) c = 1.88 ⫻ 10⫺3 g/ cm3, (b) c = 3 ⫻ 10⫺3 g/cm3, (c) c = 6 ⫻ 10⫺3 g/cm3, (d) c = 1.125 ⫻ 10⫺2 g/cm3, and (e) c = 2 ⫻ 10⫺2 g/cm3 at temperature T = 45⬚C. Dashed lines indicate the onset of the micelles-to-unimers transition. (Adapted from Ref. 64.)

explore CMD possibilities further, a series of welldefined poly(tert-butylmethacrylate) (PTBM)-b-poly(fluorooctylmethacrylate) (PFOMA) samples with varying PTBM lengths have been synthesized (E. Yoshida et al., in preparation). These are the first series of diblock copolymers containing fluoropolymer segments made by anionic polymerization. The polymers have controlled molar masses and narrow molar mass and chemical composition distributions. With varied PTBM lengths, a series of phase diagrams have been generated

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13.

14. 15. 16. 17. 18. 19. FIG. 14 Phase diagram in the copolymer–CO2 density plane at a fixed temperature T = 45⬚C. Points (●) represent the cloud line (solubility line), points (⽧) represent the spherical micelles-unimers transition, and points (䡩) represent the overlap concentration C*. (Adapted from Ref. 65.)

for PTBM-b-PFOMA block copolymer solutions at 25⬚C. These phase diagrams illustrate how the CO2surfactant system can be manipulated and tailored to fit particular applications by small changes in both copolymer composition and CO2 density. These innovative tools could have a major impact on CO2 cleaning and extraction processes.

20. 21. 22.

23. 24. 25. 26.

27.

REFERENCES 1. 2. 3. 4.

5. 6. 7. 8. 9. 10.

K. Zosel, U.S. Patent 3,806,619 (1974). R. Prasad, M. Gottesman, and R. Scarella, U.S. Patent 4,341,804 (1982). P. Villard, J. Phys. 5:455 (1896). S. Barer and K. Stern in Catalytic Activation of CO2 (S. Barer and K. Stern, eds.), American Chemical Society, Washington, DC, 1988, p. 1. D. Canelas and J. M. DeSimone, Chemistry in Britain August:38 (1998). T. Romack, E. Maury, and J. DeSimone, Macromolecules 28:912 (1995). F. Keyes and J. Kirkwood, Phys. Rev. 36:754 (1930). K. O’Shea, K. Kirmse, M. Fox, and K. Johnston, J. Phys. Chem. 95:7863 (1991). J. Hyatt, J. Org. Chem. 49:5097 (1984). K. Bartle, A. Clifford, S. Jafar, and G. Shilstone, J. Phys. Chem. 20:728 (1991).

28.

29.

30. 31.

32. 33. 34.

M. King, A. Mubarak, J. Kim, and T. J. Bott, Supercrit Fluids 5:296 (1992). M. McHugh and V. Krukonis, Supercritical Fluid Extraction: Principles and Practice, 2nd ed., ButterworthHeinemann, Stoneham, MA, 1994. I. Sanchez and C. Panayiotou, in Equation of State Thermodynamics of Polymer and Related Solutions (I. Sanchez and C. Panayiotou, eds.), Marcel Dekker: New York, 1993, pp. 187–285. M. O’Neill, Q. Cao, M. Fang, and K. Johnston, Ind. Eng. Chem. Res. 37:3067–3079 (1998). I. Yilgor, J. McGrath, and V. Krukonis, J. Polym. Bull. 12:499 (1984). V. Krukonis, Polym. News 11:7 (1985). Z. Guan, J. C. Y. Menceloglu, and J. DeSimone, Macromolecules 26:2663 (1993). J. DeSimone, Z. Guan, and C. Elsbernd, Science 257: 945 (1992). Z. Guan, J. Combes, C. Elsbernd, and J. DeSimone, Polym. Prepr. (Am. Chem. Soc. Div. Polym. Chem.) 34:446 (1993). P. Ehrlich, Chemtracts Org. Chem. 6:92 (1993). J. DeSimone, Int. Patent Appl. PCT/US93/01626 (1993). V. Krukonis, Supercritical fluid fractionation: An alternative to molecular distillation, presented at AIChE Meeting, Houston, TX, March 1983. G. Dris and S. Barton, J. Appl. Polym. Sci. 55:773 (1995). Y. Xiang and E. Kiran, Polymer 36:4817 (1995). X. Zhao, R. Watkins, and S. Barton, J. Appl. Polym. Sci. 55:773 (1995). Z. Guan, C. Elsbernd, and J. DeSimone, J. Polym. Prepr. (Am. Chem. Soc. Div. Polym. Chem.) 34:329 (1992). J. B. McClain, D. Londono, J. R. Combes, T. J. Romack, D. A. Canelas, D. E. Betts, G. D. Wignall, E. T. Samulski, and J. M. DeSimone, J. Am. Chem. Soc. 118: 917–918 (1996). D. Chillura-Martino, R. Triolo, J. B. McClain, J. R. Combes, D. E. Betts, D. A. Canelas, J. M. DeSimone, E. T. Samulski, H. D. Cochran, J. D. Londono, and G. D. Wignall, J. Mol. Struct. 383:3 (1996). E. Maury, H. Batten, S. Killian, Y. Menceloglu, J. Combes, and J. DeSimone, Polym. Prepr. (Am. Chem. Soc. Div. Polym. Chem.) 34:664 (1993). D. Zhu and Z. Schelly, Langmuir 8:48 (1992). J. L. Fulton, D. M. Pfund, J. B. McClain, T. J. Romack, E. E. Maury, J. R. Combes, E. T. Samulski, J. M. DeSimone, and M. Capel, Langmuir 11:4241 (1995). J. DeSimone, E. Maury, Y. Menceloglu, J. McClain, T. Romack, and J. Combes, Science 265:356 (1994). Y. Hsiao, E. Maury, and J. DeSimone, Macromolecules 28:8159–8166 (1995). D. Canelas, D. Betts, and J. DeSimone, Macromolecules 29:2818 (1996).

Surfactants for Supercritical Fluids 35. 36.

37.

38. 39. 40. 41.

42. 43.

44. 45. 46. 47. 48.

49. 50. 51.

Z. Guan and J. DeSimone, Macromolecules 27:5527 (1994). J. D. Londono, R. Dharmapurikar, H. D. Cachran, G. D. Wignall, J. B. McClain, D. E. Betts, D. A. Canelas, J. M. DeSimone, E. T. Samulski, D. Chillura-Martino, and R. Triolo, J. Appl. Crystallogr. 30:690–695 (1997). A. Dardin, J. B. Cain, J. M. DeSimone, C. S. Johnson, and E. T. Samulski, Macromolecules 30:3593–3599 (1997). D. Canelas, D. Betts, and J. DeSimone, Macromolecules 31:6794 (1998). A. Cooper, W. Hems, and A. Holmes, Macromolecules 32:2156 (1999). R. Mertsch and B. Wolf, Macromolecules 27:3289 (1994). C. Elsbernd, J. DeSimone, A. Hellstern, S. Smith, P. Gallagher, V. Krukonis, and J. McGrath, Polym. Prepr. (Am. Chem. Soc. Div. Polym. Chem.) 31:673 (1990). T. Hoefling, D. Newman, R. Enick, and E. J. Beckman, J. Supercrit. Fluids 6:165 (1993). M. Yates, K. Lim, G. Li, J. Shim, S. Maniar, K. Johnston, and S. Webber, Macromolecules 32:1018–1026 (1999). D. Canelas and J. DeSimone, Macromolecules 30: 5673–5682 (1997). T. Hoefling, D. Stofesky, M. Reid, E. Beckman, and R. Enick, J. Supercrit. Fluids 5:237 (1992). D. Newman, T. Hoefling, R. Beitle, E. Beckman, and R. Enick, J. Supercrit. Fluids 6:205 (1993). F. A. Adamsky and E. J. Beckman, Macromolecules 27: 312–314 (1994). A. Yazdi, C. Lepilleur, E. Singley, W. Liu, A. Adamsky, R. Enick, and E. Beckman, Fluid Phase Equilibria 117: 297 (1996). A. Yazdi and E. J. Beckman, Mater. Res. 10:530 (1995). C. Lepilleur and E. Beckman, Macromolecules 30:745 (1997). E. Ghenciu and E. Beckman, Ind. Eng. Chem. Res. 36: 5366 (1997).

143 52. 53. 54.

55. 56. 57. 58. 59.

60. 61.

62.

63. 64.

65. 66.

J. Fulton and R. Smith, J. Phys. Chem. 92:2903 (1988). R. Lemert, R. Fuller, and K. Johnston, J. Phys. Chem. 94:6021 (1990). K. Johnston, G. McFann, and R. Lemert, in ACS Symposium Series 406 (K. Johnston, G. McFann, and R. Lemert, eds.), American Chemical Society, Washington, DC, 1989. K. Harrison, J. Goveas, K. Johnston, and I. O’Rear, Langmuir 10:3536 (1994). J. Oates, Ph.D. dissertation, University of Texas at Austin, 1989. K. Consani and R. J. Smith, J. Supercrit. Fluids 3:51 (1990). G. McFann, K. Johnston, and S. Howdle, AIChE J. 40: 543 (1994). K. Johnston, K. Harrison, M. Clarke, S. Howdle, M. Heitz, F. Bright, C. Carlier, and T. Randolph, Science 271:624 (1996). K. Bartscherer, M. Minier, and H. Renon, Fluid Phase Equilibria 107:93 (1995). G. McFann and K. Johnston, Microemulsions: Fundamental and Applied Aspects, Marcel Dekker, New York, 1999. A. I. Cooper, J. D. Londono, G. Wignall, J. B. McClain, E. T. Samulski, J. S. Lin, A. Dobrynin, M. Rubinstein, A. L. C. Burke, J. M. M. Frechet, and J. M. DeSimone, Nature 389:368 (1997). S. Stevelmans, J. Am. Chem. Soc. 118:7398–7399 (1996). J. B. McClain, D. E. Betts, D. A. Canelas, E. T. Samulski, J. M. DeSimone, J. D. Londono, H. D. Cochran, G. D. Wignall, D. Chillura-Martino, and R. Triolo, Science 274:2049 (1996). E. Buhler, A. V. Dobrynin, J. M. DeSimone, and M. Rubinstein, Macromolecules 31:7347 (1998). S. Zhou and B. Chu, Macromolecules 31:7746–7755 (1998).

6 Acid- and Oxidatively Labile Vinyl Ether Surfactants: Synthesis and Drug Delivery Applications JONG-MOK KIM and DAVID H. THOMPSON

I.

Purdue University, West Lafayette, Indiana

OVERVIEW OF LAMELLAR-HEXAGONAL PHASE TRANSITIONS TRIGGERED BY CLEAVABLE SURFACTANTS

II) have been utilized for their ability to promote the HI phase, and 1,2-dioleoyl-sn-glycero-3-phosphoethanolamine (DOPE)—one of the most widely studied materials in membrane fusion research—has been employed in binary lipid mixtures to facilitate the formation of the HII phase upon exposure to a triggering impulse (Section III).

Liposomes have evolved during the last 35 years from a laboratory curiosity to an effective delivery vehicle for several important drugs. This was made possible by overcoming initial problems with reproducible particle size, plasma stability, high encapsulation efficiency, long circulation times, and selective deposition in vivo that were encountered with first-generation carrier systems. It is now clear that the great potential of liposomes as drug delivery vehicles will not be fully realized until more effective targeting and membrane fusion mechanisms have been designed and incorporated in their formulations. This chapter summarizes our recent advances toward these goals and the membrane fusion aspect of this challenge. An essential requirement of fusogenic liposomes is that they display compositional and mechanical stability during systemic circulation yet undergo sufficient structural transformation upon exposure to an applied stimulus that they promote rapid fusion with target cell membranes. Many candidate systems have been investigated for these properties [1–3]; however, there are no generally applicable systems that display both fusogenicity and plasma stability. Our work has focused on the development of new triggerable materials, based on the intrinsic lipid curvature model (Fig. 1) [4,5], that are designed to undergo L␣, HI, or HII phase transitions upon exposure to either acidic or oxidative environments. Plasmenylcholine-type phospholipids (Section

II.

PLASMENYLCHOLINE AND DISPLASMENYLCHOLINE LIPOSOME SYSTEMS

Plasmenylcholine (also known as plasmalogen) and diplasmenylcholine are naturally occurring Z-vinyl ether–linked phospholipids [6]. Although only one source of diplasmenylcholine has been reported, plasmenylcholine is widely distributed in mammals, particularly in electrically active tissues. Little is known about their role in biological systems. Plasmenylcholines and plasmenylethanolamines are highly enriched in arachidonate at the sn-2 position. This observation has led to the proposal that their role in biology is as a nascent source of arachidonic acid for the initiation of signal transduction pathways. One structural study has even suggested that the sn-1 Z-vinyl ether linkage enforces a unique glycerol backbone conformation at the membrane-water interface, thereby providing an interfacial signature for phospholipase recognition of the arachidonate-rich plasmenyl lipid pool [7]. An alternative proposal for their occurrence is to serve as a membrane-localized antioxidant [8]. The latter hypoth145

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FIG. 1

Intrinsic curvature and lipid packing morphology.

esis is closely related to the strategy we have employed for photooxidative triggering of the lamellar-hexagonal I phase transition in plasmenylcholine-based liposome systems (Sections II.B and II.C). A second triggering pathway is also possible by taking advantage of the known sensitivity of vinyl ether bonds to acidic conditions (Scheme II.D) [9]. These reactions, both of which convert a double-chain lamellar phase forming lipid into single-chain HI surfactants (Fig. 2), are the foundation for creating liposomes that can be triggered to undergo L␣-HI phase transitions.

A.

Lipid Synthesis

Early triggered-release experiments with plasmenylcholine liposomes utilized semisynthetic palmitoylplasmenylcholine (PPlsC) derived from bovine heart phosphatidylcholine [10–12]. Total syntheses have been developed in our laboratory for both plasmenylcholine (Fig. 3) [13] and diplasmenylcholine (Fig. 4) [14,15]. Bittman and coworkers have also recently reported a plasmenylcholine synthesis using alkynyl ethers as the key synthetic intermediate [16].

FIG. 2 Plasmenylcholine photooxidation and acid-catalyzed hydrolysis reactions (top) and the resulting L␣-HI phase change that vinyl ether bond cleavage produces (bottom).

Labile Vinyl Ether Surfactants

FIG. 3

B.

147

Total synthesis of plasmenylcholine from monopalmitin [13].

Photooxidative Triggering of Plasmenylcholines [10,11]

Irradiation of PPlsC liposomes that contain bacteriochlorophyll (solubilized within the membrane bilayer) and calcein (entrapped in the inner aqueous compartment at self-quenching concentrations) produces release of contents as detected by calcein fluorescence dequenching (Fig. 5). Release rates were shown to be dependent on fluency, oxygen concentration, and plasmenylcholine concentration.

FIG. 4

Electron microscopic (EM) evidence also indicated that the liposome morphology changed during the course of the photolysis, from lamellar to multilamellar with interlipidic particles, as a result of membranemembrane fusion events. Time-resolved EM experiments also suggested that these changes occurred on the same kinetic time scale as contents release. A model involving membrane fusion at photooxidized lesions between adjacent liposomes was proposed for this system. Repetitive cycles of this process are thought to be responsible for the accumulation of multilamellar lipid.

Total synthesis of diplasmenylcholine from solketal [15,16].

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FIG. 5 (Top) Photorelease of calcein from Bchl:PPlsC liposomes using 800-nm excitation under various experimental conditions. (Bottom left) Freeze-fracture TEM micrograph before liposome irradiation. (Bottom center) Cryo-TEM micrograph taken after 5 min of irradiation. (Bottom right) Freeze-fracture TEM micrograph 48 h after liposome irradiation. (Data from Ref. 11.)


C.

Cascade Triggering of Diplasmenylcholines

Photooxidation of diplasmenylcholine liposomes bearing internalized control elements such as catalysts or cofactors offers intriguing possibilities to either transduce or amplify the initial photochemical process. It can also reduce the amount of diplasmenylcholine required to elicit a release response. This principle was demonstrated using Bchl-containing dipalmitoylplasmenylcholine (DPPlsC) liposomes with internalized calcium ions. Because Ca2⫹ is a required cofactor for calcium-dependent phospholipase A2 (CD-PLA2) activity, release from a second population of CD-PLA2 – sensitive liposomes (e.g., dipalmitoylphosphatidylcholine, DPPC) can be controlled by phototriggering the release of Ca2⫹ from DPPlsC liposomes. This elicits a cascade response wherein phototriggered Ca2⫹ activates DPPC liposome contents release via CD-PLA2 hydrolysis (Fig. 6). Bchl:DPPlsC liposomes irradiated at 800 nm in the presence of oxygen were observed to release their internalized calcium ions rapidly. After a brief lag period, presumably for CD-PLA2 activation and hydrolysis of a critical amount of DPPC, contents release from the DPPC liposomes was also observed (Fig. 7). The cascade reaction is made possible in this case because diplasmenylcholine liposomes are insensitive to CD-PLA2 hydrolysis, so they can retain their contents even in the presence of phospholipase. Because calcium ion concentrations are so tightly regulated in biology, there is a potentially wide array of Ca2⫹-based cascade processes that could be addressed

FIG. 6

149

using this concept. Nonbiological reactions (e.g., calcium phosphate mineralization) could also be controlled in a spatiotemporal manner using this cascade reaction principle. D.

Drug Delivery via Acid-Catalyzed Triggering of Diplasmenylcholines [18]

Contents release from DPPlsC liposomes is also triggerable under acidic conditions, with release rates that vary as a function of solution pH (Fig. 8). Because the observed release rate at pH 4.5 gave a t50% release of approximately 90 min, these liposomes were tested for their ability to undergo intracellular triggering upon exposure to acidic endosomes that can achieve a pH of 5. A folate receptor–mediated uptake pathway was chosen as the route of entry into the endosomal compartment (Fig. 9). KB cells, cultured in folate-deficient media to stimulate the overexpression of folate receptors, were used as the test system for contents release from folate-targeted DPPlsC liposomes. After exposure to propidium iodide–loaded DPPlsC liposomes containing 0.5 mol% folate-conjugated poly(oxyethylene)distearoylphosphatidylethanolamine (PEG-DSPE) for 4 h, the cells were washed and monitored for their distribution of propidium iodide fluorescence. Within 8 h of the washing step, the cells had become extensively stained with propidium iodide, suggesting that the liposomal contents had efficiently escaped both the liposomal and endosomal compartments. These observations were supported by a similar experiment with arabinofuranosylcytosine (AraC). As the data in Fig. 10

Conceptual diagram of cascade triggering. (Adapted from Ref. 17.)

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exceptionally low plasma stability and poor cell uptake characteristics because of their enzymatic lability, size, and hydrophilicity. III.

FIG. 7 Cascade release of Ca2⫹ and calcein from Bchl: PEG-DPPE:DPPlsC and DPPC liposomes, respectively, upon irradiation at 800 nm (37⬚C). Note that little appreciable release occurs from either liposome in the absence of light. (Data from Ref. 17.)

show, AraC delivered via folate-targeted DPPlsC liposomes is 6000-fold more cytotoxic than the free drug and 100-fold more toxic than the folate-targeted drug encapsulated within a pH-insensitive liposome. These results clearly demonstrate a synergistic enhancement of AraC activity when endosomal targeting and acid triggering mechanisms are combined within a DPPlsC liposomal delivery vehicle. They also suggest that substantially improved biological responses may be attainable with other water-soluble drugs if a similar delivery approach is used. This may be particularly important for peptides, plasmids, and oligonucleotides that have

Kirpotin et al. have reported a dePEGylative triggering approach using 3–6 mol% of a thiol-cleavable poly(ethylene glycol)-grafted distearoylphosphatidylethanolamine as guest lipid to stabilize the lamellar phase of DOPE [19]. Treatment of N-(2-(␻-methoxypoly(oxyethylene)-␣ -aminocarbonyl)ethyl)dithioproionyl-DSPE (mPEG-DTP-DSPE):DOPE liposomes with dithiothreitol (DTT) leads to cleavage of the liposomal steric stabilization layer and ‘‘unmasking’’ of the latently fusogenic, DOPE-rich liposomes. Clearance of PEG from the liposome surface destabilizes the lamellar phase, leading to membrane fusion and contents release promoted by the HII phase. This strategy retains the appealing characteristics of plasma stable, long-circulating liposomes prior to thiol cleavage, but unfortunately, the high concentrations of thiolytic agent required (10 mM DTT) to effect liposome destabilization greatly limits the potential of this method in vivo. This problem has been addressed with a new thiol-cleavable PEG-lipid conjugate, but the concentrations of thiol required to activate the system are still quite high [20]. Lipid phase transitions induced by dePEGylation have also been described by Holland et al. [21]. This method is based on exchange of the PEG coating (2 mol% PEPEG2000 in 1:1 POPS:DOPE liposomes) onto an acceptor population of ‘‘sink’’ 1-palmitoyl-2-oleylphosphatidylcholine (POPC) liposomes. DePEGylation of these liposomes produces membrane fusion in the presence of calcium ions with rates that are dependent on the molar ratio of PEG-lipid initially present as well as the chain length and degree of unsaturation of the lipid anchor. A.

FIG. 8 Calcein leakage rates from DPPlsC liposomes at 37⬚C. (●) pH 2.3; (䡲) pH 3.2; (䊱) pH 4.5; (⽧) pH 5.3; (䡩) pH 6.3. (Data from Ref. 18.)

DEPEGYLATIVE TRIGGERING OF DOPE: VINYL ETHER–LINKED POLY(ETHYLENE GLYCOL) LIPOSOMES

Synthesis of a Vinyl Ether PEG Lipid Conjugate

We have also investigated dePEGylative triggering based on the same vinyl ether degradative reactions reported for plasmenylcholine and diplasmenylcholine liposomes (Fig. 11) [12,18]. DOPE liposomes were stabilized as a lamellar phase by incorporation of 1–5 mol% 1,2-di-O-(1Z⬘,9Z⬘-octadecadienyl)-sn-glycero-3poly(␻-methoxyethylene[115]glycol)ate (BVEP). This

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FIG. 11 Diffusion of methyl orange from an aqueous solution (upper phase in figure) into a unimolecular dendritic micelle in liquid CO2 (lower phase) at 23.5⬚C, 340 atm. Video images taken 1 min (a), 6 min (b), 30 min (c), and 150 min (d) after the addition of CO2. (Adapted from Ref. 61.)

methyl orange, a CO2-insoluble ionic dye, from aqueous solution into carbon dioxide. When there was an excess of the dendrimer molecule, analysis showed that no residual dye was detected in the aqueous phase, indicating complete extraction from the aqueous layer. The maximum number of methyl orange molecules extracted per dendritic core was approximately 12, calculated from the ultraviolet spectroscopy. The maximum number of extracted molecules (seven) was lower when a larger dye molecule, rose bengal, was extracted. VII.

NEW FRONTIERS—REVERSIBLE CONTROL OF SELF-ASSEMBLY

McClain et al. were the first to postulate the existence of a critical micelle density (CMD), analogous to a critical micelle concentration, where polymeric surfactants undergo a unimer-to-aggregate transition in supercritical fluids on changing the solvent (quality) density [64]. In the PS-b-PFOA systems, when the solvent density was increased, smaller and more polydisperse micelles formed. The decrease in the size of the micelles was attributed to the increased solvation of both

the PS and PFOA blocks, thereby decreasing the aggregation number and the size of the micelles. Although there was a decrease in aggregation number with increasing CO2 density, the data did not indicate that the micelles actually broke apart into single chains in the range of densities studied. A true CMD transition was realized when Triolo et al. studied the solution properties of PVAc-b-PFOA diblock copolymers in CO2 by SANS and SAXS (R. Triolo et al., unpublished results). Figure 12 shows the SANS scattering curve for 6 w/v% of a PVAc-b-PFOA (PVAc: Mn = 10.3 kg/mol; PFOA: Mn = 63.1 kg/mol) sample in CO2 at 45⬚C as a function of pressure. As the pressure (density) of the solution increased, there was a reduction in the size of the peak until the peak disappeared. The disappearance of this peak is indicative of the aggregate-to-unimer (single copolymer chains) transition, which occurred around 292 bar for this system. This first realization of a CMD has led to the synthesis, characterization, and study of a new series of molecularly engineered polymeric surfactants. Buhler et al. were the first to use high-pressure light scattering methods to study the micellization and CMD


FIG. 9

151

Conceptual model of endosomal uptake and release pathway for targeted DPPlsC liposomes and their contents.

acid-labile PEG conjugate was synthesized by coupling the corresponding PEG acid with 1,2-di-O-(1Z⬘,9Z⬘-octadecadienyl)-sn-glycerol (compound 6 in Fig. 4) in the presence of dicyclohexylcarbodiimide. B.

FIG. 10 Cytotoxicity of AraC to KB cells as a function of delivery vehicle. (●) Free AraC; (䡲) AraC encapsulated within folate-targeted egg phosphocholine liposomes (pH-insensitive control liposomes); (䊱) AraC encapsulated within folate-targeted DPPlsC liposomes.

Acid-Triggered Release Characteristics of DOPE:BVEP Liposomes

Acidification of binary DOPE:BVEP mixtures triggers vinyl ether hydrolysis and dePEGylation, with subsequent destabilization of the lamellar phase and contents release as the DOPE host lipid reverts back to its preferred hexagonal phase (Fig. 11). The onset of calcein leakage with time at pH 4.5 (Fig. 12) indicates that dePEGylative triggering can be achieved in acidic media at rates that are higher than in neutral solutions (pH 7.4). These acid-triggerable formulations are also relatively stable in 10% serum (data not shown). Collectively, these results suggest that the dePEGylative triggering approach may prove to be a useful technique

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FIG. 11 Conceptual diagram for dePEGylative triggering to induce a lamellar-hexagonal II phase transition. DOPE, 1,2dioleoyl-sn-glycero-3-phosphoethanolamine; BVEP, 1,2-di-O-(1⬘,9⬘-octadecadienyl)-sn-glycero-3-poly(␻-methoxyethylene[115]glycol)ate or any other labile PEG-lipid.

for promoting endosomal escape of liposomal contents via liposome-endosome membrane fusion (Fig. 9).

IV.

CATIONIC VINYL ETHER LIPIDS IN GENE DELIVERY

Many different cationic lipids have been synthesized for transfection applications. However, few of these compounds have been designed from a mechanistic standpoint to promote decomplexation and transgene expression in vivo. Because most of the effective DNA: cationic lipid complexes bear a net positive charge, their adsorption to the negatively charged cytoplasmic membrane surface leads, in most cases, to internalization via the endosomal uptake pathway. Gene expression can be limited at this stage if specific endosomal escape mechanisms have not been incorporated within the DNA delivery vector. It has become clear that the constitutive acidification that occurs within these transient compartments provides an intrinsic pathway for triggering intracellular contents release from appropri-

ately designed vehicles. Our approach for improving gene expression, therefore, is to promote DNA:cationic lipid decomplexation and endosomal escape using the same acid-catalyzed vinyl ether hydrolysis chemistry described earlier that is known to promote cytoplasmic delivery of hydrophilic materials.

FIG. 12 Calcein release kinetics from 97:3 DOPE:BVEP liposomes at 37⬚C. (●) pH 7.4; (▫) pH 4.5.


FIG. 13

A.

Synthesis of BCAT from 1,2-di-O-(1⬘,9⬘-octadecadienyl)-sn-glycerol [22].

Synthesis of BCAT

An adaptation of the DPPlsC/DOPlsC synthesis (Fig. 4) was used to prepare 1,2-di-O-(1Z⬘,9Z⬘-octadecadienyl)-sn-glyceryl-3-O-carbamoyldiethylenetriamine (BCAT) (Fig. 13). The cationic headgroup was installed using dipyridyl carbonate (DPC) in a standard carbamate coupling methodology. Alcohol 6 (i.e., compound 6 in Fig. 4) was added to DPC, generating a mixed carbonate intermediate that was subsequently displaced with N,N⬘-diphthalamidyldiethylenetriamine, giving a protected carbamate product. This intermediate was then deprotected with hydrazine hydrate to give BCAT (free base) in 56% isolated yield from 6 (16% overall yield from (S)-(⫹)-2,2-dimethyl-1,3-dioxolane-4-methanol). B.

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Uptake and Expression of DNA: Cationic Vinyl Ether Lipid Complexes

Flow cytometry was used to monitor cells treated with DNA complexes of BCAT, DCAT (a saturated analogue of BCAT), and DOTMA/Chol (a commercially available transfection agent). Psoralen-labeled DNA and green fluorescent protein (GFP) expression levels from

a GFP vector were monitored as a function of lipid type (Fig. 14) (J. A. Boomer, D. H. Thompson, and S. Sullivan, submitted). After a 2.5-h exposure to DNA:cationic lipid complexes, the DOTMA/Chol formulation showed the highest levels of DNA uptake (two- to fourfold higher than BCAT or DCAT). GFP expression levels, however, were substantially better with the BCAT and DCAT formulations in spite of their lower uptake levels. These observations underscore the utility of decomplexation and endosomal escape from labile lipid carriers. V.

CONCLUSIONS

These investigations indicate a promising future for drug and gene delivery applications using vinyl etherbased delivery systems. The most significant obstacles to their widespread use at this time are their lack of commercial availability and their relaively slow acid hydrolysis kinetics. Most of the desired applications of these materials will require activation of the lipid phase transition at pH values in the range of 5–6. This limitation can be addressed by varying the stereoelectronics of the vinyl ether or by increasing negative charge at the membrane interface. Once this problem has been surmounted, more flexible synthetic methods must be developed to simplify the preparation of many different classes of vinyl ether conjugate. Experiments in progress are aimed at addressing both of these impediments. ACKNOWLEDGMENTS The financial support of NIH Grant R01 55266 and the Purdue Research Foundation is greatly appreciated. The efforts of Mr. Junhwa Shin and Dr. Jeremy Boomer in assisting with the preparation of this manuscript are also gratefully acknowledged.

FIG. 14 Comparison of fluorescent DNA uptake with green fluorescent protein expression for various cationic lipid:DNA complexes in NIH 3T3 cells (J. A. Boomer, D. H. Thompson, and S. Sullivan, submitted).

REFERENCES 1.

O. V. Gerasimov, Y. Rui, and D. H. Thompson, in Vesicles (M. Rosoff, ed.), Marcel Dekker, New York, 1996, pp. 679–746.

154 2.

3.

4. 5. 6. 7. 8.

9.

10. 11.

Kim and Thompson O. V. Gerasimov, J. A. Boomer, M. M. Qualls, and D. H. Thompson, Adv. Drug Delivery Rev. 38:317–338 (1999). D. F. O’Brien and D. A. Tirrell, in Bioorganic Photochemistry, Vol. 2: Biological Applications of Photochemical Switches (H. Morrison, ed.), Wiley, New York, 1993, pp. 111–167. P. R. Cullis and B. deKruijff, Biochim. Biophys. Acta 559:399–420 (1979). J. N. Israelachvili, S. Marcelja, and R. G. Horn, Q. Rev. Biophys. 13:121–148 (1980). F. Paltauf, Chem. Phys. Lipids 74:101–139 (1994). X. Han and R. W. Gross, Biochemistry 29:4992–4996 (1990). R. A. Zoeller, A. C. Lake, N. Nagan, D. P. Gaposchkin, M. A. Legner, and W. Lieberthal, Biochem. J. 338:769– 776 (1999). J. R. Keeffe and A. J. Kresge, in The Chemistry of Enols (Z. Rappoport, ed.), Wiley, New York, 1990, pp. 399–480. V. C. Anderson and D. H. Thompson, Biochim. Biophys. Acta 1109:33–42 (1992). D. H. Thompson, O. V. Gerasimov, J. J. Wheeler, Y. Rui, and V. C. Anderson, Biochim. Biophys. Acta 1279: 25–34 (1996).

12. 13. 14. 15.

16. 17. 18. 19. 20.

21. 22.

O. V. Gerasimov, A. Schwan, and D. H. Thompson, Biochim. Biophys. Acta 1324:200–214 (1997). Y. Rui and D. H. Thompson, Chem. Eur. J. 2:1505– 1508 (1996). Y. Rui and D. H. Thompson, J. Org. Chem. 59:5758– 5762 (1994). Y. Rui, Stereocontrolled total syntheses of plasmalogen and diplasmalogen lipids and their activities in an intracellular drug delivery system, Ph.D. dissertation, Purdue University, West Lafayett, IN, 1996. D. Qin, H.-S. Byun, and R. Bittman, J. Am. Chem. Soc. 121:662–668 (1999). N. Wymer, O. V. Gerasimov, and D. H. Thompson, Bioconj. Chem. 9:305–308 (1998). Y. Rui, S. Wang, P. S. Low, and D. H. Thompson, J. Am. Chem. Soc. 120:11213–11218 (1998). D. Kirpotin, K. Hong, N. Mullah, D. Papahadjopoulos, and S. Zalipsky, FEBS Lett. 388:115–118 (1996). S. Zalipsky, M. Qazen, J. A. Walker, N. Mullah, Y. P. Quinn, and S. K. Huang, Bioconj. Chem. 10:703–707 (1999). J. W. Holland, C. Hui, P. R. Cullis, and T. D. Madden, Biochemistry 35:2618–2624 (1996). J. A. Boomer and D. H. Thompson, Chem. Phys. Lipids 99:145–153 (1999).

7 Three Principles for Active Control of Interfacial Properties of Surfactant Solutions JASON Y. SHIN, LANA I. JONG,* NIHAL AYDOGAN, and NICHOLAS L. ABBOTT University of Wisconsin–Madison, Madison, Wisconsin

I. A.

INTRODUCTION

solution and the dynamic surface tensions of freshly created surfaces of the solution. Finally, we illustrate how these three strategies for active control of surface tension can provide new principles for microfluidics where the behavior of liquids on millimeter and smaller scales are often dominated by interfacial stresses. We report the use of these surfactants to (1) achieve vectorial transport of droplets of liquid through a network of fluidic channels, (2) pattern the dewetting of liquids on energetically homogeneous surfaces, and (3) trigger, by using illumination, the release of pendant droplets of aqueous solutions from an array of capillaries.

Overview

Here we review three strategies that permit active control of interfacial properties of aqueous solutions of water-soluble surfactants. These strategies are based on the use of three water-soluble surfactants, each of which hosts either redox- or light-active groups, and make possible spatial and temporal control of the surface tension of aqueous solutions. The first strategy revolves around the oxidation and reduction of ferrocenebased surfactants such that changes in the oxidation state of the ferrocene substantially perturb the equilibrium partitioning of surfactant between an interface and bulk solution. The second strategy is based on reduction of a bolaform surfactant containing a disulfide bond. This transformation leads to the formation of monomeric, thiol-containing fragments. We demonstrate the use of this transformation to create nonequilibrium, interfacial states that possess surface tensions that are substantially lower than any equilibrium surface tensions measured in the same system. The third strategy revolves around a mixed surfactant system containing a water-soluble surfactant that hosts the photosensitive group azobenzene. We demonstrate that illumination of this surfactant system leads to substantial changes in both the states of aggregation of the surfactant in bulk

B.

Motivation

The three principles described in this chapter lead to spatial and temporal control of the interfacial properties of aqueous surfactant systems. The work described herein is motivated, in part, by the potential usefulness of these principles in microscale systems suitable for chemical synthesis and analysis. The development of simple and general principles for the pumping and positioning of liquids on submillimeter scales has the potential to enable fabrication of microanalytical systems that will make procedures such as blood chemistry analysis, flow cytometry and polymerase chain reactions, and DNA screening both rapid and inexpensive [1,2]. Current methods used to pump liquids within networks of channels, or to position liquids within arrays, generally rely on electrokinetic phenomena driven by high voltages (several kilovolts) [3,4], mechanical ac-

*Current affiliation: University of California, Davis, Davis, California. 155

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tuators that are complicated to fabricate and too expensive to be disposable [5], or passive fluid phenomena such as capillary wetting [6]. These methods are used to achieve largely serial manipulations of liquids within permanent channels that direct the liquid motion. Because the motions of liquids on submillimeter scales are generally dominated by the effects of interfacial stresses, we believe principles for spatial and temporal control of interfacial properties using redox- and lightactive surfactants will provide useful ways to move, position, and mix liquids using simple but highly functional microfabricated structures. In the following we review our recent efforts that have been directed toward this challenge. We first present three principles that permit active control of surface tension using redox- and light-active surfactants. Second, we illustrate the use of these principles for the control of liquids on millimeter and smaller scales.

II.

PRINCIPLE 1. TRANSFORMATIONS BETWEEN EQUILIBRIUM STATES: FERROCENYL SURFACTANTS

A.

Bulk Solution–Interface Equilibration

The first principle we describe for active control of interfacial properties of surfactant-based systems is based on use of redox-active surfactants and electrochemical methods [7–13]. The essential idea underlying the design of these surfactant systems is that a change in oxidation state of a surfactant can lead to a substantial change in the equilibrium partitioning of the surfactant between the bulk of the solution and the interface (Fig. 1a). The resulting transport of surfactant to or from the interface, as well as the change in state of surfactant at the interface, can lead to changes in interfacial properties. Although the concept of ‘‘active control’’ of interfacial properties of surfactant systems necessarily implies the study of systems away from equilibrium states, the essential element of the strategy described here is that transformations of surfactants that are performed slowly relative to relaxation times of solutions will give rise to time-dependent properties of systems that can be qualitatively understood from knowledge of the equilibrium properties of the system. When dealing with a well-mixed solution of an ionic surfactant with millimolar activity, the characteristic time for equilibration of the surface of the solution with the bulk is likely to be only a few seconds [14–16]. For example, using a value of the surface area per surfactant mole˚ 2/molecule and a diffusion coefficient of cule of 40 A

FIG. 1 Schematic illustration of three principles that permit active control of interfacial states of aqueous surfactant systems. (a) The first principle is based on the presence of an equilibrium between the interface and bulk solution. The transformation in the state of the surfactant (characterized by ␶3) takes place more slowly than processes that lead to the establishment of equilibrium between the interface and bulk solution (characterized by ␶1 and ␶2). (b) The second principle is based on a transformation in the state of surfactant hosted at an interface at a rate that is fast (characterized by ␶4) compared with the rate of desorption of the surfactant from the surface of the solution (characterized by ␶5). (c) The third principle is based on control of the extent of aggregation of the surfactant and thus its rate of transport to the surface of the solution. The time required to transport surfactant in aggregates to the surface (␶6) is large compared with the time required to disrupt the aggregates (␶7) and transport the monomeric species (␶8) to the surface.

Active Control of Interfacial Properties

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FIG. 2 Dynamic surface tension of an aqueous solution of 5 mM SDS measured using the maximum bubble pressure method. Surface tension is plotted as a function of the bubble interval. (Data from Ref. 16.)

10⫺6 cm2/s, ␶d, the characteristic time for diffusive transport of surfactant from bulk solution to the surface, is only ⬃0.1 s (see Section IV). This estimate of the diffusion time is consistent with experimental measurements of dynamic surface tensions of aqueous solutions of ionic surfactants (Fig. 2). Thus, an electrochemical process that gives rise to a change in state of a solution of redox-active surfactant over a period of a few tens of seconds will probably result in a series of interfacial states that can be largely understood from knowledge of the composition of the bulk solution. In summary, the strategy described in this section for active control of interfacial properties considers the system to follow a path of near-equilibrium states (i.e., the path is quasi-reversible). The design rule describing this pathway is, therefore, simply the equality of chemical potential of the surfactant species at the surface and in the bulk:

␮bulk = ␮interface B.

is therefore an electrically neutral complex. The com˚ 3 (roughly three times the plex has a volume of ⬃150 A volume of a methyl group) and low solubility in water (5 ⫻ 10⫺5 M) [20]. Ferrocene, when hosted in surfactants having the preceding structure, can undergo a reversible one-electron oxidation in aqueous solution to form the ferrocenium cation. The redox potential for the oxidation is typically around 0.15 V (versus saturated calomel electrode, [SCE]). Oxidation of the ferrocene to the ferrocenium cation transforms the ferrocenyl surfactant with a single ionic headgroup to a surfactant with two ionic headgroups (one at each end of the molecule). We have synthesized ferrocenyl surfactants with n = 8 (Iⴙ), 11 (IIⴙ), and 15 (IIIⴙ) as well as a dimeric ferrocenyl surfactant (DI2ⴙ) (Fig. 3).

(1)

Ferrocenyl Redox Chemistry

Here we illustrate this first principle for active control of interfacial properties using results from our studies of a series of ferrocenyl surfactants that have the structure Fc(CH2)nN⫹(CH3)3Br⫺, where Fc is the redoxactive ferrocene group [7–13]. A surfactant with this structure (n = 11) was first synthesized by Saji and coworkers and subsequently used in studies of the deposition of thin films of organic dyes on electrodes [17– 19]. The ferrocene group consists of an Fe2⫹ ion sandwiched between two cyclopentyldienyl anions, and it

FIG. 3

Molecular structures of four ferrocenyl surfactants.

158

Figure 4 shows equilibrium surface tensions of aqueous solutions (0.1 M Li2SO4, pH 2) of II⫹ and II2⫹ that were measured using the Wilhelmy plate method (and confirmed using the pendant drop and du Nouy methods). The reduced surfactant (II⫹) has a critical micellar concentration (cmc) of 0.1 mM and a limiting surface tension of 49 mN/m (measured at concentrations above the cmc). The oxidized surfactant (II2⫹) is not measurably surface active below concentrations of 0.1 mM. Oxidation of II⫹ and II2⫹ at a concentration of 0.1 mM, therefore, changes the equilibrium surface tension of the aqueous solution from 49 to 72 mN/m. The oxidation of II⫹ and II2⫹ is reversible over many cycles, and we have found that the reduction of II2⫹ to II⫹ results in a return of the equilibrium surface tension to 49 mN/m (see later). The results in Fig. 4 demonstrate that the equilibrium surface tension of an aqueous solution of 0.1 mM II⫹ is substantially lower than the equilibrium surface tension of a 0.1 mM solution of II2⫹. We have also measured dynamic surface tensions of solutions of these surfactants as the solutions were cycled in composition (> nine cycles) on time scales of minutes by repeatedly oxidizing and reducing II⫹/II2⫹ (using electrochemical methods). The measurements of dynamic surface tension were performed with a maximum bubble pressure tensiometer (Fig. 5) with a bubble rate of 0.3 to 1.0 bubbles/s. Although the dynamic surface tensions of the aqueous solutions of 0.1 mM II⫹ measured by using the maximum bubble pressure method are higher by ⬃8 mN/m than the equilibrium ones measured by using the Wilhelmy plate, the qualitative response of the system during the oxidation of II⫹ to II2⫹ in Fig. 5 can be understood in terms of the changes in equilibrium surface tension shown in Fig. 4. That is, the process of oxidation of II⫹ to II2⫹ leads to an increase in surface tension, whereas the reverse process leads to a decrease in surface tension. In the following, by using disulfide-based surfactants and transformations that are faster than those shown here using ferrocenyl surfactants, we demonstrate that the correspondence between dynamic surface tension during a change in state of a surfactant and the equilibrium properties of the system does not always hold. The measurements shown in Fig. 4 reveal that the largest changes in equilibrium surface tension (⬃23 mN/m) upon oxidation of II⫹ to II2⫹ occur at a concentration of 0.1 mM. At concentrations of surfactant above 0.1 mM, the change in surface tension upon oxidation of II⫹ to II2⫹ is smaller than the maximum value (22 mN/m at 0.1 mM) because the surface tensions of the solutions of II2⫹ are lower than the surface tensions

Shin et al.

FIG. 4 Equilibrium surface tensions of aqueous solutions (0.1 M Li2SO4, pH 2, 25⬚C) of II⫹ (open circles) and II2⫹ (filled circles) as measured by the Wilhelmy plate method. The lines show surface tensions predicted by a molecular thermodynamic model of Gibbs monolayers of these surfactants. See text for details.

of the aqueous solution of electrolyte (not containing surfactant). We found that the surface tension of aqueous solutions of II2⫹ decreases with increasing concentration of II2⫹ without any sign of a cmc. Surprisingly, at concentrations above 10 mM, oxidation of II⫹ to II2⫹

FIG. 5 Dynamic surface tensions of an aqueous solution (0.1 M Li2SO4, pH 2, 25⬚C) of 0.3 mM II⫹/II2⫹ measured during repeated electrochemical cycling of the surfactant between oxidized (II2⫹) and reduced (II⫹) states. The dynamic surface tensions were measured by the maximum bubble pressure method at a bubble rate of 0.3 to 1 bubble/s.


no longer leads to an increase in surface tension but rather results in a decrease in the surface tension. This decrease in surface tension can be reversed by reduction of II2⫹ back to II⫹. We also point out that the changes in surface tension shown in Fig. 4 have been observed when using both chemical [Fe2(SO4)3 as oxidizer] and electrochemical oxidation of II⫹ to II2⫹. By using the Gibbs adsorption equation [21], we estimate the limiting surface areas occupied by molecules of II⫹ ˚ 2, respectively. and II2⫹ to be 85 ⫾ 4 and 65 ⫾ 4 A This result is also somewhat surprising because it suggests that oxidation of II⫹ to II2⫹ at concentrations greater than ⬃1 mM leads to an increase in the excess surface concentration of these surfactants even though the charge carried by each surfactant is increased upon oxidation. In order to understand the origin of the interfacial behavior of II⫹ and II2⫹ just described, we developed a molecular thermodynamic model for Gibbs monolayers of these surfactants. The model, which is described in detail elsewhere [13], assumes that equilibrium exists between surfactants dissolved in the bulk solution and at the interface [Eq. (1)]. The results of the model are in good agreement with experimental measurements of surface tension (Fig. 4) and offer several insights into the balance of forces that controls the surface activity of ferrocenyl surfactants. First, the model reveals that the limiting surface area occupied by a molecule of II⫹ hosted within a Gibbs monolayer is large because II⫹ adopts a looped conformation at the surface of the aqueous solution (Fig. 6). This looped configuration is a result of an effective attraction between the ferrocene group of the surfactant and the aqueous subphase. Second, the model indicates that the

FIG. 6 Schematic illustrations of typical conformations assumed by II⫹ and II2⫹ within Gibbs monolayers at the surfaces of aqueous solutions.

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desorption of surfactant from the surface of the solution, which accompanies oxidation at a 0.1 mM solution to II⫹ to II2⫹, is caused by a reduction in the hydrophobic driving force for adsorption and a change in the electrostatic contribution to the standard free energy of formation of the Gibbs monolayer. In particular, the configurational (chain packing) contribution to the standard free energy of formation of the monolayer does not drive the oxidation-induced desorption of the surfactant from the surface of the solution because the surfactant adopts a looped conformation in both oxidized and reduced states. Third, the model also offers an explanation of the oxidation-induced adsorption of the ferrocenyl surfactant to the surface of a solution containing high (>1 mM) concentrations of the surfactant. As noted earlier, aqueous solutions of II⫹ have a cmc of 0.1 mM, and thus at concentrations greater than 0.1 mM II⫹, the chemical potential of the surfactant changes little with concentration. In contrast to aqueous solutions of II⫹, II2⫹ was found not to aggregate in solutions containing up to 30 mM of II2⫹ (the highest concentration investigated). That is, oxidation of II⫹ in aqueous solutions with concentrations of II⫹ between 0.1 and 30 mM leads to the dissolution of micelles of II⫹ to singly dispersed molecules of II2⫹. Accompanying the disruption of the micelles is an increase in the cratic (concentration-dependent part of the chemical potential) contribution to the chemical potential of the surfactant in the aqueous solution (Fig. 7). For example, when the cratic contribution to the chemical potential is 0.58 (corresponding to the cmc of II⫹), the surface area of the solution occupied by a mol˚ 2. With the same cratic contribution ecule of II⫹ is 84 A to the chemical potential, molecules of II2⫹ occupy a larger surface area. At higher surfactant concentrations, the area occupied by each molecule for II2⫹ continues to decrease with increasing concentration. When the cratic contribution to the chemical potential is 5.15 (7 mM of oxidized surfactant), the surface area occupied by each molecule of II2⫹ is calculated to be as small ˚ 2. In short, upon oxidation, the dissolution of as 62 A micelles leads to an increase in the chemical potential of surfactant in bulk solution and thus a partitioning of surfactant toward the surface of the solution. The increase in the excess surface concentration of molecules as well as the increase in the charge carried by each surfactant molecule cause the decrease in surface tension of the solution that is measured upon oxidation at high concentrations of surfactant. The experimental measurements of surface tensions of aqueous solutions of II⫹ show that oxidation and reduction can lead to large (up to 23 mN/m) and re-

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FIG. 7 Calculated surface areas occupied by molecules of II⫹ and II2⫹ at surfaces of aqueous solutions as a function of the concentration-dependent part of the chemical potential. See text for details. The dashed arrow indicates the change in surface area per molecule that accompanies oxidation of II⫹ to II2⫹ at the surface of the 7 mM solution of surfactant.

versible changes in surface tension. However, the range of concentrations over which these changes in surface tension take place is limited (concentrations close to the cmc, Fig. 4). In order to increase the window of concentrations over which large changes in surface tension can be driven by using ferrocenyl surfactants, we explored the interfacial properties of the dimeric surfactant DI2⫹ (Fig. 3) [10]. Surface tension measurements of the dimeric ferrocenyl surfactant show that the onset of surface tension reduction for the reduced surfactant occurs at a concentration that is almost three decades lower than that of the oxidized surfactant (Fig. 8a). The change in surface tension upon oxidation also occurs over a wider range of concentrations (Fig. 8b) for the dimeric surfactant as compared with I⫹ (the corresponding monomeric surfactant). The maximal change in surface tension (⬃21 mN/m) occurs over almost two decades of concentration of the dimeric surfactant. We believe that the wide range of concentrations over which dimeric ferrocenyl surfactants can drive large changes in surface tension will make this class of surfactant useful for applications in microfluidics. In summary, measurements of the surface tensions of aqueous solutions of ferrocene-based surfactants demonstrate that redox-active surfactants, when combined with use of electrochemical methods, permit large and reversible changes in the surface tensions of aqueous solutions. When the changes in oxidation state of the surfactant occur on time scales of tens of seconds, the surface tensions measured during the change in state of the system can be largely understood in

terms of the equilibrium properties of the system. As described in Section V, this capability provides new ways to design electrochemical systems that can drive liquids into motion on millimeter and smaller scales.

III.

PRINCIPLE 2. REACTION-INDUCED, EXCESS SURFACE CONCENTRATIONS: DISULFIDE-BASED SURFACTANTS

A.

Interfacial States Far from Equilibrium

The second strategy we review for active control of interfacial properties of aqueous solutions of surfactants relies on the creation of interfacial states that are far from equilibrium. This principle involves transformations of the states of surfactants hosted at interfaces on time scales that are fast compared with their rates of relaxation (e.g., via desorption) (Fig. 1b). These ‘‘fast’’ transformations lead to transient, excess surface concentrations of the surfactants that are not in equilibrium with the bulk of the solution. Whereas the rate of accumulation of surfactant at a freshly formed interface is typically dominated by the rate of diffusion of surfactant molecules from the bulk of the solution to the interface, the kinetics of desorption of surfactant from a surfactant-laden interface is often substantially slower than that of adsorption because of the cohesive interactions between aliphatic chains of surfactants hosted at the interface. Past studies have reported that slow desorption kinetics give rise to transient states of surfactant-laden interfaces with properties that differ substantially from equilibrium ones. For example, Lin


161

FIG. 8 (a) Equilibrium surface tensions of aqueous solutions (0.1 M Li2SO4, pH 2, 25⬚C) of DI2⫹ and DI4⫹. (b) Comparison of the change in surface tension upon oxidation of DI2⫹ to DI4⫹ and I⫹ to I2⫹.

et al. [22,23] have reported measurements of the dynamic surface tension of aqueous solutions of a nonionic surfactant (C12E8) following reduction of the surface area of a pendant bubble. A 20% reduction in the surface area resulted in a transient lowering of surface tension of ⬃6 mN/m (Fig. 9). These authors interpreted the time-dependent evolution in surface tension to reflect the slow desorption of surfactant from the surface of the solution. The equilibrium surface tension was recovered in ⬃100 s. Here we describe the generation of nonequilibrium states of an interface through transformations in the states of surfactants rather than changes in the surface area of the system. The properties of these nonequilibrium states can be strikingly different from equilibrium properties of the system. For example, whereas the transformation of state of the surfactant may ultimately lead to an increase in the equilibrium surface tension of a system, the transient state of the interface during the transformation can have a surface tension that is

substantially lower than the initial surface tension of the system. Although the lifetimes of these transient interfacial states are strongly coupled to rates of desorption of surfactants from surfactant-laden interfaces (typically about 0.1–1 s⫺1 for ionic surfactants), we show in the following that it is possible to prolong these nonequilibrium interfacial states by replenishing the concentration of surfactant at the interface by transport to the surface. We report the creation of nonequilibrium states with lifetimes of minutes. B.

Bolaform Disulfide

We illustrate this second principle for active control of interfacial properties through the use of a bolaform surfactant that has a disulfide group in its aliphatic chain (IV) (Fig. 10). We report here the equilibrium and nonequilibrium properties that accompany the reduction of the disulfide group to thiols and the consequent fragmentation of the surfactant into monomeric products

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FIG. 9 Dynamic surface tension (filled circle) of an aqueous solution of C12E8 (7.32 ⫻ 10⫺6 M) upon reduction of the area (open circle) of the surface of the solution. (Data from Ref. 22.)

(V). We believe that this type of transformation is a particularly interesting one because the reduction of disulfide bonds to thiol groups can be accomplished by chemical [24], electrochemical [25], and photochemical [26] methods. Here we focus on the properties of this surfactant system during chemical reduction of the disulfide bond to thiol products by using dithiolthreitol (DTT) [27]. Next, we report the equilibrium interfacial properties of this system and then demonstrate the creation of nonequilibrium interfacial states that are not anticipated by consideration of the equilibrium properties of the system. 1. Equilibrium Surface Tension Equilibrium measurements of the surface tensions (obtained using a pendant drop) of aqueous solutions of IV and V are reported in Fig. 11. Surfactant IV reduces the surface tension of its aqueous solution at concentrations that are substantially lower than the concentra-

FIG. 10 Molecular structures of disulfide- and thiol-based surfactants.

tions at which V (the thiol fragments) reduces the surface tension of its aqueous solution. We measured the equilibrium surface tension of a 1 mM solution of IV as 49 mN/m and estimated (using the Gibbs adsorption equation) the area occupied by each molecule of IV at ˚ 2. In contrast, the the surface of the solution as 130 A equilibrium surface tension of an aqueous solution containing 2 mM of V is not measurably different from that of the aqueous solution of electrolyte that is free of V. The area occupied on average by a molecule of ˚ 2. This result is consistent with V is greater than 500 A past studies of surface tensions of aqueous solutions of bolaform and monomeric surfactants in which the length of the aliphatic chain of the bolaform was twice that of the monomeric surfactant [28]. Unlike measurements of the ferrocene-based surfactants in Fig. 3, the measurements shown in Fig. 11 (and comparisons with other bolaform surfactants) demonstrate that the introduction of the disulfide bond into the aliphatic chains of IV, as well as the presence of the thiol group on V, has a relatively small influence on the equilibrium properties of these surfactant systems. This characteristic of disulfide/thiol groups (‘‘invisibility’’) makes these surfactants especially interesting because structure-properties relationships established for classical surfactants can be readily used in the design of surfactants capable of being placed under active control. 2. Nonequilibrium Surface Tension The equilibrium measurements of surface tension shown in Fig. 11 suggest that processes in which an aqueous solution of IV is slowly reduced to V will be


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FIG. 11 Equilibrium surface tensions of aqueous solutions (50 mM phosphorus buffer) of IV (open circles) and V (filled circles) as a function of concentration as measured by the pendant drop method.

accompanied by an increase in surface tension. This increase in surface tension is largely the result of the partitioning of V away from the interface and into the bulk solution. Indeed, our experimental measurements do show that a slow reduction of IV to V is accompanied by a monotonic increase in surface tension (as described by principle 1 earlier). However, when the rate of reduction of IV to V is increased by addition of ⬃2 mM of reducing agent (DTT), we measure the sur-

face tension during the reduction of IV to V and find that it assumes values that are far from any equilibrium ones measured in the system (Fig. 12). Indeed, the first 10 min of the transformation are accompanied by a decrease in surface tension by up to ⬃10 mN/m. A number of experimental observations demonstrate that the minimum in surface tension observed in Fig. 12 can be understood in terms of a nonequilibrium, excess surface concentration of surfactant (IV and V)

FIG. 12 Dynamic surface tensions measured during the reduction of a 1 mM solution of IV to a 2 mM solution of V (filled circles). The measurements were performed by the maximum bubble pressure method (bubble rate 3–10 bubbles/s) and 50 mM phosphate buffer at pH 7. Upon the addition of acid (and lowering of pH from 7 to 4) the reaction is quenched (open circles); readjustment of the pH to 7 results in resumption of the reaction.

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that is generated through the reduction of IV to V by DTT at the surface of the solution. In particular, attempts to describe the presence of the minimum in terms of equilibrium properties of the system were unsuccessful. For example, we measured the equilibrium surface tensions of solutions containing mixtures of IV and V to determine whether the low surface tensions shown in Fig. 12 resulted from synergism [29]. The equilibrium surface tensions of the mixed surfactant systems were found to increase monotonically with composition of the system (Fig. 13), indicating that the minimum in Fig. 12 is not a result of synergism between IV and V. Further support for the reaction-dependent minimum is found through the influence of pH on the presence of the minimum. For example, upon addition of acid, the reaction leading to the reduction of IV to V is quenched and a rapid increase in surface tension is observed. When the system is returned to neutral pH, the reduction of IV to V resumes and the low surface tension is recovered. In addition, low surface tensions can be produced using a different reducing agent such as sodium sulfite. These experimental observations lead us to conclude that the low surface tensions measured during the reduction of IV to V are the result of an excess surface concentration of surfactant that is formed by the reduction of IV to V at the surface of the solution. Support for this proposition has been derived from a simple diffusion-kinetic model that we have developed to describe the interfacial states (excess surface concentration and surface pressure) created by the transformation of IV to V. This model, which is described in detail elsewhere [30], combines a diffusion-kinetic model (to

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describe the adsorption, desorption, and transport of surfactant to and from the interface) and a surface equation of state to correlate the changes in excess surface concentration with changes in surface tension. The diffusion-kinetic model differs from past work [31–35] in that it accounts for the reaction leading to the conversion of IV to V within the Gibbs monolayer and bulk solution. We used the model to investigate the effect of the reaction on the surface excess concentration of IV and V. The predicted reduction of IV to V based on physically reasonable reaction rate constants, when combined with estimates of the rates of desorption of IV and V from the surface of the solution, was shown to lead to interfacial compositions (rich in V and lean in IV) with surface tensions that were smaller (by ⬃1–10 mN/m) than equilibrium ones corresponding to the same bulk composition of the solution. The model demonstrates that when the rate of formation of V is comparable to the rate of desorption of V from the surfactant-laden interface, an excess concentration of V builds up and thereby lowers the surface tension of the solution. Control of the rate of transformation of IV to V does, therefore, provide a means by which to exercise active control over the interfacial state of the system. In summary, the results described here demonstrate that it is relatively straightforward to design a surfactant system such that nonequilibrium states of the interface can be accessed by transforming the surfactant between states. We believe these transient states may find use, for example, in processes that require control of interfacial states for short lengths of time (e.g., during emulsification).

FIG. 13 Surface tensions of premixed solutions of IV and V (no reaction) as measured by the maximum bubble pressure method. The compositions of the mixtures correspond to compositions sampled during the reaction shown in Fig. 12.


IV.

PRINCIPLE 3. DIFFUSION-LIMITED SURFACE EXCESS: AZOBENZENEBASED SURFACTANTS

A.

Effects of Aggregation on Surface Tension

The third principle we describe for active control of the interfacial properties of aqueous solutions of surfactant achieves control of dynamic surface tensions via manipulation of the state of aggregation of surfactant in bulk solution (Fig. 1C). Changes in the state of aggregation of surfactant in bulk solution can potentially give rise to changes in the dynamic surface tension of the solution through one of several mechanisms. For example, when dealing with diffusion-limited adsorption of surfactant to an interface, the characteristic time for surfactant molecules to diffuse to a freshly formed interface and form an interfacial assembly, tD, is given by tD ⬃ ⌫ 2/C 2D [36], where ⌫ is the excess surface concentration of surfactant at equilibrium, C is the bulk concentration of surfactant, and D is the effective diffusion coefficient of surfactant in bulk solution. For aqueous solutions of ionic surfactants (e.g., a 10 mM solution of sodium dodecyl sulfate), the monomer activity is high (approximately equal to the cmc or 8 mM) and thus changes in the state of aggregation of surfactant will have relatively little effect on the effective diffusion coefficient (because transport of the surfactant will be dominated by the diffusion of monomer in solution). When dealing with mixed surfactant systems of anionic and cationic surfactant, however, the situation can be very different. First, the activity of the monomer

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in these solutions can be very low by virtue of the electrostatic interaction between surfactant molecules of opposite charge [37–41]. For example, Villeneuve et al. [39] have measured parts of the phase diagram of mixtures of sodium decyl sulfate and decyltrimethylammonium bromide. Whereas the cmc of decyltrimethylammonium bromide was ⬃100 mM, upon addition of sodium decylsulfate, the monomer concentration decreased by almost two orders of magnitude (Fig. 14). Under circumstances in which the activity of the surfactant is lowered to submillimolar concentrations, the diffusion of surfactant in solution is likely to be dominated by the transport of aggregates of surfactant and not monomeric species. Second, the size of the aggregates in these systems can be very large and thus they diffuse slowly [40,41]. At concentrations of mixed surfactants that are well below the cmc of the single-surfactant systems, these mixed solutions consist largely of vesicles in equilibrium with low concentrations of monomer [39]. By using the Stokes-Einstein relationship, the diffusion coefficient for aggregates with hydrodynamic diameters of ⬃150 nm (e.g., vesicles) is estimated to be ⬃10⫺8 cm2/s. For systems of these types in which the extent of aggregation of surfactant can be manipulated (see later), a process of disassembly of large aggregates into monomers can plausibly increase the effective diffusion coefficient of surfactant in the system by roughly two orders of magnitude (from 10⫺8 to 10⫺6 cm2/s). This change in diffusion coefficient can lead to similar changes in the time required for the surfactant to lower the surface tension of a freshly created interface [36].

FIG. 14 Phase diagram for mixtures of decyl trimethylammonium bromide and sodium decylsulfate: (a) monomer, (b) monomer ⫹ vesicle, (c) monomer ⫹ vesicle ⫹ micelle, (d) monomer ⫹ micelle. X-axis is fraction of anionic surfactant in mixture. Y-axis is total surfactant concentration. (Data from Ref. 39.)

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We also note a second mechanism by which changes in the extent of aggregation of a surfactant can influence the dynamic surface tension of a system. This mechanism is through changes in the lifetimes of aggregates of surfactants. For example, the lifetimes of foams have been correlated with the lifetimes of aggregates within solution [42]. The lifetimes of micelles in sodium dodecyl sulfate (SDS) solutions vary from milliseconds (near the cmc) to ⬃1 s at SDS concentrations well above the cmc (⬃150 mM). Several past studies have suggested that the lifetimes of micelles in solutions containing high concentrations of surfactant do influence dynamic surface tensions of these solutions [43–45]. B.

Photoresponsive Surfactant

We illustrate this third approach to active control of interfacial properties by using a water-soluble surfactant that hosts the azobenzene moiety [46]. Azobenzene is a widely used photoactive group that can assume one of two isomeric states (cis or trans) depending on the wavelength of light used to illuminate the compound. The trans isomer absorbs ultraviolet (UV) light with a wavelength of 360 nm and is transformed upon illumination to the cis isomer. The cis isomer absorbs light with a wavelength of 460 nm, and illumination of the cis state with visible light causes the cis isomer to relax back to the trans isomer. Although a number of past studies have reported water-soluble and water-insoluble amphiphiles containing azobenzene [47–49], past studies based on water-soluble surfactants have been largely unsuccessful in driving substantial changes in surface tension upon illumination with light.

FIG. 15

C.

Catanionic System

Our approach is based on a mixed surfactant system containing a cationic, bolaform surfactant (VI) that hosts azobenzene (Fig. 15) and the anionic surfactant SDS. We designed and synthesized VI rather than a monomeric azobenzene surfactant because the conformations of bolaform surfactants within aggregates are constrained as compared with surfactants with a single polar headgroup. We hypothesized that the presence of constraints on the packing of bolaform surfactants would lead to larger changes in aggregation as compared with single-headed surfactants upon photoisomerization. In addition to the cationic bolaform surfactant, the system contained SDS, an anionic surfactant, so as to cause the monomer activity to be low. The influence of the attraction between cationic and anionic surfactants in solution (which leads to low monomer activity) is apparent in the small interfacial areas occupied by surfactants in aggregates of these mixtures of surfactants. For example, surfactant molecules hosted within vesicles formed from mixtures of cetyltrimethylammonium bromide and sodium octyl˚ 2/molecule [40]. sulfate occupy areas as small as 36 A It is also plausible that the close packing of surfactant molecules will increase the impact of isomerization on the aggregation behavior through constraints imposed on the packing of the surfactant chains within the aggregates. Dynamic and static light scattering measurements reveal that photoisomerization of aqueous solutions of 0.1 mM BTHA and 1.6 mM SDS leads to large and reversible changes in the extent of aggregation of surfactant in the system. Before illumination, the hydro-

Photoisomers of azobenzene-based surfactant.


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dynamic diameters of aggregates were measured as 150 nm ⫾ 10 nm and the intensity of scattered light was 2500 kcnts/s. After 3 min of illumination with UV light, the measured hydrodynamic diameters were similar to that measured prior to illumination (140 nm ⫾ 10 nm). However, the intensity of scattered light was lowered by almost a factor of 2 (1480 kcnts/s) after illumination with UV light. Because the intensity of light scattered from aggregates of similar size is proportional to the number density of aggregates in solution, these measurements indicate that illumination of the mixed surfactant system with UV light decreases the number density of aggregates in solution by a factor of 2. The dissolution of the aggregates will lead to a large change in the monomer (or small aggregate) concentration. Measurements of the surface tension of the mixed VI and SDS surfactant system obtained using the du Nouy ring also reveal that isomerization is accompanied by large changes in the surface tension of the solution. The du Nouy ring method (Fig. 16a), which characterizes the surface of the solution with an age of ⬃10 s, shows that the dynamic surface tensions of the illuminated and nonilluminated solutions are quite different. The illuminated solution has a dynamic surface tension that is lower than that of the solution prior to illumination over a wide range of concentrations of VI. As shown in the following, these large, light-induced changes in surface tension can be exploited by control (by illumination) the release of liquids from capillaries. D.

Mass Transport

Several experimental observations support our view that changes in dynamic surface tension caused by illumination of mixed solutions of VI and SDS are largely controlled by the rate of delivery of surfactant onto the surface of the solution. First, by using a Wilhelmy plate (Fig. 16b), we have demonstrated that illumination of this surfactant system leads to relatively small changes in the equilibrium surface tension of the solution. That is, the difference in surface tension that is seen when the age of the surface of the solution is ⬃10 s largely vanishes when the system is provided sufficient time to deliver surfactant onto the surface of the solution. Second, we have measured the surface tensions of this system when the age of the surface of the solution is small compared with 10 s (by using the maximum bubble pressure method, Fig. 16c). Here, too, we observe that the influence of illumination on the dynamic surface tension of the system is small. In this case, however, the surface tension of the system is

FIG. 16 Surface tensions of mixed solutions of VI and SDS measured before (filled circle) and after (open circle) illumination with UV light. (a) du Nouy ring method; (b) Wilhelmy plate method; (c) maximum bubble pressure method. All measurements were performed using aqueous solutions of 1.6 mM SDS and at 25⬚C.

similar before and after illumination because the interface is starved of the mixture of surfactant. Figure 17 compares values of surface tension measured before and after illumination by UV light for solutions of 0.1 mM VI and SDS as measured with the maximum bubble pressure, du Nouy ring, and Wilhelmy plate methods. Although our experimental investigation does not permit identification of one of the several possible mechanisms (see earlier) by which the change in state of aggregation of the surfactant in solution can change

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control dynamic surface tension by using light is used to demonstrate the controlled release of pendant drops from tips of capillaries. V.

ACTIVE CONTROL OF LIQUIDS ON MILLIMETER AND SMALLER SCALES

The final section of this chapter illustrates the manner in which the principles discussed earlier for active control of the interfacial properties of liquids can be exploited to form the basis of new ways to drive liquids into motion, release liquids from capillaries, and position liquids on surfaces in periodic arrays. A.

FIG. 17 Surface tensions of aqueous solutions containing VI (0.1 mM) and SDS (1.6 mM) before and after illumination with UV light.

the rate of delivery of surfactant to the interface, and thus the surface tension measured by the du Nouy ring, we point out that the time scales on which we observe the light to induce changes in surface tension are consistent with the influence of mass transport. As noted earlier, past studies have established that diffusion coefficients of aggregates of surfactants with hydrodynamic diameters of ⬃150 nm (e.g., vesicles) are ⬃10⫺8 cm2 s⫺1 whereas diffusion coefficients of monomeric surfactants are ⬃10⫺6 cm2 s⫺1. A change in the effective diffusion coefficient from 10⫺8 to 10⫺6 cm2/s will lead to changes in tD by up to two orders of magnitude. For ˚ 2/ example, using values of C = 0.3 mM, 1/⌫ = 50 A ⫺8 2 ⫺1 molecule, and D = 10 cm s , the characterisic diffusion time is ⬃100 s. That is, when transport of surfactant to the interface is controlled by the diffusion of aggregates, it takes ⬃100 s to transport a sufficient amount of surfactant to the interface to form a monolayer and thereby lower the surface tension. In contrast, if the transport of surfactant to the interface is dominated by diffusion of monomers (D = 10⫺6 cm2 s⫺1), the characteristic diffusion time decreases to ⬃1 s. The change in characteristic diffusion times described earlier compares well with the dynamic surface tension behavior of the VI and SDS system before and after illumination (Figs. 16 and 17) and suggests that the dynamic surface tension of the mixed surfactant systems may well be controlled through the regulation of mass transport. In the next section, the capability to

Electrochemical Control of Marangoni Effects

Electrochemical control of the oxidation state of the ferrocenyl surfactant II⫹ can lead to large and reversible changes in the surface tension of its aqueous solutions. When dealing with solutions containing concentrations of II⫹ of 0.1 mM, oxidation of II⫹ to II2⫹ leads to a large increase in surface tension (Figs. 4 and 5). Here we illustrate that a simple arrangement of electrodes can be used to dispense or consume II⫹ at localized regions of an aqueous system, thus creating gradients in the surface excess concentration of ferrocenyl surfactant between the electrodes. The resulting gradients in surface tension cause surface flows (Marangoni phenomena) directed away from the cathode and toward the anode. Figure 18 shows Marangoni flows created by reduction of II2⫹ to II⫹ in a system with two working electrodes. Sulfur dust sprinkled on the surface is used to visualize the flow. Application of a reducing potential (⫺0.3 V vs. SCE) at the upper electrode and an oxidizing potential (0.3 V vs. SCE) at the lower electrode (Fig. 18b) causes the surface fluid to flow away from the cathode (Fig. 18c) and toward the anode. Reversal of the oxidizing and reducing potentials causes the surface to flow in the opposite direction (Fig. 18d). We have also used electrochemical control of the surface activity of ferrocenyl surfactants to direct the flow of liquid through networks of channels. Figure 19 shows a top view of a network of four intersecting channels. Three of the four channels end at Pt electrodes, and the channel at the top ends at a reference electrode and a counterelectrode. The fluidic network was filled with 0.3 mM II2⫹ to a depth of ⬃1 mm. Small drops of a nematic liquid crystal (LC), 4-n-pentyl-4⬘-cyanobiphenyl, were placed on the surface of the aqueous solution within the channels so that the fluid


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flow could be visualized easily through crossed polarizers. Application of oxidizing (0.3 V vs. SCE) and reducing (⫺0.3 V vs. SCE) potentials to any pair of electrodes caused the LC droplets to be pumped between the two electrodes. In addition, the velocity of the droplets was controlled by the magnitude of the potential applied to the electrodes (Fig. 19d). The oxidation and reduction of II⫹ were also used to demonstrate pumping of LC droplets across an unconfined surface (Fig. 19e). Whereas application of ⫺0.3 V (vs. SCE) to either the top or left electrodes produced vertical or horizontal motion of the LC droplets across the image shown in Fig. 19e, respectively, simultaneous application of ⫺0.3 V (vs. SCE) to the top and left electrodes produced a motion of the droplets in a direction given by the addition of the vectors of the single-electrode flows. B.

FIG. 18 Top view of petri disk filled with 0.1 mM II⫹ (0.1 M Li2SO4, pH 2). Sulfur dust is sprinkled on top of the solution to visualize the displacement of fluid. (a) Electrode setup with two working electrodes, a counterelectrode, and a reference electrode. (b) Application of ⫺0.3 V to the top working electrode and 0.3 V to the bottom electrode causes displacement of the surface (c). Reversal of working electrode potentials causes fluid displacement in the opposite direction (d).

Addressable, Patterned Dewetting

Because localized changes in the interfacial tension of aqueous solutions (solid-liquid and liquid-vapor interfaces) can give rise to localized imbalances of force at the three-phase contact line of liquid supported on a surface and thereby place a liquid in motion, we have used ferrocenyl surfactants in strategies that permit the patterned wetting and dewetting of aqueous solutions on surfaces. We illustrate this capability here by using ferrocenyl surfactant to direct a thin film of liquid to dewet into a two-dimensional array of droplets supported on a surface (Fig. 20). The experiments are based on glass microscope slides that were patterned ˚ of titanium and 500 A ˚ of gold by evaporating 50 A through a micromachined aluminum mask. The patterned surface was made energetically homogeneous by immersing into a solution of 0.9 mM 11-mercaptoundecanoic acid and 0.1 mM hexadecyl mercaptan. The patterned electrode surface was inclined at ⬃20⬚ from the horizontal with the lower edge touching a shallow pool of aqueous solution (0.01 M Li2SO4, pH 1.3) containing 0.3 mM II⫹, an SCE, and a Pt counterelectrode. Surfactant solution pipetted onto the slide formed a continuous film (20 to 50 ␮m in thickness). When no external potential was applied to the electrodes, the film of liquid supported on the surface drained uniformly from the surface (that is, no fluid pattern was formed). However, when an oxidizing potential (0.5 V vs. SCE) was applied to the array of electrods, the aqueous solution dewet the gold electrodes while the glass surfaces remained covered by liquid (Fig. 20). Through this process, a continuous film of liquid was transformed into a periodic array of droplets.

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FIG. 19 Time lapse images of pumping of liquid crystal (LC) droplets across the surface of an aqueous solution of 0.3 mM II2⫹ (0.01 M Li2SO4) confined to four channels. Platinum electrodes protrude through the surface of the solution at the ends of the left, right, and lower channels. The end of the top channel contains an SCE and a counterelectrode. (a) Droplet of LC is dispensed at the bottom channel. The LC droplet is pumped by application of ⫺0.3 V to the bottom electrode and 0.3 V to the right electrode. (b) Droplet of LC is pumped to the left electrode by application of ⫺0.3 V to the right electrode and 0.3 V to the left electrode. (c) Droplet of LC dispensed at the bottom is pumped by application of ⫺0.3 V to the bottom electrode and 0.3 V to the left electrode. (d) The velocity of the LC on the surface measured as a function of the potential used to pump fluid in a straight 4-mm-wide channel. The x-axis is the magnitude of the potential applied to the cathode and anode. (e) Sulfur particles supported on an unconfined surface pumped in the direction indicated by the arrow by application of ⫺0.3 V to two electrodes at top and at left. All potentials are versus SCE.

Whereas gradients in surface tension caused by changes in the oxidation state of II⫹ drive the phenomena shown in Figs. 18 and 19, the patterned dewetting of solutions of II⫹ is driven by electrochemically induced changes in the contact angle of the solution on the surface. At equilibrium, no net force acts on the three-phase contact line of a liquid supported on a surface. An electrochemically induced increase in the local values of the interfacial free energies can, however, change the equilibrium contact angle from ␪i to ␪f and thus create a net force of magnitude ␥LV (cos ␪i ⫺ cos ␪f) that leads to motion of the contact line. Figure 21a shows that static contact angles (measured to be constant for times greater than 10 to 20 s) of aqueous solutions of 0.3 mM II⫹/II2⫹ placed on the surface of treated gold do increase with oxidation of II⫹. A variety of experimental measurements (described elsewhere) demonstrate that II2⫹ does not measurably affect contact angles of these solutions. The increase in receding

contact angle (0.3 mM II⫹/II2⫹) from 1 M, much greater than counterion concentration in the surrounding aqueous pseudophase, which is usually in the range 0.001–0.01 M [1,11,12]. There are two models describing the ionic distribution at charged aqueous interfaces. In the pseudophase ion exchange (PIE) model, micellar surfaces are treated as selective ion exchangers saturated with counterions; using the Poisson-Boltzmann equation (PBE) modified for specific ion interactions, ion distributions are computed within a reaction region at the micelle surface [89] (see also Section III). Distribution of counterions is usually characterized by the micellar degree of ionization, ␣, and for most ionic micelles ␣ is in the range 0.1–0.3 and is seen to depend little on the overall concentration of counterions; in other words, the surface of an ionic micelle is treated as if it is saturated with counterions [11]. The remaining counterions are distributed in the diffuse Gouy-Chapman layer, and their distribution is governed by their nonspecific electrostatic interactions with the micelle, which can be regarded as a bulky macroion [12]. Values of ␣ are determined for many ions, including different values for the same ion, by a variety of methods [31]. A new method is based on chemical trapping of ‘‘free’’ counterions in the aqueous pseudophase, based on the dediazoniation reaction developed by Romsted et al. [68,90]. Extensive kinetic data have been fitted by the PIE model with data on the ion-exchange parameters for pairs of ions [89], including estimates for Cl⫺ and Br⫺ and estimates based on the method of ion flotation of Warr et al. [91–93].

Reactivity Control by Self-Assembling Systems

Counterions are bound primarily by the strong electrical field created by the headgroup, but also by specific interactions that are dependent on headgroup and counterion type [9,89,94]. The nature of the counterion has an important bearing on ␣ for cationic surfactants: ions that have a lower hydration enthalpy, higher affinity for Dowex 2 (a tetralkylammonium ion resin), and a higher lyotropic number are more strongly bound to cationic micelles and highly effective in charge neutralization of the micellar headgroups. Generally speaking, we can say that micelles bind counterions selectively, and several properties such as size, shape, phase stability, binding of ions and neutral molecules, and their effects on the rates and equilibria of chemical reactions are sensitive to counterion concentration and type. Some lyotropic series or affinity orders have been established for the relative affinities of both anions and cations to micelles [31,94]. When salts are added to micellar solutions, the counterions of the salts compete for the ionic headgroup of micelles with the surfactant counterions that already exist in solution. Thus, displacement can occur, depending on the relative affinities of counterions for the headgroups. Interesting kinetic effects can arise. If the added salt is reactive, micellar rate enhancements are observed after displacement. If added ion is inert and the reactive ion is the surfactant counterion, the addition can cause inhibition. Kinetic salt effects are peculiar in micellar systems [31]. Ion selectivity has been treated thermodynamically, and it was concluded that partial ionic dehydration at the micellar interface is of crucial importance [95]. Evidence indicates that strongly hydrated ions, such as OH⫺ and F⫺ are readily displaced from cationic micelles by relatively weakly hydrated anions such as Br⫺ and Cl⫺ [89]. Results of a chemical trapping method are consistent with partial dehydration of counterions of CTABr and CTACl micelles at the sphere-to-rod transition [96]. Morini et al. [97] used ion-selective electrodes to demonstrate that in mixtures of DTABr and DTAOH, the breakpoints used to estimate the cmc differ for Br⫺, OH⫺, and the amphiphile cation; that the degree of ionization decreases continuously up to about 0.2 M amphiphile; and that the exchange constant for OH⫺ and Br⫺ depends on solution composition, consistent with theoretical models [98]. As for organic neutral substrates and also for organic anions, the structure of both the surfactant and the ion can affect location at the interface. Binding of salicylate and o-, m-, and p-nitrobenzoate anions to MTABr micelles has been examined by 1H NMR spectroscopy

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[99]. Competition is treated by the PIE model, although these polarizable anions may perturb the micellar structure. With organic counterions there is often micellar growth, which is sensitive to counterion type. Two-dimensional NMR spectroscopy, capable of revealing spatial relationships among proximal protons (NOESY, ROESY), can be very useful, giving insight into structural details of micelle-solute interactions. Results with both 1D and 2D NMR show that the 3,5-dichlorobenzoate ion intercalates further into cationic rodlike micelles than does the 2,6-iosmeric ion into spherical micelles [100]. Other 1H NMR data show that micellar growth in alkylpyridinium micelles to form entangled wormlike micelles depends on counterion structure; it was observed for o-hydroxybenzoate but not for the phydroxy isomer and was observed for p-chlorobenzoate but not for benzenesulfonates [101]. Growth induced by added organic anions is probably not due to charge reversal of the micelle surface, because the surface potential, estimated by using an indicator, approaches zero with added salicylate ion but does not change sign [102], consistent with Poisson-Boltzmann equation (PBE) treatments [77,89]. For the aromatic anion 2naphthoate in cationic micelles, 1H chemical shifts and NOESY spectra led to the conclusions that the aromatic section of the molecule is embedded in the palisade layer whereas the charged parts are located near the micellar interface, so they can still be solvated by water [103]. In spite of the neutral nature of zwitterionic surfactants and their well-documented insensitivity to ionic strength, electrolytes do bind to zwitterionic micelles. Binding of various ions to micelles was suggested in several papers [104–108], and it was unambiguously established from radioactive tracer, self-diffusion, and fluorescence quenching data [109,110]. Micellar aggregates of zwitterionic carboxybetaine, sulfobetaine, or phosphobetaine surfactant can be represented as a hydrophobic sphere surrounded by a spherical shell where positive charges are distributed on the inner layer and negative charges on the outer layer. In this purely electrostatic model, a positive electrostatic potential exists inside the shell as a function of the distance from the center of the sphere. The number of positive and negative charges is the same, but the surface where the positive charges lie is less extended. Positive charge density is consequently greater [110,111]. This model explains the strongest anion binding to zwitterionic micelles but does not explain the strongest binding of the softer anions [112]. Another failure of the model is the dependence of the electrostatic potential on the thickness of the double-charged shell, corresponding to the

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intercharge distance of the micellized monomers. The polymethylene arm is indeed flexible, and intercharge distance increases monotonically but not linearly with increasing number of methylenes [113–115]. Intercharge arms fold and loop inside the hydrophobic micellar core because of both electrostatic attraction between the two oppositely charged groups and hydrophobic interactions of the tether with the micellar interior. The surface areas of the monomers become larger as the intercharge arms become longer and as micelles become smaller [115–117]. As shown by selfdiffusion and elastic and quasi-elastic light scattering studies, micellar dimensions increase on anion incorporation due to reduced electrostatic interactions between the two opposite charges and unfolding of the headgroup [117].

III. A.

QUANTITATIVE TREATMENTS OF MICELLAR RATE EFFECTS

SCHEME 2

order rate constants. The binding constant, KS, is written in terms of the molarity of micellized surfactant, but it could equally be written in terms of the molarity of micelles. The concentration of micellized surfactant is that of total surfactant less that of monomer, which is assumed to be given by the critical micelle concentration (cmc). The overall first-order rate constant kobs is then given by Eq. (2). k obs =

k⬘W ⫹ k⬘MKS([D] ⫺ cmc) 1 ⫹ KS([D] ⫺ cmc)

(2)

Pseudophase Model

Most kinetic treatments are based on the so-called pseudophase model. This model has been generally accepted on the reasonable assumption that for most activated thermal chemical reactions, transfer of material between water and micelle is so fast that reaction does not perturb the equilibrium distribution of reactants between the pseudophases. This generalization cannot be applied to photochemical reactions, where some steps of the reaction may be very rapid and therefore faster than solute transfer [9,118]. Provided that equilibrium is maintained between the aqueous and the micellar pseudophases, the overall reaction rate will be the sum of rates in water and in the micelles and will therefore depend on the distribution of reactants between each pseudophase and the appropriate rate constants in the two pseudophases. Menger and Portnoy [119] developed a quantitative treatment that adequately described inhibition of ester saponification by anionic micelles. Micelles bound hydrophobic esters, and anionic micelles excluded hydroxide ions and so inhibited the reaction, whereas cationic micelles speeded saponification by attracting hydroxide ions [120]. Provided that only substrate distribution has to be considered, which is the situation for micelle-inhibited bimolecular or spontaneous unimolecular reactions, Scheme 2 shows the substrate distribution and reaction in each pseudophase [121]. In Scheme 2 Dn denotes micellized surfactant, S is substrate, subscripts W and M denote aqueous and micellar pseudophases respectively, and k⬘W and k⬘M are first-

On the basis of Eq. (2), in the absence of micellized surfactant k obs = k⬘W([Dn] = 0), and when the substrate is fully micelle bound (KS[Dn] >> 1 and k⬘MKS[Dn] >> k⬘W) we have k obs = k⬘M. This equation is formally similar to the MichaelisMenten equation of enzyme kinetics, although the analogy is limited because most enzymatic reactions are studied with substrate in large excess over enzyme. Equation (2) could be rearranged to give Eq. (3), which is formally similar to the Lineweaver-Burk equation and which permits calculation of k⬘M and KS provided that k⬘W is known [119,120]. 1 1 1 = ⫹ kobs ⫺ k⬘W k⬘M ⫺ k⬘W (k⬘M ⫺ k⬘W)KS[Dn]

(3)

Variations of Eq. (2) have been developed to fit rate[surfactant] profiles for spontaneous reactions that occur after a rapid preequilibrium. For instance, decomposition of aryl-2,2,2-trichloroethanols follows an (Elcb)R type of mechanism, i.e., rapid reversible deprotonation of the alcohol by OH⫺ followed by ratedetermining loss of trichloro carbanion to give benzaldehyde product [122]. Micelle-bound substrates are completely deprotonated (because of the increased [OH⫺] at the micellar surface relative to bulk water) so that kobs depends primarily on the distribution of the alkoxide ions between aqueous and micellar pseudophases and kobs-[surfactant] profiles are fitted by Eq. (4), which is the form typically used for spontaneous reactions in micellar solutions (after correction for the


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extent of deprotonation of the trichloroethanols in the aqueous phase). kobs =

K[OH⫺ W](k⬘ MKS[Dn] ⫹ k⬘ W) ⫺ 1 ⫹ K[OHW](1 ⫹ KS[Dn])

(4)

In Eq. (4) KS is the binding constant of an alkoxide ion to the micelle and K corresponds to the preequilibrium constant in water: ⫺ K = [RO⫺ W]/[ROHW ][OH ]

total solution volume, which is approximately that of the aqueous pseudophase. k⬘W = kW [Y⫺ W] k⬘M = kMm YS = kM

[Y ] [Dn]

(7)

By combining Eqs. (2), (6), and (7), Eq. (8) is obtained for the observed pseudo-first-order kinetic constant,

(5)

Equations (2) and (3) depend on some major assumptions, in particular that the cmc gives the concentration of monomeric surfactant, that rate and binding constants in the micellar pseudophase are unaffected by reactants and products, and that reagents do not react across the micelle-water interface. These equations have been used very extensively and have provided the basis for quantitative analysis of micellar rate effects. Much of this work has been reviewed in comprehensive monographs [8,12]. Equations (2) and (3) generally fail for bimolecular, micelle-assisted reactions. Equation (2) predicts that the first-order rate constants should reach a constant, limiting value at high surfactant concentration when the substrate is fully micelle bound, but rate maxima are observed for the corresponding nonsolvolytic bimolecular reactions when surfactant counterions are inert. The rate-surfactant concentration profiles can be treated quantitatively by taking into account the distribution of both reactants between water and micelles. This can be done by extending Eq. (2), and a simple formalism involves writing the first-order rate constants in terms of second-order rate constants in water and micelles and reactant concentrations in each pseudophase [10,123– 126]. However, one immediately runs into the problem of defining concentration in the micellar pseudophase. One approach is to write concentration in terms of moles of reagent per liter of micelles or to assume some volume of the micellar pseudophase VM in which reaction takes place. Another approach is to define concentration in the micellar pseudophase in terms of a mole ratio. Concentration is then defined unambiguously, and the equations take a simple form [11,126]. However, this approach does not allow direct comparison of second-order rate constants in aqueous and micellar pseudophases, and by evading one problem one faces another. The first-order rate constants are written in Eqs. (6) and (7) as second-order rate constants, kW and kM, for reaction of a reactive anion, Y⫺, where the mole ratio ⫺ ]/([D] ⫺ cmc). Here and elsewhere, quanis mYS = [YM tities in square brackets denote molarity in terms of

(6) ⫺ M

kobs =

⫺ kW [Y⫺ W] ⫹ kMKS[YM] 1 ⫹ KS[Dn]

(8)

where the dimensions of kW are M⫺1 s⫺1 and those of kM are s⫺1. This equation readily explains why firstorder rate constants of micelle-assisted bimolecular reactions typically go through maxima with increasing surfactant concentration if the overall reactant concentration is kept constant and if surfactant counterion is inert. Addition of surfactant leads to binding of both reactants to micelles, and this increased concentration increases the reaction rate. Eventually, however, increase in surfactant concentration dilutes the reactants in the micellar pseudophase and the rate falls. This behavior supports the original assumption that substrate in one micelle does not react with reactant in another and that equilibrium is maintained between aqueous and micellar pseudophases. Equation (8) and others that are essentially identical but are written in different ways can be applied to bimolecular micelle-assisted reactions provided that the distribution of both reactants can be determined. In some cases, the problem is relatively simple. Ion binding can be estimated by conductivity. For example, Eq. (8) was applied to fit rate-[surfactant] profiles with the concentration of ions determined by conductivity for mixed systems, such as mixtures of CTABr and nonionic surfactant C10E4 [127]. Estimation of the extent of micellar binding is not a problem if the organic ion is very hydrophobic, because then it is completely micelle bound under essentially all conditions [123]. The problem is more difficult for bimolecular reactions of hydrophilic ions. The conductivity method is not useful for estimating ␤ for CTAOH, because it seems that ␤ increases with increasing surfactant concentration [128] and then ␤ has to be calculated. A variety of theoretical treatments have been developed to estimate the ionic distribution between water and micelles [12,77] and some of them will be illustrated in this section. The problem of quantifying the transfer equilibrium of a nucleophile between water and micelles is simplified by using functional amphiphiles in which the head-

184

group is the nucleophile. The mole fraction of nucleophile to micellized surfactant is therefore 1. In comicelles, allowance is made for dilution of functional headgroups by inert surfactants. This treatment has been applied to several reactions involving hydroxamate or oximate-functionalized surfactants [129,130] and reactions catalyzed by metallomicelles [131]. In this chapter we will not deal with functional micelles and comicelles. Anyway, it is worth mentioning that due to an additional catalyzing action, rate enhancements by functional micelles are considerably larger than those by nonfunctional micelles of comparable structure, and bifunctional micelles are better catalysts than monofunctional micelles [132–168]. The most widely reported functional groups are hydroxyl [166– 168], imidazole [137,140,169,170], thiol [135,136, 163], and some — OH-bearing groups such as hydroxyalkyl [139,141,150–156,159–161,164,166,168,171], hydroximino alkyl [138,162,168], hydroxylamine [165], and hydroxamic acid [138]. Outstanding examples of functionalized micelles are the so-called metallomicelles, and they bind substrates with enzymelike efficiency. They are made of either transition metal complexes of surfactants containing imidazole or pyridine moieties or comicelles of ligand complexes with surfactants, and they are utilized in the hydrolysis of carboxylic and phosphoric esters and amides [145,172–180]. Aggregates of amphiphilic metal complexes (metallomicelles) [146,178–184] or metallovesicles [185,186] are attracting considerable attention as hydrolytic catalysts, potentially more powerful than their hydrophilic, monomeric, siblings. The impressive rate increases are a matter of fact, but their source is a much more delicate subject. Breslow and coworkers in 1986 [187] and later Kimura et al. [188] reported impressive increases in overall second-order rate constants in comicellar aggregates. Scrimin and coworkers [131], however, showed that reactivity of various metallomicelles toward phosphate triesters is accounted for by considering the concentrations of reactants in the reaction loci, i.e., in the micellar pseudophase. There was nothing unexpected in reactivities of these metallomicelles relative to those of the monomeric analogue complexes in water. The conclusion is that in hydrolyses catalyzed nucleophilically, reactivities of micellized metal complexes do not differ significantly from those of analogous, monomeric catalysts in water. This is in spite of the enhanced electrophilicity of the metal ion in micellized complexes indicated for Cu2⫹ from electrochemical evidence [146,189] and does not significantly depend on the particular structure and intrinsic reactivity of the

Savelli et al.

substrate [190]. Therefore, the special micellar effects that are postulated to provide impressive accelerations of reactions are a chimera that disappears when transfer equilibria between the aqueous and the micellar pseudophases are taken into account [191]. 1. Ion-Exchange Model A first advance in the treatment of bimolecular reactions was made by Romsted [10,11]. The pseudophase ion-exchange (PIE) model of bimolecular ionic reactions was developed by Romsted to explain the rate maxima with increasing surfactant concentration, and inhibition by inert counterion competition between ions, e.g., Y⫺ and X⫺, is written in terms of Eq. (9), which is similar to that used with ion-exchange resins. K YX =

⫺ [Y⫺ W][XM ] ⫺ ⫺ [YM ][XW ]

(9)

The micelle is assumed to be saturated with counterions, regardless of their nature or concentration; i.e., ⫺ ␤ is constant. The value of [YM ] can the be calculated from a mass balance equation in terms of K YX and ␤. First-order rate constants are written as Eqs. (6) and (7); this last equation can be written in terms of a rate constant km2 with concentration as molarity at the micellar surface, as in Eq. (10), where VM is the molar volume of the reactive region in the micellar pseudophase. This volume is probably approximately half that of the whole micelle [11], although it may depend on the nature of the reactants. Most estimates of VM are in the range of 0.14–0.37 M⫺1 [11,12]. k m2 = kMVM

(10)

Equations (6)–(9) can be combined, and the dependence of overall rate constants on concentrations of surfactant, ionic reagent, and added inert salt can be predicted in terms of ␤, kM, kW, and the ion exchange parameter [Eq. (9)], provided that the distribution of substrate between water and micelles is known [Eq. (1)]. This treatment fits a great deal of data, and it is still extensively used. It also fit kinetic micellar effects on inorganic reactions, such as the redox reaction between bromate and bromide ions in aqueous acidic medium in both cationic and anionic surfactants [192]. Values of the ion-exchange parameters [Eq. (9)] follow the prediction that very hydrophilic ions will be displaced by less hydrophilic ions; i.e, affinity of ions for micelles follows the Hofmeister series. The PIE model merely considers the nature of the surface of the micelle and not its size or overall structure. As noted later, models that involve solution of the Poisson-Boltzmann


equation are sensitive to changes in micellar size and shape. Development of the PIE model was a crucial breakthrough in the study of micellar rate effects, but it has been found to be a first approximation that breaks down under some conditions, especially when concentrations of the reactive ions are greater than about 0.1 M [193,194] and for competition involving very hydrophilic anions [195]. Furthermore, kinetic data are fitted with values of K OH Br generally in the range of 12–20, so that OH⫺ in large excess should displace Br⫺ from cationic micelles. However, fluorescence spectroscopy [196] shows that very hydrophilic anions, e.g., OH⫺ and F⫺, are singularly ineffective in displacing Br⫺, although competition between Br⫺ and other moderately hydrophilic anions follows the PIE model, based on both fluorescence and kinetic data. This is confirmed by evidence from the variation of the NMR line width of halide ions: the PIE does not fit NMR data for competition involving OH⫺ and F⫺ in CTABr or CTACl [98]. The PIE model is based on a postulated constant ␤, even though Eq. (9) predicts that ions have different affinities for micelles, and there is evidence that ␤ is low for hydrophilic counterions. However, addition of a weakly bound dilute anion, e.g., OH⫺, to CTABr probably does not markedly reduce ␤, so the assumption of a constant value is satisfactory in these cases.

TABLE 1

185

Another problem with the PIE model in its original form is that the concept of ionic distribution between micelles following a step function and the concept of a constant ␤ fail to explain the marked increases of rates of reactions of hydrophobic substrates such as elimination from DDT and related chlorides, in moderately concentrated OH⫺ [193,194]. Ionescu et al. postulated incursion of a reaction path across the Stern layer for the attack of OH⫺ in the aqueous pseudophase upon micelle-bound substrate [193,194]. Nome et al. [197] could fit dehydrochlorination of 1,1-diphenyl2,2,2-trichloroethane (DTE) using Eq. (11): [OH⫺]M = [OH⫺]M /[Dn]V ⫹ [OH⫺]W

where V is the reactive volume in liters/mole of reactive region, i.e., using a modification of the PIE model, which includes the concept of variable ␣ and the contribution of the counterion in the aqueous phase to the interfacial counterion concentration. The PIE treatment was also tested for reactions of 2,4-dinitro-1-chloronaphthalene (DNCN) and p-nitrophenyl diphenylphosphate (pNPDPP) in mixtures of OH⫺ and Cl⫺ or Br⫺, with up to 0.5 M OH⫺ [198]. The fit with theory is satisfactory for dilute OH⫺, but rates increase faster than predicted with increasing [OH⫺]. Fits for reaction in 0.5 M OH⫺ would require a large increase in kM relative to the value in dilute OH⫺ (Table 1). Alterna-

Reactions with Concentrated Hydroxide Iona km2, M⫺1 s⫺1

Substrate

(C6H5)2CHCCl3 a

[OH⫺], M Surfactant

PIE

PBE

Mass action

0.03 0.5 0.05 0.5

CTACl CTACl CTABr CTABr

0.014a 0.022a 0.013b 0.017a

0.0115b 0.0105b 0.012b 0.012b

0.0168a 0.0182a 0.0196a 0.0196a

0.03 0.5 0.05 0.5

CTACl CTACl CTABr CTABr

0.076a 0.161a 0.071a 0.143a

0.07b 0.08b 0.075b 0.085b

0.0980a 0.133a 0.105a 0.140a

1

CTAOH

6.50–6.80 ⫻ 10⫺4c

For fitting parameters see Ref. 198. For fitting parameters see Ref. 217. c For fitting parameters see Ref. 197; the range is for variations of k m2 with various added salts. b

(11)

186

Savelli et al.

tively, the two other models that follow have been used to investigate this problem (Table 1). 2. Mass Action Model Values of ␤ are not constant if counterions are very hydrophilic e.g., with CTAOH, CTAF, or CTAformate. Kinetic data for reactions of these anions in the absence of inert anions cannot be fitted with constant ␤ because overall rate constants increase with increasing concentration of the reactive anion even though the substrate is fully micelle bound [199,200]. In these systems the micellar surface does not appear to be saturated with counterions. The kinetic data can be treated on the assumption that the distribution between water and micelles of reactive anion, e.g., Y⫺, follows a Langmuir equation [200]: K⬘Y

[Y⫺ M] ⫺ ⫺ [YW]([Dn] ⫺ [YM ])

(12)

The Langmuir parameter K⬘Y is low for hydrophilic ions and increases with decreasing hydrophilicity of the ion. Although kinetic data can be fitted to the mass law model, its physical significance is uncertain. For example, ion binding is assumed to follow a site model, with the micelle having a number of binding sites whose occupancy depends on an affinity parameter, K⬘Y, and on the concentration of ions in the aqueous pseudophase. In other words, ␣ and ␤ are not constant. But they will be approximately constant if K⬘Y is large, as it should be for ions such as bromide. Alternatively, we could suppose that micelles of a hydroxide ion surfactant, for example, have a large size distribution and that micelles, regardless of their size, can bind nonionic substrates but that the small micelles are relatively ineffective at binding hydrophilic ions. On this basis, the ionic distribution represented by Eq. (12) may be due to an increase in the average size of the micelle upon addition of the counterion. Another possibility is that the micellar reaction is not restricted to reactants in the Stern layer. There is not a great deal of physical evidence related to these questions. For example, CTAOH forms micelles that have small aggregation numbers and larger fractional charge, ␣, than micelles of CTACl or CTABr, but the evidence available at present is not sufficient to show that the properties of CTAOH micelles are constant over a range of conditions [200–202]. Despite these uncertainties, values of kM for reactions of hydroxide ion in CTAOH and in mixtures of CTABr or CTACl with NaOH calculated using the ion-exchange or the mass action model agree reasonably well [12]. On extending the mass action model to systems containing

both reactive and inert counterions, Eq. (12) has to be modified to include competition between Y⫺ (reactive) and X⫺ (inert) for the micellar surface, and two independent equations have to be considered, one for each ion, Eqs. (13) and (14). K⬘X =

[X⫺ M] ⫺ ⫺ ⫺ [XW ]([Dn] ⫺ [XM ] ⫺ [YM ])

(13)

K⬘Y =

[Y⫺ M] ⫺ ⫺ [Y ]([Dn] ⫺ [YM ] ⫺ [XM ])

(14)

⫺ W

The ion-exchange constants, K Yx, in Eq. (9) should be related to the individual K⬘X and K⬘Y mass action constants, and this seems to be correct. A detailed data analysis shows that the value of the ion-exchange constant is consistent with values of the individual constants [203]. The advantage of using K⬘X and K⬘Y and not K YX is that assumptions regarding values of ␤ are eliminated. This model is also better than the ionexchange model for reaction in moderately concentrated OH⫺, where the ion exchange fails for [OH⫺] > 0.1 M but that based on K⬘Br and K O⬘H is satisfactory up to 0.5 M OH⫺ [198] (Table 1). The concept of counterion binding to micelles in a well-defined Stern layer provides a very convenient means of describing micellar effects on reaction rates and equilibria, but there are serious questions about its physical significance. These equations fit a great amount of kinetic data in aqueous micelles, also with surfactants of different structures, and several of them will be discussed in Section V. It has also been successfully used to fit data for reaction of Br⫺ with methyl naphthalene-2-sulfonate in micelles of CTABr and CTEABr modified by 1-butanol [204,205]. Rate constants at micellar surfaces are proportional to the mole ratio of bound Br⫺ and bound butanol, and their distribution (Br⫺ and butanol) between water and the micelles is described by the equation of the form of the Langmuir isotherm. 3. Poisson-Boltzmann Equation The distribution of counterions around a colloidal macroion can be calculated in terms of Coulombic interactions between the macroion and the counterions, which are treated as point charges [206–209]. The cell model provides a straightforward method of estimating surface electrical potentials of spherical association colloids in terms of their radius and charge density and the ionic content and dielectric constant of the bulk solvent, which is typically water [209,210]. This treatment neglects specific interactions between a macroion, e.g., a micelle, and counterions and therefore does not


187

explain the apparent differences in affinities of various counterions for micelles [10,11]. However, it gives values for ␣ for SDS that are in reasonable agreement with experimental data, although specific binding of counterions in the micellar Stern layer is not taken into account [210]. The Poisson-Boltzmann equation (PBE) was used to fit, for instance, reactions of hydroperoxide ion (formed in situ from OH⫺ and hydrogen peroxide) with p-nitrophenyl diphenyl phosphate in CTACl and CTAOMs micelles [211] on the assumption that the hydroperoxide ion interacts only Coulombically with the micelle. However, the high specific interactions between cationic micelles and anions such as Br⫺ or NO⫺3 show that models based on purely Coulombic interactions of point-charge ions with charged surfaces do not explain the data. [The ion-exchange equation (9) explicitly considers the specificity of ion-micelle interactions.] It is necessary to include specific ion-micelle interactions that are largest for bulky ions that have low charge densities and are not very strongly hydrated [212–215]. One approach is to assume that counterions that bind specifically neutralize the charge of an equivalent number of micellar headgroups. These specific interactions are written in terms of Volmer or Langmuir isotherms, and the former is better for more concentrated ionic solutions [213–214]. The factor f, where f is the fractional coverage by counterions, describes neutralization of the micellar headgroups. In terms of the Volmer isotherms, f is given by Eq. (15): f=

␦ exp(⫺f/(1 ⫺ f ))[X⫺ W] 1 ⫹ ␦ exp(⫺f/1 ⫺ f )[X⫺ W]

(15)

⫺ where [XW ] is the concentrations of X⫺ in moles per liter of the aqueous pseudophase and ␦ is a specificity parameter related to the non-Coulombic affinity of X⫺ for micellized cationic surfactant. Values of ␦ are low for hydrophilic ions and larger for polarizable ions. Therefore, ions compete both Coulombically and specifically. On this hypothesis, an ion such as OH⫺, which interacts only Coulombically (␦ = 0), should not completely expel Br⫺, with its strong specific interaction (typically ␦ = 120 M⫺1), from a cationic micelle, in agreement with spectroscopic evidence from fluorescence quenching [196] and from examination of the Br⫺ NMR line width [98]. This treatment, based on the solution of the PBE in spherical symmetry [209–215], involves a variety of assumptions. The solution is treated as an assembly of identical uniform spherical cells, each containing one micelle. The micellar surface is assumed to be smooth

and of uniform charge density given by the micellar aggregation number and from the radius at the charged surface. Selected size parameters are consistent with physical measurement [77]. However, the treatment typically involves two disposable parameters. The first is an ion specificity coefficient, ␦: OH⫺ was assumed to interact only Coulombically, which provides a reference, and allows specific interaction parameters to be assigned to other ions [212–214]. Micellar reactions are assumed to occur in a shell at the surface whose width, ⌬, is the second disposable parameter. The firstorder rate constant for reaction of a substrate, S, and an anionic reagent, Y⫺, is given by Eq. (16) [212–214]: kobs =

m ⫺ kW [Y⫺ M] ⫹ k 2 KS[Dn][Y⌬ ] 1 ⫹ KS[Dn]

(16)

The rate constants in Eq. (16) have the same significance as in Eqs. (8) and (10), and [Y⫺ ⌬ ] is molarity integrated over the shell. (Reaction in the aqueous region can be neglected for hydrophobic substrates except with very dilute surfactant.) In this model the substrate is assumed to be distributed uniformly over the micellar region of thickness ⌬, as in the other pseudophase models, but counterion concentrations decrease in this region with increasing distance from the charged surface. The PIE model, on the other hand, assumes that concentrations of both nonionic substrate and ionic reagent are uniform within the reaction region, e.g., the Stern layer. The concept of ionic competition is common to both models, but in the PBE model counterions are assumed to compete in two different ways. Addition of counterions reduces the surface electrical potential of an ionic association colloid and therefore reduces the Coulombic attraction of counterions and repulsion of coions [209–215]. But counterions such as Br⫺ that interact specifically with the headgroups also neutralize their charge, and this reduction of the surface charge density further reduces the surface potential. Bivalent anions, such as SO2⫺ 4 , sharply reduce the surface electrical potential [210] and the Coulombic attraction for other counterions, but, because they are strongly hydrated, they probably do not intercalate between micellar headgroups [214]. They are effective inhibitors of reactions of univalent anions, and this inhibition is fitted by the PBE model [213], whereas the PIE model in its simplest form does not fit the results. This and similar treatments include both nonspecific, Coulombic interactions and ion-specific interactions of ions that intercalate in the micellar surface. PBE has been used to treat several rate effects associated with nucleophilic substitution [216] anions

188

such as hydroxide, azide, bromide and chloride, and anionic concentration was treated by considering both specific and nonspecific interactions. It is important to recognize that the model applies to micelles whose charge is at the surface and not screened by bulky groups. It is not clear whether it can be applied usefully to micelles that have bulky headgroups, and here the mass action model is often successfully used [77]. As already noted, there is evidence for the failure of the PIE model for cationic micelles at high hydroxide concentrations, for anionic micelles at high hydrogen concentrations, and for both micelles at high salt concentrations. The PBE equation was used to fit data for reactions of OH⫺ with pNPDPP, DNCN, and 1,1,1trichloro-2,2-bis( p-chlorophenyl)ethane (DDT): the treatment includes both specific and nonspecific ionmicelle interactions and considers a rough rather than a smooth micellar surface; i.e., a roughness parameter, ␴, was introduced. It seems that it improves fits for reactions in concentrated OH⫺ [217] (Table 1). There is also evidence that the PIE model is unable to explain results for positively [209,218–221] and negatively [203,221] charged substrates. Vera and Rodenas [222] and Chaimovich et al. [223] tried to explain results for negatively charged substrates by using them as micellar counterions, but in this way it is not possible to explain all the kinetic data. It was deduced that for charged substrates bound to charged micelles, it is necessary to consider electrostatic interactions depending on the micellar surface potential. A treatment developed by Rodenas and coworkers considers the ion distribution around micelles according to the PoissonBoltzmann equation, by considering specific interaction between bromide ions of CTABr and the micellar surface; it was used and nicely explained results for hydrophilic charged substrates in CTABr micelles, such as basic hydrolysis of the positively charged crystal violet [224] and of negatively charged substrates such as acetylsalicylic acid and 3-acetoxy-2-naphthoic acid [225]. The treatment was further improved by considering specific interactions between all the ions in solution, micellar counterion and hydroxide reactive ions, and the micellar surface [226], and it has been applied to study the hydrolysis of crystal violet and of acetylsalicylic acid in cationic micelles of DTABr [227] (Table 2). 4. Treatment of Coion Reactions Ionic micelles inhibit bimolecular reactions of coions by taking up the substrate and repelling the coion [8,9]. Menger and Portnoy showed that, to a first approximation, the extent of inhibition followed the extent of

Savelli et al. TABLE 2

Reactions of Charged Substratesa

Reaction Crystal violet ⫹ OH⫺ Acetyl salicylate ⫹ OH⫺

Surfactant CTABr DTABr CTABr DTABr

k , M s

W ⫺1 ⫺1

0.201 0.201 0.124 0.124

m 2 ⫺1 ⫺1

M

k , s

0.260b 0.064c 0.706 ⫻ 10⫺2b 0.540 ⫻ 10⫺2c

a

From PBE treatment; for fitting parameters see references in b and c. b From Ref. 226. c From Ref. 227.

transfer of nonionic substrate into the micellar pseudophase where the reaction rate was small or zero [119]. However, Chaimovich et al. showed that there was a small but finite reaction of OH⫺ with very hydrophobic carboxylic esters in anionic micelles of SDS and that this reaction was accelerated by addition of NaCl [228]. They suggested that Na⫹ competed with H3O⫹ at the micellar surface so that autoprotolysis of water leads to the presence of a finite concentration of OH⫺ at that surface. Romsted and coworkers found corresponding results for the H3O⫹-catalyzed hydrolysis of hydrophobic acetals in cationic micelles of alkyltrimethylammonium chloride or bromide, although reactions were much slower than those of chemically similar hydrophilic acetals in aqueous strong acid [229,230]. The micellar reactions were accelerated by added salt, and NaBr was more effective than NaCl. The PIE model explains these results in terms of competition between cations and H3O⫹, or anions and OH⫺, at the micellar surface with a consequent effect on the concentrations of lyate or lyonium ion (OH⫺ or H3O⫹, respectively). There are finite rates of SN2 reactions of thiocyanate and sulfite ions with methyl naphthalene-2-sulfonate in aqueous anionic micelles, but these reagents are conjugate bases of relatively strong acids, so any explanation based on autoprotolysis is inapplicable for these reactions and it is necessary to consider alternative models [231]. The dependence of concentrations of coand counterions on distance from the surface of a spherical colloidal macroion can be predicted from electrostatic considerations, for example, by solution of the Poisson-Boltzmann equation [209,210,212–215]. The electrostatic potential decreases with increasing distance from the micellar surface. Added electrolyte reduces the surface potential and therefore also reduces the attraction of counterions. The net effect of the reduced potential and increased total counterion concen-


189

Rate-[surfactant] profiles for reaction of OH⫺ with fully bound hydrophobic esters in SDS and rate enhancements by added salts can be fitted by calculating the concentration of OH⫺ at the anionic micellar surface by solving the PBE in spherical symmetry [231]. The method has been applied only to the reaction of OH⫺ with p-nitrophenyl diphenyl phosphinate and alkanoate and not to the reaction with MeONs. This last substrate reaction with water makes a significant contribution to the overall rate in high [SDS] so that there is uncertainty about the contribution of reactions of the anions and they cannot be followed over the wide range of conditions needed for the simulation. Second-order rate constants are not very different from those in water or in cationic micelles (Table 3). The effects of cationic surfactants and added salts on the H3O⫹-catalyzed hydrolyses of hydrophobic acetals [229,230] can also be explained in terms of an electrostatic model. Added salts increase the rate of re-

tration is that there is little change of counterion concentration at the surface [209,210,212–215]. But the decreased repulsion of coions and the increase of their total concentration lead to a sharp increase in their concentration adjacent to surface [231] and an increase of rate of reaction with a coion. This treatment neglects specific ionic interaction with the micelle. If counterions intercalate the micellar surface and partially neutralize headgroup charges, the coion concentration at the surface will increase, as will the rate of reaction. Tetramethylammonium ion is more effective than Na⫹ in speeding the reaction of OH⫺ with hydrophobic esters in solutions of SDS [231] and the H3O⫹-catalyzed hydrolysis of hydrophobic acetals in solutions of cationic micelles is faster when the counterion is Br⫺ rather than Cl⫺ [229,230]. These specific effects are consistent with the stronger binding of Me4N⫹ as compared with Na⫹ for anionic micelles and of Br⫺ as compared with Cl⫺ for cationic micelles [11].

TABLE 3

Examples of Reactions of Anions in Anionic Micelles of SDSa [X⫺], M

Substrate

Added salt, M — NaCl, 0.20

8.8 6.1

0.7 0.7

0.0193

— NaCl, 0.02–0.20

5.6 5.6

0.6 0.6

4.0

0.65

8.7 3.65

3.75 3.75

0.03–0.15 0.03–0.15

⫺d 4

(CH3CH2CH2CH2)2S ⫹ IO

a

From From c From d From b

km2, M⫺1 s⫺1

0.0193 0.0193

0.0193

(CH3CH2CH2)2S ⫹ IO⫺d 4

kW, M⫺1 s⫺1

—

— NaCl, 0.30

0.0029–0.0044

—

3.3 ⫻ 10⫺2

1.4–1.8 ⫻ 10⫺3

0.00203

Me4NBr, 0.10–0.25

3.2

1.5

0.00203

—

0.00203 0.00203 0.00203

— NaCl, 0.10–0.25 Me4NBr, 0.10–0.25

PBE treatment; for fitting parameters see references in b, c, and d. Ref. 231. Ref. 234. Ref. 233.

0.8 1.55 1.55 1.55

0.6 0.5 0.4

190

Savelli et al.

action of substrate fully bound to cationic micelles. The PIE model predicts that first-order rate constants, kobs, will increase linearly with added salt concentration, but under some conditions increases are not linear [229, 230]. Plots of kobs against [salt] have a break and slopes decrease at high [salt]. Application of the PBE model, as applied earlier to reactions of OH⫺ in SDS, predicts linear slopes at low [salt] and curvature at higher [salt] in agreement with experiment [232] (Table 3). The same treatment to calculate the anion distribution in anionic micelles of SDS has been applied in kinetic studies of the oxidation of sulfides by periodate ion [233], the reactions of a series of nucleophiles ⫺ (OH⫺, SO2⫺ 3 , N 3 ) with N-methyl-N-nitroso-p-toluensulfonamide (MNTS), and reactions of OH⫺ with 1,2dichloroethyl-3-cyclohexyl-1-nitrourea in SDS micelles [234]. In the presence of SDS micelles the reaction of MNTS with azide ion appears to occur in both the aqueous and micellar pseudophases (Table 3), whereas its reaction with SO2⫺ and OH⫺ appears to occur ex3 clusively in the aqueous phase, and it was explained on the basis of the location of the substrate and of the different anions (different polarizability and charge) in the micellar surface. Khan has also studied effects of anionic micelles on rates of bimolecular reactions involving anionic reactants and observed increases in the rate of hydroxide ion–catalyzed hydrolysis of anionic acetyl salicylate [235] and of anionic N-phthaloylglycine [236]. He explained the increase in kobs with an increase in [SDS] at constant [NaOH], thinking that the micelle-mediated reaction occurs in the Gouy-Chapman layer or at the junctural region of the Gouy-Chapman and the Stern layer, where the concentrations of water and hydroxide ions may be similar to their corresponding concentrations in the aqueous pseudophase. Such a reaction is regarded as a cross-border reaction. The mass action model has not been applied to coion reactions. B.

Other Treatments

Other general ways of treating micellar kinetic data should be noted. Piszkiewicz [237] used equations similar to the Hill equation of enzyme kinetics to fit variations of rate constants and surfactant concentration. This treatment differs from that of Menger and Portnoy [119] in that it emphasizes cooperative effects due to substrate-micelle interactions. These interactions are probably very important at surfactant concentrations close to the cmc because solutes may promote micellization or bind to submicellar aggregates. Thus, Eq. (2) and others like it do not fit the data for dilute sur-

factant, especially when reactants are hydrophobic and can promote micellization (see Section VI.B). Srivastava and Katiyar have also developed equations that attempt to take into account the way in which reactant interactions affect reactivity in micelles [238]. A refinement of Eq. (2) has been proposed including the possibility of different reaction domains within the micelle. The pseudophase model, distinguishing only between a micellar and an aqueous phase, turns into a model of three [239,240] or multiple [241,242] domains (multiple micellar pseudophase, MMPP), which is compatible with the transition state pseudoequilibrium constant approach of Kurz [243,244]. In the limit of an infinite number of domains, this model provides the exact rate constant as the integral over the domains with their local rate constant. For a spontaneous reaction, for instance, there is a reaction in the first domain, i.e., the core of the micelle, with a rate constant kC; a reaction in the Stern region, a second domain, with a rate constant kS; and a reaction in bulk water, the third domain, with a rate constant kW. Using the three-domain model and assuming that in the hydrophobic core no hydrolysis takes place, Engberts and colleagues [245] obtained the following equation, (17), for kobs for a hydrolysis reaction: kobs =

k⬘W ⫹ k⬘MKM(VM /VW) 1 ⫹ KM(VM /VW)

(17)

This relation resembles the ordinary Menger-Portnoy equation, but k⬘M is now given by Eq: (18): k⬘M = kS

再

冎再冎

VMKM ⫺ VCKWSKSC VSKWS = kZ VMKM VMKM

(18)

where VM and KM are the micellar volume and the partition coefficient, respectively, VC is the micellar core volume, KWS is the water–Stern region partition coefficient, KSC is the partition coefficient for the Stern region–core equilibrium, and VS is the Stern region volume. Alternatively, the application of the pseudophase model is considered as an adaptation of the Olson-Simonson model [246] to micellar systems. It can be demonstrated that the latter, frequently used in the interpretation of kinetic salt effects, is an alternative formulation of the Brønsted equation [247,248] that can be deduced from the transition state theory. For a reaction (A ⫹ B that yield products), this equation gives: kobs = k0

␥A␥B ␥≠

(19)

where ␥A, ␥B, and ␥≠ are the activity coefficients of the


reactants and of the activated state, respectively, and k0 is the reaction rate constant when this is carried out in the reference state. The possibility of applying the Brønsted equation to interpret the micellar kinetic effect was suggested several years ago by Bunton and Robinson [121], who later considered it again [249] but the model has not been frequently used, also because some authors have been against its use [250]. When ionic reactants are largely in the aqueous pseudophase, kinetic salt effects have been treated with a combination of the Brønsted equation and the extended DebyeHu¨ckel approach for estimating activity coefficients. Sa`nchez and coworkers used this approach to fit rate constants of reactions of oppositely charged di- and trivalent ions in SDS [251], of like charged ions in SDS micelles [252], and the oxidation of Fe(CN)2(bpy)2 with S2O2⫺ in AOT micelles and microemulsions [253]. 8 They also applied the equation to a system where both reactants are partitioned between the two pseudophases present in the system and studied a ligand substitution process in CTACl (Scheme 3) [254]. Interestingly, results from fits based on the Brønsted equation are equivalent to those based on the pseudophase model for this reaction, and this confirms the idea that both models are equally valid for interpretation of kinetic data in micellar systems. IV.

SPONTANEOUS, UNIMOLECULAR, AND WATER-CATALYZED REACTIONS

The quantitative treatment of micellar rate effects upon spontaneous reactions is simple in that the overall effect can be accounted for in terms of distribution of the substrate between water and the micelles and of the first-order rate constants in each pseudophase (Scheme 2). The micelles behave as a submicroscopic solvent and to a large extent their effects can be related to known kinetic solvent effects upon spontaneous reactions. It will be convenient first to consider unimolecular reactions and then water-catalyzed uni- and bimolecular reactions. A.

191

SCHEME 3

involving only one molecule or ion. Also, the cyclization of o-3-halopropoxyphenoxide ion (halo = Br, I) and the parameter kM(I) /kM(Br) have been used as indicators of micellar properties because their values depend largely on interactions with phenoxide ions in the initial states and charge delocalized transition states, which differ for bromide and iodide substrates. These reactions have also been useful monomolecular models for SN2 reactions; in fact, they can be regarded as intramolecular SN2 reactions [257]. Kinetic analysis of these reactions can be carried out simply using the Menger-Portnoy equation [Eq. (2)]. The E1cb decompositions have been studied as a spontaneous decomposition of the anions formed in a rapid preequilibrium. Correia and coworkers [258] interpreted only qualitatively the inhibition of decomposition of m-nitrophenyl-9-fluorene carboxylate by CTABr by assuming that the ground state carbanion formed by deprotonation of the substrate at the micellar surface is more stabilized by trimethylammonium headgroups of surfactants than the transition state in which the charge is being transferred to the oxygen of the m-nitrophenyl group. This explanation is consistent with the rate enhancement they observed for the same reaction in anionic micelles and with the absence of any rate effect in nonionic micelles. Nome and coworkers [122] studied the decomposition of p-substituted aryl-2,2,2-trichloroethanols (Scheme 4) in aqueous NaOH and analyzed quantitatively the ratesurfactant profiles (Table 4) using Eq. (4) reported in Section III. They analyzed a series of substrates. In the presence of surfactant there is a three- to fivefold decrease in

Unimolecular Reactions of Anionic Substrates

The solvent-dependent unimolecular decarboxylation of 6-nitrobenzisoxazole-3-carboxylate (6-NBIC) [255] and hydrolyses of 2,4-dinitrophenyl phosphate dianion (DNPP2⫺) [256] have provided popular probes of micellar structures [12] because with fully bound substrate, rate effects are due wholly to changes in the relative free energies of the initial and transition states

SCHEME 4

192

Savelli et al.

TABLE 4 Decomposition of p-Substituted Aryl-2,2,2,trichloroethanols in Aqueous NaOHa Substrate

X=H

X = CH3

X = OCH3

X = Cl

a

Surfactant

104 kM⬘ , s⫺1

CTABr CTACl CTAOH CTABr CTACl CTAOH CTABr CTACl CTAOH CTABr CTACl CTAOH

5.9 7.4 8.9 6.9 8.3 11.6 9.7 10.0 14.3 5.2 5.8 8.4

SCHEME 5

From Ref. 122.

rate constant and the dependence of k⬘M on substituent effect was also quantitatively analyzed in terms of the Hammett plot: ␳ values are similar in water and in micelles of CTABr, CTACl, and CTAOH. 1. Variations in Surfactant Structure A variety of new surfactants have been investigated using unimolecular spontaneous reactions as probes of micellar structure. Here we focus attention on studies of systematic variations in covalent surfactant structures. For instance, single-chain surfactants with increasing headgroup bulk (Scheme 5) have been investigated: CTABr, CTEABr, CTPABr, and CTBABr (Tables 5 and 6). For decarboxylation of 6-NBIC [259] and hydrolysis of DNPP2⫺ [260] rate enhancements increase with increasing headgroup bulk (Table 5). Bulky groups should decrease the polarity at the micellar surface and, for dephosphorylation rate enhancements, have been associated with decreases in activation enthalpies [260]. Rate effects are not due solely to a change in the bulk of the N-alkyl group, because the morpholine (CMMABr) and the quinuclidine (MQBr) derivatives are little more effective than CTABr in accelerating decarboxylation [259]. The quinuclidinium and morpholinium moieties probably extend away from the micellar surface so that reaction takes place in a region exposed to water. Bulky alkyl groups in CTBABr do not extend into the water but are oriented along the micellar surface [86] to reduce water–alkyl group contact, so de-

carboxylation and dephosphorylation of bound substrates take place in a region of relatively low polarity. For decarboxylation, the effect of headgroup size is present to a limited extent in p-octyloxy surfactants (pOOTABr and pOOTBABr) [259]. For cyclization of o-3-halopropoxyphenoxide ion rate enhancement increases sharply in the sequence of surfactant headgroups (Table 6) [261] and increases are larger for reaction of the iodide than for the bromide. Micellar headgroups can control reactivity by excluding water from the surface, which increases the reactivity of the oxide ion but decreases the hydration of the leaving halide ion. But cationic headgroups interact readily with leaving halides, and more strongly with I⫺ than with Br⫺, so they can provide electrophilic assistance to reactions. A series of 1-alkyl-4-alkylpyridinium halide surfactants has been investigated by Engberts [262] (Table 5). Variation of the 1-alkyl substituent from methyl to ethyl and n-propyl and n-butyl resulted in increases in k⬘M values, as for cetyltrialkylammonium surfactants. The same author also investigated other kinds of systematic variations (Table 5). Introduction of a rigid acetylenic segment in the center of the 4-dodecyl substituent and branching of the alkyl moiety hardly influenced the micellar catalytic effect, and the k⬘M value still depended little on the alkyl chain length. Replacement of a cationic by a zwitterionic headgroup does not inhibit decarboxylation of 6-NBIC [263], hydrolysis of DNPP2⫺ [260], and cyclization of o-3-halopropoxyphenoxide ion [263] at micellar sur-


193

TABLE 5

Unimolecular Reactions of Anionic Substratesa

Substrate

Surfactant

104 k⬘M, s⫺1

Ref.

CTABr CTEABr CTPABr CTBABr (CDA)2C32Br CMMABr MQBr pOOTABr pOOTBABr

⬇3.3 (100) 10 (330) 41 (1400) 85 (2800) 7.7 (290) 4.8 (160) 6.6 (220) >2.2 (>73) 3.7 (124)

259

CTACl CTA(SO4)0.5 CTAOTs CTAOH DDDACl

3.2 3.9 >6.6 1.8 >14

(110) (130) (220) (60) (500)b

264

SB3-14 SB3-16 SBPr3-14 AOMe-14 AOPr-14

6.6 9.2 32 7.1 >55

(220) (307) (1100) (240) (1800)

263

262c

R1

R2

n-C8H17 n-C10H21 n-C11H23 n-C12H25 — (CH2)4C — — C — C6H13 — n — CH — (CH3)(n-C10H21) — (CH2)8C(CH3)3

CH3 CH3 CH3 CH3 CH3 CH3 CH3

3.2 3.3 3.7 3.5 4.1 3.9 4.2 6.2

(42) (43) (49) (46) (54) (51) (55)d (82)e

— (CH2)7CH(C2H5)2 — (CH2)5CH(n-C3H7)2 n-C12H25 n-C12H25 n-C12H25 n-C12H25

CH3 CH3 C2H5 n-C3H7 i-C3H7 n-C4H9

4.6 4.0 5.2 6.2 8.6 9.8

(61) (52) (68) (82) (113) (129)

CTABr CTEABr CTPABr CTBABr

0.048 0.080 0.143 0.193

(24) (40) (71) (96)

280


0.068 0.164 0.333 0.558

(32) (78) (159) (266)

280

194

Savelli et al. TABLE 5 Substrate

Continued 104 k⬘M, s⫺1

Ref.

2.4 3.0 3.8 4.2 4.8 ⬃7 8.5 1.6 3.7 >0.6

(28) (35) (44) (49) (56) (81) (99) (19) (43) (7)

265

CTABr CTPABr CTBABr MQBr SB3-14 SBEt3-14 SBPr3-14 SBBu3-14

2.2 3.3 4.1 3.1 2.8 2.8 3.2 3.6

(26) (38) (48) (36) (33) (33) (37) (42)

260

CTABr CTPABr CTBABr

1.7 (14) 2.5 (21) 2.6 (22)

f

CTABr CTPABr CTBABr

1.1 (11) 1.4 (14) 1.6 (16)

f

Surfactant CTACl CTA(SO4)0.5 CPCl CDMPCl DDDACl DDDABr DDDA(SO4)0.5 Bolaform (22) Br2 Bolaform (22) SO4 Bolaform (16) Br2

a

Values in parentheses are k⬘M/k⬘W; data are for 25⬚C if not otherwise specified. At [surfactant] 0.02 M. c At 30⬚C. d Spherical micelles. e Rodlike micelles. f M. Tugliani et al., Langmuir, in press, 2000. b

faces (Tables 5 and 6), although under some conditions it may slow the overall reaction by decreasing micellar incorporation of anionic substrates. For hydrolysis of DNPP2⫺, first-order rate constants continue to increase even up to 0.2 M sulfobetaine because the substrate is not strongly bound [260]. A carboxylate ion (such as 6-NBIC) will interact unfavorably with sulfonate or carboxylate centers in a betaine micelle, and the interaction will decrease as charge moves out of the carboxylate ion in the transition state. The situation is similar for spontaneous dephosphorylation [260] and for reactions in micellized amine oxides. Micellar catalysis is increased by an increase in headgroup bulk in cati-

onic surfactants and by a change from cations to zwitterions, but the situation is more complicated when the two effects are combined. For example, decarboxylation is increased by a factor of about 2 to 3, dephosphorylation by a factor of about 1.3 [260], and cyclization of o-3-halopropoxyphenoxide ion by a factor of about 1.4 to 1.5 going from CTABr to SB3-14 [263], but with bulky headgroups, cationics are more effective than zwitterionic surfactants, especially for decarboxylation and dephosphorylation reactions. Twin-tailed surfactants that spontaneously solubilize in water at relatively high concentration (for dilute surfactant see Section VI.A) are better catalysts than

Reactivity Control by Self-Assembling Systems TABLE 6

Cyclization Reactionsa

Substrate

Y=I

Y = Br

195

104 k⬘M, s⫺1

Ref.

CTABr CTACl CTANO3 CTA(SO4)0.5 CTEABr CTPABr CTBABr

5.5 (3.9) 5.6 (1.4) 4.7 (3.4) 6.5 (4.6) 10 (7.1) 26 (19) 41 (29)

261

SB3-14 CB1-14 CB1-16

8.4 (6.0) 7.3 (5.2) 11 (7.9)

263

SB3-12 C12E23

7.1 (5.1) ⬇3.5 (2.5)

459

Surfactant

n=7

n=7

CTABr CTACl CTANO3 CTA(SO4)0.5 CTEABr CTPABr CTBABr

4.1 4.4 3.4 4.8 6.1 13.0 17.0

(1.8) (1.9) (1.5) (2.1) (2.6) (5.6) (7.3)

261

SB3-14 SB3-16 SBPr3-14 CB1-14 CB1-16

5.5 6.2 13.0 4.6 6.5

(2.4) (2.7) (5.6) (2.0) (2.8)

263

SB3-12 C12E23

4.9 (2.1) >2.9 (1.2)

459

279

Y = Br

n = 10 n = 12 n = 16

CTABr CTABr CTABr

0.059b 0.036b 0.017b

Y = Br

n = 10 n = 12 n = 16

CTBABr CTBABr CTBABr

0.130b 0.094b 0.037b

a b

Values in parentheses are k⬘M/kW⬘ . Values of k W in water are not available, for the insolubility of the substrates.

CTABr for decarboxylation [264] and for hydrolysis of DNPP2⫺ [265]. Packing of two hydrophobic alkyl chains could give lower surface charge density (Table 5). As regards the counterion effect for decarboxylation of 6-NBIC, k⬘M (Table 5 and Ref. 264) increases with decreasing fractional micellar charge, ␣, in the order CTAOTs > CTA(SO4)0.5 > CTABr > CTAOH. Micelles

with high fractional charge, i.e., high surface charge, should interact most strongly with substrates. For hyis drolysis of DNPP2⫺, reactions are faster when SO2⫺ 4 the counterion than when Br⫺ is the counterion in solutions of single-chain cetyltrimethylammonium surfactants and also in solution of bolaform(22) and of twin-chain DDDAX surfactants [265]. For cyclization of o-3-halopropoxyphenoxide ion [261], rate constants

196

Savelli et al.

follow the sequence SO2⫺ > Cl⫺ > Br⫺ > NO⫺3 (Ta4 ble 6). A considerable number of investigations have been reported on the surface and micellar properties of surfactants containing two hydrophilic or two hydrophobic groups in the molecule, called dicationic or gemini or dimeric surfactants. These include molecules that contain either a flexible hydrophilic [266–269], flexible hydrophobic [270,271], or rigid hydrophobic [272,273] linkage (spacer) between the two hydrophilic groups. The interest in these molecules appears to be due to their unusual surface and bulk properties. These include unusually high surface activity, low critical micelle concentration (cmc) values, and [274] unusual increases in cmc when the chain length of the alkyl group is increased beyond a critical length [272,273,275]. In decarboxylation of 6-NBIC [259] the dicationic surfactant (CDA)2C22Br gives larger rate enhancement than CTABr, probably because the bridging methylene groups should force water molecules away from the micellar surface. An investigation of the cyclization of o-3-bromopropoxyphenoxide was carried out in aqueous micelles of 1,4-(N-hexadecyl-N,N-dimethylammonium)butane dibromide and (2S,3S)-2,3-dimethoxy1,4 - bis(N - hexadecyl - N,N - dimethylammonium)butane dibromide [276]. As for decarboxylation, dicationic surfactants are better catalysts than the corresponding monocationic ones, probably because the spacer decreases the extent of water penetration at the aggregate surface and the cyclization rate is increased in a less polar reaction site. But the rate-surfactant profile with dicationic surfactant is peculiar in that kobs increases until a limiting value that is constant over a range of concentration but then increases again at high [surfactant] (only with the first of the two dicationic surfactants used). Regarding decarboxylation, Engberts and colleagues [277] have reported that a plot of enthalpies versus entropies of activation show a linear relationship, giving an isokinetic temperature of 336 K for a series of different micellar structures, independent of the nature of the headgroup and counterion. The analysis gives different results in bilayer assemblies. Despite mechanis-

tic differences between cyclization and decarboxylation, plots of log k⬘M for cyclization versus log k⬘M for decarboxylation are linear for a number of cationic and zwitterionic sulfobetaine micelles [278]. This result fits the widely used pseudophase model of rate effects.

SCHEME 6

SCHEME 7

2.

Investigation of Variation in Substrate Structure Systematic variations of the structure of the substrates that undergo unimolecular reactions have been investigated. Attention has been focused on substrate hydrophobicity. Longer chain phenoxides, analogues of o-3-halopropoxyphenoxide bromide (Table 6), were investigated in CTABr and CTBABr [279] and values of kobs at relatively high surfactant concentrations were found to increase with increasing headgroup bulk for all substrates, the effect being more important for the shorter chain and quite the same for all the longer chain ones (Scheme 7). More recently, analogues of 6-NBIC [280] and of DNPP2⫺ (M. Tugliani et al., Langmuir, in press, 2000), bearing a long alkyl chain of 14 carbon atoms, have been investigated (Schemes 8 and 9). Their reactivities were compared with those of their short-chain analogues (bearing an OCH3 group in the same position) in order to separate accurately substituent electronic effects from substrate hydrophobicity effects. Reactivities have been studied in cationic surfactants with increasing headgroup bulk, and values of k⬘M for fully bound substrates increase in the sequence CTABr < CTEABr < CTPABr < CTBABr (Table 5). For decarboxylation, micellar rate enhancements are decreased by introduction of an alkoxy group, based on k⬘M for reaction of 6NBIC, and surfactant headgroup effects are larger with the tetradecyloxy than with the methoxy derivative (Table 5). It is tempting to assume that the higher hydrophobicity of the former takes the reaction center deeper into the micellar interfacial region and away from water. For dephosphorylations, introduction of a long alkyl chain leads to a decrease in k⬘M relative to that of the short-chain analogue. This decrease is insensitive to surfactant structure, its value being about 0.7.


197

SCHEME 8

SCHEME 9

B.

Water-Catalyzed, Uni- and Bimolecular Reactions

Spontaneous hydrolyses of alkyl halides, sulfonic esters, and acid chlorides and deacylations are typically micelle inhibited. The rate constant in the micellar pseudophase, k⬘M, is generally simply estimated by analysis of rate-surfactant profiles, using the equation developed by Menger and Portnoy. These reactions are also inhibited by a decrease in the water content of aqueous-organic solvents [282], and qualitatively the micellar inhibitions are consistent with the interfacial region being less polar and aqueous than water. Comparisons of reaction rates in micelles and aqueous organic solvents have been used to estimate effective dielectric constant or polarities at micellar surfaces [281,282]. The high electrolyte content of ionic interfacial regions may also inhibit hydrolyses. Engberts and coworkers [283] (Table 7) have contended that observed micellar retardation of the hydrolysis of 1-benzoyl-3phenyl-1,2,4-triazole and p-methoxyphenyl dichloroacetate is dominated by a salt effect. A comparison was made between medium effects in micellar solutions of cationic, anionic, and nonionic surfactants and in solutions of model compounds (tetramethylammonium bromide, TMABr, for cationic; sodium monomethylsulfate, NMS, for anionic; and tetra- and heptaethyleneglycol, TEG and HEG, for nonionic surfactants), and the micellar rate constants matched or nearly matched the rate constant for hydrolysis in the model compound solution at rather high concentrations. The matching occurs at 4.3 M aqueous solution of NMS for

SDS micelles, at 4.2 M TEG for dodecylheptaoxyethylene glycol ether, and around 5 M TMABr for CTABr. There is also a micellar charge effect that is related to reaction mechanism [281]. The charge effect of micelles on spontaneous hydrolyses appears to be related to charge asymmetry in the interfacial region and contrasting charge distributions in the transition states of bimolecular deacylations, SN2 hydrolyses, or SN1 hydrolyses. All the results to date are covered by a simple generalization: if bond making is dominant in the transition state k⫹/k⫺ > 1, but if bond breaking is dominant k⫹/k⫺ < 1, and compounds that react at the extremes of the SN1-SN2 spectrum fit the generalization (k⫹ and k⫺ are values of k⬘M in cationic and anionic micelles, respectively [281]). In the transition state for hydrolysis of sulfonate esters, or in deacylations, negative charge builds up on the organic moiety and interacts unfavorably with the anionic headgroup of an SDS micelle as compared with a cationic headgroup. Conversely, in an SN1 reaction positive charge at the alkyl center in the transition state interacts unfavorably with a cationic headgroup [281]. Therefore, in analyzing kinetic micellar effects on spontaneous hydrolyses, not only polarity and water content but also surface charge distributions at micellar surfaces, which also depend on interactions between counterions and headgroups, have to be considered. 1.

Investigation of Systematic Variations in Surfactant Structure Systematic investigations of variations in surfactant charge and structure, including the effect of headgroup

198

Savelli et al. TABLE 7

Water-Catalyzed Reactionsa

Substrate

Surfactant

7.33 7.23 6.93 7.01 7.03 7.94 7.27 1.85 7.73 7.40 7.22 6.81 7.06 2.81

(0.59) (0.58) (0.55) (0.56) (0.56) (0.64) (0.58) (0.15) (0.62) (0.59) (0.58) (0.54) (0.56) (0.22)

284

CTABr DTABr CTACl SDS C12E7

67 126 145 48 58

(0.053) (0.10) (0.115) (0.038) (0.046)

283

16 (0.005) 47 (0.015) 6 (0.002)

283

Substrate

Surfactant SDS CTACl CTAOMs CTABr CTEABr CTBABr SB3-14 SBPr3-14 SB4-14 SB5-14 SB3-14 ⫹ NaClO4 SBPr3-14 ⫹ NaClO4

b

Ref.

CTAOMs CTAOMs ⫹ MeSO3Na CTPAOMs CTPAOMs ⫹ MeSO3Na SB3-14 SB3-14 ⫹ MeSO3Na SB3-14 ⫹ MeSO3H SB3-14 ⫹ NaClO4 SBBu3-14 SBBu3-14 ⫹ MeSO3Na AOMe-14 ⫹ MeSO3H AOMe-14 ⫹ MeSO3H AOPr-14 ⫹ MeSO3H SDS

CTABr SDS C12E7

a

106 k⬘M, s⫺1

103 k⬘M, s⫺1 1.00 8.6 8.3 5.2 4.8 4.0 8.3 6.5 ⬃7 CH3SO⫺3 > Br⫺ for univalent ions. Hydrolysis in sulfobetaine micelles is inhibited by NaClO4 (Table 7), which interacts strongly with micelles of SB3-14; solubilities of SB4-14 and SB5-14 are sharply increased by NaClO4. Physical evidence (NMR spectroscopy and conductivity data) shows that ClO⫺4 binds readily to micelles of SB3-14, which therefore become anionic [112], which by analogy with the behavior of SDS micelles should inhibit reaction. However, reaction in mixtures of sulfobetaines and NaClO4 is, with high [NaClO4], slightly slower than in high [SDS], where substrate is largely micelle bound. Hydrolysis of methylnaphthalene-2-sulfonate (Fig. 3) is slower in SB3-14 and NaClO4 than in high [SDS], which shows that the rate decrease is due not only to the development of anionic character in micelles of SB3-14 but also to displacement of water from the interfacial region by ClO⫺4.

FIG. 3 Rate constants for the spontaneous hydrolysis of MeONs in 0.05 M SB3-14 with addition of MeSO3Na (●) or NaClO4 (䡲).

Interfacial regions of betaine micelles are very open [114,117] and accessible to water, which will be displaced by ClO⫺4 or other low-charged-density anions.

V.

BIMOLECULAR REACTIONS

Micelles have effects on spontaneous reactions that can be related to the mechanism and to the properties of the micellar surface. Micellar inhibition of bimolecular reactions is also straightforward because micelles keep reactants apart. For micelle-assisted bimolecular nonsolvolytic reactions it is necessary to consider both medium and proximity effects. The term ‘‘micellar catalysis’’ is often used synonymously with ‘‘micellar rate enhancement,’’ but a distinction is needed for bimolecular reactions in which changes in free energy of activation (effect on rate constant) should be separated from free energies of transfer from water to micelles (concentration effect). Analysis of the variation of the overall rate constant of reaction with [surfactant] was discussed in Section III, and the treatment allows calculation of the secondorder rate constants of reaction in the micellar pseudophase. These rate constants can be compared with second-order rate constants in water provided that both constants are expressed in the same dimensions, and typically the units are M⫺1 s⫺1. The calculation of this rate constant, km2 [Eq. (10)], involves assumptions regarding the location of the substrate and the volume of reaction region at the micellar surface. In fits based on the PIE or mass action models, this volume has been approximated by the micellar molar volume, or that of the Stern layer, VM. In the PBE model, reaction is assumed to take place in a shell whose thickness, ⌬, has been approximated by the size of a cationic group. Inevitably, the comparison depends upon the assumed volume element of reaction; this may well differ from one type of micelle to another and probably also depends on the structure of the reactants and especially on the hydrophilicity of a reactive ion. Different investigators make different assumptions about values of this volume, but most estimates are within a factor of 2 [10,11]. In addition, some micelles grow with increasing concentration of surfactant and electrolyte, so these

200

Savelli et al.

factors may influence the volume element of reaction. Fortunately, the uncertainties so introduced may be more apparent than real; for an approximately spherical micelle the volume of the Stern layer is approximately half the total volume of the micelle, and estimates of the volume element of reaction and of the second-order rate constants should therefore be within a factor of 2 provided that the reactant composition is uniform within the Stern layer. Estimates of the value of VM, molar volume of reaction, vary from 0.14 to 0.3 M⫺1, and a variety of values within this range is used [12]. Regarding the value of ⌬, simulations of rate data for a variety of anionic nucleophiles have been made with ˚ [213,214]. Variations in this value for other ⌬ 2.4 A kinds of reactions have been considered, and this var˚ iation affects values of km2. For instance, values of 4 A have also been used [233]. Most of our treatment will concern discussion of the source of micellar rate enhancement, as can be rationalized after a quantitative treatment to separate medium and concentration effects. Data for bimolecular reactions analyzed in terms of various models are given in Tables 1 to 3 and also Tables 8 to 12; values of the second-order rate constant in the micellar pseudophase and, when reported by the authors, values of km2/kW are given. For some reactions in Table 12, only overall rate effects have been reported, but in this section we will also consider some of them because they are of considerable chemical importance.

A.

Relation to Mechanism

On the basis of the observation that most values of km2/kW are not very different from unity, especially in view of the approximations involved in their estimation, it is generally accepted that the major factor in micellar acceleration of bimolecular reactions of basic and nucleophilic anions is the increased ionic concentration in the interfacial region of cationic micelles. However, important relations of second-order rate constants to reaction mechanism and to charge dispersion are evident. It is interesting to mention the case of oxidation of sulfides by periodate ion. Despite extensive

exclusion of the anion from an SDS micelle, the overall reaction is approximately twice as fast as in CTACl micelles, and the source of this rate enhancement is related to values of km2/kW being larger in SDS than in CTACl by two orders of magnitude [233]. This is rationalized in terms of an unfavorable interaction between the cationic headgroup of the cationic micelle and the developing positive charge on sulfur in transition state formation. Regarding relations of values of km2/kW with the mechanism, it is useful to consider reactions of the same anion, for instance, hydroxide. Values of km2/kW are less than unity for carboxylic esters such as phenylbenzoates [286,287], t-butyl perbenzoate, and 2naphthyl benzoate [288] and inorganic esters such as pNDPP [217]. Values of km2/kW are close to unity for SN2 reaction with MeONs [289] but are greater than unity for aromatic nucleophilic substitution with DNCN [290] and E2 elimination from 2-phenethyl derivatives [291–293]. The variation in km2/kW is generally not large in view of differences in the parameters, especially VM, used in the calculations, but they seem to be significant. The mechanisms of reactions of anionic nucleophiles with carboxyl derivatives and phosphate esters are similar in that negative charge tends to be localized on oxygen in the transition states, as shown for deacylation in Scheme 11. The transition state here should be stabilized by hydrogen bonding to water molecules, which may be less available at the surface of an ionic micelle than in bulk water. The situation is different for aromatic nucleophilic substitution (where the transition state will be like a Meisenheimer complex with its negative charge delocalized over the nitroaromatic moiety) and for E2 elimination, where five centers are involved. These bulky, low-charge-density anions should interact favorably with cationic micellar headgroups and be stabilized by this interaction. We can also describe the differences between these reaction types in terms of Pearson’s hard-soft description [294,295]. Cationic micellar headgroups interact best with soft bases, e.g., relatively large anions of low charge density such as bromide or arenesulfonate, or anionic transition states such as those for nucleophilic aromatic substitution or elim-

SCHEME 11

Bimolecular Nucleophilic Substitutions KS, M⫺1

K YX

␤

CTABr CTABr CTAOMs CTA(SO4)0.5

120 120 120 150

—

0.8

CTABra CTAOMsa

120 120

CTACl CTACl CTAOMs CTA(SO4)0.5

120 120 115 150

CTACla CTAOMsa N⫺3 Br⫺

K⬘Y, M⫺1 K⬘X, M⫺1 104 kM, s⫺1

km2 /kW

Ref.

8 8 45 6

0.37 0.37 0.23 0.28

311

— —

0.37 0.23

216

2.8 2.9 1.6 1.75

0.30 0.32 0.18 0.20

311

120 120

— —

0.3 0.66

216

CTAN3a CTAOMsa

115 115

— —

0.375 0.085

CTABr CTABr CTAOMs CTA(SO4)0.5

65 65 65 80

7.3 6.1 2.5 2.75

1.7 1.4 0.23 0.64

311

CTABr CTEABr CTBABr

65 65 65

6.0 9.80 14.0

1.40 2.29 3.27

f

CTACl CTACl CTAOMs CTA(SO4)0.6

50 70 65 80

1.6 1.5 0.8 0.8

0.8 0.8 0.41 0.41

311

OH⫺

CTAOH CTPAOH

OH⫺ Br⫺

Substrate

Surfactant

Y Br

⫺

Cl⫺

Cl⫺

2000

—

2.5 90

— — 2.0 65

—

0.8 230

—

0.8 2200

—

2000 1500 750

— — —

220

—

65 65

55 25

— —

18 14

0.24 0.19

293

CTAOH CTPAOH

58 58

55 25

— —

140 165

0.50 0.58

293

CTABr CTEABr CTBABr

50 58 58

2000 1500 750

— — —

70.0 95.0 200

2.58 3.5 7.37

f

2.5 90

—

0.8

2 65


TABLE 8

201

202

TABLE 8

Continued KS, M⫺1

K YX

␤

CTABr CTABr CTAOMs

120 120 120

—

0.8

CTABra CTAOMsa

120 120

CTACl CTACl CTAOMs

120 120 120

CTACla CTAOMsa

120 120

OH⫺

CTAOH CTPAOH

130 130

55 25

Br⫺

CTABr CTEABr CTBABr

130 130 130

OH⫺

CTAOH CTPAOH

Br⫺

CTABr CTEABr CTBABr

OH⫺

K⬘Y, M⫺1 K⬘X, M⫺1 104 kM, s⫺1

km2 /kW

Ref.

3.5 3.4 1.75

1.6 1.6 0.66

311

— —

1.6 0.66

216

1.0 1.1 0.6

0.6 0.66 0.37

311

— —

0.6 0.37

216

— —

50.0 48.0

0.44 0.43

f

2000 1500 750

— — —

23.0 34.5 60.0

2.35 3.53 6.13

120 120

55 25

— —

47.0 44.0

0.44 0.42

120 120 120

2000 1500 750

— — —

21.0 21.0 54.0

2.56 2.56 6.75

CTAOH CTPAOH

55 25

— —

12.0 8.20

0.26 0.17

Br⫺

CTABr CTEABr CTBABr

2000 1500 750

— — —

5.10 7.60 10.0

1.24 1.85 2.43

OH⫺

CTAOH CTPAOH

55 25

— —

7.10 4.75

0.18 0.12

Br⫺

CTABr CTEABr CTBABr

2000 1500 750

— — —

2.50 3.90 4.80

0.75 1.16 1.43

Substrate

Surfactant

Y Br⫺

Cl⫺

2200

—

2.5

—

0.8 220

—

2

f

f

f

Savelli et al.


1000 1000 1000 1000

475 350 290 155

— — — —

1.34 2.00 2.53 3.51

1.76 2.63 3.33 4.62

296


1000 1000 1000 1000

2000 1500 1100 750

— — — —

8.5 11.0 15.0 18.0

1.6 2.1 2.9 3.4

290

0.75–0.30 0.56–0.18

1.2b 1.4b

9.1 13.8

0.75–0.46 400–53 23 0.32 0.56–0.35 95–28 13 0.23

1.4b 1.4b 1.6b 1.6b

⬃9.2 12 16–15 21

⬃1.69 2.21 ⬃2.85 3.87

205

0.025 M CTABr ⫹ C10E4 0.05 M CTABr ⫹ C10E4

10.0 11.5

1.84 2.12

127

[Br⫺] var. [Br⫺] const.

[CTABr] ⫹ [C10E4] = 0.05 M [CTABr] ⫹ [C10E4] = 0.05 M

10.4 13.0

1.92 2.39

Br⫺

SB3-13 SBEt3-14 SBPr3-14 SBBu3-14 SB4-14 SBPr4-14 SB5-14 SBPr5-14

CTABr ⫹ BuOH CTEABr ⫹ BuOH CTABr ⫹ BuOH ⱕ 0.6 M CTABr ⫹ 0.8 M BuOH CTEABr ⫹ BuOH ⱕ 0.6 M CTEABr ⫹ 0.8 M BuOH

1500–530 510 1500–530 510

1000 1000 1000 1000 1000 1000 1000 1000

4.3 3.2 2.6 1.8 4.3 2.6 4.3 4.5

— — — — — — — —

112

7.0 12 18 29 9.5 22 10 15

SB3-16a

Cl⫺

204

1.82

315

AOMe-14 AOPr-14 AOMe-14 ⫹ H⫹ AOPr-14 ⫹ H⫹ MTABr

500 500 500 500 1000

1.8 1.5 20 15 475

— — — — —

12 18 12 18 9.5

2.1 3.1 2.1 3.1 1.7

317

CTACl CTEACl CTPACl CTBACl

1000 1000 1000 1000

80 70 45 45

— — — —

0.23 0.39 0.45 0.48

1.53 2.60 3.00 3.20

296

1.36

315

SB3-16a


Br⫺

203

204

TABLE 8

Continued

Substrate

Surfactant

Y

Cl⫺

KS, M⫺1

K YX

␤

K⬘Y, M⫺1 K⬘X, M⫺1 104 kM, s⫺1

OH

SO⫺2 3 ⫺

Ref.

OdTACl CTACl MTACl DTACl DeTACl OcTACl OcTAClc HeTAClc TMAClc

1537 1093 556 310 154 0.65 0.34 0.005 0.0044

268 74.2 40.0 42.0 22.9 0.66 0.66 0.0005 0.0004

— — — — — — — — —

2.18 1.82 1.97 1.67 1.61 0.64 0.94 1.00 1.09

2.07 1.73 1.80 1.53 1.53 1.0 — — —

298

CTEACl CTPACl CTBACl CTPeACl CQCl

1000 1000 1000 213 1000

70.5 50.0 35.0 18.8 165.0

— — — — —

2.50 2.51 2.61 9.01 3.20

2.92 2.92 3.08 10.5 3.75

297

CDMHEACl CTHEACl

911 700

112.0 4300

— —

1.50 0.91

1.78 1.08

297

0.13

315

0.34 ⬃0.40 0.31 ⬃0.37 0.25 ⬃0.38 0.31 ⬃0.42 0.40 0.57

289

0.34

315

SB3-16a ⫺

km2 /kW

CTAOH CTAOH ⫹ 0.05–0.5 M OH⫺ CTEAOH CTEAOH ⫹ 0.1–0.5 M OH⫺ CTPAOH CTPAOH ⫹ 0.1–1.0 M OH⫺ CTBAOH CTBAOH ⫹ 0.5–1.0 M OH⫺ CQOH CQOH ⫹ 0.5 M OH⫺

— 1090 1090 1000 1000 1000 1000 1000 1000 1000 1000

55 55 45 45 25 25 12 12 50 50

SB3-16a

— — — — — — — —

19.5 ⬃22.7 18.5 ⬃21.5 15.0 ⬃22.3 18.0 ⬃25.0 23 33

—

I

SB3-14

Br⫺

CTABr CTPABr CTBABr

1000 1000 1000

2000 1100 750

— — —

4.3 14.9 19.3

0.60 2.1 2.7

OH⫺

CTAOH CTPAOH

1000 1000

55 25

— —

8.57 10.2

0.13 0.15

112

35

21

g

Savelli et al.

CTABr CTEABr CTPABr CTBABr CTAOMs CTPAOMs

2000 2000 2000 2000 2000 2000

2000 1500 1100 750 2000 1500

— — — — 500 250

7.90 12.0 15.0 18.0 10.0 17.3

1.4 2.1 2.6 3.2 1.8 3.0

OH⫺

CTAOH CTEAOH CTPAOH CTAOMs CTPAOMs

2000 2000 2000 2000 2000

55 45 25 55 25

— — — 500 250

21.0 16.8 17.5 19.5 14.5

0.32 0.25 0.26 0.29 0.22

Br⫺

CTABr CTEABr CTPABr CTBABr CTAOMs CTPAOMs

3000 3000 3000 3000 3000 3000

2000 1500 1100 750 2000 1500

— — — — 500 250

9.80 13.8 23.0 27.5 13.7 23.0

1.7 2.4 4.0 4.8 2.4 4.0

OH⫺

CTAOMs CTPAOMs

3000 3000

55 25

500 250

24.5 21.5

0.37 0.32

R = C12H25

Br⫺


4000 4000 4000 4000

2000 1500 1100 750

— — — —

16.5 20.5 29.0 40.0

2.9 3.6 5.1 7.0

h

n=2

Br⫺

CTABr CTPABr CTBABr

2500 2500 2500

2000 1100 750

— — —

0.670 0.820 0.910

1.8 2.2 2.5

h

n=8

Br⫺


3000 3000 3000 3000

2000 1500 1100 750

— — — —

1.15 1.40 1.45 1.56

3.1 3.8 3.9 4.2

h

R = C6H13

h

h


Br⫺

R = CH3

205

206

TABLE 8

Continued

Substrate

Surfactant

Y

KS, M⫺1

K YX

␤

K⬘Y, M⫺1 K⬘X, M⫺1 104 kM, s⫺1

km2 /kW

Ref. 309

CH3COO⫺

CTAOAc CTACl

120 110

0.02 0.018

C5H11COO⫺

CTAHexanoate CTACl

300 270

0.05 0.045

C9H19COO⫺

CTACl

400

0.093

C13H27COO⫺

CTACl

600

—

⬃1000 1200 ⬃1200 ⬃1275 ⬃1325 ⬃1650 ⬃1975 ⬃2100 ⬃925 ⬃1150 ⬃1250 ⬃1200 ⬃1000 ⬃1300

2.7 2.7 2.8 2.8 3.6 3.6 4.7 4.7

⫺

OH

OH⫺ ⫺ 3

CTABr CTABr CTEABr CTEABr CTPABr CTPABr CTBABr CTBABr CCHDMABr CCHDMABr CMMBr CMMBr MQBr MQBr

1600 1600 1600 1600 1600 1600 1600 1600 1600 1600 1600 1600 1600 1600

CTACla

600

a

CTACl CTABra CTAN3a

8.5 70 85

N⫺3

CTABr

34

0.80

14

0.75

14

0.70

14

0.60

14

0.75

14

0.75

14

0.75

55

2000

45

1500

25

1100

12

750

50

1700

50

1700

50

1700

290

0.5–4.2 216 0.011 0.011 0.008

1

1.1

301

Savelli et al.

N

14

CTABr

3228

9

40

301

N⫺3

CTABr

196

2

0.5

301

N⫺3

CTABr

1956

2

0.9

301

N⫺3

CTABr

240

1

10

301

N⫺3

CTABr

67

2

52

301

N⫺3

CTABr

17.5

2

48

301


N⫺3

207

208

TABLE 8

Continued

Substrate

Surfactant

Y F⫺ OH⫺

SB3-16 SB3-16a

IB⫺d

SB3-16 CTAIB CTAIB

⫺e

OIB

⫺ 2

KS, M⫺1

K YX

␤

K⬘Y, M⫺1 K⬘X, M⫺1 104 kM, s⫺1

⬃0.7 10,000

1500

SB3-16 a

HO

CTACl CTACl ⫹ KCla CTAOMsa

10,000 10,000 10,000

C4H9NH2 Piperidine Pyrrolidine

CTABr CTABr CTABr

8500 8400 10,440

⬃3 ⬃1 ⬃0.7

km2 /kW

Ref.

0.6 1.25

315

59,000 ⬃60,000 45,000

0.83 0.84 0.63

59,000

0.83

54.0 24.6 64.7

⬃0.18 0.18 0.18

211

0.011 0.011 0.011

236

a

PBE model. KBuOH. c Ion-exchange model in complexes of ion pairs and substrate. d IB = o-iodose benzoate. e OIB⫺ = 5-(octyloxy)-2-iodosobenzoate. f L. Brinchi et al., Eur. J. Org. Chem., in press, 2000. g L. Brinchi et al., unpublished results (or submitted). h L. Brinchi et al., J. Colloids Interface Sci., in press, 2000. b

Savelli et al.


Bimolecular Eliminations by Hydroxide Ion KS, M⫺1

KOH X

␤

CTABr CTAOH

⬃420 230

27

0.76

CTANO3 CTABr CTACl

285 295 305

37 32 7

0.75 0.77 0.75 ⫹ 0.5 [NaCl]a

CTABr CTAOH

⬃330 200

32

0.77

CTAOH CTPAOH

Substrate

Surfactant

X = Cl X=H

X = NO2

a

209

K⬘OH, M⫺1

K⬘X, M⫺1

30

104 kM, s⫺1

km2/kW

Ref.

⬃7.5 ⬃7.45

2.0 2.0

291

1.9 2.5 2.5

292

30

⬃2.5 2.5

1.1 1.1

291

340 260

55 25

1.0 1.8

0.38 0.69

293

SB3-14 SBBu3-13

260 260

0.35 0.25

0.45 1.63

0.27 0.63

319

CTANO3 CTABr CTACl

280 290 310

38 32 9

0.75 0.77 0.72 ⫹ 0.5 [NaCl]a

CTABr CTAOH

⬃360 250

32

0.77

CTAOH CTPAOH

590 640 640

292

640 640

3.4 3.4

291

30

420 420

55 25

400 1100

2.3 6.4

293

SB3-14 SBBu3-14

450 500

0.35 0.25

420 1160

2.5 6.8

319

CTACl CTAOH CTPAOH DDDACl DDDAOH

3000 3000 3000 3000 3000

55 55 25 55 55

300 — — 300 —

7.7 9.3 13.0 14.0 10.0

0.14 0.16 0.23 0.25 0.17

300

CTACl CTAOH CTPAOH DDDACl DDDAOH

3000 3000 3000 3000 3000

55 55 25 55 55

300 — — 300 —

220 250 400 435 270

0.56 0.64 1.02 1.11 0.69

300

␤ linearly increases with [NaCl].

ination. They interact less readily with hard bases, e.g., high-charge-density anions such as OH⫺, or anionic transition states for deacylation. The relation between micellar kinetic effect and charge dispersion in the transition state seems to be a general phenomenon. In deacylation, electron-donating groups increase charge lo-

calization, whereas electron-withdrawing groups have the opposite effect, and there is a clear relation with values of km2/kW, which decrease by a factor of 8 as the substituent changes form CN to OMe [286]. Similar reasoning can be applied to the effect of the nitro group in elimination [291–293].

210 TABLE 10

Savelli et al. Alkaline Hydrolyses

Substrate

Surfactant

KS, M⫺1

X=H

CTABr CTEABr CTPABr CTBABr MQBr CTAOH

X = OCH3

␤

K⬘OH, M⫺1

K⬘X, M⫺1

104 kM, s⫺1

km2/kW

Ref.

2000 2000 2000 2000 2000 2000

55 45 25 12 50 55

2000 1500 1100 750 1700 —

⬃8400 ⬃6400 5000 ⬃5900 ⬃7800 1200

0.030 0.023 0.018 0.021 0.027 0.044

287

CTABr CTEABr CTPABr CTBABr MQBr

1500 1500 1500 1500 1500

55 45 25 12 50

2000 1500 1100 750 1700

1400 900 600 500 1100

0.018 0.012 0.007 0.006 0.014

286

X = CH3


3000 3000 3000 3000 3000

55 45 25 12 50

2000 1500 1100 750 1700

3000 2200 1700 1800 2700

0.021 0.016 0.012 0.012 0.019

286

X = Cl


2000 2000 2000 2000 2000

55 45 25 12 50

2000 1500 1100 750 1700

3900 2800 2500 3300 3000

0.057 0.041 0.036 0.048 0.044

286

X = CN


2000 2000 2000 2000

55 45 25 12

2000 1500 1100 750

55,000 47,000 55,000 72,000

0.12 0.10 0.12 0.16

286

CTACl CTAOH

⬃783 800

⬃967 1100

0.042 0.042

288

CTACla

⬃780

0.044

216

CTACl CTAOH

2100 2200

0.026 0.026

288

CTACla

2100

0.028

216

MTACl MTABr CTACl CTABr

6500 6500 8000 8000

4 8 4 8

0.75 0.75 0.8 0.8

15.3 12.7 18.1 17.0

0.54 0.64 0.62 0.60

460

CTABr

184

23

0.7

1040

0.17

461

KOH X

4

0.8 55

5

0.8 55

⬃1100 1100


Continued

Substrate

a

211

KS, M⫺1

␤

K⬘OH, M⫺1

K⬘X, M⫺1

104 kM, s⫺1

km2/kW

Ref.

CTABra

0.121

225

CTABra

0.097

225

Surfactant

KOH X

PBE model.

B.

Ion Specificity

The same kind of reasoning can explain the different behavior of different nucleophiles toward the same substrate. Values of km2/kW are less than unity for SN2 reaction of MeONs with OH⫺ but are bigger for reaction of softer anions, such as chloride and bromide (Table 8) [289,290,296,297]. For SN2 substitution with butyl 4-nitrobenzenesulfonate [216], values of km2/kW depend upon the hydrophilicity or polarizability of the nucleophile, i.e., follow the sequence N⫺3 > Br⫺ > Cl⫺ (Table 8). The intrinsic nucleophilicity of soft anions is different in water and in micelles, being higher in cationic micelles. This effect is related to partial disruption of soft ion hydration shells, as consistent with increases in NMR line width for bromide and chloride ions in cationic surfactants [86,297,298]. This effect on intrinsic reactivity of soft anions will be considered again later. Still specific interactions between the highly polarizable borohydride anion and cationic micelles have been invoked to rationalize the high inhibition in reductions of ketones observed by Cerichelli et al. (Table 11) [299]. Here, specific interactions with the reagent stabilize it, while the transition state with a partially negative oxygen atom is likely to be stabilized more effectively by water than by the micellar surface. Specific interactions between cationic headgroups and soft anions nicely explain the different electrophilic assistance to the leaving anion in intramolecular cyclization [261] (Table 6) of o-(3-halopropyloxy)phenoxide ion (halogen = I, Br), with values of kW(I) /kW(Br) being 0.60, and values of kM(I) /kM(Br) being 1.3 in cationic micelles of CTABr, and also in elimination from 1,2-dihalo-1,2diphenylethanes (halogen = Br, Cl), with values of kW(Br) /kW(Cl) approximately 7 in the absence of surfactant and values of kM(Br) /kM(Cl) about 27–31 in cationic surfactants (Table 9) [300].

The behavior of azide ion in nucleophilic aromatic substitution is quite peculiar and leads to values of km2/kW much bigger than 1 [12]. Broxton et al. found values of km2/kW up to ⬃40–50 for the substrates in Scheme 12 [301]. Actually, these high values are observed only for some of the numerous substrates studied, with catalysis being smaller for other substrates (reported in Table 8) with fluoronitro compounds and for substrates that, on the basis of NMR studies, are more buried inside the micelle. It is difficult to explain these results, although there seems to be a relation between the anomalous behavior of the azide ion in micellar reactions of aromatic substrates and its nucleophilicity in water and similar polar, hydroxylic solvents. Azide is a very powerful nucleophile toward carbocations, based on Ritchie and Sawada’s N⫹ scale, but in water it is much less reactive toward 2,4-dinitrohalobenzenes than predicted, whereas the reactivity of other nucleophiles fits the N⫹ scale [302]. Therefore, the large values of km2/kW may reflect the fact that azide ion is unusually unreactive in

SCHEME 12

212

TABLE 11

Other Bimolecular Reactions KS, M⫺1

KYX

CTABr CTACl

31 27

CTABr

km2 /kW

Ref.

2 4

44.3 60.0

0.036 0.048

299

52

2

31.0

0.029

299

CTABr CTACl

85 60

2 4

57.5 75.0

0.028 0.036

299

CTABr

70

2

3.80

0.018

299

CTABr

100

2

39.0

0.022

299

CTACla

140

0.004

233

Surfactant

Savelli et al.

(CH3CH2CH2)2S ⫹ IO⫺4 → (CH3CH2CH2)2S — —O

␤

104 kM, s⫺1

Reaction

340

0.0008

233

313

RCH — —CH2 ⫹ Br2 → Products R = C4H9

CTABr ⫹ NaBr ⱕ 0.01 M CTABr ⫹ 0.1 M NaBr

⬃3.6 ⫻ 10⫺6 5.9 ⫻ 10⫺7

R = C5H11


⬃2.2 ⫻ 10⫺6 6.25 ⫻ 10⫺7

R = C6H13


⬃2.0 ⫻ 10⫺6 5.9 ⫻ 10⫺7

R = C8H17

CTABr CTABr ⫹ 0.01–0.1 M NaBr

1.1 ⫻ 10⫺6 ⬃4.4 ⫻ 10⫺7

R = C10H21

CTABr CTABr ⫹ 10⫺2 M NaBr CTABr ⫹ 0.1 M NaBr

1.9 ⫻ 10⫺6 1.2 ⫻ 10⫺6 5.7 ⫻ 10⫺7

CTABr CTABr ⫹ 10⫺2 M NaBr CTABr ⫹ 0.1 M NaBr

3.9 ⫻ 10⫺6 2.9 ⫻ 10⫺6 1.9 ⫻ 10⫺6

313

0.071

307

0.071

307

a

CTABr

0.8

CTABr

35

0.08


CTACla

PBE model.

213

214

TABLE 12 Reaction

Other Bimolecular Reactions with Other Treatments Surfactant

Remarks

Ref.

Anionic micelles of SDS inhibit the reaction and with hexanoate, decanoate, and tetradecanoate the observed first-order rate constants go through a minimum.

309

CTACl SDS

CTACl and SDS micelles catalyze the reactions with methyl- and dimethylamine. CTACl inhibits the reaction of methyl pyridinium with trimethylamine (this acts as a general base catalyst rather than as a nucleophile) and the reactivities of the other two substrates with methyl- and trimethylamine go through maxima. SDS inhibits the reactions of the three substrates with trimethylamine, with the inhibition increasing with increasing substrate hydrophobicity.

305

CTABr CTACl CTAN3

Reactivity of the methyl derivative goes through a minimum with increasing [CTABr] due to weak substrate binding, whereas reactivity of the hexyl derivative increases as [CTABr] or [CTACl] increases due to cooperative binding of reactants. The most hydrophobic substrates’ reactivities are strongly enhanced in CTABr and CTACl micelles (krel up to 1.5 ⫻ 104): the ratesurfactant profiles go through a maximum and rate enhancement was unexpectedly larger in CTABr than in CTACl. The profiles can’t be fitted by an ion-exchange model, because the substrates can self-micellizate or induce micellization at low [surfactant], and micellar binding is cooperative. The minimum value of km2 / kw for the hexadecyl derivative was estimated to be 440.

218

SDS CTABr

In the presence of SDS micelles the rate of the acid-catalyzed hydrolysis is faster than in water for all HCl concentrations and the pH-rate profile shows no plateau, indicating that there is a higher percentage of initial amide cleavage in SDS than in water. In the presence of CTABr micelles the rate of base-catalyzed hydrolysis is much slower than in water, probably because the NH group (pKa = 12.4) is more ionized.

462

Savelli et al.

SDS

Zwitterionic micelles of CB1-14 and CB1-16 catalyze the hydroxy dehalogenation reaction, thanks to weak binding of hydroxide ions to the dipolar micelles. Indeed, catalysis is less effective in zwitterionic than in cationic micelles and increases linearly with increasing [OH⫺].

463

[Fe(CN)5L]⫺3 ⫹ L⬘ → [Fe(CN)5L⬘]⫺3 ⫹ L L, L⬘ = pyridine derivatives

Triton X-100 SDS CTABr

With uncharged L, the reaction is catalyzed, at about the surfactant cmc, especially when L is hydrophobic and the surfactant is neutral or anionic: krel ⬵ 8 in Triton X-100 with L = 4(1-butylpentyl)pyridine and L⬘ = 1,4 pyrazine. With cationic L the reaction rate is unaffected by Triton X-100 but is modestly speeded by SDS due to electrostatic and hydrophobic interactions. In reverse micelles of CTABr in n-hexanol, the most hydrophobic Ls are the best leaving groups. With L = 4(1-butylpentyl)pyridine, as the water content increases, kobs tends to the value in water.

464

[Fe(CN)5(4-CNPy)]⫺3 ⫹ CN⫺ ` Fe(CN)⫺4 6 ⫹ 4-CNPy

CTACl

The reaction follows a dissociative mechanism. Both pseudophase and Brønsted equation models fit kinetic data and calculate the same value of krel 2 in water = 0.110 [rate constant for the reaction of CN⫺ with Fe(CN)⫺3 5 , relative to the rate constant of the reaction of 4-CNPy with the iron moiety].

254

C12E10 C12E23

In nonionic micelles of C12E10 and C12E23 the reaction is inhibited with both nucleophiles, due to incorporation of the substrate in the palisade layer, where ionic concentrations are lower than in water because of the large volume of the palisade layer and of the partial penetration of anions. OH⫺ is more reactive than F⫺ and it seems that the micellar environment has no effect on the second-order rate constants. Added hydrophobic anions, as ␤-naphthalene sulfonate, perchlorate, and p-toluene sulfonate, compete with the nucleophiles for the occupation of the micellar psuedophase and increase inhibition: krel = 0.30–0.60. Added (C7H15)4N⫹ makes the micelles positively charged and speeds the reaction with F⫺ (krel ⬵ 2).

303


CB1-14 CB1-16

215

216

TABLE 12

Continued

Reaction

Surfactant

[Fe(CN)5H2O] ⫹ [␤-Co(trien)(pzCO2)] → [␤-(trien)Co(␮-pzCO2)Fe(CN)5]⫹2 ⫹ H2O trien = triethylentetraammine pzCO2 = pyrazinecarboxylate ⫺3

⫹2

Ref.

SDS

In SDS micelles the reaction rate goes through a minimum in 0.03 M SDS due to complete Co(III) complex incorporation into micelles. A subsequent increase in [SDS] results in a decrease in the interfacial electrical potential, ⌬⌿. It will favor the approaching process between the two oppositely charged reactants. This means that the electrostatic contribution to the activation free energy is the main factor that influences reactivity. Indeed, added alcohol and electrolytes decrease ⌬⌿ and increase kobs in the order Li⫹ < Na⫹ < Cs⫹ and Et4N⫹ < Pr4N⫹ < Bu4N⫹.

465

CTABr

The reaction is catalyzed in CTABr micelles, where both reaction centers are located at the interface: kmin obs /kw = 2.33 at 73⬚C.

314

CTABr

The reaction is inhibited in CTABr micelles due to different locations of the two reactions centers: kmin obs /kw = 0.30 at 73⬚C.

314

CTABr

The reaction with PhNH2 is inhibited in CTABr micelles due to different locations of the two reaction centers: kmin obs /kw = 0.14 at 31⬚C. The reaction rate is instead unaffected in CTABr with n-PrNH2: kmin obs /kw = 1.06 at 31⬚C.

314

CTABr

The two bulky tertiary amines act as specific-base catalysts and activate water as nucleophile. In CTABr the reaction is faster: kmin obs /kw = 13.3 at 73⬚C and 13.8 at 57⬚C for TMED and DMAE, respectively. As both substrate and amines are located in the micellar interior, water can penetrate inside the aggregates too.

314

Savelli et al.

Remarks

Reactions with PhNH2 and n-PrNH2 are catalyzed in CTABr micelles because both reaction centers are located in the micellar interface: kmin obs /kw = 18.4 and 14.0 at 31⬚C for PhNH2 and nPrNH2, respectively.

314

CTABr

The two bulky tertiary amines act as specific-base catalysts and activate water as nucleophile. In CTABr the reaction is faster: kmax obs /kw = 6.4 at 73⬚C and 8.4 at 57⬚C for TMED and DMAE, respectively.

314

SDS CTABr MTABr C16E20

Alkaline hydrolysis is inhibited in SDS micelles due to exclusion of OH⫺ from the negatively charged micelle. The reaction in CTABr micelles was quantitatively treated by the psuedophase ion exchange model (see Table 10). In the presence of MTABr, kobs values go through a maximum (krel ⬵ 3), in agreement with the model. In the nonionic surfactant C16E20 inhibition occurs, due to effective substrate association (Ks = 243 cm3 g⫺1) and to the absence of significant amounts of OH⫺ in the micellar environment.

461

SDS CTABr MTABr C16E20

In the presence of SDS the transnitrosation reaction with sarcosine (SAR) is inhibited by substrate micellar association (Ks = 75 M⫺1) and anion repulsion from the negatively charged micellar surface. The same reaction is catalyzed by MTABr, where reaction rate goes through a maximum (krel = 1.7). The reaction with DMA is inhibited in SDS, CTABr, and C16E20.

461

CTACl SDS

The diazocoupling reaction is catalyzed by both CTACl and SDS micelles. Values of krel (= kmax /k1PhN⫹2 in H2O): R = Cl: 71.2 in SDS and 39 in CTACl; R = CH3: 21 in SDS and 74 in CTACl; R = C6H13: 109 in SDS and 8.9 in CTACl; R = C10H21: 89.6 in SDS and 65.2 in CTACl; R = C14H29: 55 in SDS and 70 in CTACl; R = C16H33: 37.5 in SDS and 96.6 in CTACl.

308


CTABr

217

218

TABLE 12 Reaction

Continued Surfactant

Ref.

SDS

The reaction with Br is effectively suppressed by SDS, whereas the reactions with OH⫺, SCN⫺, and SO⫺2 3 are strongly but not completely inhibited by SDS. The Poisson-Boltzmann equation model was not applied because the reaction with water makes a significant contribution. Added inert salts such as NaCl and Me4NCl speed micellar and nonmicellar reactions, the ammonium salt being more effective: in 0.18 M SDS, 105 kobs = 3.04 and 1.46 without salt, 4.55 and 3.85 in 0.4 M Me4NCl for ⫺ 0.1 M SO⫺2 3 and for 0.3 M SCN , respectively.

466

SB3-16

Both substrates in alkaline hydrolyses are catalyzed by SB3-16 and kinetics are treated by means of an enzymatic model. For DeCP: Ks = 120 M⫺1, kM = 0.139 s⫺1 at pH = 11.63; for DoCP: Ks = 1640 M⫺1, kM = 0.125 s⫺1 at pH = 11.63. Catalysis is reduced by adding Br⫺ or Cl⫺, Br⫺ being more effective than Cl⫺. The dissociation constants of the inhibitor-micelle-like complex, KI, Br were calculated using a competitive inhibition model: K Cl I /K I = 4.5 for DoCP.

318

SDS

Alkaline hydrolysis of acetyl salycilate is speeded in anionic micelles of SDS, and the rate-surfactant profiles follow the empirical relationship: kobs = C ⫹ F [SDS]. Up to [SDS]T = 0.16 M, the observed data may be explained in terms of a dynamic pseudophase model, where 1 >> KOH[Dn] and 1 >> Ks[Dn] (Ks = 0.13 M⫺1). The fitting parameters show that the micelle-mediated reaction probably occurs in the interfacial region of the Stern and Gouy-Chapman layers, where counterions (nearly 30% of the total Na⫹ ions) are loosely associated with SDS micelles.

235

CTABr

At constant temperature and [HOCH2CH2OH]T, kobs values decrease as [CTABr] increases, and rate-surfactant profiles were quantitatively treated using a pseudophase model: Ks and micellar pseudo-first-order rate constant values (k MROH) increase ROH ROH as [HOCH2CH2OH]T increases. Values of k ROH are >1 (k NM NM /k M = nonmicellar pseudo-first-order rate constant) due to loss of intramolecular general base catalysis and of HOCH2CH2OH ROH content in the micellar pseudophase. At 30⬚C, 104k M = 7.95, ⫺1 ⫺1 ROH 12.6, and 20.6 s ; Ks = 6960, 2480, and 1740 M ; k ROH = NM /k M 6.1, 5.6, and 3.9 in 20%, 30%, and 40% (v/v), respectively.

467

Savelli et al.

Remarks ⫺

318

SDS

Psuedo-first-order rate constants for the alkaline hydrolysis of ionized N-phthalolglycine increase nearly 50% in 0.2 M SDS. The micellar reaction is supposed to occur in the GouyChapman layer or in its junctural region with the Stern layer, where [H2O]m ⬵ [H2O]w and [OH⫺]m ⬵ [OH⫺]w. The ratedetermining step of the micelle-mediated reaction involves the collapse of the ion-pair complex formed between the ionized substrate and Na⫹.

468

CTANO3 SDS

Addition of CTANO3 or SDS has a little inhibitory effect on the redox process of Ce(IV) with MeMA and EtMA, whereas CTANO3 significantly catalyzes and SDS retards to a larger extent the reaction of BzMA. Increasing amounts of CTANO3 decrease the induction period of the oscilalting Ce(IV) Belousov-Zhabotinsky reactions. In 0.05 M SDS induction periods are shortened for MeMA and EtMA: from 410 to 341 min and from 361 to 344 min, respectively, and oscillation occurs for BzMA, too (IP = 763 min). CTANO3 and SDS also affect oscillation period (␶) and duration of the raising portion of an oscillating circle (␶rais): ␶ and ␶rais increase for MeMA and EtMA but decrease fo BzMA as [CTANO3] increases. In 0.05 M SDS ␶ and ␶rais are shorter for MeMA and EtMA and longer for BzMA with respect to the value obtained in 0.05 M CTANO3.

310

CTABr SDS C12E7 Cu(DS)2 Zn(DS)2

The Diels-Alder reaction is retarded by micelles of CTABr, SDS, and C12E7. Apparent micellar second-order rate constants are slightly smaller than those in water. Diene is located in the micellar interior and inhibition occurs both when dienophile is electrostatically repelled and attracted by the micellar surface. In the second case inhibition is even more pronounced because of different locations of the micelle-bound reactants, and the reaction senses a waterlike environment. Micelles of Cu(DS)2 induce rate enhancements (up to 1.8 ⫻ 106 compared to the uncatalyzed reaction in acetonitrile), due to incorporation of the Lewis catalyst in the micellar environment and subsequent efficient complexation of the micelle-bound dienophile (k m2 = 5.9 ⫻ 10⫺6 M⫺1 s⫺1 and 3.1 ⫻ 10⫺5 M⫺1 s⫺1 for sulfonate and ammonium derivatives).

443

219

The alkaline hydrolysis is inhibited in SB3-16 aqueous micellar solution and kinetics are treated by means of an enzymatic model. At pH = 11.10, Ks = 6.63 ⫻ 103 M⫺1, kM = 4.8 ⫻ 10⫺4 s⫺1. Inhibition is stronger if Br⫺ or Cl⫺ is added, Br⫺ being more effective than Cl⫺. The dissociation constants of the inhibitor-micelle-like complex, KI, were calculated using a Br competitive inhibition model: K Cl I /K I = 4.0. Fluorescence quenching studies showed greater affinity of Br⫺ for the micellar surface: KSV = 1 and 40 M⫺1 for Cl⫺ and Br⫺, respectively.


SB3-16

220

TABLE 12 Reaction

Continued Surfactant

Remarks

Ref.

In the presence of hexanol, pentanol, butanol, and propanol both reactions are inhibited due to an increase of ␣. The ion exchange model fails in [NaOH] > 0.01 M. In these conditions the reaction is supposed to occur in the aqueous pseudophase.

469

SDS C12E23 Triton X-100

Both reduction reactions are catalyzed in the presence of the nonionic surfactants C12E23 and Triton X-100, whereas they are inhibited in SDS. The kinetic data were fitted by a multiple micellar pseudophase model based on the transition state psuedoequilibrium constant approach. It models the micelle as n pseudophases consisting of adjacent layers extending from the middle and ascribes micellar catalysis or inhibition to differences between binding constants or reagents (K PH mic) and transition states (K TS ). Best-fit parameters show that transition states are mic stabilized by nonionic micelles and destabilized by SDS, with TS respect to the peracids: K PH mic /K mic = 0.40, 0.37, and 69.9 for pernonanoic acid; 0.30, 0.25, and 38.4 for 3-chloroperbenzoic acid in C12E23, Triton X-100, and SDS, respectively.

241

MTABr MTACl CTABr CTACl

Overall first-order rate constants for the acid hydrolysis of the dioxolanes decrease as [surfactant] increases, reaction never being completely suppressed. Added NaCl at constant [CTACl] increases residual activity, and a Poisson-Boltzmann equation model predicts the downward curvature of plots of kobs against [NaCl]. The so calculated values of k m2 are smaller than kw: k m2 = 0.23, ⬃0.20, 0.19, and 0.30 M⫺1 s⫺1 for the R = C13H27 derivative in MTACl, MTABr, CTACl, and in 0.02 M CTACl ⫹ NaCl, respectively; 0.16 and 0.24 M⫺1 s⫺1 for the R = C15H31 derivative in CTACl and in 0.02 M CTACl ⫹ NaCl, respectively. The PBE approach also predicts that with no added salt kobs increases linearly with [surfactant] provided that reaction occurs wholly in the micellar psuedophase.

232

Savelli et al.

MTABr


aromatic nucleophilic substitution in water rather than that it is abnormally reactive in micelles. C.

Kinetic Salt Effects, Effects of Other Additives

For several reactions, values of km2/kW are similar in the presence and absence of an inert counterion [12,77]. But if we look not at the value of km2 but at that of kobs, addition of inert salts generally induces inhibition of reaction by changing the binding of reactive ions and the binding of the substrate (there is often linear experimental behavior for a KS vs. [NaX] plot; for instance, see Ref. 292). The salt effects are specific, and both electrostatic and specific interactions play a significant role; effects are larger for low-charge-density and hydrophobic ions [89]. This ion specificity has been the subject of a deep investigation in nonionic and zwitterionic micelles, where the use of perchlorate ions is possible (in cationic micelles perchlorate ion associates with the cation and a precipitate forms). Reactions of OH⫺ and F⫺ with pNPDPP [303] (Table 12) in micelles of nonionic dodecyl polyoxyethylene glycol ethers C12E10 and C12E23 are inhibited by inert anions, but the effects are small except for bulkier inorganic anions such as ClO⫺4 and also for organic ions such as naphthalene-2-sulfonate, ONs⫺, and tosylate, OTos⫺, that penetrate the palisade layer. The maximum value of the observed inhibition is a factor of ⬃0.3. The anion order for inhibition is ONs⫺ > ClO⫺4 > OTos⫺ > Br⫺ > SO2⫺ 4 , and this observed kinetic salt order is similar to that observed with ionic micelles [10,89]. On the other hand, addition of a cation, (C7H15)4N⫹, accelerates reaction of F⫺ by attracting the anion into the micelle. Addition of ClO⫺4 strongly inhibits reaction of Br⫺ with MeONs (Fig. 4), and this inhibition is effective even with NaBr in large excess over NaClO4 and is evident for various sulfobetaines [112]. Changes in the cation from Na⫹ to Cs⫹, (Me)4N⫹, (n-Bu)4N⫹, have little effect on the binding of Br⫺ and on reactivity, as is consistent with the relatively weak, unspecific interaction of cations with sulfobetaine micelles [110,117]. Also, addition of nonionic surfactants C10E4 or 1BuOH inhibits reaction of Br⫺ with MeONs in aqueous CTABr and CTEABr because they decrease the concentration of reactants at the micellar surface, but quantitative analysis shows that second-order rate constants at the micellar surface are very similar to those in the absence of additives [204,205,304] (Table 8). However, values of km2/kW sometimes change if a counterion is present. This is consistent with there be-

221

ing a small, but significant, effect, possibly due to shrinkage of the volume element of reaction owing to the presence of additional electrolyte in the solution [12]. Alternatively, one could assume that added electrolyte increases the micellar radius, and provided that the headgroup area is constant the potential at the micellar surface will also increase [36]. Therefore, more ions, reactive and inert, will be attracted by the micelle. Evidence for changes in the structure of headgroups and possibly of the micelles of SB3-14 on addition of NaClO4 has been given by an increase in 14N NMR line width [112]. The increase is initially steep, probably because the location of ClO⫺4 close to the quaternary ammonium center affects the environment and symmetry of the nitrogen, but there is thereafter a gradual increase in line width as the micelle become saturated with ClO⫺4 due to a change in micellar structure, consistent with an increase in the aggregation number, N, at high [SB3-14] and high [NaClO4] [112]. D.

Substrate Structure

Micellar rate effects critically depend on the interaction of the micelle with the substrate. Two aspects of substrate structure play an important role: substrate hydrophobicity and the nature of its polar substituents. 1. Hydrophobicity Association constants of nonionic solutes with aqueous micelles are sensitive to hydrophobicity (Section II.C), and there are a number of systems where apolar groups have been introduced with the aim of increasing association with micelles but also changing substrate locations and orientations in the interfacial region in order to induce chemo- or regioselectivity in product formation (as will be discussed further in Section VII). There are several examples of the variation of reactivity with substrate hydrophobicity in terms of observed rate effects. N-Alkyl-2-chloropyridinium ions have been extensively investigated (Scheme 13). Reactions with azide ion are enhanced by CTACl and CTABr, and rate enhancement increases markedly with substrate hydrophobicity, with values of kref (value of kobs relative to reaction of methyl derivative in water) going from ⬃100 for the methyl derivative up to

SCHEME 13

222

Savelli et al.

FIG. 4 First-order rate constants for reaction of MeONs with 0.5 M Br⫺ in SB3-14 with no NaClO4 (䡲), 0.005 M NaClO4 (●), 0.05 M NaClO4 (䊱). Solid lines are theoretical.

⬃15,000 for the n-hexadecyl derivative (Table 12) [218]. Reactions with alkylamines were also investigated, and CTACl, for example, slightly catalyzes (and for trimethylamine inhibits) reaction of the methyl derivative but accelerates greatly the reactions of the more hydrophobic derivatives (n-C10H21 and n-C14H29) [305]. Alkaline hydrolysis was accelerated by CTABr and SB3-16 for the long-chain derivative (n-C8H17 and n-C12H25), and there was also an effect on the regioselectivity (see Section VII) [306,307]. Effects of substrate hydrophobicity on diazo coupling reactions have also been investigated (Table 12) [308], and the acceleration by CTACl increased greatly with increasing hydrophobicity of the electrophiles, whereas for reaction in SDS the rate increased with hydrophobicity from the 4-methyl to the 4-hexyl ion but then started to decline with further increase to 4-decyl, 4-tetradecyl, and 4hexadecyl derivatives. Another kind of variation in hydrophobicity can be related to the second reagent. Al-Lohedan [309] examined reactions of a series of carboxylate ions, from formate to tetradecanoate, with 4-methylbenzenesulfonyl chloride in CTACl and in SDS (Scheme 14). Cationic micelles give greater acceleration with increasing hydrophobicity of the carboxylate, whereas micelles of SDS inhibit reaction of the substrate with hydrophilic carboxylate (formate and acetate), but with hydrophobic carboxylate values of kobs go to a minimum and then increase. Cavasino et al. [310] observed that different hydrophobicity of the substrates induces

different behavior in the micellar effects on cerium(IV) oxidation of substituted malonic acid derivatives and on oscillatory parameters of the Belousov-Zhabotinsky system with these substrates. Benzyl-substituted malonic acid exhibits a peculiar kinetic and oscillatory behavior that has been related to its greater hydrophobic nature as compared with methyl and ethylmalonic acids. Despite evident variations in kobs, quantitative analysis indicates that changes in substrate hydrophobicity do not introduce high specificity in micelle-mediated reactions, and rate constants in the micellar pseudophases do not change significantly. For instance, kM values for SN2 reactions of various nucleophiles with MeONs and with benzenesulfonate in various cationic micelles are very similar (Table 8) [289,290,293,296, 311] as are values of kM for deacylation of p-methyl and p-propyl- and o-propylbenzoates in various cationic micelles [286]. For bigger variations in substrate hydrophobicity, changes in kM are often within a factor of about 2 [312], and results with a series of derivatives

SCHEME 14


223

SCHEME 15

of MeONs with 6-alkyl substituents (alkyl = methyl, nhexyl and n-dodecyl, Scheme 15) also show that values of second-order rate constants in the micellar pseudophase are affected little by substrate hydrophobicity (Table 8) (L. Brinchi et al., J. Colloids Interface Sci., in press, 2000). A larger effect was observed in micellar effects on alkene brominations. Values of second-order rate constants of 1-alkenes depend on chain length, and the value of kM for 1-decene is lower by a factor of about 7 than the value for 1-hexene (Table 11) [313]. It seems that there is an optimum chain length, because rate constants increase going from 1-decene to 1-dodecene. The different reactivities are related to different locations of the double bond of the alkenes in the micelles. The longer the alkene chain, the deeper the location of the double bond in the micelle, with a deeper location meaning a less polar medium and a slower reaction. Changes in the structure of the alkene also change the product distribution, as will be seen in Section VII. 2. Polar Substituents Regarding polar substituents, we have already observed, when speaking about SNAr reactions by azide ions, that reaction is highly micelle catalyzed only for some of the substrates used. This effect has been related to the location of the substrates, as suggested by NMR experiments (Table 12) [301]. Broxton and Marcou continued these kinds of studies, selecting some nitroactivated halobenzoates with charged carboxylate substituents in ortho and para positions to locate the substrates at the micellar interface and more deeply in the micellar core [314]. The carboxylate moiety plays a role in orienting the substrate in that it prefers to protrude from the micelle into the more polar aqueous

pseudophase; on the other hand, nitro groups also affect location in that they prefer to be buried in the less polar region of micellar aggregates (Scheme 16). The SNAr reactions of aniline, which resides at the micellar surface, with compounds 1 and 2 (Scheme 16) are catalyzed by CTABr, whereas its reactions with compounds 3 and 4 are inhibited. Conversely, reactions of tertiary amines, which reside in the micellar interior, with more deeply buried substrates 3 and 4 were catalyzed more effectively than their reactions with substrates 1 and 2, residing at the micellar interface. Another kind of variation associated with polar substituents is related to their electronic effects. Al-Lohedan studied SN2 substitution of Cl⫺ and Br⫺ and with substituted alkylbenzenesulfonate [311] in CTACl, CTABr, CTAOMs, and CTA(SO4)0.5 (Table 8), and quantitative analysis showed a different effect of the nitro group in water and in micelles, with values of km2 /k W being higher by a factor of ⬃2–3 for the methyl derivative with respect to the nitro derivative. Wilk and Burczyk analyzed elimination from 2-phenylethyl derivatives in CTAOH (Table 9) [291] and found values of km2 /kW of 3.4, 2.0, and 1.1 for NO2, Cl, and H substituents. A more direct comparison was carried out by comparing elimination from 2-phenylethyl derivatives and the SN2 reaction of OH⫺ with methyl benzenesulfonates under the same set of experimental conditions and with the same quantitative treatments (Tables 8 and 9, Scheme 17) [293]. It is clear that introduction of a nitro group has a significant effect on relative reactivities in water and micelles, which is related to the extent of charge dispersion in formation of the transition state. For the SN2 reactions of methyl benzenesulfonates the inductive effect of the nitro group increases reactivity by a factor

SCHEME 16

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SCHEME 17

of ⬃4 in water and ⬃8 in CTAOH. However, there is a strong resonance interaction of the nitro group in the E2 reactions of phenylethyl derivatives, and rate increases by the nitro group are 67-fold in water and ⬃400-fold in CTAOH. In other words, micelles favor reactions with the most charge dispersion, even though they have the same molecularity and charge type. More detailed analyses of substituent effects on reactions in micelles have been carried out by using the Hammett equation. An example of these analyses has already been mentioned in Section IV regarding E1cb reactions. For bimolecular reactions, values of ␳ for reactions of aryl benzoates with OH⫺ [286] (Scheme 18), for example, are higher in cationic micelles of CTABr than in water, showing that the micellar interfacial region is less polar than water. Reactions of methyl p-substituted benzenesulfonates with OH⫺, Br⫺, and H2O in water and micelles, have also been studied (L. Brinchi et al., Eur. J. Org. Chem., in press, 2000). The analysis yielded values of ␳ over a range of conditions and nucleophiles (Scheme 19). Values of ␳ show that SN2 reactions of the methyl benzenesulfonates (for which ␳ = 1.13, 0.94, and 1.00 in water for reaction with water, hydroxide, and bromide, respectively, and 1.41, 1.41, 1.58 in micelles of CTAOMs, CTAOH, CTABr) are less sensitive to electronic effects than saponification of phenyl benzoates, for which ␳ = 1.76 in water and 2.6 in CTABr [286]. These differences are understandable in view of differences in relative locations of reaction centers and substituents in the two sets of reactions, which facilitate transmission of electronic effects in reactions of the phenyl benzoates. Attack of OH⫺ on phenyl benzoates involves rate-limiting addition to the acyl group, which

is accelerated by electron-withdrawing substituents, but in SN2 reactions we have to consider both nucleophilic attack and loss of the leaving sulfonate ion. Comparisons of second-order rate constants in water and micelles depend on parameters whose values are uncertain, e.g., those that describe interionic competition and the volume of the interfacial reaction region. We therefore have to be cautious in using kinetic data for the overall reaction to compare medium properties of water and micellar interfacial regions, because in some conditions kinetic fits are indeterminate for reactions of weakly interacting ions, e.g., OH⫺ in the presence of strongly interacting ions. However, comparison of values of ␳ eliminates some of these uncertainties. E.

Surfactant Structure

Last but not least, an important factor that affects the micellar rate effect is the structure of the surfactant, as already discussed in Section IV. Regarding bimolecular reactions, few researchers studied systematic variations in surfactant structure if we exclude the change in counterion, already examined. Concerning the systematic variation in the alkyl chain length of cationic surfactants Bacaloglu et al. examined the reaction of MeONs with Cl⫺ in a series of alkyltrimethylammonium chlorides (Table 8) [298]. Values of kobs increase with the length of the alkyl chain, and the effect has been rationalized by quantitative analysis. In fact, the experimental association constant of Cl⫺ increases with alkyl chain length, but the value of km2 also increases in going from octyl surfactant (for which the value is approximately equal to that in water) to octadecyl surfactant, for which this

SCHEME 18


SCHEME 19

value is higher by a factor of ⬃3. The effect on secondorder reaction rates in the micellar pseudophase has been related to partial disruption of the hydration shell of the nucleophile, as supported by a parallel increase in 35Cl NMR line width. Introduction of a covalently bound anionic charge to the cationic group, i.e., formation of a zwitterionic surfactant, does not suppress bimolecular reactions. Despite the absence of overall charge, micelles of zwitterionic surfactants can interact favorably with ions (see Section II), and this interaction induces high ionic discrimination. For instance, zwitterionic sulfobetaine micelles [315,316] and zwitterionic amine oxide surfactants (AOMe-14) [317] speed SN2 reaction of soft ions with MeONs, and decrease, but do not suppress, reaction of even such hydrophilic and weakly associated anions as OH⫺ and SO2⫺ 3 . In SB3-16 surfactants the relative reactivity of bromide and hydroxide is dif-

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ferent from that in water, with kM(Br) > kM(OH) [315] (Fig. 5). Moreover, zwitterionic micelles were found to speed reaction of hydrophilic ions such as OH⫺ and also F⫺ in reactions with pNPDPP [315], to speed alkaline hydrolysis of N-decyl- and N-dodecyl-4-cyanopyridinium [318], and to speed E2 reaction from 4-nitrophenethyl bromide [319]. A particular effect on reactivity is related to headgroup bulk of cationic and also zwitterionic surfactants. For reactions of MeONs with Br⫺ and Cl⫺, the observed constants increase with increasing headgroup bulk, whereas a decrease for reaction of OH⫺ with the same substrate is observed [289,296]. The binding constants of all counterions to micelles decrease with increasing headgroup bulk, as experimentally determined by various kinds of techniques [86,296–298], and that accounts for the decreased rate constants observed for reaction with OH⫺. Quantitative analysis shows that values of kM change little with surfactant for reaction of OH⫺ [289] but increase with increasing headgroup bulk size, modestly for reaction of Cl⫺ and more strongly for reaction of Br⫺ [296–298], so that kM (Br) > kM (OH) for reactions in CTPAX and CTBAX, as in sulfobetaine SB3-16 and SBBu3-14 surfactants [315, 316]. Therefore, micelles generate an inversion of the reactivity sequence for anionic nucleophiles reacting

FIG. 5 Corrected rate constants for reactions of MeONs with anions in SB3-16; broken line represents reaction with water. For reaction with OH⫺, Cl⫺, Br⫺, and H2O, n = 5; for reaction of SO2⫺ 3 , n = 4.

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with a common substrate. There are clear differences between the behavior in cationic micelles of a very strongly hydrophilic anion, OH⫺, a moderately hydrophilic ion, Cl⫺, and a weakly hydrophilic ion, Br⫺. The effects are probably due to differences in the hydration shell of the ions. Hydroxide ion interacts so strongly with water that its hydration should be little perturbed by cationic micelles, regardless of the headgroup, but hydration of Br⫺ and Cl⫺ is decreased when they interact with the micellar surface, with consequent increase in their nucleophilicity. The increase in ion discrimination with increasing surfactant headgroup bulk is also observed in the increased electrophilic assistance to the leaving anion in intramolecular cyclization (Table 6) [261] of o-(3-halopropyloxy)phenoxide ion (halogen = I, Br), with values of kM(I) /kM(Br) going from 1.3 in CTABr to 2.5 in CTBABr, and also in elimination from 1,2-dihalo-1,2diphenylethanes (halogen = Br, Cl), with values of kM(Br) /kM(Cl) going from ⬃27 in CTAOH to ⬃31 in CTPAOH (Table 9) [300]. The generalizations about the relation between reaction mechanism (in particular the softness of the transition relative to the initial state) and micellar kinetic effect can be extended to consideration of the role of headgroup bulk. For SN2 reactions of OH⫺ with benzenesulfonate and MeONs, an increase in headgroup bulk slightly decreases kM , but it slightly increases kM for the reaction of methyl 4-nitrobenzenesulfonate. The headgroup effect is considerably larger for E2 than for SN2 reactions of OH⫺, where values of kM in CTPAOH are larger than in CTAOH by factors >2. The situation is similar for increase in headgroup bulk in sulfobetaine surfactants; i.e., for eliminations from the same substrates, values of kM in SBBu3-14 are larger than in SB3-14 by factors >2 [319] (Table 9). The conclusion that an increase in headgroup bulk favors reactions in which charge is dispersed in the transition state is consistent with observations on reactions of OH⫺ with phenyl p-substituted benzoates, where there is a clear relation between kinetic headgroup and electronic substituent effects (Table 10) as the headgroup is changed from NMe3 to N(n-Pr)3 and N(n-Bu)3. Generally speaking, an increased dispersion of charge leads to higher values of kM(CTPAOH) /kM(CTAOH). Although second-order rate constants of reactions of ions with nonionic substrates are often similar in the aqueous and micellar pseudophases, relations between substrate structure and reaction mechanism and relative rate constants in aqueous and micellar pseudophases show that dispersion of negative charge in the transition state leads to higher rate constants in micelles, espe-

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cially those with bulky headgroups. This relation between effects of bulk of the headgroup and charge dispersion, or ‘‘softness’’ of the transition state, seems to be general. It is evident in unimolecular decarboxylations and dephosphorylations and intramolecular cyclization, where kinetic analysis does not involve the transfer equilibrium of a second reactant.

VI.

REACTIONS IN NONMICELLAR AGGREGATES

A.

Vesicles

Closed bilayer vesicles formed by phospholipids were first described by Bangham and Horne [320] and are intensely explored structures. The work of Kunitake et al. showing that the synthetic surfactant dioctadecyldimethylammonium bromide, DODABr, forms vesicles marked the beginning of membrane mimetic chemistry [321]. This pioneering finding was soon followed by the description of vesicles prepared with a simple phosphate diester (sodium dihexadecyl phosphate, SDHP) [322]. Liposomes are vesicles made of phospholipids, and the assemblies formed from synthetic surfactants have been described as surfactant vesicles [9]. New vesicles have been prepared from a variety of surfactants, including single-chain surfactants [323, 324], synthetic glycolipids [325], and nonionic surfactants (referred to as niosomes) such as hexadecyldiglycerol ether, sorbitan monostearate [326], and sugar esters [327]. Mixtures of single-chain cationic and anionic micelles, referred to as catanionic systems, able to form vesicular systems are currently a subject of intensive investigation [328]. Surfactants used are often commercial ones, such as CTABr and SDS; vesicles are formed in coexistence with mixed micelles; and phase diagrams are currently under investigation [329,330], as are the morphologies of the aggregates [331]. A microscopic model for such mixed surfactant vesicles has been proposed [332]. Large vesicular systems, referred to as giant vesicles, have received great attention because of their large size. One of the simplest giant vesicles was produced simply by dispersing oleic acid in water at pH 8.5 [333]. This resulted in an oleic acid–oleate giant vesicle having a diameter of about 70 ␮m with a total of 1011 oleic acid–oleate molecules. They are particularly attractive to investigate because their formation and the behavior of one single supramolecular entity can be observed by light microscopy. The size of giant vesicles is typically in the range 10–100 ␮m, corresponding to an amphiphile aggregation number of typ-


ically 8 ⫻ 108 –8 ⫻ 1010 per vesicle. The concept of self-reproduction has also been extented to giant vesicles [334]. An up-to-date review of this subject is the volume prepared as the proceedings of the Workshop ‘‘Giant Vesicles,’’ which was held in Ascona, Switzerland, in 1998 [335]. Earlier work on giant vesicles by Ringsdorf et al. [336] and the current work of Menger and coworkers [337–339] on a variety of chemical and biochemical aspects of giant vesicles have been reviewed. Furthermore, much is known today about the physicochemical properties of giant vesicles and biomembranes thanks to the studies of Sackmann and coworkers [340]. The systems most investigated are vesicles formed by surfactants that have two n-alkyl groups. An excellent review on DODACl and SDHP vesicles by Carmona-Ribeiro [341] focuses attention on physicochemical characteristics of the systems, on analogies with and differences from phospholipid systems, and on their practical use. A wide range of applications take advantage of these systems, and some of them are briefly outlined in Section VII. Vesicles are single or multicompartment closed bilayer assemblies, and life without an inside-outside separation is unimaginable. The compartmentalization in vesicular media makes these systems quite interesting as membrane models. Here we focus attention on the properties of twin-chain surfactant vesicles as reaction media and on efforts to model the vesicular rate effects, taking into account the various reaction environments provided by vesicles. Vesicles prepared with synthetic amphiphiles constitute useful microreactors where reaction rates can be finely controlled. DODABr and SDHP salts are sparingly soluble; vesicles are formed from dispersions of these salts by bath or tip sonication or by chloroform evaporation [342,343]. The structure of vesicles formed from a given surfactant depends on the preparation method. The first method yields multilamellar vesicles, the second gives small unilamellar vesicles (SUVs) and/or bilayer fragments, and the third gives large unilamellar vesicles (LUVs) [341]. Usually, vesicles obtained by sonication are not stable; they fuse and separation of phases occurs, and the ease of fusion depends on vesicular charge and the extent to which it is neutralized by added electrolyte. In contrast, vesicles prepared by chloroform evaporation are apparently stable for days [343]. Vesicles are multicompartmentalized microreactors capable of concentrating reactants or maintaining reactants separated in solution. They are permeable to apolar nonionic solutes and, if ionic, can bind counterions at the inner and outer surfaces; therefore, vesicles

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can catalyze reactions by significant factors. Counterion binding is also a crucial point in vesicles as in micelles. They play a major role in defining the permeability of vesicles formed by twin-chain cationic or anionic surfactants [344]. Carmona-Ribeiro and coworkers have investigated [345] the effect of the counterion in DODAX vesicles (X = Cl, Br, acetate). Vesicles with acetate as the counterion, i.e., the largest and the most hydrated, have the smallest size and the largest zeta potential. The phase equilibria of didodecyldimethylammonium surfactants have been shown to be sensitive to the counterion [346]. A multitechnique approach [347] used to study the aggregate structures showed that with OH⫺ and acetate as counterions, vesicles coexist with normal micelles within certain concentration ranges, above which micelles are the only stable aggregates. Quantitative analysis of vesicle-modified reaction rates, made possible by using models initially developed for analyzing micellar rate effects, allows dissection of factors leading to catalysis or inhibition. It has been used extensively in analysis of the kinetic effect with surfactants such as didodecyldimethylammonium hydroxide and chloride in the region of their spontaneous solubility in water. Probably only micelles exist under these conditions, and they have been treated in Sections IV and V. Mechanistic studies of organic reactivities in vesicles have focused on two questions: the application of the pseudophase model to reactions in vesicles and the reactions at the inner and outer vesicular surfaces. The complexity of vesicular systems offers multiple applications for reaction control. The rates of vesicle-modified bimolecular reactions were first quantitatively analyzed using a pseudophase model with explicit consideration of ion exchange [348,349], with the models derived for micellar solutions. Quantitative analysis, using PIE, suggests that the rate enhancement is due primarily to reagent concentration in the dimensionally restricted environment provided by the vesicle, coupled with contributions from enhanced dissociation and reactivity of the nucleophile at the vesicle surface [350]. One of the conditions for the application of PIE models is the exchange of ions at the interface. Direct evidence for exchange and determination of selectivity constants for ion binding have been obtained directly by fluorescence quenching methods [351]. The fluorescence of 1-pyrenenonanoic acid (1-Py), incorporated in large vesicles of DODACl and DODABr, is quenched by iodide addition [352]. The selectivity constants for I⫺/Br⫺ exchange (KI/Br ,) at the outer and inner surfaces are 8

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and 7, respectively. The average value of KI/Cl at both interfaces is 31 ⫾ 5. An exchange constant of ⬃4 for the Br⫺/Cl⫺ exchange was calculated from the experimentally determined selectivity coefficients for exchange of halides with I⫺. The value of KBr/Cl obtained for the exchange at the surface of DODACl vesicles is very similar to data obtained with positively charged micelles of comparable headgroup, i.e., cetyltrimethylammonium (CTA) halide [196]. Quantitative analysis of vesicle rate effects using models developed for micellar rate effects permits dissection of factors leading to catalysis or inhibition, but use of a single rate constant to represent reactivity in the vesicle ignores the fact that a solution containing vesicles has, in principle, several potential reaction sites, and no a priori theory predicts that reactivity at all the sites is equal or comparable. In a solution containing vesicles one can distinguish at least five reaction sites: (1) the inner compartment, (2) the internal interface, (3) the hydrophobic bilayer itself, (4) the external interface and (5) the aqueous phase [353] (Fig. 6). With the purpose of site dissection, Chaimovich and Cuccovia prepared vesicles of various sizes, determined some of their physical properties, and developed theoretical and experimental tools for probing vesicular sites [354]. Small unilamellar vesicles (SUVs, hydrodynamic diameter, Dh < 50 nm) are not adequate for the purpose of site dissection because they do not permit the entrapment of analytically convenient amounts of substrate. Larger unimolecular vesicles (LUVs) of DODACl and SDHP (Dh > 300 nm) were obtained by chloroform vaporization at 70⬚C [355]. Several vesicular properties are size sensitive. In particular, the decrease in ␣ with size is probably related to decreasing headgroup area and the increasing counterion association needed to relax the surface electrostatic potential [356]. The kinetic effects of vesicles in reaction rates are sensitive to the structural consequences of size variation. Even small differences in bilayer packing, with no changes in medium or aggregate composition, modulate the rates of chemical reactions occurring at vesicular interfaces. The rate-[surfactant] dependence obtained by studying the effect of small and large DODACl vesicles on the thiolysis (heptyl mercaptan) of esters (p-nitrophenyl octanoate) are quite different [357]. Smaller vesicles are two- to fivefold more efficient as reaction catalysts. The analysis with fit of the PIE model demonstrated that the size-dependent differences in kinetic efficiencies are attributable to differences in ion dissociation, substrate binding constants, and small changes in nucleophilic reactivity

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FIG. 6 Potential reaction sites in a vesicle: 1, inner compartment; 2, inner interface; 3, membrane; 4, outer interface; 5, intervesicle compartment.

related to different packing of amphiphile in the bilayer of vesicles of different sizes [357]. Reactions at the inner aqueous compartment of unilamellar vesicles were investigated using water-soluble probes reacting with hydrophilic ions. The reaction probe chosen by Cuccovia and Chaimovich [358] to study the inner aqueous compartment of DODAX vesicles is the alkaline hydrolysis of N-methyl-4-cyanopyridinium ion (MCP). Reactivity of substrate in the large internal aqueous compartment is identical to that in free solution, and results indicate that slow OH⫺ diffusion through the membrane is responsible for the difference observed in the rate of MCP hydrolysis in the outer and inner aqueous compartments. Other experimental data demonstrating slow OH⫺ permeation have been reported [359]. In a solution containing vesicles, ions can reside in the continuous solution around the vesicles or in the internal aqueous compartment. The PBE equation was solved numerically assuming water- and ion-permeable hollow spheres and by treating specific ion adsorption using a Volmer isotherm [360]. The calculations suggest that the distribution of ions in the internal aqueous core of DODAX vesicles is measurable and that the value of the electrical potential at the vesicle center is not negligible at moderately low salt concentration. The PBE calculations showing appreciable concentrations of counterions in the inner aqueous compartment of the vesicle are consistent with results showing that the reactivity of OH⫺ in DODACl is comparable in the inner and outer compartments. Direct measurement of ion concentrations in the internal aqueous core of synthetic amphiphile vesicles has been performed using the dediazoniation method first described by Romsted (Section II). It can also be applied to the determination of Cl⫺ in the aqueous compartment of DODACl vesicles [354], and preliminary data suggest that the internal chloride ion concentration is consistent with calculations of ion distribution with the PBE equation.


Reactivity at the vesicular interfaces has been probed with substrates that bind and/or react preferentially in the inner or outer surfaces. The negatively charged 5,5⬘-dithiobis-(2-nitrobenzoic acid), DTNB, and OH⫺ bind to the positive surfaces of DODABr [361]. DTNB was selectively incorporated in the inner and/or outer surfaces of positively charged DODABr vesicles in order to probe reactivity with OH⫺ at both surfaces. Results show that the reactivity of OH⫺ at both surfaces is identical, and the reaction rate at the external surface can be modulated by changing the nature of the added salt. Addition of NaBr at the external aqueous compartment of DODABr vesicles in the presence of NaOH changes the ratio kout /kin, indicating that the externally bound OH⫺ and DTNB are exchanged by Br⫺. These results, exemplifying selective reaction site control by surface composition, nicely demonstrate that differential ion binding at the surface can promote rate modulation of compartmentalized substrates. This in/out selectivity can be magnified in asymmetric vesicles, where the composition of the external leaflet is different from that in the internal interface [362–364]. In fact, natural selection has provided cells with a variety of bilayer bordered compartments with asymmetric distribution of lipids between inner and outer leaflets. B.

Premicelles

Very dilute amphiphiles do not significantly affect rates of many reactions, but with increasing concentration micelles form and rate or equilibrium constants change. Micellization occurs at the critical micelle concentration (cmc), which in some systems marks the onset of the rate increase, but rates often increase below the cmc, either because reactants induce micellization or because other species, so-called premicelles, are kinetically effective. As a result, a ‘‘kinetic’’ cmc is often used empirically in fitting rate-surfactant profiles, and Buckingham et al. noted physical evidence for the possible existence of premicelles [365]. The term ‘‘premicelles’’ seems to be applied to submicellar assemblies that form spontaneously or are generated by interactions with reactants. In the latter case it is not easy to distinguish between reactant-induced micellization and formation of premicelles [366]. Although the pseudophase model in its simplest form predicts that rate constants will increase only at the onset of micellization, they often increase monotonically well below the cmc, which could be ascribed to reactant-induced miscellization or to interactions with premicelles. For example, values of kobs for reactions of hydrophobic substrates

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with small inorganic ions typically increase at [surfactant] < cmc and increase to maxima as predicted by pseudophase treatments. Similar behavior is often seen with micelle-mediated reactions of multivalent inorganic complexes and may be ascribed to interactions with premicelles [367]. Drennan et al. give a critical analysis of formation of complexes of Ni(II) in dilute sodium dodecyl sulfate where rate constants increase at surfactant concentrations below the cmc in water and show that it is not necessary to invoke the intervention of premicelles [366]. Micellization induced by interactions with multivalent inorganic ions is a common phenomenon in inorganic reactions. Nonmicellar assemblies can influence reaction rates. Hydrophobic ammonium ions, which do not micellize, often increase reactivities, although generally concentrations are too low to allow physical identification of the assemblies [368–372]. In a few reactions in surfactants that generate micelles, there are extrema in plots of rate constants against [surfactant] at concentrations near or below the cmc [264,373–375]. These extrema cannot be ascribed to reactant-induced micellization, which gives monotonic changes in observed rate constants. It is easiest to identify this kinetic behavior in spontaneous, unimolecular reactions where only one species is partitioned between water and micelles or other assemblies. For example, in bimolecular ionic reactions one has to consider electrolyte effects on the cmc and competition between reactive and inert ions for the association colloids. The expected kinetic form is observed for many spontaneous reactions, although kobs often increases at surfactant concentrations below the cmc, and occasionally values of kobs increase sharply with [surfactant] < cmc but then decrease and follow Eq. (2) at higher concentrations [264,373]. This anomalous behavior has been observed in two spontaneous reactions. The first is decarboxylation of 6-NBIC in a solution of DDDACl [264] and the second is cyclization of o-(␻-haloalkoxy)phenoxide with a long-chain alkyl tether in solutions of cationic surfactants CTABr and CTBABr and also of gemini surfactants (CDA)2C42Br [373]. It has been speculated that these ‘‘premicellar’’ rate effects on cyclization require a hydrophobic interaction between substrate and, at most, a limited number of surfactant monomers. Alkoxy derivatives of 6-NBIC with groups of various lengths have been recently studied [280]; see also Section IV and Table 5. Introduction of a methoxy substituent decreases rate constants of reactions of fully bound substrates in micelles, as predicted [255], and surfactant effects are similar to those for the unsubstituted derivative [264]

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except that micellar rate enhancements are lower. However, the behavior of the tetradecyloxy derivative is strikingly different. Values of kobs are much higher than expected from the behavior of the methoxy derivative in dilute surfactant at concentrations well below the cmc and then decrease and become consistent with predictions. The surfactant concentrations at the rate maxima are in the sequence CTABr ⬇ CTEABr > CTPABr > CTBABr. Values of kobs increase so steeply in dilute

Savelli et al.

CTPABr and CTBABr that only the descending part of the plots can be observed because of very low solubilities. The rate maxima in CTABr and CTEABr are at [surfactant] values that yield data for both the ascending and descending parts of the plots (Fig. 7). Rate constants increase as substrate is transferred from water into surfactant-derived assemblies and then decrease to approximately constant values as substrate becomes micelle bound; i.e., the rate maxima demon-

FIG. 7 (a) Decarboxylation of tetradecyloxy derivative of 6-NBIC in CTABr (䡲) and CTEABr (䊱) and (b) in CTPABr (䊲) and CTBABr (●). The lines are drawn to guide the eye, and rate constants in water are very close to zero.


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strate the existence of three distinct reaction environments, depending on [surfactant]. The situation is similar to that for detection of premicelles by fluorescence spectra where the spectra are characteristic of aqueous, premicellar, and micellar environments [376]. The rate maxima cannot be ascribed to reactant-induced micellization. Once micelles form, they dissolve premicellar species, the substrate becomes micelle bound, and kobs decreases toward the value of k⬘M. The headgroup bulk influences the rate extrema: intervention of premicelles is most evident with CTBABr, and the initial increase of kobs is seen in very dilute surfactant (1.5 ⫻ 10⫺4 M). It is not possible to know the stoichiometry of the effective species in reactions in premicelles. The apparent maxima are obtained with approximately a 3fold excess of CTABr and CTEABr, a 2-fold excess of CTPABr, and less than a 1.5-fold excess of CTBABr. The authors suggest a simple assumption—1:1 pairs are the active species—and in that event we could regard them as tight ion pairs held together by Coulombic forces and hydrophobic interactions of the long alkyl groups. Actually, small assemblies of substrate and hydrophobic quaternary ammonium ions can have a variety of conformations. For example, effects of submicellar cationic surfactants on the fluorescence spectrum of 2-p-toluidino-naphthalene-6-sulfonate were interpreted by assuming that long n-alkyl groups of the surfactant wrap around the organic moiety of the probe [376]. However, this conformation does not explain the premicellar rate increases, which require the hydrophobic quaternary ammonium ion to shield the carboxylate residue of long-chain substrate from water. Exclusion of water from the heterocyclic moiety would disfavor decarboxylation because, in the transition state, charge moves into this region with formation of a phenoxide ion [255]. Benzisoxazole carboxylate ions probably bind to micelles with the aryl residue insert-

ing toward the apolar region, which leaves the carboxylate moiety adjacent to headgroups in the interfacial region. The rate increases in premicelles require association of the substrate with at most a few surfactant ions (Scheme 20). This association can be ascribed to the hydrophobic interactions of the long alkyl groups, but the rate increases require interactions to stabilize the transition relative to the initial state. If interactions in premicelles are similar to those in micelles, reactions should not be faster in the former. It is then necessary to assume that in premicelles the carboxylate ion is shielded from water, and in the transition state charge dispersion is favored by interaction with the quaternary ammonium ion (Scheme 20). Derivatives of dianionic DNPP2⫺ bearing a methoxy or the long-chain tetradecyloxy substituent in position 5 have also been investigated (M. Tugliani et al., Langmuir, in press, 2000); see also Section IV and Table 5. As already observed for reactions of DNPP2⫺, reaction rate constants for the methoxy derivative increase with [surfactant] and reach constant values characteristic of complete substrate association. When the headgroup bulk of the surfactant is increased, rate constants increase sharply on initial addition of cationic surfactant. Rate-surfactant profiles are characteristic of micelle-assisted reactions, and kinetic data fit the predicted behavior, based on Eq. (2). The introduction of a long alkyl chain in the substrate leads to complex variations of kobs with [surfactant], as already observed in decarboxylations. Here values of rate constants go through a maximum at very dilute [surfactant] (in the range 8 ⫼ 10 ⫻ 10⫺5 M surfactant, well below the cmc), then through a minimum (at least when big head surfactants are present), and then they seem to reach a limiting constant value. Small clusters form in dilute surfactants with an average of four surfactant molecules per substrate mole-

SCHEME 20

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cule, and they are catalytically more effective than normal micelles because the relative free energy of activation is lower. Also for dephosphorylation nonmicellizing trioctylammonium salts speed hydrolysis [372,377]. Attempts to measure rate constants below 8 ⫻ 10⫺5 M failed because of solubility problems of substrate and/or products, probably related to ion pairing; therefore, even higher maxima could be possible at more dilute surfactant, especially with big-headgroup surfactants. Rate maxima seem not to be sensitive to headgroup bulk, and we have only a slight increase in kobs in going from CTABr to CTBABr. VII.

APPLICATIONS OF SURFACTANTS

Self-organized systems composed of amphiphilic molecules have particular features that make them attractive, not only as relates to chemical reactivity aspects but also for a large variety of applications. For instance, surfactants have been used for extraction of metal ions [378]. Surfactant-based processes have attracted much attention in the past few years and it is now well established that metal ions can be removed by taking advantage of the association of the metal ion itself [379] or of the extractant/metal with the micellar entities. The removal of metal ions at low concentration can be performed in that way using ultrafiltration membranes with pore diameters smaller than the size of the particles. Such extraction processes operate in the absence of organic solvent and in 99% aqueous solution. Extraction processes using micellar particles as the extracting phase are currently under investigation in many places because of their potential in helping to solve specific environmental problems. These processes can completely avoid or at least considerably reduce the use of organic solvents. Not only undesirable metal ions but also, for instance, dyes [380] and organic pollutants can be removed [381]. Another field of possible development of the preceding processes is that of enantiomeric separations. There have been attempts to use chiral surfactants in order to perform selective transport of enantiomers [382–384]. Considering also chromatographic methods, for example, Camilleri et al. have investigated the use of anionic surfactants, which when used above their cmc in micellar electrokinetic capillary chromatography (MECC) allow the resolution of a number of structurally unrelated racemic mixtures [385–387]. The formation of noncovalent ‘‘diasteroisomers’’ between the micelles and the enantiomers leads to chiral discrimination if the energies of formation of these transient species differ sufficiently. Subsequently [388], they

showed that the chiral separation efficiency of D-glucopyranoside anionic surfactants depends strongly on the orientation of the C14 hydrocarbon chain at the anomeric carbon center. Moreover, the possibility of using micellar particles for the transport of different solutes across liquid membranes has been investigated in the past 15 years [382,389–393]. The application of surfactant-based systems as drug delivery vehicles [394,395] is a growing research area that may develop further in the coming years. It is quite interesting that cationic amphiphiles are now widely used as an effective tool in delivering DNA into cells [396,397] even mammalian cells [398–402]. An investigation by Engberts and colleagues [403] yielded the conclusion that although membrane fusion may play a key role in DNA packaging, amphiphile/DNA complex formation [404] is probably a translocation via a ‘‘perturbed target membrane’’ mechanism, rather than by fusion, may be the mechanism by which nucleic acids are introduced into the cells. Mention should also be made of microemulsions incorporating fluorocarbons, which have specific potential for oxygen transport [405]. Bilayer-forming synthetic surfactants have been extensively used as membrane mimetic models, and some synthetic amphiphiles such as dihexadecyl phosphate or dioctadecyldimethylammonium salts have found many different uses in strategic applied areas [341]. In particular, synthetic cationic liposomes have been successfully employed to interact with negatively charged surfaces or biomolecules such as prokaryotic [406– 408] or eukaryotic cells [409], antigenic proteins [410], nucleic acid [411,412], synthetic polymers and latex [413–416], and mineral surfaces [417–420]. In the following discussion, we focus our attention on chemical reactivity. Aqueous association colloids as reaction media offer alternatives to the use of organic solvents, and there is considerable interest in their use in water as a reaction medium; they are attractive candidates in ‘‘green’’ chemistry [19,21,22,421,422]. For instance, Moss et al. [423,424] observed 1000- to 2000-fold rate enhancements in overall rate constants of hydrolyses of phosphate triesters catalyzed by different iodosocarboxylate ions of varying hydrophobicities in comicelles with CTACl and CTAOH. Here, product isolation is unimportant, but the solubilizing properties of micelles and their minimal toxicity compared with organic solvents make them useful as media for detoxification and organic synthesis. In the latter application, however, the amphiphile must be removed when the reaction is complete. In this case, as is often the case, studies of micellar effects on rates or products of organic reactions


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have been made with very low concentrations of reactants, and this small scale is not very useful to the synthetic organic chemist. An additional disadvantage is that surfactants complicate product separation by extraction or distillation, and to date most studies in this general area have been exploratory and aimed at solving these problems. Jaeger and coworkers have developed a more general approach based on the synthesis of chemically labile surfactants [425–427]. Surfactant-based reaction media have such kinds of features that make them useful in industrial-scale synthesis and interesting in developing ‘‘clean’’ processes. In fact, they are expected to be nontoxic and nonhazardous, they enhance reaction rates, reactions can usually be carried out under mild conditions, and in favorable cases surfactants can be separated and reused. Mashraqui et al. used micelles of CTABr as benign, economical, and mild reaction systems to afford chalcones [428] in high yield by an aldol reaction under weakly alkaline conditions and to prepare a variety of organic sulfides [429]. In both cases a preparative scale was used. Kobayashi et al. [430] demonstrated the utility of SDS in providing a hydrophobic micellar medium to perform Ln(OTf)3- or Cu(OTf)2-catalyzed Mannich-type reactions of aldehydes, amines, and silyl enolates to prepare ␤-amino ketones or esters in high yield without any side reaction adduct (Scheme 21). They also carried out successfully three-component Mannich-type reactions of aldehydes, amines, and silyl enolates in water in the presence of dodecylbenzenesulfonic acid as a Brønsted acid–surfactant catalyst [431]. Other Mannich-type reactions in aqueous surfactant-rich media involved HBF4-catalyzed condensation of aldehydes, amines, and silyl enolates for the synthesis of ␤-amino carbonyl compounds [432]. Kobayashi et al. also found that lanthanide triflates catalyze aldol reaction of silyl enolates with aldehydes with the aid of SDS [433,434] and also developed threecomponent coupling reactions of aldehydes, amines, and allyltributyltin in micellar systems [435]. The strategy of multiple assembly within micelles was even applied for the synthesis of porphyrins [436]. Micelles were viewed as potential wells able to bind products more tightly than reactants in catalyzing condensation

reactions. Various functionalized porphyrins, difficult to make by direct aldehyde-pyrrole condensation in various organic solvents with micelle-like polarity, were conveniently prepared from the corresponding aldehydes in aqueous sodium dodecyl sulfate, with micelles directing the course of the synthesis. Rathman et al. [437,438] have developed so-called micellar phase transfer catalysis: addition of a phase transfer catalyst (tetrabutylammonium bromide) to surfactant systems results in a remarkable synergism, applied to the Williamson synthesis of phenyl butyl ether. The system provides higher reaction rates and conversions than observed in conventional micellar systems, and it is also successful at high reactant loading (>50 wt%) that exceeds the solubilization capacity of micellar solutions. Moreover, reagent organization in and different microenvironments provided by aqueous micelles open the possibility of controlling product formation, providing chemo-, regio-, or stereoselectivity [9,31]. There are a number of examples of this type in the literature, and they are often easily explained in terms of the generally accepted model of kinetic micellar effects. Often the micelle-mediated specificity may be simply a polarity effect. Under given conditions, cationic micelles favor E2 over SN2 (and SN1) reactions. It has been shown that the reaction of phenethylnaphthalene-2-sulfonate in water gives 100% phenethylalcohol, whereas reaction in CTAOH gives 37% styrene and only 63% alcohol [439]. This preference is rationalized on the basis of previous kinetic studies [293], and it is related to a higher second-order rate constant at micellar surfaces than in water for elimination as compared with substitution. Politi and Chaimovich [307] studied the reaction of N-alkyl-4-cyanopyridinium ions (alkyl = Me, n-Bu, n-octyl, n-dodecyl) with hydroxide ion. Ratios of the reaction products, N-alkyl-4-pyridone and N-alkyl-4-carboxamidopyridinium, are shifted in favor of the pyridone in CTABr and SB3-12 for the longchain substrates, whereas the product distribution is not sensitive to the presence of SDS. The regiochemical preference for pyridone is rationalized in terms of decreased polarity of the reaction microenvironment. In other cases, regioselectivity induced by micelles has been rationalized in terms of a preorientational ef-

SCHEME 21

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fect or anisotropy of the aggregate-water interface. For instance, surfactant control of the ortho/para ratio in the bromination of anilines was studied by Cerichelli et al. [440]. A range of different anilines were investigated in CTABr or CTABr3, and the regioselectivity observed in water is opposite to that in micelles. High ortho/para ratios in micelles were observed and increased with greater steric hindrance in the ortho position. Further investigation showed a dependence not only on the substituents on the nitrogen of the aniline but also on the temperature, and that was explained by the authors as related to thermal shaking, which makes the interaction of substrate with the aggregate less specifically oriented [441]. Alignment of reactants at the micellar surface was at the basis of the observed regioselectivity control in Diels-Alder reactions in which both reactants were surface active. The Diels-Alder reaction is an important tool in organic synthesis, and there are a number of studies of this reaction in aqueous surfactant systems [442]. A deep kinetic investigation was carried out by Engberts and colleagues [443] (Table 12). Jaeger and Wang observed that when the reactions between surface-active diene (1, Scheme 22) and dienophile (2) were run in organic solvent, two regioisomers (3 and 4) were obtained in equal amounts, but when reactions were carried out in aqueous mixed micelles formed by the two surfactant reagents, one regioisomer (3) prevailed over the other (4) by a factor of 3 [442]. No effects have been observed when only diene was surface active [444], indicating that the regioselectivity is controlled by substrate orientation related to the long alkyl chain. A considerable degree of chemoselectivity in SN2 reactions of different sulfonate esters in solutions of

SCHEME 22

OH⫺ and Br⫺ was obtained based on micelle-induced ion discrimination [439]. Cationic or zwitterionic surfactants have been shown to allow SN2 reactions of Br⫺ to proceed quantitatively, even in alkaline solutions, and protect the alkyl bromide from subsequent reaction with OH⫺. Affinities of these micelles for anions follow the Hofmeister series and are large for polarizable, ‘‘soft,’’ low-charge-density ions such as Br⫺ and low for ‘‘hard’’ high-charge-density ions such as OH⫺. The Br⫺ binds so much more strongly than OH⫺ to cationic and sulfobetaine micelles that nucelophilic attack of Br⫺ is strongly preferred over that of OH⫺ and the kinetically controlled product, the alkyl bromide, is protected from OH⫺. Variations in surfactant structure with increasing headgroup bulk (use of CTBABr) further increase the ion discrimination and the chemoselectivity, and moreover it was possible to use a hexane-water system with extraction of the products and reuse of the aqueous surfactant. Chemoselectivity was also observed in the electrophilic bromination of olefins. A combination of kinetic study (reported in Section V) and product analysis for the bromination of a series of 1-alkenes in CTABr showed that decreased reactivities correspond to a decrease in bromohydrin product and correspond to different locations of the double bond of the alkenes in the micelle. The longer the alkene chain, the deeper the location in of the double bond: 1-decene gives the least bromohydrin [313]. The chemoselectivity in epoxidation of alkenes was studied. Olefins such as cyclooctene and cyclohexene could be oxidized with NaClO in homogeneous micellar media to give good yields of the epoxides in the presence of tailor-made micelle-bound metalloporphyrins [445]. The stereoselectivity of a reaction can also be altered

Diels-alder reaction between surface active diene (1) and surface active dienophile (2).


SCHEME 23

Homochiral quaternary ammonium salts.

in micellar systems. In this respect, the main factor to consider is the preorganizational effect of micelles. Denis et al. [446] obtained high regioselectivity and stereoselectivity in the reduction of ␣,␤-unsaturated ketones to the corresponding allylic alcohol in the presence of glycosidic surfactants or amphiphilic carbohydrates. For instance, carvone was converted to (⫺)cis-carveol in 99% yield, 99% regioselectivity, and 93% cis-stereoselectivity. The use of micelles to induce enantioselectivity is currently of high interest. The most widely studied stereochemical reactions are the hydrolyses of p-nitrophenyl esters of N-protected D or L amino acids in the presence of dipeptide or tripeptide catalysts [31]. Values of up to 131 for the k /k ratio in CTABr micelles have been reported [447]. However, asymmetric synthesis using chiral micelles as an asymmetric environment is a relatively new area. Goldberg et al. in 1978 first reported the reduction of prochiral ketones in an aqueous micellar solution, but with only 1.7% enantiomeric excess [448]. Zhang et al. have investigated the use of chiral cationic micelles [in several cases homochiral quaternary ammonium salts prepared from (⫺)(1S,2R)-ephedrine, Scheme 23] in the reaction of many types of prochiral substates such as the epoxidation of chalcones, reduction of prochiral ketones, and oxidation of prochiral sulfides [449–451]. Zhang and Wu prepared ␤-hydroxy esters by the Reformatsky reaction [452] and oxiranes (Scheme 24) by the reaction of dimethylsulfonium methylide and aromatic aldehydes and ketones, with an enantiomeric excess up to 55% in the latter case [453]. Diego-Castro and Hailes [454] have used novel cationic chiral surfactants to study enantioselectivity in Diels-Alder reactions, and they had an enantiomeric L

SCHEME 24

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excess up to 15%, which compares with that cited for Diels-Alder in cyclodextrins. High values of enantioselectivity were obtained by Brosch and Kirmse in the nitrous acid deamination of amines [455]. Deamination of 1-octamine affords mixtures of isomeric ocetenes, octanols, and octyl nitrites; the aggregation of the amine⭈ HClO4 in micelles induces the formation of dioctylether and 1-nitrooctane as additional products. The deamination of [1-2H]-1octamine in submicellar aqueous conditions (the cmc of the amine⭈ HClO4 is 0.105 M) gives [1-2H]-1-octanol with ⬃95% inversion of configuration, and above the cmc the enantiomeric purity decreased, whereas [1-2H]1-nitrooctane was formed with ⬃90% retention of configuration. Selke et al. obtained what they called an impressive enhancement of the enantioselectivity for a hydroxy-containing rhodium(I) biphosphine catalyst in aqueous solutions by micelles [456]. The hydrogenation of some chelating olefinic substrates with a rhodium biphosphine catalyst is influenced by micelles of SDS, CTABr, and Triton X in water. They obtained up to ⬃77% enantiomeric excess, with a difference in enantiomeric excess with blanks of 70%.

D

Enantioselective synthesis of oxiranes.

VIII.

CONCLUSIONS

Surfactants are now widely used in different fields, and they are being widely applied in developing the chemistry of the future [457]. Quite often, however, only a few marketed preparations are used, with almost an empirical approach. This chapter illustrates how small modifications in the surfactant structure lead to changes in microaggregate structure, properties, and functions. The key point is that aggregates created by design contain what Lehn [458] would call ‘‘instructed molecular components.’’ In this chapter we have focused attention on new surfactants studied by or used for kinetic effects. In particular, regarding kinetics, we spoke about systematic variations in surfactant headgroup bulk, alkyl chain length, and the number of alkyl chains and about the use of gemini surfactants. Regarding applications, a greater range of surfactants have been encountered. The ultimate goal is to develop the synthesis and applications of novel, more effective amphiphiles, capable of performing selectively the function that they were ‘‘engineered’’ for. Therefore, it seems important for physicochemical studies of micellar structure and properties to continue. It will become an important challenge to synthesize new amphiphiles with different headgroups, alkyl chains, and functional groups in order to achieve improved micellar effects.

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ACKNOWLEDGMENTS Our work in this area has depended on the help and enthusiasm of our colleagues and students: Giorgio Cerichelli, Giovanna Mancini, Luciana Lucchetti, Antonio Cipiciani, Nicoletta Spreti, Pietro Di Profio, Luisa Marte, Massimiliano Giovannini, Antonella Bartoletti, Simona Bartolini, Francesca Del Rosso, Vittoria Giacomini, Francesca Micheli, Monica Tugliani, and especially Clifford A. Bunton.

SURFACTANTS (CDA)2C32Br (CDA)2C42Br AOMe-14 AOPr-14 AOT Bolaform (n) X2 C10E4

SYMBOLS

␣ ␤ cmc [D] [Dn] KS K⬘Y kobs k⬘W kW k⬘M kM

VM km2 K XY m XS ⌬ f ␦

Degree of micellar ionization Fraction of counterions bound to micelle, ␤ =1⫺␣ Critical micelle concentration Stoichiometric concentration of surfactant (detergent) Concentration of micellized surfactant: generally [Dn] = [Dt] ⫺ cmc Binding constant* of solute based on concentration of micellized surfactant (M⫺1) Mass action binding constant* of ion Y (M⫺1) Observed first-order rate constant (s⫺1) First-order rate constant (s⫺1) in the aqueous pseudophase Second-order rate constant (M⫺1 s⫺1) in the aqueous pseudophase First-order rate constant (s⫺1) in the micellar pseudophase Second-order rate constant in the micellar pseudophase (s⫺1), with concentration expressed as mole ratio Molar volume element of reaction in the micelle (M⫺1) Second-order rate constant in the micellar pseudophase (M⫺1 s⫺1): km2 = kMVM Ion-exchange constant* for ions of like charge Mole ratio of X in the micelle Width of shell of reactive region in the micelle Fractional coverage by counterions Specificity parameter for ion association in the Volmer equation

C12E7 C12E10 C12E23 C16E20 CB1-14 CB1-16 CCHDMABr CDMHEACl CDMPCl CMMBr CPCl CQCl CQOH CTA(SO4)0.5 CTABr CTABr3 CTACl CTAF CTA formate CTAIB

*We use the word constants as usual in the literature, but we have to indicate that they are not thermodynamic constants.

CTAN3 CTANO3 CTAOAc

1,3-Bis-(N-cetyl-N,N-dimethylammonium)-propane dibromide 1,4-Bis-(N-cetyl-N,N-dimethylammonium)-butane dibromide Myristyldimethylamine N-oxide Myristyldipropylamine N-oxide Bis(2-ethylhexyl) sodium sulfosuccinate Me3N⫹(CH2)n N⫹Me32X⫺ Decyltetraoxyethylene glycol ether Dodecylheptaoxyethylene glycol ether Dodecyldecaoxyethylene glycol ether Dodecyltricosanoxyethylene glycol ether Cetyleicosanoxyethylene glycol ether Myristyldimethylammonium carboxybetaine Cetyldimethylammonium carboxybetaine Cetylcyclohexyldimethylammonium bromide Cetyldimethyl-2-(hydroxyethyl)ammonium chloride Cetyl-4-(dimethylamino)-pyridinium chloride N-Cetyl-N-methylmorpholinium bromide Cetylpyridinium chloride Cetylquinuclidinium chloride Cetylquinuclidinium hydroxyde Cetyltrimethylammonium sulfate Cetyltrimethylammonium bromide Cetyltrimethylammonium tribromide Cetyltrimethylammonium chloride Cetyltrimethylammonium fluoride Cetyltrimethylammonium formate Cetyltrimethylammonium oiodosobenzoate Cetyltrimethylammonium azide Cetyltrimethylammonium nitrate Cetyltrimethylammonium acetate


CTAOH CTAOHexanoate CTAOMs CTAOTs CTBABr CTBAOH CTEABr CTEAOH CTHEACl CTPABr CTPAOH CTPAOMs CTPeACl Cu(DS)2 DDDABr DDDACl DDDAOH DDDA(SO4)0.5 DeTACl DODABr DODACl DTABr DTACl DTAOH HDS HeTACl MQBr MTABr

Cetyltrimethylammonium hydroxyde Cetyltrimethylammonium hexanoate Cetyltrimethylammonium methanesulfonate Cetyltrimethylammonium ptoluenesulfonate Cetyltributylammonium bromide Cetyltributylammonium hydroxide Cetyltriethylammonium bromide Cetyltriethylammonium hydroxide Cetyltrihydroxyethylammonium chloride Cetyltripropylammonium bromide Cetyltripropylammonium hydroxide Cetyltripropylammonium mesylate Cetyltripentylammonium chloride Copper didodecylsulfate Didodecyldimethylammonium bromide Didodecyldimethylammonium chloride Didodecyldimethylammonium hydroxide Didodecyldimethylammonium sulfate Decyltrimethylammonium chloride Dioctadecyldimetylammonium bromide Dioctadecyldimetylammonium chloride Dodecyltrimethylammonium bromide Dodecyltrimethylammonium chloride Dodecyltrimethylammonium hydroxide Hydrogen dodecyl sulfate Hexyltrimethylammonium chloride N-Myristylquinuclidinium bromide Myristyltrimethylammonium bromide

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MTACl MTANO3 OcTACl OdTACl pOOTABr pOOTBABr SB3-14 SB3-16 SB4-14 SB5-14 SBBu3-14 SBEt3-14 SBPr3-14 SBPr4-14 SBPr5-14 SDHP SDS TMABr TMACl Triton X-100 Zn(DS)2

Myristyltrimethylammonium chloride Myristyltrimethylammonium nitrate Octyltrimethylammonium chloride Octadecyltrimethylammonium chloride Paraoctyloxybenzyltrimethylammonium bromide Paraoctyloxybenzyltributylammonium bromide Myristyldimethylammonium propanesulfonate Cetyldimethylammonium propanesulfonate Myristyldimethylammonium butanesulfonate Myristyldimethylammonium pentanesulfonate Myristyldibutylammonium propanesulfonate Myristyldiethylammonium propanesulfonate Myristyldipropylammonium propanesulfonate Myristyldipropylammonium butanesolfonate Myristyldipropylammonium pentanesolfonate Sodium dihexadecylphosphate Sodium dodecyl sulfate Tetramethylammonium bromide Tetramethylammonium chloride Polyethylene glycol tert-octylphenyl ether Zinc didodecylsulfate

SUBSTRATES 6-NBIC DDT DNCN DNPP2⫺ DTE DTNB MCP MeONs MNTS pNPDPP

6-Nitrobenzisoxazole-3-carboxylate 1,1,1-Trichloro-2,2-bis(p-chlorophenyl)ethane 2,4-Dinitro-1-chloro-naphthalene 2,4-Dinitrophenylphosphate dianion 1,1-Diphenyl-2,2,2-trichloroetane 5,5⬘-Dithiobis-(2-nitrobenzoic acid) N-Methyl-4-cyanopyridinium ion Methylnaphthalene-2-sulfonate N-Methyl-N-nitroso-ptoluenesulfonamide p-Nitrophenyl diphenylphosphate

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REFERENCES 1. 2. 3.

4. 5. 6. 7. 8.

9. 10.

11.

12. 13. 14. 15. 16. 17.

18. 19. 20. 21. 22. 23. 24. 25. 26.

J. N. Israelachvili, Intermolecular and Surface Forces, Academic Press, London, 1985. F. Vo¨gtle, Supramolecular Chemistry, Wiley, Chichester, UK, 1991. J. H. Fuhrhop and J. Koning, Membranes and Molecular Assemblies: The Synkinetic Approach, The Royal Society of Chemistry, 1994. G. S. Hartley, Q. Rev. 2:152–183 (1948). E. F. J. Duynstee and E. Grunwald, J. Am. Chem. Soc. 81:4540–4542 (1959). J. L. Kurz, J. Phys. Chem. 66:2239–2246 (1962). V. A. Motsavage and H. B. Kostenbauder, J. Colloid Sci. 18:603–615 (1963). J. H. Fendler and E. J. Fendler, Catalysis in Micellar and Macromolecular Systems, Academic Press, New York, 1975. J. H. Fendler, Membrane Mimetic Chemistry, Wiley, New York, 1982. L. S. Romsted, in Micellization, Solubilization and Microemulsion (K. L. Mittal, ed.), vol. 2, Plenum, New York, 1977, pp. 489–530. L. S. Romsted, in Surfactants in Solution (K. L. Mittal and B. Lindman, eds.), vol. 2, Plenum, New York, 1984, p. 1015. C. A. Bunton and G. Savelli, Adv. Phys. Org. Chem. 22:213–309 (1986). P. L. Luisi and F. J. Varela, Origins Life Evol. Biosphere 19:633–643 (1989). P. A. Bachamann, P. Walde, P. L. Luisi, and J. Lang, J. Am. Chem. Soc. 113:8204–8209 (1991). P. A. Bachmann, P. L. Luisi, and J. Lang, Nature 357: 57–59 (1992). P. Walde, R. Wick, M. Fresta, A. Mangone, and P. L. Luisi, J. Am. Chem. Soc. 116:11649–11654 (1994). K. Morigaki, S. Dallavalle, P. Walde, S. Colonna, and P. L. Luisi, J. Am. Chem. Soc. 119:292–301 (1997). R. Wich, P. Walde, and P. L. Luisi, J. Am. Chem. Soc. 117:1435–1436 (1995). K. Holmberg, Adv. Colloid Interface Sci. 51:137–174 (1994). J. Sjoblom, R. Lindberg, and S. E. Friberg, Adv. Colloid Interface Sci. 95:125–287 (1996). R. Schoma¨cher, J. Chem. Res. (S):92–93 (1991). M. J. Schwuger, K. Stickdorn, and R. Schomacker, Chem. Rev. 95:849–864 (1995). M. P. Pileni, Structure and Reactivity in Reverse Micelles, Elsevier, Amsterdam, 1989. H. Kunieda and K. Nakamura, Adv. Mater. 4:291–293 (1992). H. Kunieda, K. Nakamura, and D. F. Evans, J. Am. Chem. Soc. 113:1051–1052 (1991). H. Kunieda and M. Yamagata, J. Colloid Interface Sci. 150:277–280 (1992).

27.

28.

29. 30. 31. 32. 33. 34. 35. 36. 37. 38. 39. 40. 41.

42. 43. 44.

45. 46. 47. 48.

49.

50. 51.

P. Mukerjee and K. J. Mysels, Critical Micelle Concentration of Acqeous Surfactants Systems, National Bureau of Standards, Washington, DC, 1970. C. Tanford, The Hydrophobic Effect: Formation of Micelles and Biological Membranes, 2nd ed., Wiley, New York, 1980. A. Ben-Naim, Hydrophobic Interactions, Plenum, New York, 1980. Y. Ishikawa, H. Kuwahara, and T. Kunitake, J. Am. Chem. Soc. 116:5579–5591 (1994). S. Tascioglu, Tetrahedron 52:11113–11152 (1996). G. S. Hartley and R. C. Murray, Trans. Faraday Soc. 31:183–189 (1935). P. H. Elworthy and K. J. Mysel, J. Colloid Interface Sci. 21:331–347 (1966). P. Mukerjee, Adv. Colloid Interface Sci. 1:241–275 (1967). G. Stainsby and A. E. Alexander, Trans. Faraday Soc. 46:587–597 (1950). D. F. Evans and B. W. Ninham, J. Phys. Chem. 87: 5025–5032 (1983). D. F. Evans, D. J. Mitchell, and B. W. Ninham, J. Phys. Chem. 88:6344–6348 (1984). D. F. Evans, M. Allen, B. W. Ninham, and A. Fouda, J. Solution Chem. 13:87–191 (1984). J. B. Hayter, Langmuir 8:2873–2876 (1992). N. M. van Os, G. J. Daana, and G. Haandrikman, J. Colloid Interface Sci. 141:199–217 (1991). N. M. van Os, J. R. Haak, and L. A. M. Rupert, Physico-Chemical Properties of Selected Anionic, Cationic and Nonionic Surfactants, Elsevier Science, Amsterdam, 1993. N. M. van Os, B. Smit, and S. Karaborni, Rec. Trav. Chim. Pays-Bas 113:181–185 (1994). D. W. R. Gruen, J. Colloid Interface Sci. 84:281–283 (1981). D. W. Gruen and E. H. B. de Lacey, in Surfactants in Solution, vol. 1, New York, Plenum, 1984, pp. 279– 306. J. Bocher, J. Brickmann, and P. Bopp, J. Phys. Chem. 98:712–717 (1994). J. Shelley, K. Watanabe, and M. L. Klein, Int. J. Quantum Chem. Quantum Biol. Symp. 17:103–117 (1990). S. Karaborni and J. P. O’Connell, J. Phys. Chem. 94: 2624–2631 (1990). B. Smith, P. A. J. Hilbers, K. Esselink, L. A. M. Rupert, N. M. van Os, and A. G. Schlijper, Nature 348: 624–625 (1990). S. Karborni, K. Esselink, P. A. J. Hilbers, B. Smith, N. M. van Os, and R. Zana, Science 266:254–256 (1994). M. A. Floriano and E. Caponetti, Langmuir 15:3143– 3151 (1999). A. Khatory, F. Kern, F. Lequeux, J. Appell, G. Porte, N. Morie, A. Ott, and W. Urbach, Langmuir 9:933– 939 (1993).

Reactivity Control by Self-Assembling Systems 52. 53. 54. 55. 56. 57. 58. 59. 60. 61. 62. 63. 64. 65.

66.

67. 68. 69. 70. 71. 72. 73.

74.

75. 76. 77.

78.

R. Mikulski, Pol. J. Chem. 67:1623–1629 (1993). M. Leaver, I. Furo´, and U. Olsson. Langmuir 11: 1524–1529 (1995). E. Y. Sheu and S. H. Chen, J. Phys. Chem. 92:4466– 4474 (1988). F. H. Quina, P. M. Nassar, J. B. S. Bonilha, and B. L. Bales, J. Phys. Chem. 99:17028–17031 (1995). S. Kumar, V. K. Aswal, H. N. Singh, P. S. Goyal, and K. ud-Din, Langmuir 10:4069–4072 (1994). V. K. Aswal, P. S. Goyal, S. V. G. Menon, and B. A. Dasannacharya, Physica B 213&214:607–609 (1995). M. Delsanti, A. Mussaid, and J. P. Munch, J. Colloid Interface Sci. 157:285–290 (1993). P. van der Schoot and M. E. Cates, Langmuir 10:670– 679 (1994). R. Nagarajan, Langmuir 10:2028–2034 (1994). D. A. Amos, S. Lynn, and C. J. Radke, Lamgmuir 14: 2297–2306 (1998). F. M. Menger, Acc. Chem. Res. 12:111–117 (1979). P. Fromherz, Chem. Phys. Lett. 77:460–466 (1981). K. A. Dill and P. J. Flory, Proc. Natl. Acad. Sci. U.S.A. 78:676–680 (1981). K. A. Dill, D. E. Koppel, R. S. Cantor, J. D. Dill, D. Bendedouch, and S.-H. Cheng, Nature 309:42–45 (1984). B. Jo¨nsson, P.-G. Nilsson, B. Lindman, L. Guldbrand, and H. Wennerstro¨m, in Surfactant in Solution (K. L. Mittal and B. Lindman, eds.), vol. 1, Plenum, New York, 1984, pp. 3–21. F. M. Menger, and C. E. Mounier, J. Am. Chem. Soc. 115:12222–12223 (1993). A. Chauduri and L. S. Romsted, J. Am. Chem. Soc. 113:5052–5053 (1991). L. S. Romsted and J. Yao, Langmuir 15:326–336 (1999). L. S. Romsted and J. Yao, Langmuir 12:2425–2432 (1996). O. A. El Seoud, A. Blasko, and C. A. Bunton, Ber. Bunsenges. Phys. Chem. 99:1214–1220 (1995). O. A. El Seoud, A. Blasko, and C. A. Bunton, Langmuir 10:653–657 (1994). M. E. L. McBain and E. Hutchinson, Solubilization and Related Phenomena, Academic Press, New York, 1955. P. H. Elworthy, A. T. Florence, and C. B. Macfarlane, Solubilization by Surface/Active Agents and Its Application in Chemistry and the Biological Sciences, Chapman & Hall, London, 1968. M. Almgren, F. Grieser, and J. K. Thomas, J. Am. Chem. Soc. 101:279–291 (1979). Y. Moroi, H. Noma, and R. Matuura, J. Phys. Chem. 87:872–876 (1983). C. A. Bunton, in Surfactants in Solution (K. L. Mittal and D. O. Shah, eds.), vol. 11, Plenum, New York, 1991, p. 17. L. Sepulveda, E. Lissi, and F. Quina, Adv. Colloid Interface Sci. 25:1–57 (1986).

239 79. 80. 81.

82.

83.

84.

85. 86. 87. 88. 89. 90. 91. 92. 93. 94. 95. 96. 97. 98. 99. 100. 101. 102. 103. 104. 105.

F. H. Quina, E. O. Alonso, and J. P. S. Farah, J. Phys. Chem. 99:11708–11714 (1995). E. Abuin and E. Lissi, Bol. Soc. Chil. Quim. 42:113– 134 (1997). M. A. Rodriguez, E. O. Alonso, C. Yihwa, J. P. S. Farah, and F. H. Quina, Langmuir 15:6770–6774 (1999). H. Abraham, H. S. Chadha, J. P. Dixon, C. Rafols, and C. Treiner, J. Chem. Soc. Perkin Trans. 2:887–894 (1995). M. H. Abraham, H. S. Chadha, J. P. Dixon, C. Rafols, and C. Treiner, J. Chem. Soc. Perkin Trans. 2:19–24 (1997). B. Lindman, O. Soderman, and H. Wennerstrom, in Surfactant Solutions: New Methods of Investigation (R. Zana, ed.), Marcel Dekker, New York, 1987. J. C. Eriksson and G. Gillberg, Acta Chem. Scand. 20: 2019–2027 (1966). R. Bacaloglu, C. A. Bunton, G. Cerichelli, and F. Ortega, J. Phys. Chem. 93:1490–1497 (1989). Y. S. Kang, P. Baglioni, and L. Kevan, J. Phys. Chem. 95:7944–7947 (1991). Y. S. Kang, H. J. D. Mamanus, and L. Kevan, J. Phys. Chem. 96:7473–7478 (1992). C. A. Bunton, F. Nome, F. H. Quina, and L. S. Romsted, Acc. Chem. Res. 24:358–363 (1991). I. M. Cuccovia, I. N. da Silva, H. Chaimovich, and L. S. Romsted, Langmuir 13:647–652 (1996). J. D. Morgan, D. H. Napper, G. G. Warr, and S. K. Nicol, Langmuir 10:797–801 (1994). G. G. Warr, Langmuir 13:1451–1456 (1997). N. Kellaway and G. G. Warr, J. Colloid Interfase Sci. 193:312–314 (1997). L. S. Romsted and C.-O. Yoon, J. Am. Chem. Soc. 115:989–994 (1993). J. D. Morgan, D. H. Napper, and G. G. Warr, J. Phys. Chem. 99:9458–9465 (1995). G. Mancini, C. Schiavo, and G. Cerichelli, Langmuir 12:3567–3573 (1996). M. A. Morini, P. C. Schulz, and J. E. Puig, Colloid Polym. Sci. 274:662–668 (1996). A. Blasko´, C. A. Bunton, G. Cerichelli, and D. C. McKenzie, J. Phys. Chem. 97:11324–11331 (1993). S. J. Bachofer and U. Simonis, Langmuir 12:1744– 1754 (1996). P. J. Kreke, L. J. Magid, and J. C. Gee, Langmuir 12: 699–705 (1996). K. Bijma, E. Rank, and J. B. F. N. Engberts, J. Colloid Interface Sci. 205:245–256 (1998). M. A. Cassidy and G. G. Warr, J. Phys. Chem. 100: 3237–3240 (1996). S. J. Bachofer, U. Simonis, and T. A. Nowich, J. Phys. Chem. 95:480–488 (1991). C. A. Bunton, M. M. Mhala, and J. R. Moffat, J. Org. Chem. 52:3832–3835 (1987). C. A. Bunton, M. M. Mhala, and J. R. Moffat, J. Phys. Chem. 93:854–858 (1989).

240 106.

107. 108. 109. 110. 111.

112.

113.

114. 115. 116. 117. 118.

119. 120. 121. 122.

123.

124. 125. 126. 127. 128. 129. 130.

Savelli et al. S. Brochsztain, P. Berci-Filho, V. G. Toscano, H. Chaimovich, and M. J. Politi, J. Phys. Chem. 94:6781– 6785 (1990). M. S. Baptista and M. J. Politi, J. Phys. Chem. 95: 5936–5942 (1991). D. J. Hodge, R. G. Laughlin, R. H. Ottewill, and A. R. Rennie, Langmuir 7:878–884 (1991). N. Kamenka, Y. Chevalier, and R. Zana, Langmuir 11: 3351–3355 (1995). N. Kamenka, M. Chorro, Y. Chevalier, H. Levy, and R. Zana, Langmuir 11:4234–4240 (1995). M. da Silva Baptista, I. Cuccovia, H. Chaimovich, M. J. Politi, and W. F. Reed, J. Phys. Chem. 96:6442– 6449 (1992). P. Di Profio, R. Germani, G. Savelli, G. Cerichelli, M. Chiarini, G. Mancini, C. A. Bunton, and N. D. Gillitt, Langmuir 14:2662–2669 (1998). G. Weers, J. F. Rathman, F. U. Axe, C. A. Crichlow, L. D. Foland, D. R. Scheuing, R. J. Wiersema, and A. G. Zielske, Langmuir 7:854–867 (1991). Y. Chevalier and P. Le Perchec, J. Phys. Chem. 94: 1768–1774 (1990). Y. Chevalier, Y. Storet, S. Pourchet, and P. Le Perchec, Langmuir 7:848–853 (1991). Y. Chevalier, F. Me´lis, and J. P. Dalbiez, J. Phys. Chem. 96:8614–8619 (1992). Y. Chevalier, N. Kamenka, M. Chorro, and R. Zana, Langmuir 12:3225–3232 (1996). J. K. Thomas, Chemistry of Excitation at Interface, ACS Monograph, American Chemical Society, Washington, DC, 1984. F. M. Menger and C. E. Portnoy, J. Am. Chem. Soc. 89:4698–4703 (1967). F. M. Menger, Pure Appl. Chem. 51:999–1007 (1979). C. A. Bunton and L. Robinson, J. Am. Chem. Soc. 90: 5972–5979 (1968). M. A. B. Marin, F. Nome, D. Zanette, C. Zucco, and L. S. Romsted, J. Phys. Chem. 99:10879–10882 (1995). K. Martinek, A. K. Yatsimirski, A. V. Levashov, and I. V. Berezin, in Solubilization and Microemulsion (K. L. Mittal, ed.), vol. 2, Plenum, New York, 1977, p. 489. A. A. Balekar and J. B. F. N. Engberts, J. Am. Chem. Soc. 100:5914–5920 (1978). I. M. Cuccovia, E. M. Schroter, P. M. Montiero, and H. Chaimovich, J. Org. Chem. 43:2248–2252 (1978). C. A. Bunton, L. S. Romsted, and G. Savelli, J. Am. Chem. Soc. 101:1253–1259 (1979). C. A. Bunton, S. Wright, P. M. Holland, and F. Nome, Langmuir 9:117–120 (1993). M. F. Neves, D. Zanette, F. Quina, M. T. Moretti, and F. Nome, J. Phys. Chem. 93:1502–1505 (1989). C. A. Bunton, N. D. Gillitt, and H. J. Foroudian, Langmuir 14:4415–4421 (1998). C. A. Bunton, H. J. Foroudian, and N. D. Gillitt, Langmuir 15:1067–1074 (1999).

131. 132. 133. 134. 135. 136. 137. 138. 139. 140. 141. 142. 143. 144. 145. 146. 147. 148. 149.

150. 151. 152. 153. 154. 155. 156. 157. 158.

C. A. Bunton, P. Scrimin, and P. Tecilla, J. Chem. Soc. Perkin Trans. 2:419–425 (1996). R. A. Moss, T. F. Hendrckson, and G. O. Bizzigotti, J. Am. Chem. Soc. 108:5520–5527 (1986). T. Kunitake, Y. Okahata, and T. Sakamoto, J. Am. Chem. Soc. 98:7799–7806 (1976). T. Kunitake, S. Shinkai, and Y. Okahata, Bull. Chem. Soc. Jpn. 49:540–545 (1976). R. A. Moss, R. C. Nahas, and T. J. Lukas, Tetrahedron Lett. 507–510 (1978). R. A. Moss, G. O. Bizzigotti, T. J. Lukas, and W. J. Sanders, Tetrahedron Lett. 3661–3664 (1978). W. Tagaki, D. Fukushima, T. Eiki, and Y. Yano, J. Org. Chem. 44:555–563 (1979). C. A. Bunton, F. H. Hamed, and L. S. Romsted, J. Phys. Chem. 86:2103–2108 (1982). C. A. Bunton, L.-H. Gan, and G. Savelli, J. Phys. Chem. 87:5491–5498 (1983). Y. Ihara, M. Nango, Y. Kimura, and N. Kuroki, J. Am. Chem. Soc. 105:1252–1255 (1983). C. A. Bunton and E. L. Dorwin, J. Org. Chem. 51: 4093–4096 (1986). T. J. Connolly and V. C. Reinsborough, Can. J. Chem. 70:1581–1585 (1992). Y. Ihara, M. Nango, and J. Koga, Bull. Chem. Soc. Jpn. 60:815–817 (1987). E. Dutkiewicz, A. Jakubowska, and W. Knoche, Z. Phys. Chem. (Munich) 171:255–260 (1991). K. Ogino, K. Nishi, H. Yamamato, T. Yoshida, and W. Tagaki, Tetrahedron Lett. 31:7023–7026 (1990). F. M. Menger, L. H. Gan, E. Johnson, and D. H. Durst, J. Am. Chem. Soc. 109:2800–2803 (1987). R. Fornasier, P. Scrimin, P. Tecilla, and U. Tonellato, J. Am. Chem. Soc. 111:224–229 (1989). G. De Santi, P. Scrimin, and U. Tonellato, Tetrahedron Lett. 31:4791–4794 (1990). K. Ogino, N. Kashihara, T. Ueda, T. Isaka, T. Yoshida, and W. Tagaki, Bull. Chem. Soc. Jpn. 65:373–384 (1992). K. A. Wilk, J. Phys. Chem. 95:3405–3409 (1991). W. B. Gruhn and M. L. Bender, J. Am. Chem. Soc. 91:5883–5885 (1969). C. A. Bunton, L. Robinson, and M. Stam, J. Am. Chem. Soc. 92:7393–7400 (1970). C. A. Bunton and L. G. Ionescu, J. Am. Chem. Soc. 95:2912–2917 (1973). C. A. Bunton, A. A. Kamego, and P. Ng, J. Org. Chem. 39:3469–3471 (1974). C. A. Bunton and S. Diaz, J. Org. Chem. 41:33–36 (1976). C. A. Bunton and S. Diaz, J. Am. Chem. Soc. 98: 5663–5671 (1976). C. A. Bunton and C. H. Paik, J. Org. Chem. 41:40– 44 (1976). K. Martinek, A. V. Levashov, and I. V. Berenzin, Tetrahedron Lett. 1275–1278 (1975).

Reactivity Control by Self-Assembling Systems 159. 160. 161. 162.

163. 164. 165. 166. 167. 168. 169. 170. 171. 172. 173. 174. 175. 176.

177. 178. 179. 180. 181. 182. 183. 184. 185. 186.

C. A. Bunton and M. McAneny, J. Org. Chem. 41:36– 39 (1976). A. Pillersdorf and J. Katzhendler, Isr. J. Chem. 18: 330–338 (1979). J. Kulic, J. Sussenbek, and A. Ptacek, Collect. Czech. Chem. Commun. 58:2891–2895 (1993). J. Epstein, J. J. Kaminski, N. Bodor, R. Enever, J. Sowa, and T. Higuchi, J. Org. Chem. 43:2816–2821 (1978). R. A. Moss, G. O. Bizzigotti, and C.-W. Huang, J. Am. Chem. Soc. 102:754–762 (1980). R. A. Moss and K. Y. Kim, Isr. J. Chem. 25:11–14 (1985). C. A. Bunton, M. M. Mhala, and J. R. Moffatt, J. Org. Chem. 52:3832–3835 (1987). T. J. Broxton, R. J. Christie, and X. Sango, J. Org. Chem. 54:1919–1922 (1989). T. J. Broxton, J. Org. Chem. 56:5958–5960 (1991). K. A. Wilk, J. Phys. Chem. 96:901–904 (1992). J. M. Brown, C. A. Bunton, and S. Diaz, J. Chem. Soc. Chem. Commun. 971–972 (1974). T. E. Wagner, C. Hsu, and C. S. Pratt, J. Am. Chem. Soc. 89:6366–6368 (1967). G. Biresaw and C. A. Bunton, J. Org. Chem. 51:2771– 2777 (1986). K. Ogino, K. Inoue, and W. Tagaki, Tetrahedron Lett. 33:4191–4194 (1992). Y. Y. Lim, E. H. L. Tan, and L. H. Gan, J. Colloid Interface Sci. 157:442–446 (1993). T. J. Broxton and R. A. Cox, Can. J. Chem. 71:670– 673 (1993). V. Faivre, A. Brembilla, and P. Lochon, J. Mol. Catal. 85:45–56 (1993). G. R. Newkome and C. N. Moorefield, Polym. Prep. (Am. Chem. Soc. Div. Polym. Chem.) 34:75–76 (1993). J. G. J. Weijnen, A. Koudjis, and J. F. J. Engbersen, J. Org. Chem. 57:7258–7265 (1992). P. Scrimin, P. Tecilla, and U. Tonellato, J. Org. Chem. 59:4194–4201 (1994). P. Scrimin, P. Tecilla, and U. Tonellato, J. Org. Chem. 56:161–166 (1991). P. Scrimin, P. Tecilla, and U. Tonellato, J. Org. Chem. 59:18–24 (1994). W. Tagaki and K. Ogino, Top. Curr. Chem. 128:143– 147 (1985). R. Fornasier, P. Scrimin, P. Tecilla, and U. Tonellato, J. Am. Chem. Soc. 111:224–229 (1989). J. G. J. Weijnen, A. Koudijs, and J. F. J. Engbersen, J. Chem. Soc. Perkin Trans. 2:829–834 (1992). J. G. J. Weijnen, A. Koudijs, and J. F. J. Engbersen, J. Org. Chem. 57:7258–7265 (1992). P. Scrimin, P. Tecilla, and U. Tonellato, J. Am. Chem. Soc. 114:5086–5092 (1992). M. C. Cleij, P. Scrimin, P. Tecilla, and U. Tonellato, Langmuir 12:2956–2960 (1996).

241 187. 188. 189. 190. 191.

192. 193. 194. 195. 196.

197. 198.

199. 200. 201. 202.

203. 204. 205. 206. 207. 208. 209. 210. 211. 212. 213.

S. H. Gellman, R. Petter, and R. Breslow, J. Am. Chem. Soc. 108:2388–2394 (1986). E. Kimura, H. Hashimoto, and T. Koioke, J. Am. Chem. Soc. 118:10963–10970 (1996). G. Ghirlanda, P. Scrimin, and L. A. Echegoyen, Langmuir 12:5188–5194 (1996). P. Scrimin, G. Ghirlanda, P. Tecilla, and R. A. Moss, Langmuir 12:6235–6241 (1996). P. Scrimin, P. Tecilla, U. Tonellato, and C. A. Bunton, Colloids Surf. A Physicochem. Eng. Aspects 144:71– 79 (1998). A. Domıńguez and E. Iglesias, Langmuir 14:2677– 2683 (1998). F. Nome, A. F. Rubira, C. Franco, and L. G. Ionescu, J. Phys. Chem. 86:1881–1885 (1982). E. Stadler, D. Zanette, M. C. Rezende, and F. Nome, J. Phys. Chem. 88:1892–1896 (1984). T. J. Broxton and D. B. Sango, Aust. J. Chem. 36: 711–717 (1983). E. B. Abuin, E. Lissi, R. Araujo, R. M. V. Alexeio, H. Chaimovich, N. Bianchi, L. Miola, and F. Quina, J. Colloid Interface Sci. 96:293–295 (1983). L. C. Mello Ferreira, C. Zucco, D. Zanette, and F. Nome, J. Phys. Chem. 96:9058–9061 (1992). R. Germani, P. P. Ponti, G. Savelli, N. Spreti, C. A. Bunton, and J. R. Moffatt, J. Chem. Soc. Perkin Trans. 2:401–404 (1989). C. A. Bunton, J. Frankson, and L. S. Romsted, J. Phys. Chem. 84:2607–2611 (1980). C. A. Bunton, L.-H. Gan, J. R. Moffatt, L. S. Romsted, and G. Savelli, J. Phys. Chem. 85:4118–4125 (1981). P. Lianos and R. Zana, J. Phys. Chem. 87:1289–1291 (1983). V. Athanassakis, J. R. Moffatt, C. A. Bunton, R. B. Dorshow, G. Savelli, and D. F. Nicoli, Chem. Phys. Lett. 115:467–471 (1985). E. Rodenas and S. Vera, J. Phys. Chem. 89:513–516 (1985). C. R. A. Bertoncini, F. Nome, G. Cerichelli, and C. A. Bunton, J. Phys. Chem. 94:5875–5878 (1990). C. R. A. Bertoncini, M. S. Neves, F. Nome, and C. A. Bunton, Langmuir 9:1274–1279 (1993). D. Stigter, J. Phys. Chem. 68:3603–3611 (1964). D. Stigter, Prog. Colloid Polym. Sci. 65:45–52 (1978). G. M. Bell and A. J. Dunning, Trans. Faraday Soc. 66:500–508 (1970). M. R. Mille and G. Vanderkooi, J. Colloid Interface Sci. 59:211–224 (1977). G. Gunnarsson, B. Jonsson, and H. Wennerstrom, J. Phys. Chem. 84:3114–3121 (1980). C. A. Bunton and H. J. Foroudain, Langmuir 9:2832– 2835 (1993). C. A. Bunton and J. R. Moffatt, J. Phys. Chem. 89: 4166–4169 (1985). C. A. Bunton and J. R. Moffatt, J. Phys. Chem. 90: 538–541 (1986).

242 214. 215. 216. 217. 218. 219. 220. 221. 222. 223.

224. 225. 226. 227. 228.

229.

230. 231. 232.

233. 234. 235. 236. 237. 238.

Savelli et al. C. A. Bunton and J. R. Moffatt, J. Phys. Chem. 92: 2896–2902 (1988). E. Rodenas and F. Ortega, J. Phys. Chem. 91:837–840 (1987). H. A. Al-Lohedan, J. Chem. Soc. Perkin Trans. 2: 1707–1713 (1995). C. A. Bunton and J. R. Moffatt, Langmuir 8:2130– 2134 (1992). H. A. Al-Lohedan, J. Chem. Soc. Perkin Trans. 2: 1401–1406 (1990). F. Ortega and E. Rodenas, J. Phys. Chem. 90:2408– 2413 (1986). F. Ortega and E. Rodenas, Can. J. Chem. 67:305–309 (1989). E. Rodenas and S. Vera, J. Phys. Chem. 90:3414–3417 (1986). S. Vera and E. Rodenas, An. Quim. Ser. A 84:174– 178 (1988). H. Chaimovich, V. R. Correia, P. S. Araujo, R. M. V. Aleixo, and I. M. Cuccovia, J. Chem. Soc. Perkin Trans. 2:925–928 (1985). E. Rodenas, C. Dolcet, and M. Valiente, J. Phys. Chem. 94:1472–1477 (1990). C. Dolcet and E. Rodenas, Can. J. Chem. 68:932–938 (1990). C. Dolcet and E. Rodenas, Colloids Surf. A Physicochem. Eng. Aspects 75:39–50 (1993). E. Rodenas, C. Dolcet, M. Valiente, and E. C. Valeron, Langmuir 10:2088–2094 (1994). H. Chaimovich, R. M. V. Aleixo, I. M. Cuccovia, D. Zanette, and F. H. Quina, in Solution Behavior of Surfactants (K. L. Mittal and E. J. Fendler, eds.), vol. 2, Plenum, New York, 1982, pp. 949–973. C. Armstrong, W. Gotham, P. Jennings, J. Nikles, L. S. Romsted, M. Versace, and J. Waidlich, in Surfactants in Solution (K. L. Mittal and E. J. Fendler, eds.), vol. 9, Plenum, New York, 1989, p. 197. Z.-M. He, J. A. Loughlin, and L. S. Romsted, Bol. Soc. Chil. Quim. 35:43–53 (1990). C. A. Bunton, M. M. Mhala, and J. R. Moffatt, J. Phys. Chem. 93:7851–7856 (1989). A. Blasko´, C. A. Bunton, C. Armstrong, W. Gotham, Z. M. He, J. Nikles, and L. S. Romsted, J. Phys. Chem. 95:6747–6750 (1991). A. Blasko´, C. A. Bunton, and S. Wright, J. Phys. Chem. 97:5435–5442 (1993). S. Amado, L. G. Rıó, J. R. Leis, and A. Rıós, Langmuir 13:687–692 (1997). M. N. Khan, J. Colloid Interface Sci. 170:598–601 (1995). M. N. Khan, Z. Arifin, M. N. Lasidek, M. A. M. Hanifiah, and G. Alex, Langmuir 13:3959–3964 (1997). D. Piszkiewicz, J. Am. Chem. Soc. 99:1550–1557, 7695–7697 (1977). S. K. Srivastava and S. S. Katiyar, Ber. Bunsenges. Phys. Chem. 82:1214–1219 (1980).

239. 240. 241. 242. 243. 244. 245. 246. 247. 248. 249. 250. 251. 252.

253.

254. 255. 256. 257. 258.

259.

260.

261.

262. 263.

264.

265.

C. Minero, E. Premauro, and E. Pelizzetti, Langmuir 4:101–105 (1988). R. Da Rocha Pereira, D. Zanette, and F. Nome, J. Phys. Chem. 94:356–361 (1990). D. M. Davies, N. D. Gillitt, and P. M. Paradis, J. Chem. Soc. Perkin Trans. 2:659–666 (1996). D. M. Davies and S. J. Foggo, J. Chem. Soc. Perkin Trans. 2:247–251 (1998). J. L. Kurz, J. Am. Chem. Soc. 85:987–991 (1963). J. Kraut, Science 242:533–540 (1988). N. J. Buurma, A. M. Herranz, and J. B. F. N. Engberts, J. Chem. Soc. Perkin Trans. 2:113–119 (1999). A. R. Olson and J. R. J. Simonson, J. Chem. Phys. 17:1167–1173 (1949). J. N. Brønsted, Z. Phys. Chem. 102:169–207 (1922). J. N. Brønsted, Z. Phys. Chem. 115:337–364 (1925). C. A. Bunton, J. Mol. Liq. 72:231–249 (1997). E. H. Cordes, Pure Appl. Chem. 50:617–625 (1978). P. L. Lo`pez-Cornejo, R. Jime`nez, M. L. Moya`, F. Sa`nchez, and J. Burgess, Langmuir 12:4981–4986 (1996). R. Jime`nez, M. M. Graciami, R. Rodriguez, M. L. Moya`, F. Sa`nchez, and F. Lo`pez-Cornejo, Langmuir 13:187–191 (1997). F. Sanchez, M. L. Moya`, A. Rodriguez, R. Jeme`nez, C. Go`mez-Herrera, C. Yane`s, and P. Lo`pez-Cornejo, Langmuir 13:3084–3089 (1997). F. Muriel-Delgado, R. Jime`nez, C. Go`mez-Herrera, and F. Sanchez, Langmuir 15:4344–4350 (1999). D. S. Paul and K. G. Kemp, J. Am. Chem. Soc. 97: 7305–7312 (1975). A. J. Kirby and A. G. Varvoglis, J. Am. Chem. Soc. 89:415–423 (1967). L. Mandolini, Adv. Phys. Org. Chem. 22:1–111 (1986). V. R. Correia, I. M. Cuccovia, M. Stelmo, and H. Chaimovich, J. Am. Chem. Soc. 114:2144–2146 (1992). R. Germani, P. P. Ponti, T. Romeo, G. Savelli, N. Spreti, G. Cerichelli, L. Luchetti, G. Mancini, and C. A. Bunton, J. Phys. Org. Chem. 2:553–558 (1989). F. Del Rosso, A. Bartoletti, P. Di Profio, R. Germani, G. Savelli, A. Blasko´, and C. A. Bunton, J. Chem. Soc. Perkin Trans. 2:673–678 (1995). G. Cerichelli, L. Luchetti, G. Mancini, M. N. Muzzioli, R. Germani, P. P. Ponti, N. Spreti, and G. Savelli, J. Chem. Soc. Perkin Trans. 2:1081–1085 (1989). J. B. F. N. Engberts, Pure Appl. Chem. 64:1653–1660 (1992). P. Di Profio, R. Germani, G. Savelli, G. Cerichelli, N. Spreti, and C. A. Bunton, J. Chem. Soc. Perkin Trans. 2:1505–1509 (1996). R. Germani, P. P. Ponti, G. Savelli, N. Spreti, A. Cipiciani, G. Cerichelli, and C. A. Bunton, J. Chem. Soc. Perkin Trans. 2:1767–1771 (1989). C. A. Bunton, E. L. Dorwin, G. Savelli, and V. C. Si, Rec. Trav. Pays-Bas 109:64–69 (1990).

Reactivity Control by Self-Assembling Systems 266.

267. 268. 269.

270. 271. 272. 273. 274. 275. 276. 277. 278. 279. 280.

281.

282. 283. 284.

285. 286.

287.

288. 289.

M. Okahara, A. Masuyama, Y. Sumida, and Y. P. Zhu, J. Jpn. Oil Chem. Soc. (Yukagaku) 37:746–748 (1988). Y. P. Zhu, A. Masuyama, and M. Okahara, J. Am. Oil. Chem. Soc. 68:268–271 (1991). M. J. Rosen, Z. H. Zhu, and X. Y. Hua, J. Am. Oil. Chem. Soc. 69:30–33 (1992). A. Masuyama, T. Hirono, Y. P. Zhu, M. Okahara, and M. J. Rosen, J. Jpn. Oil Chem. Soc. (Yukagaku) 41: 301–305 (1992). F. Devinsky, I. Lacko, F. Bittererova, and L. Tomeckova, J. Colloid Interface Sci. 114:314–322 (1986). R. Zana, M. Benrraou, and R. Rueff, Langmuir 7: 1072–1075 (1991). F. M. Menger and C. A. Littau, J. Am. Chem. Soc. 113:1451–1452 (1991). F. M. Menger and C. A. Littau, J. Am. Chem. Soc. 115:10083–10090 (1993). M. Rosen, J. Chem. Tech. 23:30–33 (1993). L. D. Song and M. J. Rosen, Langmuir 12:1149–1153 (1996). G. Cerichelli, L. Luchetti, G. Mancini, and G. Savelli, Langmuir 15:2631–2634 (1999). M. S. Patel, K. Bijma, and J. B. F. N. Engberts, Langmuir 10:2491–2492 (1994). G. Cerichelli, G. Mancini, L. Luchetti, G. Savelli, and C. A. Bunton, J. Phys. Org. Chem. 4:71–76 (1991). G. Cerichelli, G. Mancini, L. Luchetti, G. Savelli, and C. A. Bunton, Langmuir 10:3982–3987 (1994). L. Brinchi, P. Di Profio, R. Germani, V. Giacomini, G. Savelli, and C. A. Bunton, Langmuir 16:222–226 (2000). C. A. Bunton, in Nucleophilicity (J. M. Harris and S. P. McManus, eds.), Adv. Chem. Ser. No. 215, American Chemical Society, Washington, DC, 1987, pp. 425–441. N. Fadnavis and J. B. F. N. Engberts, J. Org. Chem. 47:152–154 (1982). N. J. Buurma, A. M. Herranz, and J. B. F. N. Engberts, J. Chem. Soc. Perkin Trans. 2:113–119 (1999). L. Brinchi, P. Di Profio, R. Germani, G. Savelli, and C. A. Bunton, J. Chem. Soc. Perkin Trans. 2:361–364 (1998). C. A. Bunton, M. M. Mhala, and J. R. Moffatt, J. Org. Chem. 50:4921–4924 (1985). A. Bartoletti, S. Bartolini, R. Germani, G. Savelli, and C. A. Bunton, J. Chem. Soc. Perkin Trans. 2:723–728 (1994). R. Germani, G. Savelli, N. Spreti, G. Cerichelli, G. Mancini, and C. A. Bunton, Langmuir 9:61–65 (1993). H. A. Al-Lohedan, J. Chem. Soc. Perkin Trans. 2: 1181–1185 (1989). C. Bonan, R. Germani, P. P. Ponti, G. Savelli, G. Cerichelli, R. Bacaloglu, and C. A. Bunton, J. Phys. Chem. 94:5331–5336 (1990).

243 290. 291. 292. 293. 294. 295. 296. 297. 298. 299. 300.

301. 302. 303.

304. 305. 306.

307. 308. 309. 310. 311. 312. 313. 314. 315. 316.

317.

R. Germani, G. Savelli, T. Romeo, N. Spreti, G. Cerichelli, and C. A. Bunton, Langmuir 9:55–60 (1993). K. A. Wilk and B. Burczyk, J. Phys. Chem. 93:8219– 8223 (1989). K. A. Wilk, J. Phys. Chem. 93:7432–7435 (1989). L. Brinchi, P. Di Profio, R. Germani, G. Savelli, and C. A. Bunton, Langmuir 13:4583–4587 (1997). R. G. Pearson, Science 151:1721–1727 (1966). R. G. Pearson and J. Songstad, J. Am. Chem. Soc. 89: 1827–1836 (1967). R. Bacaloglu, C. A. Bunton, and F. Ortega, J. Phys. Chem. 93:1497–1502 (1989). R. Bacaloglu, C. A. Bunton, G. Cerichelli, and F. Ortega, J. Phys. Chem. 94:5068–5073 (1990). R. Bacaloglu, A. Blasko´, C. A. Bunton, G. Cerichelli, and F. Ortega, J. Phys. Chem. 94:5062–5068 (1990). G. Cerichelli, M. Coreno, and G. Mancini, J. Colloid Interface Sci. 158:33–39 (1993). L. Brinchi, R. Germani, G. Savelli, N. Spreti, R. Ruzziconi, and C. A. Bunton, Langmuir 14:2656–2661 (1998). T. J. Broxton, J. R. Christie, and R. P.-T. Chung, Aust. J. Chem. 42:855–864 (1989). C. D. Ritchie and M. Sawada, J. Am. Chem. Soc. 99: 3754–3761 (1977). C. A. Bunton, H. J. Foroudian, N. D. Gillitt, and C. R. Whiddon, J. Colloid Interface Sci. 215:64–71 (1999). C. A. Bunton, S. Wright, P. M. Holland, and F. Nome, Langmuir 9:117–120 (1993). H. A. Al-Lohedan, A. M. Al-Sulaim, A. S. Al-Ayed, and Z. A. Issa, J. Chem. Res. (S):470–471 (1993). M. Politi, I. M. Cuccovia, H. Chaimovich, M. L. C. Almeida, J. B. S. Bonilha, and F. H. Quina, Tetrahedron Lett. 115–118 (1978). M. J. Politi and H. Chaimovich, J. Phys. Org. Chem. 4:207–216 (1991). H. A. Al-Lohedan, A. M. Al-Sulaim, A. S. Al-Ayed, and Z. A. Issa, J. Chem. Res. (S) 100–101 (1993). H. A. Al-Lohedan, J. Chem. Res (S) 200 (1991). F. P. Cavasino, R. Cervellati, R. Lombardo, and M. L. Turco Livieri, J. Phys. Chem. 103:4285–4291 (1999). H. A. Al-Lohedan, J. Phys. Chem. 94:8226–8231 (1990). G. B. van de Langkruis and J. B. F. N. Engberts, J. Org. Chem. 49:4152–4157 (1984). G. Cerichelli, C. Grande, L. Luchetti, and G. Mancini, J. Org. Chem. 56:3025–3030 (1991). T. J. Broxton and V. Marcou, J. Org. Chem. 56:1041– 1044 (1991). C. A. Bunton, M. M. Mhala, and J. R. Moffatt, J. Phys. Chem. 93:854–858 (1989). P. Di Profio, L. Brinchi, R. Germani, G. Savelli, G. Cerichelli, and C. A. Bunton, J. Chem. Soc. Perkin Trans. in press. L. Brinchi, C. Dionigi, P. Di Profio, R. Germani, G. Savelli, and C. A. Bunton, J. Colloid Interface Sci. 211:179–184 (1999).

244 318.

319. 320. 321. 322.

323.

324. 325. 326.

327.

328. 329. 330. 331. 332. 333. 334. 335. 336. 337. 338. 339. 340.

341. 342.

Savelli et al. S. Brochsztain, P. B. Filho, V. G. Toscano, H. Chaimovich, and M. J. Politi, J. Phys. Chem. 94:6781– 6785 (1990). L. Brinchi, R. Germani, G. Savelli, and C. A. Bunton, J. Phys. Org. Chem. 12:890–894 (1999). A. D. Bangham and R. W. Horne, J. Mol. Biol. 8: 660–668 (1964). T. Kunitake, Y. Okahata, K. Tamaki, F. Kumamuro, and M. Yakayanagi, Chem. Lett. 387–390 (1977). R. A. Mortara, F. H. Quina, and H. Chaimovich, Biochem. Biophys. Res. Commun. 81:1080–1086 (1978). Y. Q. Liang, L. X. Wu, Y. C. Tian, Z. Q. Zhang, and H. D. Chen, J. Colloid Interface Sci. 178:703–713 (1996). H. Hoffmann, D. Grabner, U. Hornfeck, and G. Platz, J. Phys. Chem. B 103:611–614 (1999). Y. Hisaeda, E. Ohshima, J. Kikuchi, and Y. Murakami, Tetrahedron Lett. 38:6713–6716 (1997). A. T. Florence, P. Arunothayanum, S. Kiri, M. S. Bernard, and I. F. Uchegbu, J. Phys. Chem. B 103:1995– 2000 (1999). D. A. Vanhal, J. A. Bouwstra, A. Vanrensen, E. Jeremiasse, T. Devringer, and H. E. Junginger, J. Colloid Interface Sci. 178:263–273 (1996). M. Ambu¨hl, F. Bangerter, P. L. Luisi, P. Skrabal, and H. J. Watzke, Langmuir 9:36–38 (1993). M. Villeneuve, S. Kaneshina, T. Imae, and M. Aratono, Langmuir 15:2029–2036 (1999). E. F. Marques, O. Regev, A. Khan, M. D. Miguel, and B. Lindman, J. Phys. Chem. B 102:6746–6758 (1998). M. Bergstrom and J. S. Pedersen, Langmuir 14:3754– 3761 (1998). D. Duque, P. Tarazona, and E. Chacoń, Langmuir 14: 6827–6834 (1998). R. Wick, P. Walde, and P. L. Luisi, J. Am. Chem. Soc. 117:1435–1436 (1995). A. Veronese and P. L. Luisi, J. Am. Chem. Soc. 120: 2662–2663 (1998). P. L. Luisi and P. Walde, Giant Vesicles, Wiley, Chichester, UK, 1999. H. Ringsdorf, B. Schlarb, and I. Venzmer, Angew. Chem. Int. Ed. Engl. 27:113–158 (1988). F. M. Menger and K. D. Gabrielson, Angew. Chem. Int. Ed. Engl. 34:2091–2106 (1995). F. M. Menger and I. S. Keiper, Adv. Mater. 10:888– 890 (1998). E. M. Menger and I. S. Keiper, Curr. Opin. Chem. Biol. 2:726–732 (1998). E. Sackmann, in Structure and Dynamics of Membranes. Handbook of Biological Physics (R. Lipowsky and E. Sackmann, eds.), vol. 1, Elsevier, Amsterdam, 1995, p. 213. A. M. Carmona-Ribeiro, Synthetic amphiphile vescicles, Chem. Soc. Rev. 209–214 (1992). A. M. Carmona-Ribeiro and H. Chaimovich, Biochim. Biophys. Acta 733:172–179 (1983).

343.

344. 345.

346. 347. 348. 349. 350.

351. 352. 353. 354. 355. 356. 357.

358. 359. 360. 361.

362. 363. 364. 365. 366. 367. 368.

A. M. Carmona-Ribeiro, L. S. Yoshida, A. Sesso, and H. Chaimovich, J. Colloid Interface Sci. 100:433–443 (1984). Y.-C. Chung and S. L. Regen, Langmuir 9:1937–1939 (1993). D. B. Nascimento, R. Rapuano, M. M. Lessa, and A. M. Carmona-Ribeiro, Langmuir 14:7387–7391 (1998). C. Kang and A. Khan, J. Colloid Interface Sci. 156: 218–228 (1993). O. Regev, C. Kang, and A. Khan, J. Phys. Chem. 98: 6619–6625 (1994). J. H. Fendler and W. L. Hinze, J. Am. Chem. Soc. 103:5439–5447 (1981). I. M. Cuccovia, F. H. Quina, and H. Chaimovich, Tetrahedron 38:917–920 (1982). H. Chaimovich, J. B. S. Bonilha, D. Zanette, and I. M. Cuccovia, in Surfactants in Solution (K. L. Mittal and B. Lindmann, eds.), New York, Plenum, 1984, pp. 1121–1138. E. A. Abuin, E. B. Lissi, E. Backer, A. Zanocco, and D. Whitten, J. Phys. Chem. 93:4886–4890 (1989). I. M. Cuccovia, H. Chaimovich, E. B. Lissi, and E. A. Abuin, Langmuir 6:1601–1604 (1990). J. Furhop and J. Mathieu, Angew. Chem. Int. Ed. Engl. 23:100–113 (1984). H. Chaimovich and I. M. Cucovia, Prog. Colloid Polym. Sci. 103:67–77 (1997). A. M. Carmona-Ribeiro, L. S. Yoshida, and H. Chaimovich, J. Phys. Chem. 89:2928–2933 (1985). I. M. Cuccovia, E. S. Feitosa, H. Chaimovich, and W. Reed, J. Phys. Chem. 94:3722–3725 (1990). M. K. Kawamuro, H. Chaimovich, E. B. Abuin, E. A. Lissi, and I. M. Cuccovia, J. Phys. Chem. 95:1458– 1463 (1991). I. M. Cuccovia and H. Chaimovich, Bol. Soc. Chil. Quim. 35:39–42 (1990). R. A. Moss, S. Ganguli, Y. Okumura, and T. Fujita, J. Am. Chem. Soc. 112:6391–6392 (1990). E. S. Feitosa, A. Agostinho, and H. Chaimovich, Langmuir 9:702–707 (1993). I. M. Cuccovia, M. K. Kawamuro, M. A. K. Krutman, and H. Chaimovich, J. Am. Chem. Soc. 111:365–366 (1989). R. A. Moss, S. Bhattacharya, P. Scrimin, and S. Swarup, J. Am. Chem. Soc. 109:5740–5744 (1987). R. A. Moss, S. Bhattacharya, and S. Chatterjee, J. Am. Chem. Soc. 111:3680–3687 (1989). R. A. Moss, Pure Appl. Chem. 66:851–858 (1994). S. A. Buckingham, C. J. Garvey, and G. G. Warr, J. Phys. Chem. 97:10236–10244 (1993). C. E. Drennan, R. J. Hughes, V. C. Reinsborough, and O. O. Soriyan, Can. J. Chem. 76:152–157 (1998). M. del M. Graciani, A. Rodriguez, G. Fernandez, and M. L. Moya, Langmuir 13:4239–4245 (1997). T. Kunitake, Y. Okahata, R. Ando, S. Shinkai, and S. Hirakawa, J. Am. Chem. Soc. 102:7877–7881 (1980).

Reactivity Control by Self-Assembling Systems 369. 370. 371. 372. 373. 374. 375. 376. 377. 378. 379.

380.

381.

382.

383. 384.

385. 386.

387. 388.

389. 390.

391. 392.

C. A. Bunton, Y. S. Hong, L. S. Romsted, and C. Quan, J. Am. Chem. Soc. 103:5784–5788 (1981). G. Biresaw, C. A. Bunton, C. Quan, and Z.-Y. Yang, J. Am. Chem. Soc. 106:7178–7184 (1984). G. Biresaw and C. A. Bunton, J. Phys. Chem. 90: 5849–5853 (1986). G. Biresaw and C. A. Bunton, J. Phys. Chem. 90: 5854–5858 (1986). G. Gerichelli, G. Mancini, L. Luchetti, G. Savelli, and C. A. Bunton, Langmuir 10:3982–3987 (1994). A. Blasko´, C. A. Bunton, and H. Fourodian, J. Colloid Interface Sci. 163:500–506 (1994). R. Bacaloglu and C. A. Bunton, J. Colloid Interface Sci. 153:140–151 (1992). N. Shufang, K. R. Gopidas, N. J. Turro, and G. Gabor, Langmuir 8:1271–1277 (1992). C. A. Bunton and C. Quan, J. Org. Chem. 50:3230– 3234 (1985). C. Tondre and M. Hebrant, J. Mol. Liq. 72:279–294 (1997). J. F. Scamehorn, S. D. Christian, and R. T. Ellington, in Surfactant-Based Separation Processes (J. F. Scamehorn and J. H. Harwell, eds.), Surfactant Science Series, Marcel Dekker, New York, 1989. E. Pramauro, A. Bianco Prevot, P. Savarino, G. Viscardi, M. De la Guardia, and E. P. Cardells, Analyst 118:23–27 (1993). H. Uchiyama, S. D. Christian, E. E. Tucker, and J. F. Scamehorn, J. Colloid Interface Sci. 163:493–499 (1994). M. He´rbant, P. Mettelin, C. Tondre, J. P. Joly, C. Larpent, and X. Chasseray, Colloids Surf. A Physicochem. Eng. Aspects 75:257–267 (1993). W. L. Hinze, R. W. Williams, Z. S. Fu, Y. Suzuki, and F. H. Quina, Colloids Surf. 48:79–94 (1990). A. L. Creagh, B. B. Hasenack, A. Van der Padt, E. J. Sudho¨lter, and K. Van’t Riet, Biotechnol. Bioeng. 44: 690–698 (1994). D. C. Tickle, G. N. Okafo, P. Camilleri, R. F. D. Jones, and A. J. Kirby, Anal. Chem. 66:4121–4126 (1994). V. de Biasi, J. Senior, J. A. Zukowski, R. C. Haltiwanger, D. E. Eggleston, and P. Camilleri, J. Chem. Soc. Chem. Commun. 1575–1576 (1995). M. Bouzige, G. Okafo, D. Dhanak, and P. Camilleri, J. Chem. Soc. Chem. Commun. 671–672 (1996). D. Tickle, A. George, K. Jennings, P. Camilleri, and A. J. Kirby, J. Chem. Soc. Perkin Trans. 2:467–474 (1998). A. Xenakis and C. Tondre, J. Phys. Chem. 87:4737– 4743 (1983). C. Tondre and A. Xenakis, in Surfactants in Solution (K. L. Mittal and B. Lindman, eds.), vol. 3, Plenum, New York, 1984, pp. 1881–1896. A. Derouiche and C. Tondre, J. Chem. Soc. Faraday Trans. 1 85:3301–3308 (1989). A. Derouiche and C. Tondre, Colloids Surf. 48:243– 258 (1990).

245 393. 394. 395. 396. 397. 398. 399.

400. 401. 402. 403.

404. 405.

406.

407. 408. 409.

410.

411. 412. 413. 414. 415. 416. 417.

C. Tondre and A. Derouiche, J. Phys. Chem. 94:1624– 1626 (1990). D. W. Osborne, A. J. Ward, and K. J. O’Neill, J. Pharm. Pharmacol. 43:451–454 (1991). J. Kemken, A. Ziegler, and B. W. Muller, Pharm. Res. 9:554–558 (1992). T. Akao, T. Osaki, J. Mitoma, A. Ito, and T. Kunitake, Bull. Chem. Soc. Jap. 64:3677–3681 (1991). R. Levantis and J. R. Silvius, Biochim. Biophys. Acta 1023:124–132 (1990). P. Pinnaduwage, L. Schmitt, and L. Huang, Biochim. Biophys. Acta 985:33–37 (1989). P. L. Felgner, T. R. Gadek, M. Holm, R. Ronas, H. W. Chan, M. Wenz, J. P. Northrop, G. M. Ringold, and M. Danielsen, Proc. Natl. Acad. Sci. U.S.A. 84:7413– 7417 (1987). B. J. Roessler and B. L. Davidson, Neurosci. Lett. 167:5–10 (1994). J. Y. Legendre and F. C. Szoka, Proc. Natl. Acad. Sci. U.S.A. 90:893–897 (1993). Y. Watanabe, H. Nomoto, R. Takezawa, N. Miyoshi, and T. Akaike, J. Biochem. 116:1220–1226 (1994). I. Van der Woude, H. W. Visser, M. B. A. Ter Beest, A. Wagenaar, M. H. J. Ruiters, J. B. F. N. Engberts, and D. Hoekstra, Biochim. Biophys. Acta 1240:34–40 (1995). H. Gherson, R. Ghirlando, S. B. Guttman, and A. Minsky, Biochemistry 32:7143–7151 (1993). G. Mathis, P. Leempoel, J. C. Ravey, C. Selve, and J. J. Delpuech, J. Am. Chem. Soc. 106:6162–6171 (1984). G. N. Ta´pias, S. M. Sicchierolli, E. M. Mamizuka, and A. M. Carmona-Ribeiro, Langmuir 10:3461–3465 (1994). S. M. Sicchierolli, E. M. Mamizuka, and A. M. Carmona-Ribeiro, Langmuir 11:2991–2995 (1995). L. M. S. Martins, E. M. Mamizuka, and A. M. Carmona-Ribeiro, Langmuir 13:5583–5587 (1997). A. M. Carmona-Ribeiro, F. Ortis, R. I. Schumacher, and M. C. S. Armelin, Langmuir 13:2215–2218 (1997). L. R. Tsuruta, W. Quintilio, M. H. B. Costa, and A. M. Carbona-Ribeiro, J. Lipids Res. 38:2003–2011 (1997). P. L. Felgner, Adv. Drug Delivery Rev. 5:163–187 (1990). J. P. Behr, Acc. Chem. Res. 26:274–278 (1993). A. M. Carmona-Ribeiro and B. R. Midmore, Langmuir 8:801–806 (1992). M. M. Lessa and A. M. Carmona-Ribeiro, J. Colloid Interface Sci. 182:166–171 (1996). L. R. Tsuruta and A. M. Carmona-Ribeiro, J. Phys. Chem. 100:7130–7134 (1996). L. R. Tsuruta, M. M. Lessa, and A. M. Carmona-Ribeiro, J. Colloid Interface Sci. 175:470–475 (1995). R. Rapuano and A. M. Carmona-Ribeiro, J. Colloid Interface Sci. 193:104–111 (1997).

246 418. 419.

420. 421. 422. 423. 424. 425. 426.

427. 428. 429. 430. 431. 432. 433. 434. 435. 436. 437. 438. 439.

440. 441. 442. 443.

Savelli et al. L. C. Salay and A. M. Carmona-Ribeiro, J. Phys. Chem. B 102:4011–4015 (1998). D. Katz, C. A. Kraaijeveld, and H. Snippe, in The Theory and Practical Application of Adjuvants (D. E. S. Stewart-Tull, ed.), Wiley, New York, 1994. R. H. Smith and B. Ziola, Immunology 58:245–250 (1986). F. M. Menger and H. Park, Rec. Trav. Chim. PaysBas 113:176–180 (1994). S. G. Oh, J. Kizling, and K. Holmberg, Colloids Surf. A Physicochem. Eng. Aspects 97:169–179 (1995). R. A. Moss, A. T. Kotchevar, B. D. Park, and P. Scrimin, Langmuir 12:2200–2206 (1996). R. A. Moss and S. Bose, Tetrahedron Lett. 38:965– 968 (1997). D. A. Jaeger and M. R. Frey, J. Org. Chem. 47:311– 315 (1982). D. A. Jaeger, J. Jamrozik, T. G. Golich, M. W. Clennan, and J. Mohebalian, J. Am. Chem. Soc. 111:3001– 3006 (1989). D. A. Jaeger, Y. M. Sayed, and A. K. Dutta, Tetrahedron Lett. 31:449–450 (1990). K. R. Nivalkar, C. D. Mudaliar, and S. H. Mashraqui, J. Chem. Res. (S):98–99 (1992). C. D. Mudaliar and S. H. Mashraqui, J. Chem. Res. (S):174–175 (1994). S. Kobayashi, T. Busujima, and S. Nagayama, Synlett 545–546 (1999). K. Manabe, Y. Mori, and S. Kobayashi, Synlett 1401– 1402 (1999). T. Akiyama, J. Takaya, and H. Kagoshima, Synlett 1426–1428 (1999). S. Kobayashi, T. Wakabayashi, and H. Oyamada, Chem. Lett. 831–832 (1997). S. Kobayashi, T. Wakabayashi, S. Nagayama, and H. Oyamada, Tetrahedron Lett. 38:4559–4562 (1997). S. Kobayashi, T. Busujima, and S. Nagayama, J. Chem. Soc. Chem. Commun. 19–20 (1998). R. P. Bonar-Law, J. Org. Chem. 61:3623–3634 (1996). C. Siswanto, T. Battal, O. E. Schuss, and J. F. Rathman, Langmuir 13:6047–6052 (1997). T. Battal, C. Siswanto, and J. F. Rathman, Langmuir 13:6053–6057 (1997). L. Brinchi, P. Di Profio, R. Germani, G. Savelli, and C. A. Bunton, Colloids Surf. A Physicochem. Eng. Aspects 132:303–314 (1998). G. Cerichelli, L. Luchetti, and G. Mancini, Tetrahedron Lett. 30:6209–6210 (1989). G. Cerichelli, G. Mancini, and L. Luchetti, Tetrahedron 50:3797–3802 (1994). D. A. Jaeger and J. Wang, Tetrahedron Lett. 33:6415– 6418 (1992). S. Otto, B. F. N. Engberts, and J. C. T. Kwak, J. Am. Chem. Soc. 120:9517–9525 (1998).

444. 445. 446.

447. 448.

449. 450. 451. 452. 453. 454. 455. 456. 457. 458.

459. 460. 461. 462. 463. 464. 465. 466. 467. 468. 469.

D. A. Jaeger, H. Shinozaki, and P. A. Goodson, J. Org. Chem. 56:2482–2489 (1991). D. Monti, P. Tagliatesta, G. Mancini, and T. Boschi, Angew. Chem. Int. Ed. Engl. 37:1131–1133 (1998). C. Denis, B. Laignel, D. Plusquellec, J. Y. Le Marouille, and A. Botrel, Tetrahedron Lett. 37:53–56 (1996). M. C. Cleij, W. Drenth, and R. J. M. Nolte, Rec. Trav. Chim. Pays-Bas 112:1–6 (1993). S. I. Goldberg, N. Baba, R. L. Green, R. Poudian, J. Stowers, and R. B. Dunlop, J. Am. Chem. Soc. 100: 6768–6769 (1978). Y. M. Zhang and W. Li, Synth. Commun. 18:1685– 1689 (1988). Y. M. Zhang, W. Q. Fan, P. Lu, and W. Wang, Synth. Commun. 18:1495–1500 (1988). Y. M. Zhang, C. L. Fu, and W. Q. Fan, Chin. J. Chem. 1:89–96 (1990). Y. Zhang and W. Wu, Tetrahedron Asymmetry 8: 3575–3578 (1997). Y. Zhang and W. Wu, Tetrahedron Asymmetry 8: 2723–2725 (1997). M. J. Diego-Castro and H. C. Hailes, J. Chem. Soc. Chem. Commun. 1549–1550 (1998). D. Brosch and W. Kirmse, J. Org. Chem. 58:1118– 1121 (1993). R. Selke, J. Holz, A. Riepe, and A. Bo¨rner, Chem. Eur. J. 4:769–771 (1998). G. M. Whitesides, Angew. Chem. Int. Ed. Engl. 29: 1209–1218 (1990). J. M. Lehn, Supramolecular Chemistry. Concepts and Perspectives. A Personal Account, VCH, Weinheim, 1995. G. Cerichelli, L. Luchetti, G. Mancini, G. Savelli, and C. A. Bunton, Langmuir 12:2348–2352 (1996). A. Cuenca, C. Bruno, and A. Taddei, Tetrahedron 50: 1927–1934 (1994). ˜ J. Chem. Soc. A. Castro, J. R. Leis, and M. E. Pena, Perkin Trans. 2:1221–1225 (1990). T. J. Broxton and S. Wright, Aust. J. Chem. 44:103– 111 (1991). A. Cipiciani and S. Primieri, Tetrahedron 47(1):83–90 (1991). J. Burgess and M. S. Patel, J. Chem. Soc. Faraday Trans. 89:783–787 (1993). G. Fernańdez, M. Graciani, A. Rodrı´guez, F. Ferranti, and M. L. Moya´, Langmuir 15:4441–4446 (1999). C. A. Bunton, M. M. Mhala, and J. R. Moffatt, J. Phys. Chem. 93:7851–7856 (1989). M. N. Khan and Z. Arifin, Langmuir 13:6626–6632 (1997). M. N. Khan, Langmuir 13:2498–2503 (1997). ˜ M. Munoz, A. Rodrı´guez, M. Graciani, and M. L. Moya´, Langmuir 15:1588–1590 (1999).

9 Diels-Alder Reactions in Micellar Media SIJBREN OTTO* and JAN B. F. N. ENGBERTS The Netherlands

I.

University of Groningen, Groningen,

INTRODUCTION TO DIELS-ALDER REACTIONS

Reactivity and selectivity in Diels-Alder reactions are often rationalized in terms of frontier molecular orbital (FMO) theory [3], emphasizing interactions between the highest occupied molecular orbital (HOMO) of one of the reaction partners and the lowest unoccupied molecular orbital (LUMO) of the other. During formation of the two new ␴-bonds, orbital symmetry is conserved. Therefore no intermediate is involved and the pericyclic reaction is concerted. There is ample experimental and theoretical evidence for the concerted mechanism [4]. Only in relatively rare cases does the Diels-Alder reaction take place via a nonconcerted two-step mechanism, involving either a zwitterionic or a biradical mechanism and leading to modified stereochemistry. FMO theory has been useful in analyzing possible asynchronicity in the activation process and in predicting kinetically controlled regioselectivity for Diels-Alder processes involving asymmetric dienes in combination with asymmetric dienophiles [5]. Much attention has also been given to Diels-Alder reactions that provide endo and exo cycloadducts (Fig. 2). The endo-exo ratio is usually the result of relatively small differences in transition state energies which appear to be primarily determined by secondary orbital interactions [6,7]. The formation of the endo product is associated with the most compact activated complex and exhibits the most negative volume of activation. Apart from secondary orbital interactions, other factors have been proposed for explaining the endo-exo ratio, including steric effects, London-dispersion interactions, and solvent effects (e.g., [8]).

The Diels-Alder reaction is a [4⫹2]cycloaddition in which a diene (four-␲ component) reacts with a dienophile (two-␲ component) to provide a six-membered ring (Fig. 1). Six new stereocenters are formed in a single reaction step. Because the conformations of the double bonds are usually fully retained, the reaction is stereospecific and consequently the absolute configuration of the two newly formed asymmetric centers can be controlled efficiently. The Diels-Alder reaction is of great value in organic synthesis and is a key step in the construction of compounds containing six-membered rings [1]. A historic account of this important conversion has been published by Berson [2]. Homo Diels-Alder reactions involve only hydrocarbon fragments. If the diene or dienophile possesses heteroatoms in any of the positions a–f (Fig. 1), heterocyclic ring systems are formed (hetero Diels-Alder reactions). Normal electron demand Diels-Alder reactions are promoted by electron-donating substituents in the diene and electron-withdrawing substituents in the dienophile. The opposite situation applies for inverse electron demand Diels-Alder reactions. Neutral Diels-Alder reactions are accelerated by both electron-withdrawing and electron-donating substituents.

*Current affiliation: University of Cambridge, Cambridge, England. 247

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Otto and Engberts TABLE 1 Second-Order Rate Constants k2 for the Dimerization of Cyclopentadiene in Solution and in the Gas Phase at 25⬚C

FIG. 1 Schematic representation of the Diels-Alder reaction. The versatility of the reaction is illustrated by the fact that heteroatoms are allowed at any of the positions a–f. Structures (a) and (b) indicate two regioisomeric products.

This chapter will describe micellar effects on DielsAlder reactions with respect to both reaction rates and stereochemical aspects. For a proper understanding of the effects induced by micelles, we will first briefly review what is known about medium and catalytic effects on Diels-Alder cycloadditions. A.

Medium and Catalytic Effects on Diels-Alder Reactions

The Diels-Alder reaction is a textbook example of a reaction that is rather indifferent toward the choice of the solvent. An extreme example [9] is the dimerization of cyclopentadiene (Table 1), but for many other homoand also for hetero Diels-Alder reactions, rate constants

FIG. 2 Endo and exo pathway for the Diels-Alder reaction of cyclopentadiene with methyl vinyl ketone. As was first noticed by Berson, the polarity of the endo activated complex exceeds that of the exo counterpart due to alignment of the dipole moments of the diene and the dienophile [17]. The symmetry-allowed secondary orbital interaction that is possible only in the endo activated complex is usually invoked as an explanation for the preference for endo adduct exhibited by most Diels-Alder reactions.

Solvent/state

k2 (M⫺1 s⫺1)

Gas phase Neat Carbon tetrachloride Nitrobenzene Ethanol

6.9 5.6 7.9 13 19

⫻ ⫻ ⫻ ⫻ ⫻

10⫺7 10⫺7 10⫺7 10⫺7 10⫺7

Source: Data from Ref. 9.

in a series of organic solvents vary only modestly. Nevertheless, attempts have been made to correlate kinetic data with solvent parameters, both for pure solvents and for binary mixtures [10,11]. Multiparameter analyses of solvent effects on Diels-Alder reactions have been carried out. For example, Gajewski [12] observed a dependence of rate constants for Diels-Alder reactions on the solvent ␣-parameter and the cohesive energy density. Intramolecular Diels-Alder reactions in highly viscous media have been related to the solvent density, which affects the translational motion of the reactants [13]. Rather unusual reaction media that have been employed for accelerating Diels-Alder reactions include solutions of lithium perchlorate in diethyl ether, dichloromethane, and nitromethane [14]. After considerable debate, it was argued that the substantial rate enhancements are largely due to Lewis acid catalysis by the lithium cation [15]. It is generally agreed that the small or modest solvent effects on the rates of Diels-Alder reactions are in accord with the concerted character of the cycloaddition that involves only a rather insignificant change of charge distribution during the activation process. The effect of the reaction medium on the regioselectivity of Diels-Alder reactions can be rationalized in terms of the FMO theory [16]. In particular, the hydrogen bond donating character of the solvent, as expressed in the ␣-parameter, affects the orbital coefficients on the terminal atoms of diene and dienophile. Medium effects on the endo-exo ratios have received extensive attention, and Berson et al. have even based an empirical solvent polarity scale [⍀ = log(endo/exo)] on the selectivity of the Diels-Alder reaction between methylacrylate and cyclopentadiene [17]. Solvent effects on the diastereofacial selectivity of the DielsAlder process have also been examined and interpreted [18]. Other factors that have been studied with the aim of increasing the rate and stereoselectivity of Diels-Alder

Diels-Alder Reactions in Micellar Media

reactions include external pressure [19], ultrasound irradiation [20], and catalytic effects exercised by clays [21], alumina [22], silica gels [23], microporous organic crystals [24], antibodies [25], cyclodextrins [26,27], and supramolecular assemblies [28,29]. By far the most effective enhancements of rate and selectivity are induced by Lewis acids [30–33]. Studies of Lewis acid catalysis of Diels-Alder reactions have been almost completely restricted to organic solvents and binary mixtures of low water content. However, highly efficient Lewis acid catalysis has been observed for Diels-Alder reactions in purely aqueous media [34–38]. The remarkable effects of Lewis acids on the kinetics of Diels-Alder reactions have been known since the early 1960s [30] and may involve accelerations of 104 to 106 in organic solvents. Also the endo/exo selectivity may clearly respond to the presence of Lewis acids such as AlCl3 ⭈ OEt2 [31]. Similarly, the regioselectivity [32] and diastereofacial selectivity [33] may be increased in the presence of Lewis acids. The mechanism of Lewis acid catalysis can be understood with the aid of the FMO theory. Binding of the Lewis acid catalyst will lower the energy of the LUMO of the reactant to which it is coordinated. This binding will decrease the HOMO-LUMO energy difference, which will in turn increase the rate of the Diels-Alder cycloaddition. It has also been proposed that binding of the Lewis acid catalyst leads to increased secondary orbital interactions, thereby increasing the endo/exo ratio [39]. Other consequences of the coordination of a Lewis acid catalyst have also been considered, including an increase of asynchronicity in the formation of the activated complex [40]. Solvent effects on the efficiency of Lewis acid catalysis of Diels-Alder reactions have received relatively little attention [41]. At present, Lewis acid catalysis of DielsAlder reactions is in everyday practice in synthetic organic chemistry. B.

Special Effects of Water on Diels-Alder Reactions

For a long time water was not a popular solvent for Diels-Alder reactions, although the pioneers Diels and Alder performed the reaction between furan and maleic acid in an aqueous medium in 1931 [42]. The latter experiment was repeated by Woodward and Baer in 1948, and a change in the endo/exo ratio was noted [43]. In 1973, Huisman et al. for the first time noticed a favorable aqueous effect on the rate of the same reaction, but the effect was not further explored [44]. Also, in two early patents the Diels-Alder reaction is

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mentioned in connection with water as the reaction medium [45]. A breakthrough came in 1980 in the work of Breslow and Rideout [26], who observed a substantial rate increase for simple Diels-Alder reactions in pure water. In subsequent extensive research it was shown that these remarkable kinetic aqueous medium effects are a general phenomenon [46–48]. Depending on the chemical structure of diene and dienophile, rate enhancements in water relative to organic solvents may amount to factors of more than 104. Rather soon after Breslow’s pioneering work, synthetic applications of Diels-Alder reactions in aqueous media were explored in some detail, in particular by Grieco and his coworkers [48]. Of course, the often limited solubility of diene and dienophile is a major drawback. In elegant work, Lubineau et al. have tackled this problem by employing dienes that were rendered water soluble by the temporary introduction of a sugar moiety in the molecule [49]. The scaling up of aqueous Diels-Alder reactions has also been studied [50]. Ever since the early work of Breslow, many studies have been devoted to the identification of the special effects of the aqueous reaction medium that lead to the remarkable rate accelerations. These studies have been reviewed [46,47]. After considerable debate and controversy, it is now almost generally agreed that the enhanced reactivity in water is the result of two major effects: the hydrogen bond donating capacity of water and enforced hydrophobic interactions [51,52]. Previous suggestions that preassociation of the reactants in water played an important role were not substantiated. For example, vapor pressure measurements indicated that cyclopentadiene did not form aggregates at concentrations used in the kinetic measurements. Similar observations were made for methyl vinyl ketone, a popular dienophile in mechanistic studies of Diels-Alder reactions in water. The peculiar nature of the Diels-Alder reaction in water was clearly revealed in a study in which Gibbs energies for the Diels-Alder reaction of cyclopentadiene with ethyl vinyl ketone over the whole mole fraction range in the mixture of 1-propanol with water were combined with Gibbs energies of transfer of the diene and dienophile from 1-propanol to the aqueous mixture and to pure water [51,53]. These data showed that the initial state (diene ⫹ dienophile) is significantly destabilized in water relative to 1-propanol (Fig. 3). By contrast, the activated complex has nearly equal chemical potentials in water and in 1-propanol. Consequently, in aqueous solution the hydrophobic parts of the activated complex have completely lost their nonpolar character

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effect of the aqueous medium are also of immediate relevance for understanding the effects of water on the endo-exo ratios and on the diastereofacial- and regioselectivity. Finally, we briefly note that studies in the 1990s have shown that many other organic reactions benefit from the use of water as the reaction medium [48,59– 62]. II. FIG. 3 Chemical potential of the initial state, the transition state, and the product of the Diels-Alder reaction between methyl vinyl ketone and cyclopentadiene in water as compared with 1-propanol. (Data from Ref. 53.)

as far as solvation is concerned. This conclusion has been confirmed in subsequent studies [52,54]. During the activation process of the Diels-Alder reaction, hydrophobic parts of the diene and the dienophile approach each other closely, a process that is particularly favorable in water (‘‘enforced’’ hydrophobic interaction) compared with nonaqueous reaction media. The term ‘‘enforced’’ is used to stress the fact that the approximation of the nonpolar reagents is driven by the reaction and only enhanced by water. In addition, the electron redistribution that takes place during the activation process leads to an enhanced electron density at the carbonyl oxygen atom of ethyl vinyl ketone and a consequent enhanced propensity for hydrogen bond interaction with a hydrogen bond donating solvent. The small size of water molecules allows a particularly efficient interaction with hydrogen-bond acceptor sites. The medium effects on the chemical potentials, as shown in Fig. 3, are fully consistent with the operation of the hydrophobic and hydrogen-bonding effect. Beautifully detailed computational studies by Jorgensen et al. [55,56] led to similar conclusions and provided more quantitative insights into the relative importance of both solvation influences in water. Attempts have been made to identify Diels-Alder reactions that are exclusively affected by either enforced hydrophobic interactions [57] or hydrogenbonding effects [58]. The overall results confirmed the analysis and illustrated how the structures of diene and dienophile determine the magnitude of the aqueous rate acceleration. It appears well established now that the hydrophobicities of diene and dienophile as well as the polarizability of the activated complex play a key role in determining the acceleration of Diels-Alder reactions in water. These insights into the nature of the special

INTRODUCTION TO MICELLAR CATALYSIS

Micelles are highly dynamic, often rather polydisperse aggregates formed from single-chain surfactants [63,64] beyond the critical micelle concentration (cmc). Micellization is primarily driven by bulk hydrophobic interactions between the alkyl chains of the surfactant monomers and usually results from a favorable entropy change [65]. The overall Gibbs energy of the aggregate is a compromise of a complex set of interactions, with major contributions from headgroup repulsions and counterion binding (for ionic surfactants) [64]. The residence times of individual surfactant molecules in the micelle are typically of the order of 10⫺5 – 10⫺6 s, whereas the lifetime of the micellar entity is about 10⫺3 –10⫺1 s. The size and shape of micelles are subject to appreciable structural variations. Average aggregation numbers are usually in the range of 40–150. For ionic micelles, a large fraction of the counterions are bound in the vicinity of the headgroups. The overall structure of the micelle is characterized by a situation in which the ionic or polar headgroups reside at the surface of the aggregates, where they are in contact with water, with the alkyl chains in the interior of the micelle forming a relatively dry hydrophobic core [66]. The alkyl chains of micellized surfactant molecules are not fully extended. Starting from the headgroup, the first two or three carbon-carbon bonds are usually trans, whereas gauche conformations are likely to be encountered near the center of the chain. As a result, the terminal methyl moieties of the chain can be located near the surface of the micelle and may even protrude into the aqueous medium [67]. Consequently, the micellar surface has a definite degree of hydrophobicity. Nuclear magnetic resonance (NMR) studies have shown that the hydrocarbon tails in a micelle are highly mobile and comparable in mobility to the chains in a liquid hydrocarbon [68]. The degree of water penetration into the micellar interior has long been a matter of debate. Small-angle neutron scattering studies have indicated that significant water penetration into the micellar core is unlikely [69].


Micellar catalysis of organic reactions has been extensively studied [70–76]. This type of catalysis is critically determined by the ability of micelles to take up all kinds of molecules. The binding is generally driven by hydrophobic and electrostatic interactions. The takeup of solutes from the aqueous medium into the micelle is close to diffusion controlled, whereas the residence time depends on the structure of the surfactant molecule and the solubilizate and is often of the order of 10⫺4 –10⫺6 s [77]. Hence, these processes are fast on the NMR time scale. Solubilization is usually treated in terms of a pseudophase model in which the bulk aqueous phase is regarded as one phase and the micellar pseudophase as another. This allows the affinity of the solubilizate for the micelle to be quantified by a partition coefficient P. Frequently P is expressed as the ratio of the mole fractions of solubilizate in the micellar pseudophase and in the aqueous pseudophase. However, for micelle-catalyzed reactions, it is more convenient to express P as a ratio of concentrations. The time-averaged location of different solubilizates in or at a micelle has been a topic of contention [78]. Apart from saturated hydrocarbons, there is usually a preference for binding in the interfacial region, that is, at the surface of the micelle [79,80]. Such binding locations offer possibilities for hydrophobic interactions and avoid unfavorable disturbances of the interactions between the alkyl groups of the surfactant molecules in the core of the aggregate. The situation is, however, complicated, and the large volume of the interfacial region as compared with the core of the micelle should also be taken into account. The preferential binding of aromatic molecules at the micellar surface has been explained at least in part by the ability of the ␲-system of the molecule to form weak hydrogen bonds with water [81]. A.

Kinetic Models

Kinetic studies of micellar catalysis and inhibition have been largely focused on organic reactions and the field has been reviewed extensively [70–76]. In these kinetic analyses the dependence of the rate constants on the surfactant concentration has usually been rationalized in terms of the pseudophase model assuming rapid exchange of the substrate(s) between the micellar and aqueous pseudophases. Different models have been developed for uni- and bimolecular reactions. For unimolecular reactions, the kinetic micellar effect depends on partitioning of the substrate between both pseudophases and on the rate constant in water (kw) and in the micellar pseudophase (km). Menger and Portnoy [82]

251

developed the classic model in 1967 and this model has been successfully employed ever since. The micellar rate effect km /kw depends on the local medium at the substrate binding sites where the substrate experiences specific effects due to hydrophobic segments of the alkyl chains, the polar or ionic headgroups, and the counterions in case of ionic micelles. For bimolecular reactions the analysis is much more complicated, and the overall kinetic effects are now also crucially affected by the local concentration of both reactants A and B in the micellar pseudophase. A classic approach has been advanced by Berezin et al. [71,83]. Again the pseudophase model is adopted, but now an independent assessment of at least one of the partition coefficients is required before the other relevant kinetic parameters can be obtained. The overall approach is illustrated in Fig. 4. The apparent second-order rate constant (kapp), which is a weighed average of the second-order rate constants in the micellar pseudophase (km) and in water (kw), is given by kapp =

km PA PB[S]Vmol,S ⫹ kw (1 ⫺ [S]Vmol,S) (1 ⫹ (PA ⫺ 1)[S]Vmol,S)(1 ⫹ (PB ⫺ 1)[S]Vmol,S) (1)

in which PA and PB are the micelle-water partition coefficients of A and B, respectively, defined as the ratios of the concentrations in the micellar and the aqueous phase, [S] is the concentration of surfactant, and Vmol,S is the molar volume of the micellized surfactant. Accurate values of Vmol,S are difficult to obtain, and the actual location of A and B in the aggregate may differ (see Section III.A). Usually, estimates of Vmol,S are introduced into Eq. (1), leading to uncertainties in km. Despite these serious limitations, the kinetic analyses framed on the basis of Eq. (1) often produce reasonable results. By far the most frequently analyzed types of bimolecular reactions are those involving an ionic reaction partner of the same charge type as the counterion

FIG. 4 Kinetic analysis of a bimolecular reaction A ⫹ B → C according to the pseudophase model.

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of the ionic surfactant. Such processes are characterized by competition in binding between the reactive ion and the inert surfactant counterion. Pioneering work has been carried out by Romsted et al. [75], and the pseudophase ion-exchange model (PPIE) has been successfully applied in the micelle-catalyzed ionic bimolecular reactions. Again, it is often observed that the local microenvironment has only a modest influence on km /kw and that the favorable entropic effect due to the increase of the local concentrations of both reactants in the micellar psuedophase is the dominant catalytic factor [84]. Over the years, the PPIE model has been severely tested; in particular, Romsted and his associates have advanced elegant methods for analyzing detailed aspects of counterion binding to micellar aggregates [85]. Studies of micellar catalysis of bimolecular reactions of uncharged substrates (such as most Diels-Alder reactions) have not been frequent. An example involves the reaction of 1-fluoro-2,4-dinitrobenzene with aniline in the presence of anionic and nonionic surfactants [86]. The apparent second-order rate constant (kapp) is increased relative to that in water as a result of compartmentalization of both reactants in the micelles. Interestingly, the second-order rate constant for reaction in the micellar pseudophase (km) was found to be roughly equal to or even lower than the rate constant in water. Similarly, the reaction of long-chain alkanethiols with p-nitrophenyl acetate [87] and the acylation of aryl oximes by p-nitrophenyl carboxylates [83] are catalyzed by micelles but, apart from local concentration effects, the influence of the micellar surface charge on the ionizaton constants of the SH and OH groups, respectively, must also be taken into account. III.

EFFECT OF MICELLES ON DIELS-ALDER REACTIONS

Because the diene and dienophile of the majority of intermolecular Diels-Alder reactions have a rather pronounced nonpolar character, efficient binding of both substrates to micelles is anticipated. This would imply that the effective reaction volume for the Diels-Alder reaction is significantly reduced, leading to micellar catalysis. Surprisingly, accounts of micelle-catalyzed Diels-Alder reactions are scarce. The first report of the influence of surfactants on Diels-Alder reactions stems from 1939, when the BASF company patented the use of detergents for promoting the yields of Diels-Alder processes in aqueous dispersions [45a]. Subsequently, more studies have appeared reporting beneficial effects of micellar systems on the yield of Diels-Alder reac-

tions [88]. More mechanistically oriented studies have focused on the effect of micelles on the kinetics (Section III.A), the endo-exo selectivity (Section III.B), and the regioselectivity (Section III.C) of model Diels-Alder reactions. Also, the first example of modest enantioselectivity in a micelle-catalyzed Diels-Alder reactions has been reported (Section III.D). Finally, highly efficient micellar catalysis of a Diels-Alder reaction has been found for micelles with counterions that act as Lewis acid catalysts (Section III.E). A.

Effect of Micelles on the Rate of Diels-Alder Reactions

Studies of the kinetics of Diels-Alder reactions in the presence of micelles typically reveal only modest catalytic effects, and usually the apparent rate constants in micellar media are strikingly similar to the rate constants in water. Little effort was made to obtain secondorder rate constants in the micellar pseudophases. We refer here to the work of Breslow et al. [89], who observed a small (15%) acceleration of the Diels-Alder reaction of cyclopentadiene with a number of dienophiles in the presence of sodium n-dodecyl sulfate (SDS) micelles as compared with water. Also, a modest micelle-induced decrease in the rate constant of a Diels-Alder reactions has been reported [90]. More detailed analyses have been performed by Hunt and Johnson [91], who studied the kinetics of the homo Diels-Alder reaction of 1,2-dicyanoethylene (1) with cyclopentadiene (2) as a function of the conentration of sodium dodecyl sulfate (SDS) surfactant. The presence of micelles induces a modest decrease of the rate of this reaction (Fig. 5). Enthalpies and entropies of activation of the reaction in micellar medium have been determined and compared with those in water, aqueous salt solutions, and organic solvents (Table 2). Gibbs energies, entropies, and enthalpies of activation for the reaction in micellar solutions resemble those in 0.5 M LiCl more than those in organic solvents or water. This seems to point toward the Stern region of the micelles as the prominent site for this Diels-Alder reaction. Wijnen and Engberts [58] have studied the effect of SDS on another homo Diels-Alder reaction between 1,4-naphthoquinone (4) and cyclopentadiene (2). The results were compared with a structurally related retro Diels-Alder reaction (Fig. 6). Close to the cmc a modest acceleration of the former bimolecular Diels-Alder reaction was observed, whereas micelles induced a small inhibition of the retro Diels-Alder. However, this


253

FIG. 5 Second-order rate constants for the Diels-Alder reaction of 1 with 2 at different concentrations of sodium dodecyl sulfate (SDS). (Data from Ref. 91.)

process is still considerably faster than that in organic solvents [58]. The same authors have studied a reversible hetero Diels-Alder reaction and compared it with an irreversible analogue (Fig. 7) [92]. This time the rates of both retro and bimolecular Diels-Alder reactions experienced a modest beneficial influence of the presence of SDS micelles. The equilibrum constant is somewhat displaced toward the adduct. This particular reaction is classified by Desimoni et al. [11] as a type C DielsAlder reaction, signifying that it is almost insensitive to hydrogen bonding effects and that its rate is mainly governed by enforced hydrophobic interactions. This

TABLE 2 Gibbs Energies, Enthalpies, and Entropies of Activation for the Diels-Alder Reaction of 1 with 2 in Different Media Medium 0.05 M SDS Water 0.5 M LiCl Ethanol Dioxane

⌬␪G ‡ (kJ/mol)

⌬␪H ‡ (kJ/mol)

T ⌬ ␪S ‡ (kJ/mol)

78.7 78.4 77.8 87.5 89.1

45.1 62.2 41.9 52.2 48.5

⫺33.6 ⫺16.2 ⫺35.9 ⫺35.3 ⫺40.6

Source: Data from Ref. 91.

FIG. 6 Relative rate constants for the retro Diels-Alder reaction (䡲) of 6 and the bimolecular Diels-Alder reaction (●) of 4 with 2 at different concentrations of sodium dodecyl sulfate (SDS). (Data from Ref. 58.)

suggests that enforced hydrophobic interactions are slightly more efficient in the Stern region of the SDS micelles than in bulk water. Van der Wel, Wijnen, and Engberts [57] have studied the influence of surfactants on the hetero DielsAlder reaction of a cationic dienophile 12 with cyclopentadiene (Fig. 8). A 10-fold acceleration is induced by anionic SDS micelles, whereas nonionic Triton X100 and cationic 1-N-dodecyl-4-methylpyridinium bromide have only modest effects on the rate of the reaction. The efficient catalysis by SDS most likely results from electrostatically enhanced binding of the dienophile to the micelles. The presence of micelles does not lead to a significant alteration of the efficiency of an intramolecular Diels-Alder reaction [93] as compared with the process in pure water. The most detailed kinetic investigation of the effect of micelles on Diels-Alder cycloadditions has focused on the homo Diels-Alder reaction between 3-(p-substituted-phenyl)-1-(2-pyridyl-2-propen-1-one

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FIG. 8 Second-order rate constants for the reaction of 12 with 2 in aqueous solutions of sodium dodecyl sulfate (SDS) (䡲), Triton X-100 (䡩), and N-dodecyl-4-methylpyridinium bromide (䊱). (Data from Ref. 57.)

FIG. 7 Relative equilibrium constants for the reversible hetero Diels-Alder reaction of 8 with 2 (䡲), relative secondorder rate constants of the addition of 8 to 10 (䊱), and relative first-order rate constants for the retro Diels-Alder reaction of 9 (●) at different concentrations of sodium dodecyl sulfate (SDS). (Data from Ref. 92.)

dienophiles (14a–g) with cyclopentadiene (2) [94]. The influence of micelles of cetyltrimethylammonium bromide (CTAB), SDS, and dodecyl heptaoxyethylene ether (C12E7) on this process has been studied (Fig. 9). Note that the dienophiles can be divided into nonionic (14a–e), anionic (14f), and cationic (14g) species. A comparison of the effect of nonionic (C12E7), anionic (SDS), and cationic (CTAB) micelles on the rates of their reactions with 2 enabled assessment of the importance of electrostatic interactions in micellar catalysis or inhibition. The most important results of this study are summarized in Table 3. Under the reaction conditions, the effect of micelles on the rate of the Diels-Alder reaction is obviously small and invariably results in a slight inhibition of the reaction. The most significant effect occurs for anionic 14f in CTAB solution and for cationic 14g in SDS solution. These are the two combinations for which one would expect essentially complete binding of the

dienophile to the micelle as a result of favorable electrostatic interactions in addition to the hydrophobic interactions. Apparently, reaction in the micellar environment is slower than reaction in the bulk aqueous phase, despite the anticipated locally increased concentrations of the reactants in the micellar pseudophase. Also, in the case where electrostatic interactions inhibit binding of the dienophile to the micelle, i.e., 14f in SDS and 14g in CTAB solution, a retardation of the reaction is observed. In these cases the dienophile will most likely reside mainly in the aqueous phase. The retardation will result from a decrease in the concentration of 2 in this phase due to its partial solubilization by the micelles. The kinetics of the aforementioned reactions have been analyzed in terms of the pseudophase model (Fig. 4). For the limiting cases of essentially complete binding of the dienophile to the micelle (14f in CTAB and 14g in SDS solution) the following expression [95] was used: 1 [2]t Vmol,S Vw cmc⭈Vmol,S = = [S] ⫹ ⫺ kapp kobs km P2 ⭈Vt ⭈km km (2) Herein [2]t is the total number of moles of 2 present in the reaction mixture, divided by the total reaction volume Vt; kobs is the observed pseudo-first-order rate con-


FIG. 9

255

A Diels-Alder reaction that is subject to Lewis acid catalysis in water.

stant; Vmol,S is an estimate of the molar volume of micellized surfactant S; km and kw are the second-order rate constants in the aqueous phase and in the micellar pseudophase, respectively; Vw is the volume of the aqueous phase; and P2 is the partition coefficient of 2

TABLE 3 Influence of Micelles of CTAB, SDS, and C12E7 on the Apparent Second-Order Rate Constants (M⫺1 s⫺1)a for the Diels-Alder Reaction of 14a, 14f, and 14g with 2 at 25⬚Cb Mediumc Water SDS CTAB C12E7

14a 4.02 3.65 3.61 3.35

⫻ ⫻ ⫻ ⫻

14f ⫺3

10 10⫺3 10⫺3 10⫺3

1.74 1.44 0.283 1.62

⫻ ⫻ ⫻ ⫻

over the micellar pseudophase and water expressed as a ratio of concentrations. From the dependence of [2]t /kobs on the concentration of surfactant, P2 and km were obtained. Table 4 shows that the partition coefficients of 2 over SDS or CTAB micelles and water are similar. Comparison of the rate constants in the micellar pseudophase calculated using the pseudophase model with those in water (Tables 3 and 4) demonstrates a remarkable retardation induced by the micelles. This retardation is unlikely to be a result of a micellar medium effect. Information concerning the mi-

14g ⫺3

10 10⫺3 10⫺3 10⫺3

2.45 1.47 2.01 2.05

⫻ ⫻ ⫻ ⫻

10⫺3 10⫺3 10⫺3 10⫺3

TABLE 4 Analysis Using the Pseudophase Model: Partition Coefficients for 2 over CTAB of SDS Micelles and Water and Second-Order-Rate Constants for the Diels-Alder Reaction of 14f and 14g with 2 in CTAB and SDS Micelles at 25⬚C

a

The apparent second-order rate constants are calculated from the observed pseudo-first-order rate constants by dividing the latter by the overall concentration of 2. b [14] ⬇ 2 ⫻ 10⫺5 M; [2] = 2.0 ⫻ 10⫺3 M. c All solutions contain 1.0 ⫻ 10⫺4 M EDTA in order to suppress catalysis by trace amounts of metal ions. The concentration of surfactant is 7.8 mM above the cmc of the particular amphiphile under reaction conditions. Source: Data from Ref. 94.

Surfactant CTAB SDS a

Dienophile

P2 (⫾10%)

km (M⫺1 s⫺1) (⫾10%)

14f 14g

65a 49a

5.9 ⫻ 10⫺6 3.1 ⫻ 10⫺5

Corrected data; see Ref. 95. Source: Data from Ref. 94.

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croenvironment experienced by the Diels-Alder reactants was obtained from analysis of the endo-exo ratio of the reaction between 14c and 2 in surfactant solution and in a number of different organic and aqueous media [94] (see also Section III.B). The results of the study clearly point toward a waterlike environment for the Diels-Alder reaction in the presence of micelles. The inhibitory effect of micelles is suggested to result from the fact that diene and dienophile are on average located in different parts of the micelles. The diene seems to prefer the hydrophobic center of the micelle, whereas the dienophile has a stronger affinity for the Stern region. Evidence comes from 1H-NMR relaxation time studies in which paramagnetic ions are added to the micellar solutions [38,94]. Multivalent ions were used with a charge opposite to that of the surfactant headgroup, ensuring strong binding of these species to the Stern region of the micelles. As these paramagnetic ions enhance the relaxation of the protons in their vicinity, species bound to the Stern region will experience a more enhanced rate of relaxation from those residing in the core of the micelle. Comparison of Fig. 10 and Fig. 11 indeed demonstrates that the relaxation rate enhancement experienced by the diene is significantly smaller than that experienced by the dienophile. In conclusion, the fact that micelles have a rather limited influence on the rate of bimolecular as well as retro and intramolecular Diels-Alder reactions suggests (1) that the micellar medium experienced by the reactants is not too different from water and (2) that concentration effect of the reactants in the micelles is not too efficient. The latter effect is probably a result of the fact that diene and dienophile prefer different binding sites in the micelle. B.

FIG. 10 Paramagnetic ion–induced spin-lattice relaxation rates (rp) of the protons of 14c (a) and 14g (b) in SDS solution and of SDS in the presence of 14c or 14g, normalized to rp for the surfactant ␣-CH2. The solutions contained 50 mM SDS, 8 mM 14c or 14g, and 0 or 0.2 mM DyCl3 and 0 or 0.6 mM cyclen. (Data from Ref. 94.)

Braun, Schuster, and Sauer [97] have studied the endo-exo ratio of the reaction of cyclopentadiene with acrylonitrile and butyl acrylate in micellar media. The endo-exo ratios were significantly larger than in organic solvents, which seems to point toward a highly polar micellar reaction medium. Unfortunately, no comparisons were made with the endo-exo selectivity in pure water. Otto et al. [94] have studied the effect of micelles of SDS, CTAB, and C12E7, on the endo-exo ratio of the Diels-Alder reaction of 14c and 2 (Fig. 9). Com-

Effect of Micelles on the Endo-Exo Selectivity

Few detailed studies have been performed regarding micellar effects on endo-exo selectivities. Diego-Castro and Hailes [96] have studied the influence of micelles on the Diels-Alder reaction of cyclopentadiene with several alkyl acrylates of different chain lengths (methyl, ethyl, pentyl, heptyl, and nonyl). Endo-exo ratios in micellar media were strikingly similar to those in water irrespective of the length of the alkyl group in the dienophile. Unfortunately, the reactions were performed using a surfactant concentration close to the cmc, where solubilization of the reactants by the micelles is rather inefficient and the reaction is more likely to take place in bulk water than in the micelles.

FIG. 11 Paramaganetic ion–induced spin-lattice relaxation rates (rp) of the protons of 2 in CTAB, SDS, or Zn(DS)2 solution and of these surfactants in the presence of 2, normalized to rp for the surfactant ␣-CH2. The solutions contained 25 mM Zn(DS)2, 50 mM CTAB or SDS, 3 mM 2, and 0 or 0.4 mM [Cu(EDTA)]2⫺ for CTAB solutions and 0 or 0.2 mM Cu(NO3)2 for SDS and Zn(DS)2 solutions. (Data from Ref. 94.)

Diels-Alder Reactions in Micellar Media TABLE 5 Endo-Exo Product Ratios of the Diels-Alder Reaction of 14c with 2 in Surfactant Solutions Compared with Water and Organic Solvents Medium 100 mM CTAB 100 mM SDS 100 mM C12E7 Water Ethanol Acetonitrile

%Endo-%exo 86-14 88-12 85-15 84-16 77-23 67-33

parison of the results with those obtained for organic solvents and pure water (Table 5) demonstrates that the beneficial solvent effect of water is still present in the micelle-mediated reaction. In summary, endo-exo selectivities in micellar media tend to be comparable to those in pure water [89] and significantly larger than those in organic solvents. Apparently, surfactants can be used in order to improve the solubility of the Diels-Alder reactants in water, without significant deterioration of the selectivity as compared with pure water. Interestingly, in microemulsions the endo-exo selectivity is reduced significantly [89,98]. C.

Micellar Effects on the Regioselectivity

Significant work in this area has been carried out by Jaeger et al. An interesting issue that was addressed in the early days of micellar catalysis involves the question of how binding to specific sites in micelles could affect the stereochemistry of the reactions. For example, extensive structural changes in substrates were expected to influence the depth of penetration of the substrate into the micellar core with a concomitant change in the efficiency of the micellar catalysis. This expectation was not borne out in practice [99,100]. In fact, one could ask how ‘‘micellar binding sites’’ can be defined with sufficient precision to allow conclusions about the details of the relevant microenvironment and orientation of the substrate. In view of the micellar structure, it is more appropriate to consider a range of binding situations of small differences in Gibbs energy of binding and involving a range of substrate orientations. Most substrates in micelle-catalyzed reactions contain at least one polar substituent that prefers to bind at or close to the micellar surface and at least partly in direct contact with water. Solely apolar molecules, such as alkanes, will preferentially bind in

257

the hydrophobic core of the micelle, assuming orientations that lead to a minimal disturbance of the chain packing of the surfactant molecules. Jaeger et al. [101] examined how monohalogenation of alkyl phenyl ethers C6H5OR (R = n-C5H11, n-C9H19, and n-C12H25) by chlorine and bromine in micellar solutions of SDS and in vesicular solutions to give 4XC6H4OR and 2-XC6H4OR exhibits ortho/para ratios and reaction rates different from those in aqueous buffer solutions in the absence of surfactants. Indeed, in the micelles the o/p ratio decreases with increasing length of R, whereas the second-order rate constant decreases in the series. These regioselectivity and kinetic data can be rationalized by assuming different solubilization sites for the aromatic ethers depending on the length of the R substituent. These differences lead to different reaction environments and concomitant kinetic differences. Lengthening of R is proposed to lead to solubilization ‘‘deeper’’ in the micelle and changes in the o/p preference. In another series of studies, Jaeger et al. examined regioselectivity control of Diels-Alder reactions for cases in which the diene or both the diene and dienophile were amphiphilic molecules themselves. In a Diels-Alder process involving a cationic surfactant 1,3diene with a neutral nonsurfactant dienophile, the orientational effects within the micellar aggregates were not sufficiently strong to overcome the intrinsically preferred regioselectivity of the reaction [102]. Modest regioselectivity was found for a Diels-Alder reaction of another cationic surfactant diene with cationic surfactant dienophiles [103,104]. The reactions were performed at 100⬚C, most likely decreasing the organizational abilities of the aqueous aggregate compared with those at lower temperatures. A substantially larger regioselectivity [105] was found in a study employing amphiphilic diene 16 (cmc = 1.0 ⫻ 10⫺4 M) and amphiphilic dienophile 17 (cmc = 4.4 ⫻ 10⫺3) (Fig. 12). The cycloadducts 18 and 19 were formed, which were separated by preparative reverse-phase HPLC and characterized by 1H-NMR spectroscopy. Since the substituents at carbons 1 and 2 in 17 are close to being electronically and sterically equivalent with respect to the dienophile reaction center, no regiochemical preference is anticipated in the absence of interfacial orientational effects in the mixed micelles formed from 16 and 17. Evidence for this assumption was also obtained from an analysis of the regioselectivity of the Diels-Alder reaction of 20 and 21 in toluene. As expected, the two analogous cycloadducts were obtained in equal amounts. Interestingly, the re-

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FIG. 12

A regioselective Diels-Alder reaction between a surfactant diene and a surfactant dienophile.

actions of 16 with 17 at concentrations above their cmc values gave an 18:19 ratio of 6.6:1. Therefore it is clear that interfacial and related orientational effects that result from surfactant aggregation can induce significant regioselectivity in a Diels-Alder reaction in aqueous solution. D.

Micellar Effects on the Enantioselectivity

Recently, a report appeared that described the first Diels-Alder reaction in aqueous chiral micellar media [106]. The novel (s)-leucine-derived chiral micellar amphiphile 22 was used as a catalyst for the DielsAlder reaction of cyclopentadiene with n-nonly acrylate (23) (Fig. 13). Preferential formation of the R-endo isomer was observed. Using a surfactant concentration of 11 mg L⫺1 and in the presence of 4.86 M LiCl, the yield was 75%, with an endo/exo ratio of 2.2 and an enantioselectivity of 15% (R). This result may be compared with the maximum enantioselectivity (21%) found for Diels-Alder reactions in the presence of cyclodextrins. In the absence of surfactant, the reaction in water gave a yield of 70% and an endo/exo ratio of 1.7. Further optimization of the structure of the chiral micellar catalyst might well lead to improved enantioselectivities. In this context it may be noticed that aqueous Diels-Alder re-

actions catalyzed by chiral Lewis acids may exhibit enantioselectivities up to 74% [36,37]. E.

Effects of Micelles with Catalytically Active Counterions

The most efficient means of accelerating Diels-Alder reactions is catalysis by Lewis acids. In aqueous media this process is hampered by the strong interaction of the catalysts with water [62]. However, one example has been reported where this difficulty was overcome by modification of the dienophiles so that they can form a chelate with the catalyst ions (Fig. 9) [35–37]. The reaction of these dienophiles with cyclopentadiene in the absence of Lewis acid catalysts has been described in Section III.A. In that case introduction of micelles into the aqueous reaction mixture induced a modest retardation of the reaction. Micellar catalysis of this reaction in combination with Lewis acid catalysis has been studied in detail [94]. The dodecyl sulfate surfactants Co(DS)2, Ni(DS)2, Cu(DS)2, and Zn(DS)2 containing catalytically active counterions are extremely potent catalysts for the Diels-Alder reaction between 14 and 2. Figure 14 shows the dependence of the rates of the Diels-Alder reactions of 14c, 14f, and 14g with 2 on the concentration of Cu(DS)2. For all three dienophiles the apparent second-order rate constant for their reaction with 2


FIG. 13

259

The first example of enantioselectivity induced by a chiral surfactant in a micelle-catalyzed Diels-Alder reaction.

increases dramatically when the concentration of Cu(DS)2 reaches the cmc (1.11 mM). Beyond the cmc, the dependence of the rate on the surfactant concentration is subject to two counteractive influences. At higher surfactant concentration, a larger fraction of dienophile will be bound to the micelle, where it reacts faster than in bulk water, resulting in an increase in the rate of the reaction. At the same time, the concentration of diene in the micellar pseudophase will drop with increasing surfactant concentration due to the increase in the volume of the micellar pseudophase. At higher surfactant concentrations the dienophile will be nearly completely bound to the micelles and the dilution effect will start to dominate the behavior. Together, these two effects result in the appearance of a rate maximum at a specific concentration of surfactant that is typical for micelle-catalyzed bimolecular reactions (see also Fig. 8). The position of the maximum depends primarily on the micelle-water partition coefficients of diene and dienophile. Interestingly, the acceleration relative to the reaction in organic media in the absence of catalyst approaches enzymelike magnitudes: compared with the process in acetonitrile (second-order rate constant = 1.40 ⫻ 10⫺5 M⫺1 s⫺1), Cu(DS)2 micelles accelerate the Diels-Alder reaction between 14a and 2 by a factor of 1.8 ⫻ 106. Also the effects of cationic (CTAB) and nonionic (C12E7) surfactants on the Cu2⫹-catalyzed reaction have been studied. However, these systems were much less efficient than Cu(DS)2, suggesting that a local high concentration of catalyst ions in the Stern region of the micelles is a prerequisite for a highly efficient interaction with the dienophile. The essentially complete binding of 14g to the Cu(DS)2 micelles allowed treatment of the kinetic data of Fig. 14 using the pseudophase model. Furthermore, complete binding of 14g to the copper ions was as-

sumed, which was supported by ultraviolet-visible analysis [94]. Using Eq. (2), a Cu(DS)2-water distribution coefficient for 2 of 86 was obtained [95]. The second-order rate constant for reaction in the micellar pseudophase was calculated to be 0.21 M⫺1 s⫺1. Comparison of this rate constant with those for the reaction in acetonitrile (0.472 M⫺1 s⫺1) and ethanol (0.309 M⫺1 s⫺1) seems to indicate a relatively apolar medium for the Diels-Alder reaction. This conclusion is hard to reconcile with the ionic character of two of the three reaction partners involved. More insight into the local environment for the catalyzed reaction was obtained from the influence of substituents on the rate of this process in micellar and in different aqueous and organic solvents. The Hammett

FIG. 14 Plots of the apparent second-order rate constant (kapp) versus the concentration of Cu(DS)2 for the Diels-Alder reaction of 14c (▫), 14f (䊱), and 14g (䡲) with 2 at 25⬚C. The inset shows the treatment of the data for the reaction of 14g according to the pseudophase model. (Data from Ref. 94.)

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␳ value in Cu(DS)2 solution was found to resemble closely that in aqueous solution rather than those in organic solvents, suggesting an aqueous microenvironment for the reaction [94]. It appears that the outcome of the analysis using the pseudophase model (a rather apolar reaction environment) is not in agreement with experimental observations (an aqueous reaction environment). Apparently, the assumptions of the pseudophase model are not valid for the Diels-Alder reaction studied. In particular, the treatment of the micellar pseudophase as a homogeneous ‘‘solution’’ might not be warranted. As noted in Section III.A, there are strong indications that the diene and the dienophile reside on average in different parts of the micelle, the diene preferring the core and the dienophile the Stern region of the micelles. Additional paramagnetic 1H-NMR relaxation rate studies of the binding location of the reactants in Zn(DS)2 micelles further support this suggestion [38,94]. Surely, spatial separation of diene and dienophile will impede their reaction. In summary, the use of anionic micelles with bivalent metal ions as catalytically active counterions can lead to accelerations of suitable Diels-Alder reactions of enzymelike magnitude. The high efficiency of these systems mainly results from the efficient interaction between dienophile and catalysts in the Stern region of the micelles, where both species are present in high local concentration. Even larger accelerations are anticipated upon modification of the diene so that this species also binds to the Stern region rather than in the core of the micelle. Examples of similar micellar systems have found application in synthetic organic chemistry [107].

improving the otherwise limited solubility of diene and dienophile in water. Finally, effects on the Diels-Alder stereochemistry were expected. Specific binding could lead to regioselectivity, whereas the use of chiral micelle-forming surfactants would provide a possibility for obtaining enantioselectivity in appropriate Diels-Alder processes. Studies have illustrated the potential power to bring about these appealing results. Micellar catalysis of Diels-Alder reactions has been pursued and could indeed induce significant accelerations. Examples have been shown in this chapter. However, it is a requisite that diene and dienophile bind to rather similar binding sites in the micelle. In the case of, for example, an apolar diene and a moderately polar dienophile, the diene will preferentially reside in the core of the micelle and encounters with the dienophile, preferentially sitting at the micellar surface, will be hampered. The overall result will then be micellar inhibition rather than catalysis. Extreme rate enhancements can be obtained by combining micellar and Lewis acid catalysis. However, a specially designed dienophile is required for such a catalytic process. Binding of dienes and dienophiles to micellar aggregates will certainly improve their solubilities in water and extend the potential for using aqueous reaction media for Diels-Alder reactions. The use of micelles with the aim of inducing favorable regioselectivity and enantioselectivity has had only modest success. However, it is anticipated that challenging developments in this area are possible through variation of the structural architectures of diene, dienophile, and micelle-forming amphiphile.

ACKNOWLEDGMENT IV.

SUMMARY AND OUTLOOK

It is now well established that many Diels-Alder reactions, both of normal electron demand and of inverse electron demand, can be substantially accelerated by using water as the reaction medium. Also, endo/exo ratios are usually improved for aqueous media. These findings had important implications for further extending the versatility of Diels-Alder reactions in organic synthesis and for providing a stimulus for detailed studies of medium effects on pericyclic reactions. These interesting developments called for studies of DielsAlder reactions in micellar solutions. By concentrating the diene and dienophile in the micellar reaction volume, further enhancements were anticipated. Furthermore, solubilization of the Diels-Alder reaction partners in the micelles could offer a solution for

The authors gratefully acknowledge Miss H. E. Wolters for typing the manuscript.

REFERENCES 1.

2. 3.

4. 5.

(a) G. Brieger and J. N. Bennett, Chem. Rev. 80:63– 97 (1980); (b) W. Oppolzer, Angew. Chem. Int. Ed. Engl. 16:10–24 (1977); (c) J. Sauer and R. Sustmann, Angew. Chem. Int. Ed. Engl. 19:779–807 (1980). J. A. Berson, Tetrahedron Lett. 48:3–17 (1992). (a) K. Fukui, Acc. Chem. Res. 4:57–64 (1971); (b) R. B. Woodward and R. Hoffman, Angew. Chem. Int. Ed. Engl. 8:781–853, 1969. K. N. Houk, Y. Li, and J. D. Evanseck, Angew. Chem. Int. Ed. Engl. 31:682–708 (1992). M. D. Rozeboom, I. Tegmo-Larsson, and K. N. Houk, J. Org. Chem. 46:2338–2345 (1981).

Diels-Alder Reactions in Micellar Media 6. 7. 8. 9. 10.

11.

12. 13. 14. 15.

16. 17. 18.

19. 20. 21. 22.

23. 24.

25.

R. Gleiter and M. C. Bohm, Pure Appl. Chem. 55: 237–244 (1983). R. B. Woodward and T. J. Katz, Tetrahedron 5:70–89 (1959). E. T., McBee, M. J. Keogh, R. P. Levek, and E. P. Wesseler, J. Org. Chem. 38:632–636 (1973). C. Reichardt, Solvents and Solvent Effects in Organic Chemistry, 2nd ed., VCH, Cambridge, 1990. Examples: (a) B. Von Blankenburg, H. Fiedler, M. Hampel, H. G. Hauthal, G. Just, K. Kahlert, J. Korn, K.-H. Muller, W. Pritzkow, Y. Reinhold, M. Rollig, E. Sauer, D. Schnurpfeil, and G. Zimmermann, J. Prakt. Chem. 316:804–816 (1974); (b) N. K. Sangwan and H. Schneider, J. Chem. Soc. Perkin Trans. 2 1223– 1227 (1989). G. Desimoni, G. Faita, P. Righetti, N. Tornaletti, and M. Visigalli, J. Chem. Soc. Perkin Trans. 2 437–441 (1989). (b) M. Burdisso, G. Desimoni, G. Faita, P. Righetti, and G. Tacconi, J. Chem. Soc. Perkin Trans. 2 845–850 (1989); (c) A. Corsico Coda, G. Desimoni, G. Faita, P. Righetti, and G. Tacconi, Tetrahedron 45: 775–788 (1989); (d) G. Desimoni, G. Faita, and P. Righetti, Tetrahedron 46:7951–7970 (1990); (e) G. Desimoni, G. Faita, D. Pasini, and P. Righetti, Tetrahedron 48:1667–1674 (1992). J. J. Gajewski, J. Org. Chem. 57:5500–5506 (1992). R. A. Firestone and S. G. Saffar, J. Org. Chem. 48: 4783–4784 (1983). P. A. Grieco, J. J. Nunes, and M. D. Gaul, J. Am. Chem. Soc. 112:4595–4596 (1990). (a) M. A. Forman and W. P. Dailey, J. Am. Chem. Soc. 113:2761–2762 (1991). (b) G. Jenner and R. B. Salem, Tetrahedron 53:4637–4648 (1997). J. M. Mellor and C. F. Webb, J. Chem. Soc. Perkin Trans. 2 26–31 (1974). J. A. Berson, Z. Hamlet, and W. A. Mueller, J. Am. Chem. Soc. 84:297–304 (1962). C. Cativiela, J. I. Garcia, J. Gil, R. M. Martinez, J. A. Mayoral, L. Salvatella, J. S. Urieta, A. M. Mainar, and M. H. Abraham, J. Chem. Soc. Perkin Trans. 2 653– 660 (1997). R. Van Eldik, T. Asano, and W. J. Le Noble, Chem. Rev. 89:549–688 (1989). T. P. Caulier and J. Reisse, J. Org. Chem. 61:2547– 2548 (1996). C. Collet and P. Laszlo, J. Phys. Org. Chem. 8:468– 472 (1995). R. M. Pagni, G. W. Kabalka, G. Hondrogiannis, S. Bains, and R. Kurt, Tetrahedron 49:6743–6756 (1993). C. Cativiela, J. I. Garcia, J. A. Mayoral, E. Pires, and A. J. Royo, Tetrahedron 51:1295–1300 (1995). K. Endo, T. Koike, T. Sawaki, O. Hayashida, H. Masuda, and Y. Aoyama, J. Am. Chem. Soc. 119:4117– 4122 (1997). (a) A. A. P. Meekel, M. Resmini, and U. K. Pandit, J. Chem. Soc. Chem. Commun. 571–572 (1995); (b) M.

261

26. 27. 28.

29.

30. 31. 32. 33. 34. 35. 36. 37. 38. 39.

40. 41. 42. 43. 44. 45.

46. 47.

Resmini, A. A. P. Meekel, and U. K. Pandit, Pure Appl. Chem. 68:2025–2028 (1996). R. Breslow and D. C. Rideout, J. Am. Chem. Soc. 102: 7816–7817 (1980). W.-S. Chung and J.-Y. Wang, J. Chem. Soc. Chem. Commun. 971–972 (1995). (a) C. J. Walter, H. L. Anderson, and J. K. M. Sanders, J. Chem. Soc. Chem. Commun. 458–460 (1993); (b) C. J. Walter and J. K. M. Sanders, Angew. Chem. Int. Ed. Engl. 34:217–219 (1995); (c) Z. Clyde-Watson, A. Vidal-Ferran, L. J. Twaman, C. J. Walter, D. W. J. McCallien, S. Fani, N. Bampos, S. R. Wylie, and J. K. M. Sanders, New J. Chem. 22:493–502 (1998); (d) M. Maurus, Z. Clyde-Watson, L. J. Twyman, M. Nakash, and J. K. M. Sanders, Chem. Commun. 2265– 2266 (1998). (a) J. Kang and J. J. Rebek, Nature 385:50–52 (1997); (b) J. Kang, G. Hilwersson, J. Santamaria, and J. Rebek Jr., J. Am. Chem. Soc. 120:3650–3656 (1998). P. Yates and P. Eaton, J. Am. Chem. Soc. 82:4436– 4437 (1960). J. Sauer and J. Kredel, Tetrahedron Lett. 51:6359– 6364 (1966). T. Inukai and T. Kojima, J. Org. Chem. 31:1121–1123 (1966). L. M. Tolbert and M. B. Ali, J. Am. Chem. Soc. 106: 3806–3810 (1984). S. Otto and J. B. F. N. Engberts, Tetrahedron Lett. 36: 2645–2648 (1995). S. Otto, F. Bertoncin, and J. B. F. N. Engberts, J. Am. Chem. Soc. 118:7702–7707 (1996). S. Otto, Boccalatti, and J. B. F. N. Engberts, J. Am. Chem. Soc. 120:4238–4239 (1998). S. Otto and J. B. F. N. Engberts, J. Am. Chem. Soc. 121:6798–6806 (1999). S. Otto, Catalysis of Diels-Alder reactions in water, Ph.D. dissertation, University of Groningen, 1998. J. Motoyoshiya, T. Kameda, M. Asari, M. Miyamoto, S. Narita, H. Aoyama, and S. Hayashi, J. Chem. Soc. Perkin Trans. 2 1845–1850 (1997). A. Venturini, J. Joglar, S. Fustero, and J. Gonzalez, J. Org. Chem. 62:3919–3926 (1997). V. D. Kiselev and A. I. Konovalov, Russ. Chem. Rev. 58:230–249 (1989). O. Diels and K. Alder, Ann 490:243–294 (1931). R. B. Woodward and H. Baer, J. Am. Chem. Soc. 70: 1161–1166 (1948). T. A. Eggelte, H. de Koning, and H. O. Huisman, Tetrahedron 29:2491–2493 (1973). (a) H. Hopff and C. W. Rautenstrauch, U. S. Patent 2,262,002 (1939); (b) L. C. Lane and C. H. J. Parker, U.S. Patent 2,444,263 (1948). J. B. F. N. Engberts, Pure Appl. Chem. 67:823–828 (1995). W. Blokzijl and J. B. F. N. Engberts, in ACS Sym-

262

48. 49.

50. 51.

52. 53. 54. 55. 56. 57. 58. 59. 60. 61. 62.

63. 64. 65. 66. 67. 68. 69.

70. 71. 72. 73.

Otto and Engberts posium Series 568 (C. J. Cramer and D. G. Truhlar, eds.), American Chemical Society, Washington, DC, 1994, pp. 303–317. P. A. Grieco, Organic Synthesis in Water, Blacky Academic and Professional, London, 1998. A. Lubineau, E. Grand, and M.-C. Scherrman, Carbohydrate Res. 297:169–174 (1997) and many previous papers. G. Chen, Diss. Abstr. Int. 57:6934-B (1997). (a) W. Blokzijl, M. J. Blandamer, and J. B. F. N. Engberts, J. Am. Chem. Soc. 113:4241–4246 (1991); (b)W. Blokzijl and J. B. F. N. Engberts, J. Am. Chem. Soc. 114:5440–5442 (1992). S. Otto, W. Blokzijl, and J. B. F. N. Engberts, J. Org. Chem. 59:5372–5376 (1994). W. Blokzijl, Ph.D. dissertation, University of Groningen, 1991. A. Meijer, S. Otto, and J. B. F. N. Engberts, J. Org. Chem. 63:8989–8994 (1998). J. F. Blake and W. L. Jorgensen, J. Am. Chem. Soc. 113:7430–7432 (1991). J. F. Blake, L. Dongchul, and W. L. Jorgensen, J. Org. Chem. 59:803–805 (1994). G. K. van der Wel, J. W. Wijnen, and J. B. F. N. Engberts, J. Org. Chem. 61:9001–9005 (1996). J. W. Wijnen and J. B. F. N. Engberts, J. Org. Chem. 62:2039–2044 (1997). C. J. Li and T. H. Chan, Organic Reactions in Aqueous Media, Wiley, New York, 1997. P. A. Grieco, Aldrichim. Acta 24:59–66 (1991). A. Lubineau, J. Auge, and Y. Queneau, Synthesis 741–760 (1994). J. B. F. N. Engberts, B. F. L. Feringa, E. Keller, and S. Otto, Rec. Trav. Chim. Pays-Bas 115:457–464 (1996). B. Lindman and H. Wennerstrom, Top. Curr. Chem. 87:1–83 (1980). J. N. Israelachvili, Intermolecular and Surface Forces, Academic Press, London, 1992. W. Blokzijl and J. B. F. N. Engberts, Angew. Chem. Int. Ed. Engl. 32:1545–1579 (1993). D. W. R. Gruen, Prog. Colloid Polymer. Sci. 70:6–16 (1985). J. Clifford, Trans. Faraday Soc. 61:1276–1282 (1965). H. Walderhaug, O. Soderman, and P. Stilbs, J. Phys. Chem. 88:1655–1662 (1984). S. S. Berr, E. Caponetti, J. S. J. Johnson, R. R. M. Jones, and L. J. Magid, J. Phys. Chem. 90:5766–5770 (1986). E. H. Cordes and C. Gitler, Prog. Bioorg. Chem. 2:1– 53 (1972). I. V. Berezin, K. Martinek, and A. K. Yatsimirskii, Russ. Chem. Rev. 42:787–802 (1973). C. A. Bunton, Pure Appl. Chem. 49:969–979 (1977). T. Kunitake and S. Shinkai, Adv. Phys. Org. Chem. 17:435–487 (1980).

74.

75. 76. 77. 78. 79. 80. 81.

82. 83. 84. 85. 86. 87. 88.

89. 90. 91. 92. 93. 94. 95.

96. 97. 98.

E. J. R. Sudholter, G. B. van de Langkruis, and J. B. F. N. Engberts, Rec. Trav. Chim. Pays-Bas 99:73–82 (1980). C. A. Bunton, F. Nome, F. H. Quina, and L. S. Romsted, Acc. Chem. Res. 24:357–363 (1991). S. Tascioglu, Tetrahedron 52:11113–11152 (1996). M. Almgren, F. Grieser, and J. K. Thomas, J. Am. Chem. Soc. 101, 279–291 (1979). F. Grieser and C. J. Drummond, J. Phys. Chem. 92: 5580–5593 (1988). M. F. Emerson and A. Holtzer, J. Phys. Chem. 71: 3320–3330 (1967). P. Stilbs, J. Colloid Interface Sci. 80:608–610 (1981). S. Suzuki, P. G. Green, R. E. Bumgarner, S. Dasgupta, W. A. Goddard III, and G. A. Blake, Science 257:942– 945 (1992). F. M. Menger and C. E. Portnoy, J. Am. Chem. Soc. 89:4698–4703 (1967). A. K. Yatsimirski, K. Martinek, and I. V. Berezin, Tetrahedron 27:2855–2868 (1971). C. A. Bunton, Catal. Rev. Sci. Eng. 20:1–59 (1979). L. S. Romsted and J. Rao, Langmuir 15:326–336 (1999). S. J. Dougherty and J. C. Berg, J. Colloid Interface Sci. 49:135–138 (1974). W. Tagaki, T. Amada, Y. Yamashita, and Y. Yano, J. Chem. Soc. Chem. Commun. 1131–1132 (1972). (a) V. K. Singh, B. N. S. Raju, and P. T. Deota, Synth. Commun. 17:1103–1109 (1987); (b) V. K. Singh, B. N. S. Raju, and P. T. Deota, Synth. Commun. 18:567– 574 (1988); (c) M. S. Kumar and J. M. Rao, Tetrahedron 46:5383–5388 (1990); (d) V. K. Singh and B. N. S. Raju, Indian J. Chem. 35B:303–311 (1996); (d) K. Chiba, M. Jinno, A. Nozaki, and M. Tada, Chem. Commun. 1403–1404 (1997). R. Breslow, U. Maitra, and D. Rideout, Tetrahedron Lett. 24:1901–1904 (1983). N. K. Sangwan and H.-J. Schneider, J. Chem. Soc. Perkin II 1223–1227 (1989). I. Hunt and D. Johnson, J. Chem. Soc. Perkin Trans 2 1051–1056, 1991. J. W. Wijnen and J. B. F. N. Engberts, Liebigs Ann. Recl. 1085–1088 (1997). D. D. Sternbach and D. M. Rossana, J. Am. Chem. Soc. 104:5853–5854 (1982). S. Otto, J. B. F. N. Engberts, and J. C. T. Kwak, J. Am. Chem. Soc. 120:9517–9525 (1998). In the original paper [94] Eq. (2) and the data calculated with it contained a small error. This has now been corrected. We gratefully acknowledge Prof. P. Walde for pointing this out. M. J. Diego-Castro and H. C. Hailes, Tetrahedron Lett. 39:2211–2214 (1998). R. Braun, F. Schuster, and J. Sauer, Tetrahedron Lett. 27:1285–1288 (1986). A. Gonzalez and S. L. Holt, J. Org. Chem. 47:3186– 3188 (1982).

Diels-Alder Reactions in Micellar Media 99. 100. 101. 102. 103.

G. A. van de Langkruis and J. B. F. N. Engberts, J. Org. Chem. 49:4152–4157 (1984). F. M. Witte and J. B. F. N. Engberts, J. Org. Chem. 50:4130–4134 (1985). D. A. Jaeger, M. W. Clennan, and J. Jamrozik, J. Am. Chem. Soc. 112:1171–1176 (1990). D. A. Jaeger, H. Shinozaki, and P. A. Goodson, J. Org. Chem. 56, 2482–2489 (1991). D. A. Jaeger and J. Wang, Tetrahedron Lett. 33:6415– 6416 (1992).

263 104. 105. 106. 107.

D. A. Jaeger and J. Wang, J. Org. Chem. 58:6745– 6755 (1993). D. A. Jaeger and D. Su, Tetrahedron Lett. 40:257–260 (1999). M. J. Diego-Castro and H. C. Hailes, Chem. Commun. 1549–1550 (1998). (a) S. Kobayashi, T. Busujima, and S. Nagayama, Synlett 545–546 (1999); (b) K. Manabe and S. Kobayashi, Synlett 547–548 (1999); (c) K. Manabe and S. Kobayashi, Tetrahedron Lett. 3773–3776 (1999).

10 Interfacial Compositions of Surfactant Assemblies by Chemical Trapping with Arenediazonium Ions: Method and Applications LAURENCE S. ROMSTED New Jersey

I. A.

Rutgers, The State University of New Jersey, New Brunswick,

INTRODUCTION

general utility because it works with both anionic and neutral nucleophiles and because it provides estimates of the distributions of nucleophiles between the oilinterfacial and water-interfacial regions of microemulsions. The method has the potential to provide information on interfacial concentrations of many of the important functional groups present in biological membranes and in commercial surfactant-based products. The aim of this chapter is to describe the logic, practical aspects, and current and potential applications of the chemical trapping method. Section I characterizes the types of information that chemical trapping provides about properties of surfactant assemblies. Section II describes the basic assumption of the method and evidence for its validity. Section III focuses on practical aspects including optimal characteristics of a trapping reagent and its preparation and protocols for product analysis and measurement of dediazoniation rate constants. Sections IV and V show how the method can be used to obtain information on a variety of properties of surfactant assemblies: (1) hydration of the interfacial region; (2) interfacial counteranion concentrations in cationic and zwitterionic micelles and vesicles, including effects of sphere-to-rod transitions; (3) degrees of ionization, ␣, of cationic micelles; (4) coion concentrations around anionic micelles; (5) exchange constants for counteranion competition; (6) distribution constants of alcohols between aqueous-interfacial and oil-interfacial regions; (7) topologies of aggregate bound poly-

Aims of the Chapter

The impetus for development of a method for determining interfacial compositions of surfactant assemblies based on the chemistry of arenediazonium ions came from several directions: (1) Most current methods for estimating the compositions of surfactant aggregates are based on physical methods that monitor only one component at a time [1]. (2) The understanding of chemical reactivity in surfactant assemblies in terms of pseudophase models developed to the point that they provide consistent qualitative and often quantitative interpretations of surfactant assembly effects on rate and equilibrium constants of chemical reactions [2–6]. (3) I sought an experimental method to answer a deceptively simple question: how can interfacial concentrations and distributions of two similar inorganic anions, e.g., Cl⫺ and Br⫺, between cationic micelles and water be measured simultaneously? Ions bind selectively to interfacial regions of aggregates, but because of interferences, physical methods often cannot discriminate between two similar ions in the same solution. Chemical trapping discriminates between these and a variety of other anions. But it does much more. It also provides simultaneous estimates of their concentrations and that of water within the interfacial region over wide ranges of surfactant and counterion concentrations. Research over the past decade shows that the method has broad 265

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peptides; and (8) distributions of antioxidants in microand macroemulsions. The experimental demands of the chemical trapping method are relatively modest. Syntheses of the arenediazonium salt probe, its water-soluble short-chain analogue, and its products are required, but they tend to be more tedious than complex. Most surfactants and other components are commercially available. A constant-temperature bath is needed for running reactions and an ultraviolet-visible (UV-Vis) spectrophotometer is required for measuring dediazoniation rate constants in previously untried systems. The workhorse tool is a high-performance liquid chromatograph (HPLC) fitted with a C-18 reverse-phase column and a UV detector for separation and quantitative analysis of reaction products. Adding an autosampler and computer for handling multiple samples and for data storage speeds collection of results. Unanticipated experimental problems sometimes appear, usually in the early stages of work with a new surfactant system. Once experimental protocols are established, results accumulate rapidly. Mathematical treatments are available for obtaining various types of information, but applications to multicomponent systems are still being developed. B.

Background

Surfactants, or amphiphiles, are surface-active nonionic molecules or organic salts that, alone or in combination with a wide variety of other ionic and nonionic solutes, aggregate spontaneously and with a high degree of cooperativity in solution to form a variety of assemblies (or association colloids) whose structures depend both on solution composition and on the structures of the components, primarily the surfactant [7–10]. Figure 1 shows some typical association colloid structures. All surfactant assemblies in homogeneous solution share an underlying organizational structure: a fluid, hydrocarbon-like region separated from an aqueous region by an interfacial region with a thickness on the order of the diameter of the surfactant headgroup. The balance of forces that drive aggregate formation and control aggregate structure and stability is determined in large part by the hydrophobic effect; that is, water molecules interact more strongly with themselves than with the nonpolar tails of the surfactant [7]. This escapist tendency is balanced by mutual interactions between the polar or ionic portions of the surfactant headgroups with water and ions in the interfacial region. Other amphiphilic or surface-active components, e.g., alcohols, benzene, polar solutes, and polypeptides, are generally assumed to associate with surfactant ag-

FIG. 1 Oversimplified images of some association colloid structures illustrating the organization of surfactant (open circle headgroups) and additives (filled circle headgroups). As in all surfactant assemblies, the headgroups (ionic surfactants also have counterions, not shown) are arrayed in a layer between aqueous and oil regions. (Adapted from Fig. 1 of Ref. 133 and used with permission of the author and the IUPAC.)

gregates in a similar fashion, i.e., with their nonpolar portions buried in the aggregate core and their polar and charged portions maintaining contact with water [10,11]. Thus, the nonpolar regions of single and multicomponent aggregates tend to be hydrocarbon-like in minimal contact with water except at the interfacial region. However, their surfaces may contain a plethora of hydrated ions and polar molecules participating in a variety of water-mediated interactions, e.g., electrostatic, charge-dipole, induced dipole, and hydrogen bonding. The more components in a surfactant assembly, the more difficult it becomes to quantify the relationships between composition and aggregate structure and stability. Changing the bulk solution composition and structures of the components alters interfacial composition and the balance of forces in this region that, because of the highly cooperative nature of surfactant aggregation, may change aggregate structure or induce macroscopic phase separation. For example, added salts

Chemical Trapping in Surfactant Assemblies

generally lower the concentration at which surfactant monomers aggregate to form micelles and often increase the aggregation number, i.e., the number of monomers per micelle [11]. Micelle growth is often attributed to coulombic screening of headgroup repulsions by counterions permitting tighter headgroup packing [12]. But changes in micelle size and shape cannot be interpreted solely in terms of coulombic interactions because they also depend upon counterion type. For example, cetyltrimethylammonium bromide, CTABr, micelles undergo a sphere-to-rod transition when the aqueous Br⫺ concentration exceeds about 0.1 M, but over 1.0 M Cl⫺ is needed to induce this transition in CTACl micelles [13–16]. Chemical trapping provides new insight into the relationships between counterion type, interfacial counterion and water concentrations, and sphere-to-rod transitions (see Section IV.B.1). Understanding relationships between solution composition and aggregate structure and stability in surfactant assemblies requires determining the compositions of their interfacial regions. This is a difficult task, especially in multicomponent systems. A variety of modern techniques, e.g., conductometry, potentiometry, and spectrophotometry [nuclear magnetic resonance (NMR), UV-Vis, fluorescence, electron spin resonance (ESR), infrared (IR), and circular dichroism (CD)], are currently used to examine compositions of these assemblies [1,10,11,17–21]. Some methods monitor only one component at a time, some are limited to narrow composition ranges, and others report on physical properties such as surface polarity but not composition. Moreover, these methods provide information only on the fraction bound of a given component. Only chemical trapping and molecular dynamics calculations [22,23] provide simultaneous estimates of concentrations (or number densities) of more than one component, including water, in the interfacial region. C.

What Does the Chemical Trapping Method ‘‘See’’ in the Interfacial Region of Surfactant Assemblies? What Information Does It Provide?

The chemical trapping method is a probe technique that reports on the concentrations of weakly basic nucleophiles in interfacial regions of surfactant assemblies [24]. The long-tailed arenediazonium ion, itself a surface active cation, is oriented with its reactive diazonio group in the interfacial region (Fig. 2). The hydrophobic tail drags the nonpolar portion of the probe into the oil region of the assemblies, but its hydrated cationic

267

FIG. 2 Cartoon of a small section of a generic surfactant assembly interface illustrating the interfacial region flanked by the oil and aqueous regions, e.g., Fig. 1, and the location of a representative arenediazonium ion probe. The surfactant headgroups could be nonionic, zwitterionic, cationic, or anionic (respective counterions not shown). An alcohol solute may be in all three regions depending upon it hydrophobicity, interfacial structure, and the relative amounts of oil and water in the system. The distribution of added salt, M⫹ and X ⫺, between the interfacial and aqueous regions depends on headgroup charge and anion and cation type. Water molecules (not shown) penetrate the interfacial region by hydrating the headgroups of the surfactants and polar solutes and merge into the oil region, surfactant tails, and any added oil (not shown). The boundaries of the interfacial region (dashed lines) are arbitrary, as are the sizes of the components.

headgroup is anchored within the interfacial region. The ensemble of aggregate-bound arenediazonium ions react via spontaneous loss of dinitrogen to give highly reactive aryl cations that are trapped by all the weakly basic nucleophiles within the interfacial region but not by those in the nonpolar or aqueous regions (see Section II.A). Nucleophiles that will or should react via this mechanism include water, alcohols, and nonionic surfactants; the peptide bond; and many types of anionic concentrations, such as Cl⫺ and Br⫺, and headgroups. All the components in solution, including the probe, are assumed to be in dynamic equilibrium throughout the time course of the overall reaction and the totality of the aggregates in solution is described as a separate phase distributed throughout the surrounding bulk

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phase, either oil or water [11,17]. The aggregate-bound probe ‘‘sees’’ the interfacial regions of the totality of the aggregates and samples this region as a mixed solvent composed of surfactant headgroups, polar solutes, ions, and water. As with other reactions that generate reactive intermediates, the selectivity of dediazoniation reactions toward different nucleophiles is very small and product yields are proportional to interfacial nucleophile concentrations and the selectivity of the reaction toward them [25,26]. Chemical trapping differs from other interfacial probe methods in two important ways. (1) The dediazoniation reaction is unaffected by medium polarity and consequently provides no information on the medium properties of the interfacial region (Section II.B). (2) Concentrations are not expressed as fractions bound but as molarities of the interfacial volume sampled by the probe (Sections II.F and IV.A and B). Another unique feature of the method is that every experiment provides, in principle, an estimate of the concentration of water in the interfacial region from the yield of the phenolic product from reaction with interfacial water (Sections IV.A and IV.B.1). The compositional information obtained by chemical trapping reflects the specific interactions between components in the interfacial region that influence the size, shape, and stability of surfactant assemblies. This information is difficult to obtain by other methods. Finally, the method can be used to estimate distribution constants of components between aqueous-interfacial and oil-interfacial regions over wide ranges of solution compositions (Section IV.C).

II.

THE LOGIC OF THE CHEMICAL TRAPPING METHOD

A.

Arenediazonium Ion Chemistry

Arenediazonium ions have a rich, complex, and still not completely understood chemistry that depends upon substituent type, Y, the nature of the solvent, and reactants such as nucleophiles, X, and electron donors, D [25,27]. Three types of reactions are common (Scheme 1): (1) addition to the terminal nitrogen by strongly basic nucleophiles (see bottom pathway), (2) heterolytic loss of dinitrogen in the presence of weakly basic nuclephiles (see top pathway), and (3) homolytic displacement of dinitrogen by electron transfer from a donor molecule (see middle pathway). This chemical richness sets limits on the range of operational conditions under which arenediazonium ions can function as interfacial probes and is responsible for the formation

SCHEME 1

of certain side products (Sections II.G and III.B). However, in the absence of UV light and reducing and electron transfer reagents, and in neutral to acidic solutions, i.e., in water at pH < 7, arenediazonium ions generally react via rate-determining loss of N2 to give aryl cations that are rapidly trapped by weakly basic nucleophiles (see top pathway) [25,28]. After some searching (Section III.A), 4-alkyl-2,6-dimethylbenzenediazonium ions z-ArN⫹ 2 were selected as the most versatile probes (Scheme 2). The long-chain derivative, 4-hexadecyl, z = 16, is used to probe interfacial regions and its short-chain analogue, 4-methyl, z = 1, provides the reference reaction in the absence of surfactant assemblies and probes the water pools of reverse assemblies (Section II.B.4). Scheme 2 illustrates the heterolytic pathway for competitive reaction with water and other weakly basic nucleophiles, X. The arenediazonium ions are prepared as their tetrafluoroborates (Section III.C). 16-ArN2BF4 is water insoluble and sufficiently hydrophobic that it binds strongly to surfactant assemblies except very near the critical micelle concentration (cmc) [24]. The reactive diazonio group of 16-ArN⫹ 2 is located in the interfacial region (Fig. 2). 1-ArN2BF4 is soluble in water and other polar solvents and is used to determine the selectivity of the dediazoniation reaction toward different nucleophiles, usually relative to water (Section II.D). We have shown by published and unpublished results that many weakly basic nucleophiles react with z-ArN⫹ 2 by the heterolytic mechanism, including the neutral nucleophiles H2O, ROH (nonionic surfactants and alcohols), amides, and


269

SCHEME 2

urea (at both N and O centers of the amide group) and the anionic nucleophiles X⫺ (Cl⫺, Br⫺, and I⫺), ⫺ ⫺ RCO⫺ 2 , RSO4 , and RSO3 . Scheme 3 summarizes re⫹ actions of z-ArN2 with a variety of nucleophiles, both heterolytically and homolytically (phenols and antioxidants). The numbers in bold indicate the reference in

which the preparation of the product is to be found and the bold asterisk (❋) indicates products obtained in as yet unpublished work. Note that Scheme 3 includes many of the weakly basic nucleophiles commonly found in both commercial surfactant systems and in biomembranes and proteins.

SCHEME 3

270

B.

Romsted

Important Characteristics of the Heterolytic Dediazoniation Reactions for Chemical Trapping

The fundamental assumption of the method is that the selectivity of the dediazoniation reaction of 16-ArN⫹ 2 toward two different nucleophiles within the interfacial region of a surfactant assembly is the same as that of 1-ArN⫹ 2 toward those nucleophiles in a reference bulk solution under comparable conditions [24]. This assumption is based on unique characteristics of heterolytic dediazoniations. Specific interpretations of the basic assumption are discussed in the section on the application of the method (Section IV). Dediazoniation reactions are spontaneous, and ratedetermining loss of N2 precedes a very fast reaction with a nucleophile (Scheme 2). Observed dediazoniation rate constants, kobs, are extraordinarily insensitive to solvent polarity and composition [25,28]. For example, the dediazoniation rate constant for the benzenediazonium ion is the same, within a factor of about 9, in concentrated sulfuric acid, methylene chloride, glacial acetic acid, methanol, and dilute aqueous acid [24,28]. In terms of transition state theory, this means that medium changes affect the ground and transition states to similar extents; i.e., the free energy of activation is essentially unchanged [29]. Ab initio calculations of charge distributions in the benzenediazonium ion and intermediate phenyl cation are very similar, consistent with the conclusion that the free energy of activation is approximately constant [30,31]. Chemical trapping results with z-ArN⫹ 2 and other arenediazonium ions are consistent with the spontaneous heterolytic mechanism. For example, kobs values for dediazoniation of 1-ArN⫹ 2 in aqueous TMAX (X = Cl, Br) solutions (0.5–3 M) and 16-ArN⫹ 2 in aqueous micellar solutions of CTAX are essentially the same ⫾20% [24]. Rate constants for dediazoniation of 2-, 3-, and 4-methylbenzenediazonium ions are independent of HCl (0 to 1 M), NaCl (0 to 1 M), and CuCl2 (0 to 0.05 M) concentrations [32,33]. Micelles of sodium dodecyl sulfate (SDS) and copper dodecyl sulfate have small effects on kobs for 2-, 3-, and 4-methylbenzenediazonium ions [34]. The lifetime of the aryl cation has never been measured, but substantial evidence suggests that it must be less than 500 ps [35]. The lifetimes of more stable carbocations such as the diphenylmethyl in 1:1 MeCH: H2O and in aliphatic alcohols [36] and isopropyl cation [37] in aqueous acetonitrile have been measured and are 750, about 70, and 50 ps, respectively. The hydride affinities of these carbocations are substantially less

than that of the phenyl cation [38], suggesting that the lifetime of an aryl cation is governed by diffusion control. Lorand found that the selectives of benzene-, 2,4dimethylbenzene-, and 2,4,6-trimethylbenzenediazonium ions toward Cl⫺ and Br⫺ are independent of solution viscosity, indicating that capture of aryl cations by halide ions is very rapid [39]. However, the lifetime of aryl cations is not zero. Zollinger and coworkers used 15N labeling experiments under N2 pressure in trifluoroethanol to show that the aryl cation lives long enough to permit scrambling of the two nitrogens and to exchange with dissolved dinitrogen during dediazoniation [40]. They interpreted these results in terms of formation of tight and solvent separate aryl cation-dinitrogen pairs [25]. The almost total insensitivity of dediazoniation rates to solvent effects and nucleophile concentrations means that the distribution of neutral and anionic nucleophiles in the immediate vicinity of the ensemble of ground state arenediazonium ions remains essentially unchanged through aryl cation and product formation. Thus, product yields reflect concentrations of nucleophiles within the immediate vicinity of the aryl cations and therefore within the immediate vicinity of the ground state arenediazonium ions. The mechanistic interpretation of dediazoniation selectivities (Section II.C) is similar to one used by Klumpp to describe ground state effects on relative reactivities of competing reactions that have the same or similar high-energy transition states [26]. Measured selectivities toward different nucleophiles are insensitive to properties of the reaction medium (Section II.D). C.

Relationship of the Dediazoniation Mechanism to Measured Selectivities

Scheme 4 shows a modified form of Zollinger’s aryl cation⭈molecule pair mechanism, a preassociation route [41,42] that describes the heterolytic dediazoniation pathway in terms of ground state, arenediazonium⭈ nucleophile, and intermediate aryl cation⭈ nucleophile pairs for a competitive dediazoniation reaction with water and a second nucleophile, X, either neutral or anionic. The aryl cation is a transient intermediate and the steady-state assumption [43] for reactive intermediates is used to derive an expression for selectivities toward two different nucleophiles. Arenediazonium ions are assumed to exist as an ensemble of z-ArN⫹ 2 ⭈ H2O and z-ArN⫹ ⭈ X pairs and their concentrations de2 pend on the value of the equilibrium constant, K XW, and the concentrations of H2O and X. Product yields depend on the concentrations of these arenediazonium


271

about 50 M, and other nucleophiles present. Note that Zollinger carried out dediazoniation reactions under N2 pressure to observed exchange between dissolved N2 (up to 3 M) and the diazonio group [40]. Thus, kX >> k X⫺1[N2] and Eq. (4) simplifies to d[(z-ArX)] = k X1 [(1-ArN⫹ 2 )⭈X] dt

(5)

A similar equation can be derived for the rate of formation of z-ArOH. Substituting the expressions for rates of formation of z-ArX and z-ArOH into Eq. (2) gives: %(z-ArX) k X1 [(z-ArN⫹ 2 )⭈X] = W %(z-ArOH) k 1 [(z-ArN⫹ 2 )⭈H2O]

SCHEME 4

(6)

The ratio of arenediazonium ion⭈nucleophile pairs is given by Eq. (1). Substituting Eq. (1) into (6) gives ion⭈ nucleophile pairs and their rate constants for dediazoniation. As shown in the following, in this mechanism, selectivities are independent of rates of the fast product-forming steps from the aryl cation. In bulk aqueous solutions K XW for the equilibrium between arenediazonium ion⭈ nucleophile pairs is given by K XW =

[(z-ArN⫹ 2 )⭈X][H2O] [(z-ArN2⫹)⭈H2O][X]

(1)

where square brackets indicate concentration in moles per liter of solution volume here and throughout the text. Product yield ratios for these two nucleophiles are proportional to their rates of formation [26]: %(z-ArX) d[(z-ArX)]/dt = %(z-ArOH) d[(z-ArOH)]/dt

(2)

Applying the steady-state approximation, we assume that: d[(z-Ar⫹)⭈X] d[(z-Ar⫹)⭈H2O] = =0 dt dt

(3)

which leads to Eq. (4) for nucleophile X with the rate constants as defined in Scheme 4: d[(z-ArX)] kX k 1X[(z-ArN2⫹)⭈X] = dt kX ⫹ k X⫺1[N2]

(4)

The rate constants for the forward, kX, and back, k X⫺1, reactions should be near the diffusion-controlled limit and numerically similar, but [N2] is very small, about 10⫺3 M, the solubility of N2 in water [44] and orders of magnitude smaller than the concentrations of H2O,

%(z-ArX) K XW k W 1 [X] = W %(z-ArOH) k 1 [H2O]

(7)

Equation (7) is directly related to the definition for the selectivity in the trapping reaction, S XW: S XW =

X W %(z-ArX) [X] KW k1 = %(z-ArOH) [H2 O] kW 1

(8)

Equation (8) shows that the selectivity of the reaction, S XW, equals the product of ratio of the rate constants for rate-determining loss of N2 from the arenediazonuim ion⭈ nucleophile pairs and the equilibrium constant for distributions of the two ion-nucleophile pairs in bulk solution and surfactant assemblies. Values of k W 1 have been estimated for a variety of arenediazonium ions in the absence of X [25,27,45], but independent estimates of K XW and k X1 are not available. However, because heterolytic dediazoniation reactions are so insensitive to medium effects and nucleophile concentrations, the rate constant ratio should be approximately one, i.e., X X kW 1 /k 1 ⬇ 1. This means that values of S W should depend X primarily on K W, i.e., on the interactions of z-ArN⫹ 2 with nucleophilic and nonnucleophilic components. D.

Some Measured Selectivities of Various Nucleophiles

Selectivities have been measured in bulk solution for both nonionic and anionic nucleophiles and this section summarizes values obtained from various sources. 1. Nonionic Nucleophiles Selectivities of these nucleophiles are essentially independent of nucleophile concentration. The selectivity BuOH of 1-ArN⫹ , 2 toward BuOH compared with water, S W

272

is about 0.30 in BuOH-H2O mixtures up to 1 M BuOH (saturation limit) and in 9:1 BuOH/H2O solutions [24,46]. For the competitive reaction of MeOH and H2O with the 2-methylbenzenediazonium ion in 0.01 M HCl at 35⬚C from 8 to 88% MeOH by weight, = 0.41 ⫾ 0.03 for 16 different MeOH concenS MeOH W trations [47]. For aqueous mixtures of tetraethylene and hexaethylene glycols, S ROH = 0.60 [48]. This value is W the same at 18 and 40⬚C, in the presence and absence of added HCl, and is independent of the molar ratio of water to oligooxyethylene glycol from 20:1 to 100:1. Both the amino N and acyl O of simple amides, acetamide, N-methylacetamide, N,N-dimethylacetamide [49,50], and urea (unpublished results) trap 1-Ar⫺. The value of S OW is approximately 1 for the three acetamides and urea, and S NW is approximately 0.1 for acetamide and N-methylacetamide and about 0.4 for urea. No product was observed from trapping of the N on N,Ndimethylacetamide by 1-Ar⫹ within our detection limits, about 1% [49]. 2. Anionic Nucleophiles Selectivities for competition between H2O and anionic nucleophiles such as halogens range between approximately 2 to 15, depending upon the structure of the arenediazonium ion and the anion [24,32,33]. Selectivities toward CH3CO2H and CH3CO⫺ 2 compared with water are essentially the same and about 2 between 0.5 and 5 M (unpublished results). The selectivities for Cl⫺ and Br⫺ decrease with added tetramethylammonium chloride, TMACl, and tetramethylammonium bromide, TMABr. As the anion concentration increases from 0.5 Br to 3.5 M, K Cl W decreases from 7.8 to 4.6 and K W from 14.5 to 8.5 [24]. However, the selectivity toward Br⫺ Br Br Cl compared with Cl⫺, K Br Cl , obtained from K Cl = K W /K W at equal salt concentrations is about 1.9 and independent of salt concentration. What is most striking about these results is the almost total absence of selectivity, i.e., S XW is near one (1). This result is particularly surprising for competition between anions and water for a cation. Such small selectivities are consistent with the heterolytic dediazoniation mechanism and the reactivity-selectivity principle; i.e., highly reactive intermediates show low Cl selectivities [26]. The decrease in K Br W and K W with increasing salt concentration is consistent with ionic strength effects on activity coefficient ratios of arenediazonium ion⭈halide ion complex to halide ion, Eq. (1) [24]. The equivalent expression for K Br Cl has structurally similar complexes and anions in the numerator and denominator and salt effects on activity coefficients should cancel. As noted before, K Br Cl is constant.

Romsted

E.

Application of the Pseudophase Model to Chemical Trapping

Scheme 5 illustrates application of the pseudophase model of aggregate effects on chemical reactivity to dediazoniations occurring in the bulk aqueous and interfacial regions [4–6]. A similar scheme may be written for reaction in bulk oil and interfacial regions. In the pseudophase model, the totality of the aggregates, micelles, microemulsions, vesicles, etc., is treated as a separate phase or, more correctly, a pseudophase distributed throughout the bulk aqueous or oil phase. The transfer rates of components, surfactant monomer, ions, water, and solutes, e.g., arenediazonium ions, are orders of magnitude higher than dediazoniation such that all components are at their equilibrium distributions throughout the time course of the reaction. In micelles and microemulsions, ions and molecules enter aggregates at rates near the diffusion-controlled limit, i.e., ⱕ1 ns, but exit rates depend upon hydrophobicity and, although slower, are still very fast, ⱕ1 ␮s [11,51,52]. The half-life for dediazoniation of z-ArN⫹ 2 is the order of 103 s [24], many orders of magnitude slower than component transfer rates. This analysis shows that product yields from dediazoniations depend upon the fraction of arenediazonium ion located in the interfacial, oil, or aqueous regions of the surfactant assemblies; i.e., its location depends on the equilibrium constant or free energy of

SCHEME 5


transfer between the three regions. Arenediazonium compounds are salts and their solubilities in the oil regions should be negligible. For 16-ArN⫹ 2 , the hexadecyl chain ensures strong binding of the arenediazonium ion to the aggregates. The distribution (or binding) constant, KS, for 16-ArN⫹ 2 (Scheme 5) cannot be measured directly because it decomposes spontaneously. However, it should be similar to that of N-1hexadecyl-3-carbamoylpyridinium bromide, KS = 3.5 ⫻ 103 M⫺1 [53]. Assuming 16-ArN⫹ 2 has the same distribution constant, it would be >97% bound in 0.01 M CTABr [24]. Thus trapping results obtained at ⱖ10 ⫻ cmc with 16-ArN⫹ 2 in cationic micelles should report only interfacial concentrations. Conversely, 1-ArN⫹ 2 is extremely water soluble and reaction occurs only in the aqueous pseudophase, KS ⬇ 0 [54]. Because the structures of the 16-Ar⫹ and 1-Ar⫹ aryl cations are almost identical to those of their arenediazonium ion precursors, their distributions in solutions of surfactant assemblies should be the same as those of the ground state arenediazonium ions. These distribution assumptions will be violated only at the extremes, e.g., anionic micelles bind both short-chain arenediazonium ions [34] and 16-ArN⫹ 2 [55]. In summary, (1) all components are in dynamic equilibrium between aggregates and the surrounding bulk phase and (2) arenediazonium ions decompose spontaneously at essentially the same rate with weakly basic in any medium and therefore (3) product distributions reflect compositions of the phase in which the probe resides. In aqueous solutions, yields of 1-ArOH and 1-ArX from dediazoniation of 1-ArN⫹ 2 are proportional to total concentrations of the nucleophiles. Similarly, yields of 16-ArOH and 16-ArX from dediazoniation of 16-ArN⫹ in surfactant assemblies are 2 proportional to the interfacial molarities of the nucleophiles because its hydrophobicity ensures that the reactive diazonio group is located only in the interfacial region. F.

Basic Assumptions of the Pseudophase Model

To estimate interfacial concentrations of nucleophiles in surfactant assemblies from dediazoniation product yields, we must assume that S XW [Eq. (6)] for reaction in surfactant assemblies using the long-chain probe, z = 16, is the same as that for reaction in bulk solutions in the absence of surfactant assemblies using the shortchain probe, z = 1. That is, Eq. (9) holds under comparable compositions in the interfacial and reference aqueous solutions:

273

X SW =

%(1-ArX) [XW] %(16-ArX) Xm = %(1-ArOH) [H2OW] %(16-ArOH) H2Om (9)

The validity of Eq. (9) is based on known low measured selectivities of weakly basic nucleophiles, their insensitivity to solution composition, and the insensitivity of kobs to solvent polarity, which implies that the very rapid trapping of the aryl cation by nucleophiles will also be insensitive to changes in solvent polarity. Equation (9) states that when product yield ratios from reaction of 1-ArN⫹ 2 in an aqueous solution of known [XW] and [H2OW] are the same as those from reaction of 16-ArN⫹ 2 in a solution containing surfactant assemblies, then the molar ratios of Xm and H2Om in the interfacial regions will be the same as that in water. This approach was used to estimate hydration numbers of nonionic micelles, where X is the terminal OH group of the surfactant (Section IV.A), and the K Br Cl exchange constant (Section IV.B.7). Results in cationic micelles are treated differently because values of S XW for competition between anions, e.g., X = Cl⫺ or Br⫺, and H2O decreases gradually with added salt. To estimate interfacial molarities of anions and H2O, we assume that when product yields in micelles and in the reference bulk aqueous solution are the same, their concentrations in micelles and the aqueous solution are the same. In brief, when yields are the same, concentrations are the same. This approach permits direct estimates of nucleophile concentrations in the interfacial region because the concentrations in the reference solution are known and because this approach automatically corrects for changes in S XW with salt concentration. This assumption was used to estimate interfacial molarities of counterions in Sections IV.B.1, 2, 4, and 6. G.

Limitations of the Chemical Trapping Method

Strongly basic nucleophiles such as OH⫺, CN⫺, SO2⫺ 3 , and N⫺3 react extremely rapidly with the terminal nitrogen (Scheme 1), typically within the mixing time of the reactants and orders of magnitude faster than dediazoniation [25,27]. These nucleophiles cannot be used in the chemical trapping method because there are no aryl cations that can be trapped by weakly basic nucleophiles and no information can be obtained on their interfacial concentrations. This limitation is unfortunate because basic nucleophiles, especially OH⫺, have been used extensively in micellar catalysis studies [4,56,57].

274

Romsted

The acid strength of a nucleophile’s conjugate acid is an imperfect indicator of its nucleophilicity [58]. Weakly basic nucleophiles are generally conjugate bases of strong acids, e.g., Br⫺, ROH, and H2O are conjugate bases of strong acids [29]. However, pKa values of HN3 and CH3CO2H are 4.72 and 4.76, respectively [59], but N⫺3 attacks the terminal nitrogen of the arenediazonium ion at diffusion-controlled rates and CH3CO⫺2 does not and reacts via the heterolytic mechanism. If the measured rate constant, kobs, significantly exceeds that for dediazoniation in water and is sensitive to nucleophile concentration, then the reaction may be occurring by attack at the terminal nitrogen or by electron transfer (Scheme 1). For example, in water in the absence of micelles, added CuCl2 in aqueous NaCl speeds the breakdown of 4-nitrobenzenediazonium ion by a factor of 10 [60]. No reduced product, 4-nitrobenzene, is observed, suggesting that a chlorocuprate complex is speeding heterolysis. Added CuCl2 has little effect on kobs for the breakdown of 2-, 3-, and 4-methylbenzenediazoium ions in the presence [34] or absence [33] of SDS micelles. However, added SDS slightly speeds dediazoniation of 4-nitrobenzenediazonium ion and both SDS and Cu(DS)2 induce the formation of product, 4-nitrobenzene, suggesting that micelles are changing the mechanism [61]. Electron withdrawing groups are known to promote the homolytic pathway (Scheme 1), and micelles may be enhancing this reaction [25,62]. Electron donors (Scheme 1) such as ascorbic acid speed the breakdown of 3-methylbenzenediazonium ions [63] and antioxidants speed the reduction of 16-ArN⫹ 2 to 16-ArH in nonionic micelles (unpublished results), probably by electron transfer [64]. High solution viscosity may also interfere with the chemical trapping reaction. If the surfactant solutions are too viscous, the arenediazonium ion and other components may not be in dynamic equilibrium [48]. The chemical trapping method has not been tried with surfactant assemblies in which the exchange of components is slow, e.g., vesicles. However, the pseudophase model has been used successfully to treat the effect of

cationic vesicles on ester thiolysis [65] and the transfers of 16-ArN⫹ 2 may still be fast enough and vesicle structure sufficiently stable so that the requirement that the components be in their equilibrium distribution is satisfied.

III.

PRACTICAL ASPECTS

A.

Dediazoniations and Chemical Trapping in Aggregates: A Brief History

Selection of 16-ArN⫹ 2 as the most suitable probe of surfactant assembly interfaces was reached through trial and error, assessment of probe properties, and serendipity. Scheme 6 shows four different diazonuim ions that have been or are being used as probes of surfactant assemblies. In 1973 Moss and coworkers published the first dediazoniation reactions in micelles [66]. They demonstrated that micellization changes the stereochemistry of deamination of 2-aminooctane via in situ preparation of its alkane diazonium ion, A. The degree of inversion versus retention of configuration of the 2octanol product from reaction with H2O depends on counterion type. The stereochemical course changed significantly with increasing concentrations of ‘‘hydrophobic’’ counterions, e.g., ClO⫺4 and tosylate, but was unaffected by concentrations of more hydrophilic counterions, e.g., Br⫺ and Cl⫺. Singer and coworkers published the first dediazoniation chemical trapping experiment in 1982 [67]. They prepared holo-micelles, i.e., single-component micelles (in this case the substrate is also the surfactant) from hexyl and octyl alkanediazonium ions, A, from their alkylammonium precursors. Spontaneous decomposition of these micellized alkanediazonium ions in aqueous acid, HX (X = Cl, Br), gave mixtures of 1- and 2-substituted alcohols and haloalkanes, showing that micellization induces a large increase in the selectivity of the dediazoniation reaction toward Br⫺ and Cl⫺ compared with water. The same trends are observed with 16-ArN⫹2 [24]. The alkanediazonium ions have several disadvantages as probes.

SCHEME 6


They decompose too rapidly to be isolated and purified. Acid and NaNO2 are added to transform the amine precursor into the alkanediazonium ion in situ, which makes experiments difficult to run in the absence of salt. The products contain no chromophores and they must be isolated prior to GC analysis. Finally, product distributions may depend on the medium properties of the aggregate interface. Our first attempt at chemical trapping was with probe B. The results demonstrated the viability of arenediazonium ions as probes, but B had some unanticipated weaknesses [68]. Comparison of product yields from dediazoniations of holomicelles of B (R = nC16H33) and of its short-tail methyl analogue (R = CH3) in aqueous solution showed an almost complete inversion of the bromo/phenolic product ratio as determined within the sensitivity of the NMR experiment, ⬃5%. At pH 4–6 in the absence of micelles, the short-chain arenediazonium ion gave only phenols and micelles of the long-chain arenediazonium ion gave only boromo product, but at pH 2 a significant amount of the phenol is formed. We now know that micelles accelerate the rates of electron transfer reactions of phenolic products with unreacted arenediazonium ion as the pH increases (see Section V.C), suggesting that in the pH range 4– 6 the phenolic product is consumed by reaction with unreacted starting material. The utility of B is limited by its long dediazoniation half-life, about 10–20 h at ambient temperature, such that complete reaction takes 4–8 days—a serious test of patience and an analytical method. Our second probe, C, was an arenediazonium ion with an ester group in the meta position. C was selected because syntheses of the long- and short-chain analogues are straightforward and the headgroup is a monocation [69,70]. The hexadecyl derivative was used in micelles and the methyl derivative in bulk aqueous solution. C traps both Br⫺ and Cl⫺ simultaneously at the micellar surface. From the ratio of the halo product yields we estimated ion-exchange constants between these two ions over a wide range of ionic strengths [69,70]. The protocol for estimating exchange constants and the results are discussed in Section IV.B.7. A major limitation of this probe is that the acid concentration in aqueous cationic micelles must be 0.1 M H⫹ or higher with the long-chain probe in aqueous cationic micelles and 0.01 M or higher with the short-chain analogue in aqueous solutions to prevent formation of an unidentified yellow side product. The requirement of high acidity limits the use of this probe in membrane mimetic systems. Probes D (Scheme 6) are in active use. Results with

275

probes D have generated new analytical methods for measurement of dediazoniation rates (see Section III.E). Mancini et al. developed a chemical trapping approach based on the formation of bromonium ion from Br2 and cyclohexene and their reaction with water to give bromohydrins and Cl⫺ to give chlorobromocyclohexane [16]. The halide ion/water product yield ratios showed marked increases at the sphere-to-rod transitions in CTABr and CTACl micelles, but interfacial counterion and water concentrations are difficult to estimate from the data because the results indicate micellar enhanced nucleophilicity of H2O toward the bromonium ion. For results with z-ArN⫹2 in cationic surfactants, see Section IV.B.1. B.

Characteristics of z-ArNⴙ 2 as a Chemical Trapping Reagent

1.

z-ArN2BF4 Salts Are Stable in the Solid State Routine handling problems with arenediazonium salts are minimal, although repeated exposure to the atmosphere and prolonged storage promote reactions with water vapor to give z-ArOH and with BF⫺4 to give zArF (the Schiemann reaction [27], Scheme 3). Care must be exerted because significant amounts of z-ArOH in the solid add to the z-ArOH yield from the trapping of H2O by z-ArN⫹2 in solution. Formation of z-ArF reduces the quantity of arenediazonium ion in the sample but does not affect analyses of products as long as it is present in small amounts. Recrystallization removes both impurities (see Section III.C). 2. Competing Side Reactions To date, the z-ArN⫹2 probes have shown few limitations on their utility. The alkyl groups minimize formation of side products as compared with earlier probes and competing reactions are minimal up to about pH 7. The primary competing reaction is formation of 16-ArH (Scheme 3), which comes from reaction of phenolic product with arenediazonium ion. This reaction is unimportant with 1-ArN⫹2 in aqueous solutions but sometimes becomes significant in surfactant assemblies that speed bimolecular reactions. This reaction competes with dediazoniation most effectively at surfactant concentrations just above the cmc, where the concentrations of aggregate-bound reactants are highest [4]. Note that the phenolic product is structurally similar to antioxidants, e.g., vitamin E, and we are using the reaction of 16-ArN⫹2 with antioxidants to estimate their distributions in microemulsions and emulsions (see Section V.C). Chaudhuri and coworkers discovered a

276

Romsted

second competing reaction, base-induced indazole formation, z-Ind (Scheme 3) [71]. This reaction consumes z-ArN⫹2 but not dediazoniation products, and as long as its yield is small, its formation does not affect quantitative analysis of interfacial concentrations from product yields formed by heterolysis. z-ArN⫹2 Has Good Characteristics for Routine Quantitative Analysis The half-life for dediazoniation is about 30 min at 40⬚C. This temperature has been used in many of our experiments because the reaction proceeds at a convenient rate and because much initial work was in aqueous CTABr, which has a Kraft point at about 25⬚C and tends to precipitate on standing. However, at 40⬚C, the CTABr and Br⫺ concentrations can be varied widely without problem. To date, we have used the probe at temperatures from 18 to 60⬚C [24,48]. Final z-ArN⫹2 concentrations are typically ⱕ1 ⫻ 10⫺4 M. At this concentration, perturbation of surfactant assemblies by 16-ArN⫹2 should be minimal with surfactant concentrations ⱖ0.01 M, i.e., at surfactant/16-ArN⫹2 ratios of ⱖ100:1. In general, product mixtures, including the surfactants, are injected into the HPLC without work-up. The greatest HPLC analysis headache was with 1-ArN⫹2 , which was eventually solved by a simple trick (see Section III.D). 3.

C.

Preparation of z-ArN2BF4 and Its Reaction Products

The arenediazonium ions are prepared as their tetrafluoroborates because these salts of arenediazonium ions have never been reported to explode, unlike those with other counterions [25], and they can be prepared from their distilled aniline precursors by a one-step nonaqueous procedure [72]. The 2,4,6-trimethylaniline precursor to 1-ArN2BF4 is available commercially. The biggest synthetic problem is preparing the precursor to 16-ArN2BF4, 4-hexadecyl-2,6-dimethylaniline. 2,6-Dimethylaniline is alkylated with 1-hexandecanol using anhydrous ZnCl2 as Lewis acid catalyst at 260⬚C for about 1 day [73]. On cooling, the once violet product mixture turns into a hard black amorphous solid and laborious isolation and purification eventually give a white crystalline product with yield of ⬃10–20%. 1HNMR spectra from multiple syntheses show that alkylation occurs without competing 1,2 hydride shift and only at the 4- position of 2,6-dimethylaniline. The 3 and 5 aryl protons give a single signal in the aromatic region and only two 1H signals are observed for — CH3 groups, the ␻ methyl on the hexadecyl chain and the equivalent 2 and 6 methyls on the ring [24].

Dediazoniation product peaks in the HPLC chromatograms are identified by spiking experiments with independently prepared samples. These products are also used to prepare calibration curves for converting peak areas into product yields. Some 1-ArN⫹2 dediazoniation products are available commercially; others are prepared from the arenediazonium salts or by independent syntheses. Details of the preparation of products are in references numbered in bold adjacent to the products in Scheme 3. Products from work in progress are indicated with a bold asterisk. Products from competing reactions are formed via the heterolytic pathway, except for the z-ArH and z-Ind products described in Section III.B. Formation of zArH and z-Ind can be minimized by making the solution more acidic or by increasing surfactant concentrations to inhibit these bimolecular reactions. Fluoro products, z-ArF, are probably formed via the Schiemann reaction with BF⫺4 during storage [48] or in their nonaqueous stock solutions used to initiate dediazoniation; see Section III.D. Arenediazonium ion stock solutions are generally prepared in either MeCN or MeOH. Reaction with MeCN at the terminal nitrogen gives a reactive intermediate that is hydrolyzed by H2O to an acetamide, z-ArOAc [48]. Reaction with MeOH gives an aryl methyl ether, z-ArOMe. All these products appear in HPLC chromatograms, but their yields are generally low, typically 1–2%, and because their formation only reduces the initial concentration of zArN⫹2 . Their presence does not interfere with the analysis of the products from the trapping reaction. D.

Protocol for HPLC Analysis of Reactions and Products

The protocol for carrying out dediazoniation reactions in surfactant solutions is that commonly used for measuring rate constants in solution spectrophotometrically, i.e., injection of a concentrated substrate stock solution into a solution containing the other components [24]. Multiple solutions are prepared, typically in 5- to 10-mL volumetric flasks, with the needed concentrations of components, surfactant, acid, salt, and other additives (e.g., alcohols) and thermally equilibrated. A 5–100 ␮L concentrated stock solution, containing a weighed amount of z-ArN2BF4 is injected into each solution, which is rapidly but thoroughly mixed and returned to the temperature bath until reaction is complete, usually for ⱖ10 half-lives. The carrier solvent is on the order of 1–3% of the final solution volume. To minimize dediazoniation of z-ArN⫹2 in the stock solutions, they are prepared just before use and


kept in an ice bath. Using a weighed amount of zArN2BF4 permits quantitative comparison of the total yield of products with the initial quantity of z-ArN2BF4. Conversion to products is generally quantitative, typically within ⫾10%. Yield variations are usually caused by combinations of weighing and measurement errors and uncertainties in calibrations of products by HPLC. Larger errors suggest unanticipated loss of products, e.g., by formation of products that are not detected by HPLC, such as ionic products that have similar retention times to ionic surfactants, or by formation of unknown products, e.g., ‘‘mystery peaks’’ in the HPLC chromatograms. Such products must be identified by the hard labor of isolation and identification, followed by confirmation by spiking experiments using independently synthesized compounds. One initially refractory problem was eventually solved by a simple trick [24]. Reactions of 1-ArN⫹2 in aqueous TMABr and TMACl solutions gave good reproducible yields of 1-ArOH, but yields of 1-ArBr and 1-ArCl varied widely and sometimes decreased with increasing salt concentration—the opposite of what was expected. The problem was eventually attributed to the very low solubility of haloarenes in water, to their salting out by added salts, and to their vapor pressures. A simple calculation showed that their dediazoniation yields are so low that were they to vaporize completely they would occupy a volume smaller than the head space in the volumetric flask. Layering a small volume of cyclohexane, 50–100 ␮L, on the aqueous solution to dissolve phase-separated products solves the problem. The contents of the volumetric flask are then diluted with sufficient MeOH or i-PrOH to ensure that the solutions are homogenous prior to HPLC analysis. This procedure gives excellent reproducibility. This problem is not observed with 16-ArN⫹2 products, probably because of their higher molecular weights and their solubilization by surfactant assemblies. Products from both 16-ArN⫹2 and 1-ArN⫹2 are separated on Microsorb-MV C-18 reverse-phase columns (4.6 mm inner diameter ⫻ 25 cm; 5-␮m particle size). These inexpensive reverse-phase columns have proved sufficiently robust for many hours of use. Each analysis usually takes from 15 to 30 min. HPLC analysis with UV detection gives high reproducibility ⫾1–2% in peak area for duplicate to triplicate analyses with ⱕ1 ⫻ 10⫺4 M z-ArN⫹2 in solution. Calibration curves for calculating product yields for each product are prepared from independently prepared and purified compounds at four to five concentrations and the correlation coefficient (cc.) are generally >0.99, spanning the range of interest and yields are obtained by interpolation. Once

277

preliminary experiments establish that conversions to expected products are essentially quantitative and reproducible and that all significant peaks are accounted for, normalized product yields are calculated for the products from reactions with components in interfacial regions of surfactant assemblies. This procedure eliminates uncertainties caused by weighing and transfer errors and gives more reproducible results. E.

Measurement of Dediazoniation Rate Constants

The rate constant for dediazoniation should be determined each time the chemical trapping reaction is used with new components. As noted in Sections II.B and II.G, because of the extraordinary insensitivity of heterolytic dediazoniation rates to solution composition, a significant change in kobs may mean a change in mechanism. Four methods are used for determining kobs for dediazoniation that are applicable for different experimental conditions: following the loss of z-ArN⫹2 spectrophotometrically or electrochemically, trapping unreacted z-ArN⫹2 as an azo dye, and monitoring formation of dediazoniation products by HPLC. Details are in the indicated references. 1. Spectroscopy In terms of ease and simplicity, UV spectrophotometry is the method of choice because, in general, z-ArN⫹2 absorbs much more strongly than the reaction products [24,32–34,47,60]. Typically, reaction is initiated by injection of a stock 30–50 ␮L of a 0.01–0.02 M freshly prepared stock solution of z-ArN⫹2 in MeCN or MeOH into an approximately 3-mL thermostated solution in a quartz cuvette containing the other components. The loss of z-ArN⫹2 is usually monitored at its ␭max. The change in absorbance, A, of the reaction is followed for about 10 half-lives. Values of kobs are obtained from standard ln(A⬁ ⫺ At ) versus t plots [74] and cc. ⱖ0.999. Other methods must be used when the spectrum of z-ArN⫹2 is completely masked. 2. Azo Dye Method Because most dediazoniation reactions are relatively slow, their rate constants can be determined by sampling techniques. Bravo-Dıáz and coworkers [32– 34,47,60] took advantage of the very fast formation of azo dyes from arenediazonium ions and naphthoate anions (Scheme 7) to quench dediazoniation reactions. The quenching solutions are buffered at an optimal pH that maximizes deprotonation of the 2-naphthol to give its reactive anion and minimize side reactions such as z-Ind and z-ArH (Scheme 3) and diazotate formation

278

Romsted

SCHEME 7

(Section II.G). Values of kobs are obtained from the increased yield of azo dye with time at its ␭max in the visible region of the spectrum. The yield of azo dye, and therefore unreacted z-ArN⫹2 , is obtained from an absorbance versus azo dye calibration curve. 3. HPLC Method The spectrophotometric and azo dye methods give kobs in terms of the rate of disappearance of the arenediazonium ion. Because quenching halts the reaction, concentrations of dediazoniation products can be measured by HPLC and kobs for their formation can be determined from their peak areas as a function of time [32–34,47,60]. 4. Electrochemical Methods Two methods have been developed by Bravo-Dıáz and coworkers [64,75]. They monitored the loss of 3-methylbenzenediazonium ion by recording differential pulsed polarograms and by using differential pulsed voltammetry to monitor formation of phenolic product. They also showed that formation of azo dye produced by the quenching of 3-methylbenzenediazonium ion (Scheme 7) can be monitored by differential pulsed polarography. Where comparable, the methods give similar values of kobs for a particular arenediazonium ion. Results are generally consistent with the heterolytic mechanism of dediazoniation with the formation of a short-lived intermediate because kobs values for loss of arenediazonium ion and product formation are the same. The primary exceptions are with 4-nitrobenzenediazonium ion (see Section II.G) and in the presence of antioxidants (see Section V.C). IV.

APPLICATIONS OF THE CHEMICAL TRAPPING METHOD

A.

Hydration Numbers of and Terminal OH Distributions in Nonionic Micelles

Chemical trapping in nonionic micelles is a unique approach for estimating the hydration state of surfactant

assemblies. Estimates of hydration numbers of nonionic micelles, e.g., the number of water molecules per ethylene oxide unit in the headgroup of a micellized oligooxyethylene monoalkyl ether, Cn Em, by chemical trapping is conceptually straightforward and we have estimated them in mixed and holo-nonionic micelles [48,76]. Hydration numbers have been estimated by a variety of methods such as light scattering [77], sedimentation equilibrium [78], water (D2O) self-diffusion by NMR [79–82], and 17O magnetic relaxation [83]. All these methods are based on a measured change in a bulk property of the system and require information or assumptions about micellar size and shape to obtain the hydration number. Chemical trapping provides a fundamentally different approach because hydration numbers are obtained from aggregate-bound 16-ArN⫹2 , which samples the composition of the interfacial region. Within the interfacial region, the probe reacts with H2O to give 16-ArOH and the terminal OH groups of the surfactant, R⬘OH, to give 16-ArOR⬘ (Scheme 8). Hydration numbers are obtained from these data (see later) without assumptions about aggregate size and shape, but if the hydration numbers change with aggregate structure chemical trapping results will reflect that change. Chemical trapping requires reproducible product yield ratios and a value for the selectivity of the reaction toward terminal OH groups versus water. Product yield ratios are determined from HPLC peak areas by using calibration curves prepared with independently synthesized and purified products. Other minor products, as discussed in Section III.C, are also formed [48]. The average hydration number of a CmEn micelle is defined as the number of water molecules, NMW , per ethylene oxide unit containing n ethylene oxide units in its En headgroup of the surfactant, RROH : Hydration number =

NMW nNROH

(10)

The molar ratio of interfacial water to oligooxyethylene chains is given by the product of the selectivity of the


279

SCHEME 8

reaction, S ROH W , and the yield ratio from trapping by interfacial water and terminal OH groups: NMW %(16-ArOH) = S ROH W NROH %(16-ArOR⬘)

(11)

The selectivity of the reaction within the interfacial region cannot be measured independently and is assumed to be equal to the selectivity, S EOH W , of the reaction of 1-ArN⫹2 toward oligoethylene glycols and water in their mixtures [48]: ROH EOH SW = SW =

%(1-ArOR⬘) Nw = 0.6 %(1-ArOH) 2NE

(12)

where %(1-ArOR⬘), %(1-ArOH), Nw , and NE are, respectively, yields from reaction with a terminal OH group of the oligooxyethylene glycol and water and moles of water and oligooxyethylene glycol. The factor ‘‘2’’ corrects for the fact that oligoethylene glycols have two terminal OH groups and twice the probability of reacting with 1-ArN ⫹2 . As noted in Section II.D, is independent of the ratio of oligoethylene glycol S EOH W to water. Our estimates of average hydration numbers in C12E6 micelles are consistent with current understanding of the properties of nonionic micelles. The interfacial regions are ‘‘wet’’ [82] and not almost ‘‘dry’’ [84]. At 40⬚C from 0.01 M to about 60 wt%, just below the liquid crystalline phase transition, the average hydration numbers decrease only slightly, from about 3.5 to 2.8. This gradual decline in hydration number and their numerical values are in good agreement with the results of water (D2O) diffusion measurements, although at different temperatures [80]. Hydration numbers in 0.01 M C12E6 decrease linearly with temperature from 4.2 (20⬚C) to 2.9 (60⬚C). Above the cloud point at 50⬚C [81], solutions are phase separated. This steady decrease of hydration number through the cloud point

shows that phase separation is not caused by a sudden dehydration of the interfacial region. When the chemical trapping reaction is carried out in binary mixtures of nonionic micelles having different lengths of polyoxyethylene chains, e.g., C10E4 and C16E8, products are formed from trapping of OH groups of both surfactants [76]. The product yield ratios from reaction with terminal OH groups of the two surfactants are not proportional to their stoichiometric mole fraction ratios. The yield from the shorter oligooxyethylene chain is always in excess over its mole fraction in the micelles. Dr. Jihu Yao developed a novel interpretation of these results. He assumed that the motions of the oligooxyethylene chains obey a radial one-dimensional random walk. Figure 3a is a cartoon of the interfacial region of a mixed nonionic micelle illustrating the orientation of 16-ArN ⫹2 within the interfacial region of a nonionic micelle composed of surfactants with different lengths of oligooxyethylene groups. The interfacial region is divided into layers one ethylene oxide unit thick and the chains are assumed to fold like a carpenter’s ruler at the oxygens with the hydrocarbon core acting as an impenetrable wall. Figure 3b shows the six possible configurations of the E4 oligooxyethylene chain, with each configuration being equally probable. Only the terminal OH groups within layer one (configurations 4 and 6) or layer two (configurations 3 and 5) are assumed to react with 16-ArN ⫹2 . The full treatment of the data provides two pieces of information (Fig. 4): (1) an excellent prediction, without disposable parameters, of the mole fraction yield excess from reaction with the short oligooxyethylene chain over that of the longer chain based on the probability that their terminal OH groups will be in layers 1 and 2, as illustrated for C10E4 /C16E8 mixtures in Fig. 4a, and (2) estimates of the hydration numbers of layers 1 and 2 as illustrated for the same surfactants in Fig. 4b. Equally good results were obtained with five different binary mixtures of

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Romsted

FIG. 3 (a) Cartoon of a small section of the core, interfacial, and aqueous regions of a mixed nonionic Cm E4/Cm E6 micelle showing the location of 16-ArN⫹ 2 with its reactive group adjacent to the micellar core and the flexibility of the alkyl and oligooxyethylene chains. (b) The six possible configurations of the tetraoxyethylene chain of Cm E4 are based on the radial one-dimensional random walk model illustrating the locations of terminal OH groups and EO units; the sticks are — CH2 — CH2 — units. Layer 1 is adjacent to the hydrocarbon core of the micelles and each OH group is assigned to the same layer as that for the EO unit to which it is attached. The inset table shows the probability, P, of finding the OH group in each layer and the ratio, r, of EO to OH groups in each layer. (Adapted from Ref. 77. Reproduced with permission of the American Chemical Society.)

surfactants with different length tails and oligooxyethylene chains. In each case, the predicted excess mole fraction yield ratios are in excellent agreement with experimental results. The hydration numbers of layers 1 and 2 are essentially independent of the ratio of the two surfactants in the micelles and are somewhat lower than the average hydration numbers obtained for holo C12E6 micelles (see earlier). These results show that chemical trapping provides a rapid, reliable method for estimating hydration numbers of holo and mixed nonionic micelles over wide ranges of solution compositions, aggregate structures, and temperatures. The binary mixed micelles studied behave ‘‘ideally’’; i.e., there is random mixing of the surfactants in the aggregates. Chemical trapping may provide insight into the differences in properties of mixed nonionic micelles with very different oligooxyethylene chain lengths that are reported to behave ‘‘nonideally’’ [85,86]. The method may even be applicable to two-phase systems because 16-ArN ⫹2 dissolves in the surfactant-rich phase.

B.

Chemical Trapping in Ionic Surfactants

1.

Interfacial Water and Anion Concentrations In micellar solutions in which the interface region is composed of only two weakly basic nucleophilic components, their interfacial concentrations can be measured unambiguously by chemical trapping. For example, in CTACl micelles, 16-ArN ⫹2 gives two products, 16-ArOH from reaction with H2O and 16ArCl from reaction with interfacial Cl⫺ (Scheme 4, X = Cl) [24]. The yields of these two products depend upon their concentrations in the interfacial region and the selectivity of the reaction toward these two nucleophiles, the first equality on the right-hand side of Eq. (13): X SW =

H2Om %(16-ArX) [H2Ow] %(1-ArX) = Xm %(16-ArOH) [Xw] %(1-ArOH)

(13)

As with chemical trapping in nonionic surfactants, selectivities of reaction at the micellar interface and in


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FIG. 4 Plots of product yield mole fraction (a) and hydration numbers (b) versus the mole fraction of C10E4 in mixed micelles of C10E4 and C16E8 from dediazoniation of 1 ⫻ 10⫺4 M 16-ArN⫹ 2 in 0.02 M total amphiphile at 18⬚C. In (A), the solid line has a slope of 1 and the dashed line is predicted by using the radial one-dimensional random walk model. In (B), hydration numbers are calculated from ratios of product yields from trapping of H2O and terminal OH groups for layers 1 and 2. Details are given in Ref. 77.

FIG. 5 Dediazoniation product yields at 40 ⫾ 0.1⬚C from reaction with H2O (upper curves) and halide ions, X (lower curves), with 1-ArN⫹ 2 in aqueous TMAX, 0.01 M HX (open symbols) and with 16-ArN⫹ 2 in aqueous CTAX, 0.01 M HX (closed symbols): (䡲, ▫) X = Cl; (●, 䡩) X = Br. Dashed lines show that when %(16-ArCl) = %(1-ArCl) = 15%, then Clm (in 0.025 M CTACl) = 1.4 M (in TMACl). Details are given in Ref. 24. Reproduced with permission of the American Chemical Society.

bulk aqueous solution are assumed to be the same; i.e., the equalities in Eq. (13) hold. However, as discussed in Section II.D, the measured selectivities toward Cl⫺ and Br⫺ versus H2O in aqueous TMAX solutions decrease gradually with increasing salt concentration. To calculate Xm and H2Om based on the assumption discussed in Section II.F, we assume that when the yields of 16-ArX and 16-ArOH in a cationic micelle are the same as 1-ArX and 1-ArOH in an aqueous TMAX solution, then Xm and (H2O)m in the micelles are the same as the [Xw] and [(H2O)w] in the aqueous TMAX solution [24]. Figure 5 illustrates graphically the calculation of Clm and (H2O)m in CTACl micelles from their total concentrations in aqueous TMACl and CTACl solutions at 40⬚C in 0.01 M HCl. The dashed lines show that when %(16-ArCl) = %(1-ArCl) = 15%, Clm (in 0.025 M CTACl) = [Clw] = 1.4 M. In practice, the product yields %(1-ArCl) and %(1-ArOH) versus [TMAX] M are fitted by equations that are used as standard curves for

estimating interfacial concentrations. Details are given in Ref. 24. Figure 6 shows the calculated values of Clm and H2Om in CTACl solutions with added TMACl, from 0 to 1.5 M at 40⬚C in 0.1 M HCl [87]. Several patterns are apparent in these data. Xm and H2Om lie on a series of almost parallel lines. Their slopes with increasing [CTACl] are gradual, increasing for Xm and decreasing for H2Om except in 1 and 1.5 M TMACl, for which they are distinctly curved. Added TMACl, at constant [CTACl], produces an approximately incremental increase in Xm and a proportional decrease in H2Om. The upward curvature at 1 and 1.5 M TMACl is in the vicinity of the salt concentrations required to induce the sphere-to-rod transition [13–16]. Figure 7 shows the results in Fig. 6 replotted against the aqueous [Clw]. [Clw] is assumed to be equal to the sum of the concentrations of added TMACl and the concentration of counterions contributed by ionized CTACl micelles, ␣[CTACl], including a correction for

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FIG. 6 Effect of increasing CTACl and increasing TMACl on Clm and H2Om in 0.1 M HCl at 40 ⫾ 0.1⬚C. Clm values were calculated from an equation finding the %(1-ArCl) versus TMACl curve in Fig. 5. H2Om values were calculated from S Cl w values, normalized product yields, and Clm. Details are given in Ref. 88. Reproduced with permission of the American Chemical Society.

the excluded volume of the micelles. Alpha is treated as a disposable parameter, and setting ␣ = 0.4 gives the smoothest profile for Clm values at all TMACl concentrations. Details are given in Ref. 87. The curves in Fig. 7 show that Clm and H2Om are continuous functions of [Clw]. The curves have three different regions: an initial relatively rapid rise in Clm, a linear section with a slope of 1, and a more rapid increase in Clm at about 1.2 M [Clw] that appears again to approach a line with a slope of 1. Note that H2Om responds in a reciprocal fashion. The absence of a plateau contradicts common assumptions used to interpret catalysis in surfactant assemblies. The application of Langmuir isotherms to counterion binding requires that the interfacial counterion concentration saturates at high salt ([88,89] and references therein). In the pseudophase ion-exchange model, the interfacial counterion concentration is assumed to be constant and independent of the concentration of added counterion [4,56,90,91]. When two counterions are present, the sums of their interfacial concentrations are assumed to be constant. For a sur-

Romsted

FIG. 7 Plots of Clm and H2Om versus [Clw] at the optimal ␣ value of 0.4 for CTACl/TMACl solutions. Data and symbols are as in Fig. 6. The straight line has a slope of 1, and the intercept was selected to give optimal contact with the linear portion of the curve. Note break from linearity at 1.2 M [Clw]. Details are given in Ref. 88. Reproduced with permission of the American Chemical Society.

factant system with only one counterion, the interfacial concentration in the pseudophase model is defined as Xm =

␤ [Xm] = Vm [Dn]Vm

(14)

where the ratio of fraction of bound counterions, ␤ ( ␤ = 1 ⫺ ␣), divided by the molar volume available to the counterions in the interfacial region, Vm, is assumed to be constant. In two-site pseudophase models in which counterions are either bound or free in the aqueous pseudophase, ␤ is defined as the molar concentration of bound counterions, [Xm], divided by the concentration of micellized surfactant, [Dn]. In pseudophase models, Vm is generally assumed to be equal to the molar volume of the whole micelle or the molar volume of the interfacial region. In interpreting chemical trapping results, we assume that Vm equals the reaction volume sampled by the diazonio group of 16ArN ⫹2 and is the same as that available to the surfactant headgroups in the interfacial region. The results in Fig. 7 suggest several new ways to view counterion binding in micelles. Both theoretical


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calculations [92–95] and experimental results [56] suggest that ␤ is essentially independent of [Xw]. Thus the relatively rapid, approximately 30–40%, increase in Clm at low [Clw] (50). This suggests a selectively induced by the micellar microenvironment that leads to preferred orientations of the substrate [91]. (b) Anodic Cyanations. Anodic cyanation of 1,3-dimethoxybenze in acetonitrile gives 2,4-dimethoxybenzonitrile (DMB) with a low yield (12%) [92]. This yield strongly increases (80%) if the reaction is carried out in aqueous cationic (CTAB) micellar solution [93,94]. The two reactants (DMB and CN⫺) are associated with the cationic micelles (by electrostatic and hydrophobic interactions). Therefore, their local concentrations in the micellar pseudophase are higher than those in homogeneous organic solutions. This favors cyanation over other competitive reactions (i.e., polymerization). These preconcentration effects are inconsistent with anionic (SDS) micelles as a consequence of the electrostatic repulsion between the negatively charged micelles and CN⫺. Thus, very low yields (4– 8%) are obtained in anionic micellar solutions [93,94]. In addition, different mechanisms occur in cationic micelles and in other solutions (see following Section B). (c) Reduction of 4-Nitrosodiphenylamine. The cathodic reduction of 4-nitrosodiphenylamine (NDPA) was studied in micellar solution by Tabakovic and coworkers [95]. The chemical dehydration step leading to quinonimine in this ECE electrochemical process (Scheme 10) is catalyzed by a base. The corresponding pseudo-first-order rate constant, k, exhibits a lower value (0.5 s⫺1) in cationic CTAB micellar solution than

SCHEME 10 Electrochemical reduction of NDPA. Adapted from Ref. 95 (Scheme 1): J. Electroanal. Chem., Vol. 280 (1990), p 376, A. Davidovic, I. Tabakovic and D. Davidovic, L. Duic, Electrochemical reduction of p-nitrosodiphenylamine in a cationic micellar system. Copyright 1990, with permission from Elsevier Science.

in water (0.9 s⫺1). As previously pointed out [27a], the k value could depend on the local OH⫺ concentration in the micellar pseudophase. In the vicinity of cationic micelles (the Stern layer), the exchange between the counterions OH⫺ and Br⫺ favors the Br⫺ more than the OH⫺ [96]. Therefore, the OH⫺ concentrations and, in consequence, the k value could be lowered in the micellar pseudophase. Thus the chemical step giving the quinonimine and the subsequent p-aminodiphenylamine (ADPA) formation are slowed down in micellar solutions. According to these k variations, preparative electrolysis with an Hg cathode give a mixture of phydroxyaminodiphenylamine and ADPA in micellar solution with high CTAB concentrations (2.7 ⫻ 10⫺2 M) whereas ADPA is the major product obtained in 94% chemical yield in water/toluene emulsions [97] and in 85% yield in CTAB micelles with low surfactant concentrations (2.7 ⫻ 10⫺3 M) [95]. (d) Selectivity. The reaction selectivity can also be controlled by the distribution of the substrate between the two pseudophases. The reduction of acetophenone at the Hg cathode in different micellar systems was studied in detail by the electrochemistry group at the University Blaise Pascal in France ([27g] and references cited therein). With CTAB in acidic aqueous buffer, the electrolysis performed at the potential of the radical reduction gave pinacol and carbinol (Scheme 2). At low acetophenone concentrations (3 ⫻ 10⫺2 and 8.5 ⫻ 10⫺2 M), the carbinol was mainly obtained (65– 70%) and the pinacol was a minor product (30–35%). With increasing concentrations of ketone, this slightly water-soluble substrate (4.5 ⫻ 10⫺2 M [3]) became more and more solubilized in the micelles. The bimolecular dimerization process was favored by the high ‘‘local’’ concentrations of acetophenone in the micellar

Electro-Organic Synthesis

pseudophase and the percentage of pinacol grew to 83% [27g]. 4. Lamellar and Vesicles Dispersions Similar effects occur in these media, but such dispersions are seldom in organic electrosynthesis. The reader will find some examples of electrochemical processes in these dispersions in a review by Rusling [18]. 5. Microemulsion Systems Electro-organic conversions are often performed in o/w and bicontinuous microemulsions. W/O microemulsions are less often used. The properties of microheterogeneous systems (including microemulsions) and electrochemistry in these systems have been treated in various reviews [16–18,98]. Two of them deal specifically with microemulsions [17,98]. The effects of ‘‘local’’ reagent concentrations in microemulsions are often similar to those observed in micellar solutions. Thus, using microemulsion systems can be a way to improve yields, selectivities, and stereoselectivity. In addition, microemulsions allow the solubilization of greater amounts of substrate than micelles. For all of these reasons, the use of conductive o/w and bicontinuous microemulsions in organic electrosynthesis is a promising research field. From a preparative point of view, different kinds of electrosynthesis have been performed in conductive microemulsions: (a) Polymer Films. The formation of polymeric films is generally realized in conductive o/w microemulsions [99–102], but some electropolymerizations have also been done in W/O inverse microemulsions [27h,103] (the influence of surfactants on electropolymerization is reported in the last section). (b) Cyanation of Aromatics. The anodic cyanations of aromatic substrates in both cationic micelles (CTAB, 4 ⫻ 10⫺2 M) and microemulsions (CTAB/n-butanol/nhexadecane/water, 33:33:17:17 wt%) have similar yields and selectivities [94]. (c) Organohalide Dehalogenation. The dechlorination of organic halides ([17] and references cited therein, [104–109]) and the detoxification of pesticides are important applications. Rusling and Zhang have shown that electrochemical catalytic dechlorination of polychlorinated biphenyls (PCBs) in a bicontinuous microemulsion is a promising technique for cleanup of soils and sediments contaminated with PCBs [108]. (d) Indirect Oxidation of Organic Molecules. Rusling et al. have reported the myoglobin-mediated electrochemical oxidation of styrene in cationic microemulsion [110]. Benzaldehyde and styrene oxide were obtained with 50-fold better yields than those ob-

309

served with electrolysis in aqueous buffer. This yield improvement was attributed to better solubility of reactants in the microemulsion than in water [110]. (e) Carbon Bond Formation. Carbon bond formation (and cyclization) ([98] and references cited therein, [111–113]) represents one of the most exciting and promising aspects of the use of microemulsions in electro-organic synthesis, as illustrated by the following examples published by Rusling and coworkers [111,113,114]. Intermolecular and intramolecular (cyclization) carbon-carbon bond formation mediated by electrochemically generated Co(I)L from vitamin B12 was realized as shown in Scheme 11. In a first electrochemical step (reaction I) the cathodic reduction of vitamin B12 gives Co(I)L, which reacts with alkyliodides R-I or with 2-bromoalkyl-2-cyclohexen-1-one (reaction II). This oxidative addition leads to the key intermediate Co(III)L, which can be cleaved either photochemically (reaction III) or electrochemically (at ⫺1.45 or ⫺1.5 V vs. SCE) (reaction IV) giving respectively a radical R• or a carbanion R⫺. In the last step (reaction V) alkycyclohexanones or bicyclic compounds are obtained by inter- or intramolecular addition of R• or R⫺ to the activated carbon-carbon double bond (cyclohexenone). (f ) Photochemistry. Using photolytic cleavage, the conjugated addition of primary alkyl iodides (n-butyl, n-octyl, n-dodecyl) to 2-cyclohexenone gives 3-alkyl cyclohexanones (Scheme 11) as the main product with good yields (68–81%) both in homogeneous DMF solution and in cationic (CTAB) and anionic (SDS) bicontinuous microemulsions [111]. In a similar way, the intramolecular cyclization of 2-(4-bromobutyl)-2-cyclohexenone to 1-decalone (Scheme 11, n = 4) occurs with high yields (75–90%) in the different homogeneous and microheterogeneous systems [111]. Photolytic and electrochemical alkyl-Co cleavages give comparable results for the intramolecular cyclization. However, smaller alkylcyclohexanone yields are observed when an electrochemical cleavage is used as a consequence of the competitive fast protonation of R⫺. The yield of decalone may not be affected by this last process because the intramolecular cyclization is much faster. These results show that conductive microemulsions, less toxic and often less expensive than organic solvents, are useful systems for carbon-carbon bond formation. (g) Stereoselectivity. The most striking effect of microemulsions is the strong increase of the stereoselectivity of the cyclization reaction. The relatively low ratio between the trans and cis isomers of 1-decalone

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SCHEME 11 Mediated electrochemical carbon-carbon bond formation in microemulsions. Adapted from Ref. 111 and 113: J. Org. Chem. Vol. 61 (1996), pp 5972–5977, J. Gao, J. F. Rusling and D. L. Zhou, Carbon-carbon bond formation by electrochemical catalysis in conductive microemulsions, and Vol. 63 (1998), pp 218–219, J. Gao and J. F. Rusling, Electrochemical catalysis of a 5-endo-trig cyclisation in bicontinuous microemulsions. Copyright 1996 and 1998, with permission from The American Chemical Society.

(from 1 to 2.5) observed in organic solution (DMF) increases to 14 when the reaction is carried out in CTAB microemulsions. A detailed mechanistic study of this stereoselective formation of trans-1-decalone in microemulsions was published by Rusling et al. in 1999 [114]. In all 15 cationic and anionic microemulsions studied, 1-decalone is produced in good yield (61–91%) and with high values of the trans/cis ratio (77:23 to 95:5). The authors attributed the selective formation of the trans diastereoisomer to equilibration of isomers via a keto-enol tautomerization. The enol is catalyzed by the OH⫺ ions formed by water reduction, which occurs faster in microemulsions than in polar organic solvents as a consequence of the large amount of water in the former solutions [114]. The intramolecular cyclization of 2-(4-bromobutyl)-2-cyclohexenone was performed in microemulsion by Rusling et al. using vitamin B12 hexacarboxylate chemisorbed to nano-

crystalline TiO2 cathodes. The trans/cis ratios for product 1-decalone were similar to those obtained with vitamin B12 and carbon cathodes, but the turnover was better [115]. The 5-endo-trig cyclization of 2-(3-bromopropyl)-2cyclohexenone (Scheme 11, n = 3) is disfavored and the photolytic cleavage of Co(III)L gives the cyclization product 4-hydrindanone with poor yields (21–24%) in both organic (DMF) solution and cationic (CTAB) microemulsions. The major produce is 2-allyl-2-cyclohexenone, whose formation is faster than the cyclization. Bad yields (7–19%) are also observed in organic and hydroorganic solutions when the cleavage is done electrochemically [113]. The carbanion R⫺ intermediary formed by the Co(III)L cleavage is quickly protonated, giving 2-propyl-2-cyclohexenone as the main product. Apparently, this protonation is strongly reduced in anionic and cationic microemulsions leading

Electro-Organic Synthesis

to 4-hydrindanone with good yields (62–70%). The authors suggest that the cyclization occurs at a site with low concentration of proton donor, i.e., in the oil phase or in the interfacial surfactant layer [113]. 6. Summary As evidenced by the preceding examples, the use of conductive bicontinuous microemulsions is a powerful method by which the control of electrochemical reactions can be realized. Thus the selectivity and even the diastereoselectivity of processes can be changed and oriented to the formation of the desired products. From this point of view, the work done by Rusling and coworkers represents a major contribution in this field. In some cases, product extraction from micellar and microemulsion systems can be difficult, because of the great amount of surfactant that is often used. An original solution is given by Bunce et al. in two papers [116,117]. They report the electroreduction of hexachlorobenzene and DDT in an emulsion formed with 0.05 M sodium sulfate aqueous electrolyte containing 1% (v/v) heptane and 0.1% (v/v) Triton-SP175. TritonSP175 is a nonionic surfactant with a hydrophobic tail attached to a polyethoxylate hydrophilic chain. The emulsion was indefinitively stable at neutral pH, but it was easily broken by a brief treatment with dilute acid. Below pH 3 the hydrophobic part is cleaved from the polyethoxylate chain and Triton-SP175 loses its surfactant properties. Thus the product extraction can be performed without difficulty [116,117]. In micelles, microemulsions, and related systems using surfactant, the solvent affects the specific interactions. Variation of the local concentrations of reactants and products can occur both in the bulk pseudophases and in the aggregates adsorbed on the electrodes. Therefore, electrode modification is an important parameter. This parameter can also play an important role in emulsions, as shown in the next section. B.

Effects Resulting from Electrode Modification

One of the most important phenomena in electrode modification is the formation of hydrophobic layers, either by wetting or by the dispersed organic phase (emulsions) or by adsorption of surfactant (micelles, microemulsions), with two main consequences: The range of usable potential can become larger than that observed in a continuous conducting aqueous phase. The kinetics of bimolecular reactions can be controlled by modification of reactant concentrations in the adsorbed layer.

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1.

Increase of the Potential Range

(a) Macroheterogeneous Systems (Emulsions). As pointed out in the first part of this chapter, in emulsions the electrode wetting by the organic phase can be important. This wetting can form a thin hydrophobic film on the electrode. This occurs during anodic nucleophilic substitutions in H2O — CH2Cl2 emulsions under phase transfer catalysis conditions. A thin CH2Cl2 film is formed on the anode [118,119]. Using thin-film contactor cells, Fleischmann and coworkers have studied the optimal synthesis conditions and developed a simple theoretical model [120,121]. The film formation depends on the anode material, the nature of the phase transfer catalyst, and the electrolytes [118,122,123]. The aqueous phase oxidation cannot be entirely suppressed. Nevertheless, the presence of a CH2Cl2 film allows the oxidation of organic compounds in a large potential range (up to 1.8 V vs. SCE) [122–124]. Since the first study published by Eberson and Helgee in 1974 [125], two-phase electrosyntheses with phase transfer catalysts have been widely developed for cyanation [118,122,125–128], acyloxylation [120,121, 123,129–131], and chlorination [119,124] of several molecules. A decrease of the aqueous electrolyte oxidation or reduction due to electrode wetting by a nonconducting organic phase is often encountered. This wetting phenomenon can be enhanced using hydrophobic electrodes prepared by composite plating nickel with hydrophobic oligomer particles. On this type of electrode the wetting by the organic droplets strongly reduces the water oxidation or reduction, and the electrochemical conversion of organic compounds emulsified in aqueous solutions has been achieved with medium to good yields [132]. (b) Microheterogeneous Systems (Micelles, Microemulsions). The adsorption of surfactants does not always enlarge the accessible potential range, and this range can be reduced in some cases. Thus, the adsorption of cationic surfactants can increase the local concentration (on the anode) of readily oxidizable counterions (e.g., CN⫺, NO⫺ 2 ) whose enhanced oxidation reduces the anodic limit [94,133]. For instance, the anodic nitration of N,N-dimethylaniline occurs with good yields (60–85%) in cationic micellar solutions formed with cetyltrimethylammonium salts [27a,133]. But the medium current efficiencies (23–47%) observed with the counterion SO4H⫺, which is not oxidized at the working potential, drop to very low values (5–10%) ⫺ counterions with the easily oxidizable NO⫺ 2 or Br [133]. However, Franklin and coworkers have devel-

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oped a series of applications of electrodes coated with hydrophobic Hyamine 2389 films (Hyamine 2389 is a cationic surfactant, mainly methyldodecylbenzyltrimethylammonium chloride) [134–144]. This film shifts the oxidation potential of water (alkaline solution) from 0.7 V to about 1.8 V (vs. SCE). It allows direct or indirect oxidation (involving the oxidized Hyamine as mediator) of numerous organic compounds in emulsions (CH3CN–aqueous NaOH) or in Hyamine micelles [137,138,140]. Franklin and coworkers have also developed a Hyamine 2389–polystyrene filmed Pt anode stable in alkaline and acidic solution. The positive limit of the potential window is shifted up to about 2 V (vs. SCE) and numerous organic substrates give oxidation waves well defined on this modified electrode [142,144]. The reader can find a more detailed account of the electrodes coating in a review by Rusling [18]. 2.

Influence of Reactant Association with the Surfactant Adsorbed Layer

(a) Emulsion Systems. The presence of surfactants adsorbed on the electrode can strongly enhance the adsorption of an organic substrate emulsified in an aqueous electrolyte. The electrochemical conversion of the substrate is thus improved. This aspect is illustrated by the following examples. The electrocatalytic hydrogenation (ECH) of unsaturated compounds (phenanthrene, limonene, and carvone) was performed on Raney Ni cathodes (Scheme 1) in hydro-organic solutions; in aqueous cationic (CTAB), anionic (SDS), and nonionic (Brij 35) mi-

TABLE 1

celles; and in emulsions with cationic surfactants (CTAB or DDAB) [27a,38,145,146]. In micellar solutions both current efficiency and the extent of hydrogenation increase compared with the homogeneous hydro-organic solutions. The highest effects are obtained with cationic micelles. The improvement of the reaction efficiency results mainly from the cathode modification caused by the surfactant adsorption. Indeed, the highest current efficiency (87%) for the ECH of carvone into four isomeric saturated alcohols was observed with this substrate emulsified in an aqueous electrolyte in the presence of very low surfactant concentrations (CTAB at 8.2 ⫻ 10⫺5 M) [38]. Moreover, the most important increase of current efficiency and extent of hydrogenation is obtained in emulsions in the presence of low amounts of didodeclydimethylammonium bromide (DDAB), a cationic non-micelle-forming surfactant [146]. This aspect is well demonstrated by comparing the ECH of limonene in different homogeneous and microor macroheterogeneous media (Table 1) [38,146]. The ECH of the sparsely water-soluble limonene emulsified in an aqueous buffer does not occur at all (entry 1, Table 1), and the hydrogen evolution reaction (HER) (reactions 5 and 6, Scheme 1) takes place alone. As already mentioned, this was attributed to the absence of substrate adsorption on the cathode. When limonene is entirely solubilized in a homogeneous hydro-organic solution, its ECH gives specifically p-menthene with good yields (62–66%) but with poor current efficiencies (18–19%) after the consumption of an excess of

ECH (30⬚C, 5–7 F/mol) of Limonene in Homogeneous and Heterogeneous Solutions

Yield (%) Entry 1 2 3 4

Solution

pH

p-Menthene

p-Menthane

Current efficiency (%)

Emulsified Homogeneous (EtOH/H2O) Micellar: CTAB 5.5 ⫻ 10⫺2 mol dm⫺3 Emulsified ⫹ DDAB 2.7 ⫻ 10⫺4 mol dm⫺3

2 (buffer) 4 (14) 2 (12) 10

0 62 (66) 9 (44) 9

0 miniemulsion > microemulsion polymerization. The polymerization recipes are designed in such a way (for instance, oil-soluble instead of water-soluble initiators) that the polymerization takes place mainly inside the preformed monomer droplets. In these techniques the stabilizers have to support the emulsification process and the stabilization of the monomer droplets, whereas in case of emulsion polymerization a separate free monomer phase must not necessarily be present. Moreover, the monomer can be fed continuously into the reactor either as neat monomer or as emulsion with the additional advantage of being able to polymerize most of the time at a conversion corresponding to the polymerization rate maximum.

INTRODUCTION

Emulsion polymerization belongs to the class of heterophase polymerizations that comprises a wide variety of different techniques generally characterized by their heterogeneous nature. This can mean liquid in gas, solid in gas, liquid in liquid, and solid in liquid heterogeneous systems. The participation of stabilizers is important in the cases in which at least one component stays liquid throughout the whole process. Considering only liquid dispersion media (or continuous phases), then suspension, microsuspension, miniemulsion, microemulsion, and dispersion polymerization belong with emulsion polymerization to the polymerization techniques leading to polymer dispersions. A polymer dispersion is considered to consist of a polymer that is finely distributed in a liquid dispersion medium in the form of stable individual particles. It does not matter whether the polymer is a solid or a highly viscous fluid at a given temperature. In principle, the liquid forming the continuous phase can be any liquid in which the polymer is insoluble. In the following, water is considered exclusively as the dispersion medium because these systems are the most technically important; furthermore, the significance of water as a dispersion medium will increase considerably in the future for environmental reasons. It is useful to define emulsion polymerization in a general way as polymerization or copolymerization in aqueous systems of any combinations of monomers that lead to water-insoluble polymers or copolymers in the form of individual polymer particles with a size distribution of diameters in a range typically lower than 429

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It is obvious that emulsion polymerization is a large topic in its own right with nearly 90 years of history and an extensive literature including monographs, textbooks, conference proceedings, and almost 800 original papers and patent applications per year. Emulsion polymerization is commercially the most important process for effecting the preparation of polymer dispersions. Almost 7% of the world polymer production is produced as a polymer dispersion, which corresponds to 107 tons calculated as dispersion with 50% solids content [1]. Concerning the variety of applications of polymer dispersions, the reader is referred to excellent overviews [2,3]. It is possible to accomplish an emulsion polymerization in very different ways, as illustrated by the following examples. The simplest emulsion polymerization recipe comprises only two components: a monomer that can undergo thermal polymerization (e.g., neat styrene) and water. Stirring at elevated temperatures (about 90⬚C) leads to polymerization mainly in the bulk monomer phase but also results in a turbid aqueous phase. The solid content of the water phase is less than 1%, and its examination by electron microscopy reveals the existence of polystyrene particles with an average size of about 100 nm. Contrary to this example, polymerization recipes for industrially important polymer dispersions comprise up to six monomers, frequently more than two emulsifiers, more than one initiating system, and a few other aids such as biocides, defoaming agents, and plasticizers for supporting film formation [4]. The monomer-to-water ratio is adjusted in such a way that a solids content typically between 40 and 60% or even higher is obtained. The amounts of surfactants and initiator (mainly persulfate) are typically between 0.5 and 2% (w/w) relative to the monomers and 0.5% (w/w) relative to water, respectively. According to the definition of emulsion polymerization given earlier, another limiting case for a recipe consists of an aqueous monomer solution (i.e., no free monomer phase) in the presence or absence of surfactants. The radicals can be produced either by light or by thermal decomposition of water-soluble initiators (azo- or peroxo- compounds). Indeed, such systems have been attracting researchers continuously for more than 50 years [5–12]. Depending on the particular conditions (type and concentration of components such as monomer, initiator, emulsifier, and reactor material), particles will be nucleated or not [11,12]. The words stabilizer and emulsifier and surfactant will be used interchangeably in the text to refer to a substance that is amphiphilic in nature, consisting of

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hydrophobic and hydrophilic parts, and is able to adsorb at any interfaces present in the aqueous phase. Stabilizers can be either polymeric or monomeric and their hydrophilic groups can be either charged or uncharged. It is not an exaggeration to say that all kinds of stabilizers have been applied in emulsion polymerizations. This chapter is organized in such a way that after briefly considering some historical aspects, an attempt is made to outline a more general mechanistic picture of emulsion polymerization. This mechanism is discussed especially with respect to nucleation, particle swelling, and particle growth, always emphasizing the role of surfactants and emulsifiers. Then follow some general remarks regarding the role of stabilizers during both the polymerization and the application of polymer dispersions. Finally, technical realizations of emulsion polymerization are briefly described before the chapter is finished with remarks on unresolved problems and possible future developments. The peculiarities of different monomers or monomer combinations in emulsion polymerization are not subject matter of this chapter but are more general aspects of emulsion polymerization. II.

HISTORICAL DEVELOPMENT

For comprehensive and detailed information concerning the early days of emulsion polymerization, the reader is referred to excellent reviews by Whitbey and Katz [13,14] and Hohenstein and Mark [15,16]. The development of heterophase polymerization techniques is closely connected to the history of synthetic rubber. The birth of emulsion polymerization can be tracked to 1909, when attempts were made to reproduce the mild conditions during the latex synthesis employed by nature in order to improve the properties of synthetic rubbers prepared by bulk polymerization initiated with metallic sodium [17]. Consequently, the first materials used as stabilizers were naturally occurring biopolymers such as gelatin, egg albumin, starch, milk, and blood serum. These substances are rather hydrophilic protective colloids and are not typical surfactants. No catalysts were used, and the polymerization was started by keeping the reaction mixtures in an autoclave stirred for several weeks at elevated temperatures in the presence of oxygen (air). In the second half of the 1920s, work on the heterophase polymerization of dienes made significant progress when typical surface-active molecules (ammonium, sodium, and potassium oleates as well as alkyl aryl sulfonates) were applied [18–20] for the first time. Furthermore, these disclosures specify

Emulsion Polymerization

the simultaneous use of surfactants and initiators (water as well as monomer soluble peroxides) and hence can be considered as the start of catalyzed emulsion polymerization. These particular experimental results from 70 years ago that use a single surfactant were sufficient to enable the manufacture of polymeric dispersions with relatively high solids at considerably increased polymerization rates compared with surfactant-free polymerizations. This advance was an essential breakthrough in the development of emulsion polymerization techniques. Emulsion polymerization grew rapidly in importance in the following 20 years mainly due to activities in German and U.S. companies. Once the strategic and economic importance of this polymerization technique was recognized, its further development in both countries was supported and sponsored by government funding. In Germany, the ‘‘Kunststoffkommission’’ (Plastics Committee) [21] was established, and in the United States the ‘‘Rubber Reserve Company; Synthetic Rubber Program of the United States Government’’ [22] was formed. A special advantage of the emulsion polymerization technique was soon recognized. It is possible to obtain simultaneously both high polymerization rates and high molecular weights in such a radical polymerization process. Other technical advantages include ease of maintaining almost isothermal conditions during the polymerization because of good heat transfer through the aqueous phase and the possibility of easily removing unreacted monomers by steam stripping. Therefore this polymerization technique not only was used for dienes but also was applied to a variety of monomers and monomer mixtures including styrene [23,24], acrylic and methacrylic acid esters [25], vinyl esters [26], vinyl chloride [27], and ethylene [21]. It was also found possible to prepare a variety of polymer dispersions by homo- as well as copolymerization that were either used as dispersions or the solid polymer was further processed after coagulation. The first such example for a direct application was a polyacrylate dispersion for leather finishing [28]. During these early days of emulsion polymerization, the pace was mainly determined by industrial researchers and hence the span of time from first laboratory results to technical application was relatively short. Unfortunately, most of the early results are summarized in nonpublic research reports or published in the form of patents. There is only one report on emulsion polymerization in the open literature before 1939, and it is in the form of an abstract. Fikentscher reported on the occasion of the annual meeting of the Plastics Division

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of the German Chemical Society in 1938 on ‘‘Emulsion polymerization and technical exploitation’’ and gave interesting information concerning the knowledge at this time in Ludwigshafen [29]. First, he pointed out that the polymerization does not take place inside the monomer droplets, rather it is the monomer that is dissolved in the aqueous emulsifier solution that is polymerized. Through diffusion from the reservoir droplets the monomer concentration is maintained constant in the aqueous phase as long as droplets are present. Second, the polymerization recipe has to be fitted for each monomer or monomer combination to find optimal polymerization conditions; furthermore, if the polymer dispersion is directly applied, it is necessary to consider by the design of the polymerization recipe requirements arising from the particular application. Finally, Fikentscher emphasized the economic importance of emulsion polymerization at this time for Germany, where the amounts of directly applied polymer dispersions based on acrylic acid ester, vinylic ester, and vinyl ether monomers were increasing rapidly. However, the amount of polymer produced by emulsion polymerization but processed as powder was much greater, with Buna S (synthetic rubber) ranking first, followed by poly(vinyl chloride). After World War II, more and more research activities to investigate the polymerization mechanism were started at universities and in independent research institutes worldwide. It is worth mentioning a few landmarks in the historic development of emulsion polymerization regarding mechanism and theory. Harkins [30,31] developed a general mechanistic picture of emulsion polymerization with two essential features. First, he considered two loci of particle formation, the monomer swollen micelles and the aqueous phase. The latter becomes more and more important with decreasing emulsifier concentration. Second, he identified the monomer swollen polymer particles as the locus in which nearly all of the polymer is formed. The most important contribution to emulsion polymerization theory was published in 1948 by Smith and Ewart [32]. These authors developed a quantitative theory of the kinetics of radical polymerization in isolated loci (monomer swollen polymer particles) where the free radicals are supplied to the loci from an external source (aqueous phase). The centerpiece of the SmithEwart theory is the famous and generally valid recursion formula for the number of particles containing a given number of growing radicals and therefrom derived an average number of radicals per particle, n¯ . With respect to n¯ , three cases are of interest: (1) where n¯ > 1. An

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approximation for the number of particles (N) formed assuming case 2 (e.g., n¯ ⬇ 0,5) suggests that N depends on the 3/5 power on the surfactant concentration (CE), to the 2/5 power on the rate of formation of free radicals, and should decrease to the ⫺2/5 power on the average growth rate of a particle. The assumptions made to derive these relations are that particle formation stops when the emulsifier micelles disappear and the rate of polymerization per particle is constant, independent of the particle size or of the rate of entrance of free radicals. Note that the constant rate of polymerization per particle means that both the monomer and the radical concentration in the particle are constant. All these assumptions are quite restrictive, and hence one would expect that these relations are fulfilled only under very special circumstances. Indeed, even for styrene, which is believed to be a very good monomer to meet the assumptions, experimental results are known confirming [33] as well as contradicting [34] the N ⬀ S 3/5 relation. Gerrens and his colleagues at BASF in Ludwigshafen have contributed greatly to the knowledge of emulsion polymerization kinetics of technically important monomers [33,35–37]. Fascinating work consists of the laboratory-scale experiments on the continuous emulsion polymerization of styrene, where the oscillation phenomena in latex surface tension and particle size distribution have been carefully investigated [38,39]. The development of a quantitative theory of nonmicellar particle formation in emulsion polymerization is entirely owing to Fitch and Tsai [40–42]. In 1965, Fitch proposed that if a growing macroradical in solution becomes insoluble, it precipitates and forms a particle [43]. Initiation, capture of growing radicals by existing particles, and coagulation of the single-chain particles are considered as individual steps. A few years later, Hansen and Ugelstad contributed considerably to homogeneous particle formation in emulsion polymerization both theoretically [44] and experimentally [34,45]. This kind of homogeneous nucleation theory in emulsion polymerization is today called HUFT theory for Hansen, Ugelstad, Fitch, and Tsai. Hansen and Ugelstad also contributed to the general kinetics of emulsion polymerization with a landmark paper published in 1976 [46]. They developed a procedure to calculate n¯ and its dependence on radical entry, exit, initiation, and termination in the aqueous phase. Napper, Gilbert, and coworkers made many important contributions to our understanding of emulsion polymerization. They pointed out the role of coagulation of primary particles during the nucleation period [47]. Furthermore, they did a great deal on developing

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methods to estimate rate constants for entry, exit, termination, and propagation [48]. The Emulsion Polymers Institute at Lehigh University headed by Vanderhoff and El-Aasser over the past decades has contributed enormously to the whole field of polymer dispersions, covering nearly all topics from the kinetics of different heterophase polymerization techniques to polymer particle characterization methods and particle morphology control. The development of miniemulsion polymerization to a topic in its own right over the past 25 years is strongly connected with El-Aasser and his coworkers [49]. It is interesting to note that this development—the polymerization inside preformed monomer droplets with diameters between 100 and 300 nm—started together with Ugelstad [50]. Emulsion polymerization research has grown enormously worldwide with strong research groups working in nearly all industrialized and developing countries. Techniques have been developed to prepare extremely monodisperse particles with special functionalities for medical applications [51] and to design the particle morphology as well as the properties of the polymer dispersions in a desired way [52]. Reviews of emulsion polymerization have been published almost regularly, and it is possible to refer the reader to a short list of excellent monographs and overviews published during the past 45 years [53–59].

III.

KINETICS AND MECHANISM

A.

Rate of Polymerization

The basic equation of emulsion polymerization kinetics with respect to monomer conversion is Eq. (1): dMT rP = ⫺ = kP CM NP n¯ ⫹ rP,W dt

(1)

where rP is the rate of polymerization MT is the overall monomer concentration in M, t is the time in s, kP is the propagation rate constant in M⫺1 s⫺1, CM is the monomer concentration within the latex particles in M, NP is the particle concentration in M, and n¯ is the dimensionless average number of radicals per particle. Note that the product n¯ NP corresponds to the overall radical concentration in radical solution or bulk kinetics if the polymerization in the aqueous phase is neglected. The monomer conversion rate in the aqueous phase is rP,W (rP,W = kP,W MW RW), where kP,W denotes the propagation rate constant in M⫺1 s⫺1, MW the monomer concentration in M, and RW the radical concentration in the aqueous phase in M.


An important assumption leading to Eq. (1) is that there are only two principal reaction loci in an emulsion polymerization: the aqueous phase and the monomer swollen polymer particles. Thus, initiation of the polymerization inside the monomer droplets (if present) takes place only to a very minor extent and can be neglected at least if water-soluble initiators are used. Again, this is a completely different situation compared with suspension, microsuspension, miniemulsion, and microemulsion polymerization, where the major part of the polymerization takes place inside the monomer phase. Equation (1) looks simple but the solution is complicated as CM, NP, and n¯ are complex functions of time. Furthermore, rP,W depends mainly on the monomer solubility in water as well as on the partition of radicals and monomer between particles and water, respectively. A detailed discussion is, however, outside the scope of this contribution. The reader is referred to a summary of a NATO Advanced Study Institute [58] and textbooks [55–57]. Emulsion polymerizations can be carried out as discontinuous (batch), semicontinuous (feed), or continuous processes. In the case of semicontinuous processes, either the neat monomer or a monomer emulsion containing water, stabilizer, monomer, and initiator is fed into the reactor over a certain time period. Feed procedures are frequently applied in industrial polymerizations. A nice prescription for a laboratory scale feed polymerization can be found in Ref. 4. Furthermore, emulsion polymerizations can be subdivided in ab initio and seed processes. Ab initio means that particle nucleation and particle growth take place consecutively in the same reactor. A seed process means that particle nucleation and particle growth are spatially separated and the growth process is usually controlled in such a way that nucleation of new particles does not occur unless the preparation of latexes with multimodal particle size distributions is desired. There are three distinct stages during an ab initio emulsion polymerization that are generally characterized as follows: Stage I: particle formation where dNP /dt > 0 Stage II: particle growth where dv/dt ⱖ 0 (v, volume of a swollen particle) Stage III: monomer starvation where dCM /dt < 0 and dv/dt < 0 (shrinkage of the monomer swollen particles) Equation (1) contains all essential quantities that are necessary to describe even quantitatively the conversion time curve of an emulsion polymerization provided kP and the functions CM (t), NP (t), and n¯ (t) are

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known. However, determining these quantities is not that easy. The minor part of the problems arises from kP, as today, with pulsed polymerization techniques, exact determinations of kP values are possible even under the conditions of an emulsion polymerization [60]. It is a good approximation to assume that rP,W is constant during stage I and stage II. With respect to n¯ (t), the situation is easy for so-called zero-one systems in which a radical inside a particle will immediately terminate when a second radical enters. In that case n¯ (t) = constant = 0.5 (Smith-Ewart case 2) and we have to determine only CM (t) and NP (t). It is easy to keep NP (t) constant during the polymerization (after particle formation is finished or during seed polymerizations when a seed is added and particle formation is avoided) by a proper choice of the stabilizing conditions. Concerning CM (t), the assumption is made that it is constant as long as a free monomer phase is present or the monomer feed is constant, e.g., during stage II [56,57]. However, the situation regarding CM (t) will be considered later in more detail. These assumptions result in an rP (t) curve for an ab initio emulsion polymerization with an emulsifier concentration above the critical micelle concentration (cmc) as shown schematically in Fig. 1. As long as NP increases, rP increases as well (stage I). When dNP /dt = 0, stage II is reached and the rate of polymerization is constant until the monomer concentration declines accompanied by a decrease in rP during stage III (curve a in Fig. 1). However, it may also happen that the situation for the growing radicals inside the particles during stage III changes in such a way that rP increases for a short period of time (curve b in Fig. 1) due to the

FIG. 1 Schematic drawing of the change of the rate of polymerization (rP) and the latex surface tension (␥) with polymerization time (t) during an ab initio emulsion polymerization obeying Smith-Ewart case 2 kinetics: (a) without Norrish-Trommsdorff effect and (b) with Norrish-Trommsdorff effect.

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Norrish-Trommsdorff effect or gel effect [61,62]. Reaction calorimetry allows on-line monitoring of the rate of polymerization during emulsion polymerizations. Systematic investigations of the emulsion polymerization of styrene in the presence of sodium dodecyl sulfate (SDS) at a concentration higher than the critical micelle concentration and potassium persulfate (KPS) as initiator (a classical Smith-Ewart case 2 system) revealed that the constant rate period during stage II does not necessarily occur [63]. There is experimental evidence that the end of the nucleation period (stage I) and the start of stage III (monomer starvation) take place at the same conversion range between 36 and 40%. Similar results have been observed for butyl methacrylate emulsion polymerization started with SDS and KPS. The results depicted in Fig. 2 show no period during the polymerization with a constant polymerization rate [the heat flow (HF) corresponds directly to the rate of polymerization] and also a decrease in the rate at a conversion of about 40%. Note that the water solubilities of n-butyl methacrylate and styrene differ only slightly [64,65]. One characteristic feature of these reaction rate profiles is the maximum in the heat flow at the beginning of the polymerization, which is independent of the KPS concentration in the same conversion range of a few percent and which seems to be a

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special feature of this monomer in emulsion polymerization [66]. Meanwhile, many examples are known which confirm that the reaction rate profiles measured with calorimetric techniques deviate more or less from the Smith-Ewart case 2 predictions [63,67–71]. These results clearly show that the schematic drawing in Fig. 1 is not a general situation in emulsion polymerization kinetics but a special case that is only rarely fulfilled in ab initio polymerizations. The schematic drawing with respect to changes of the latex surface tension is verified by experimental results, as discussed later. It is interestingly to note that in the case of the much more water-soluble methyl methacrylate, almost ideal behavior was observed with respect to rP. The polymerization was started with the redox system ceric ion and poly(ethylene glycol) with a molecular weight of 104 g mol⫺1. In that case a poly(ethylene glycol) radical starts the polymerization and stabilizes the resulting block copolymer particles. The reaction rate profile shows an increase in the heat flow at the beginning followed by a long time period in which the heat flow stays constant and finally an extremely high gel peak before rP almost linearly decreases [72]. This behavior is qualitatively comparable to results of electron spin resonance investigation of methyl methacrylate emulsion polymerizations [73]. The reason for the observed deviations from the ideal Smith-Ewart case 2 behavior is the invalidity of any of the preceding assumptions. If either NP (t), CM (t), or n¯ (t) is not constant, rP is also not constant during stage II if it is assumed that the case in which the changes cancel one another out is rather unlikely. Consequently, the development of NP, CM, and n¯ during an emulsion polymerization requires additional attention and will be discussed in the following paragraphs. B.

FIG. 2 Reaction rate profiles for ab initio emulsion polymerizations of n-butyl methacrylate depending on the initiator concentration. Polymerization recipe: 80 g of water, 20 g of n-butyl methacrylate, 0.2 g of SDS, and (a) 0.2 g of KPS, (b) 0.1 g of KPS, and (c) 0.05 g of KPS; calorimeter RM2-S (ChemiSens, Lund, Sweden).

Particle Nucleation

Before discussing particle nucleation in detail, it seems useful to try a definition. Looking at the aqueous phase polymerizations in the absence of emulsifier and a free monomer phase, it is straightforward to identify the nucleation process as formation of the second, the polymer phase (first-order transition). Consequently, all events after this phase formation such as coagulation of the particles do not belong to particle nucleation. Three basically different nucleation mechanisms are discussed in scientific papers: Micellar nucleation, according to which a particle is formed per se when a radical enters a micelle [56].


Precipitation mechanism (frequently called homogeneous nucleation, HUFT theory), according to which a particle is formed when a single growing chain becomes water insoluble and precipitates [56,57]. Aggregation nucleation, according to which nucleation occurs when a critical supersaturation of growing or dead oligomers in the aqueous phase is reached and this solution becomes unstable and separates in to a polymer phase and a less concentrated aqueous phase [74]. (In contrast to the precipitation mechanism, this is a multichain process.) The phenomenon of particle formation is probably the subject of most controversy in the scientific discussion of ab initio emulsion polymerization. There are at least two reasons for this. The first is that nucleation in emulsion polymerization is considered by most of the heterophase polymerization community to be very special and was not considered in connection with other nucleation phenomena such as bubble and droplet nucleation or crystallization processes. But especially in these fields, very well developed theoretical approaches have existed for more than 70 years [75–77] but have remained unnoticed for a long period of time. In 1975, Barrett used the classical nucleation theory (CNT) and the Flory-Huggins theory of polymer solutions to consider nucleation in dispersion polymerization without directly connecting it with polymerization kinetics [78]. This is the more surprising as the CNT was applied in 1950 by LaMer and Dinegar to a chemical reaction also leading to a colloidal system: the hydrochloric acid–catalyzed formation of sulfur hydrosols starting with thiosulfate [79]. The second reason is connected to the experimental problems of resolving particle nucleation in emulsion polymerization. Particle nucleation occurs at an extremely low conversion or solids content and there is no direct single method that allows the detection of the onset of particle nucleation. For instance, in the case of a surfactant-free styrene emulsion polymerization started with KPS, the onset of nucleation was clearly detected by a combination of on-line turbidity with online conductivity measurements [74,80]. In that particular case, nucleation occurred after a prenucleation period—in which aqueous phase polymerization takes place—of 431 s. At the moment of nucleation, 1.76 ⫻ 1013 particles are formed per cm3 of water with an average particle size of 13 nm. The amount of polymer or better oligomer formed up to this moment is 2.13 ⫻ 10⫺5 g per cm3 of water [81]. Most of the conclusions with respect to nucleation in emulsion polymerization have been based on experimental results obtained far

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away from the nucleation point. Hence, almost no hard experimental facts exist supporting or rejecting one or the other idea on nucleation. Harkins pointed out that the particles formed in the absence of micelles exhibit no essential difference in behavior from particles initiated in the presence of surfactant micelles [31]. Nucleation processes are an important part of our world. They concern researchers in meteorology, geology, biology, chemistry, and medicine, in food and beverage companies, and in the production of silicon single crystals and other crystallization processes dealing with nucleation phenomena under the umbrella of general thermodynamic considerations fitted to the particular problem. Emulsion polymerization research should make a step forward in this direction. It is also necessary to address a problem that is a direct consequence of the lack of conversation between the nucleation community and the heterophase polymerization community. Both communities use the same technical terms but mean different things. For instance, in the heterophase polymerization community, heterogeneous and homogeneous nucleation mean nonmicellar and micellar nucleation mechanisms, respectively. In the more general point of view of the nucleation community, homogeneous nucleation occurs when interfaces have no influence, whereas in the case of heterogeneous nucleation the process is influenced by any interfaces present in the reaction system. Consequently, both ‘‘micellar’’ and ‘‘homogeneous’’ nucleation in emulsion polymerization can either occur homogeneously or heterogeneously. It is frequently believed and stated that the SmithEwart theory and the relation NP ⬀ S 3/5 are based on micellar nucleation. But this not true. It is entirely owing to Roe, who showed that the same scaling laws result if the assumption is made that the particles are generated by a homogeneous reaction in the water phase [82]. The emulsifier micelles serve as a reservoir from which the single emulsifier molecules diffuse to the newly created particle-water interface and impart stability to the particles. Newly formed particles can be stabilized as long as a certain amount of free (not adsorbed) surfactant is present. There are several arguments against a micellar nucleation mechanism even if micelles are present. It was stated by Roe [82] ‘‘that some factor other than the presence of micelles exerts a strong effect on particle generation.’’ He came to this conclusion from a simple but impressive experimental fact, namely that it is possible to generate equal particle numbers in styrene emulsion polymerizations even if the micelle concentrations in the case of chemically different emulsifiers

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(potassium laurate and a nonionic emulsifier at concentrations below and well above the cmc, respectively) are widely different. Twenty years earlier, Staudinger [83] carried out emulsion polymerizations of styrene and butadiene at constant initiator and emulsifier concentrations. He used potassium dodecanoate and octadecanoate, respectively, and observed a lower initial rate of polymerization for the runs with the dodecanoate soap although there was more potassium dodecanoate in the micellar form than potassium octadecanoate. Also, Robb [84] obtained evidence for nonmicellar particle nucleation in styrene emulsion polymerization with persulfate as initiator and sodium decyl sulfate and sodium dodecyl sulfate as emulsifier. A last example is the famous paper of Priest [85] concerning the emulsion polymerization of vinyl acetate, a much more water-soluble monomer than styrene. He introduced the idea of a single-chain precipitation as nucleation mechanism followed by an interparticle combination (coalescence or coagulation) in the case of stabilizer-free polymerizations. So, the question arises, how do surfactants contribute specifically to nucleation or to the development of the particle concentration? Figure 3 shows a plot of ln N vs. ln CE for styrene emulsion polymerization initiated with persulfate and varying emulsifier concentration for potassium octadecyl sulfonate (Amphoseife, curve a) and pure SDS (dodecanol free, curve b). Although the actual condi-

FIG. 3 Double logarithmic plot of the particle numbers at the end of a styrene ab initio emulsion polymerization (N per cm3 of water) depending on the emulsifier concentration (CE in grams per cm3 of water). Curve a: emulsifier, Amphoseife C18; initiator, 0.361 g potassium peroxodisulfate per liter of water, 45⬚C (data from Ref. 33). Curve b: emulsifier, sodium dodecyl sulfate; initiator, 0.6 g potassium peroxodisulfate per liter of water, 60⬚C (data from Ref. 34).

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tions are not identical with respect to temperature and KPS concentration, the extreme difference between both types of surfactants is surprising. Curve a proves the Smith-Ewart prediction (exponent 0.61), whereas curve b has a much higher exponent (2.67). The higher exponent indicates a higher emulsifier efficiency regarding particle stabilization of the SDS compared with the C18 alkyl sulfonate. These results are understandable only if the Krafft temperatures of both surfactants are considered. The Krafft temperature (TK) is defined as the temperature at which the solubility equals the cmc and hence reflects an equilibrium between surfactants in solution and hydrated crystals. The experiments with the Amphoseife as surfactant were carried out at 45⬚C, but the TK of sodium octadecyl sulfonate is between 57 and 70⬚C [86]. Taking into account that TK can be shifted a little to lower temperatures (no pure water as dispersion medium and counterion influence), the polymerizations were carried out very close to TK. Under these conditions it is very likely that not all of the surfactant was available for stabilization. In the case of SDS with a TK between 8 and 16⬚C [86] the difference between TK and the polymerization temperature (60⬚C) is so large that all of the surfactant is available for stabilization. In a series of very well designed experiments Dunn and Al-Shahib investigated the influence of the emulsifier chain length on the emulsion polymerization of styrene [87–89]. They used C8, C10, C12, C14, C16, and C18 sodium alkyl sulfates at equal concentrations of 60 mM and came to the conclusion that the number of micelles initially present does not determine the particle concentration but rather the total surface area of the micelles governs the particle number. Figure 4, which combines the particle numbers of Al-Shahib and Dunn [87] with the number of micelles according to Amiansson et al. [90], shows that there is a negative or almost no correlation between both quantities. On the other hand, a strong correlation exist between the particle numbers and the cmc of the surfactants (Fig. 5a) and the adsorption energies (Fig. 5b), respectively. The adsorption energies were calculated according to Lunkenheimer et al. [91]. How surfactants assist with the time development of the particle concentration can now be answered. The cmc of a given surfactant and the adsorption energy are measures of the surface activity or of the stabilizing power for a given surfactant. The lower the cmc and the higher the adsorption energy, the higher is the surface activity. The same concentration provided the total micellar surface as discussed by Dunn [89] is also a measure of the surface activity. Consequently, a more


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FIG. 4 Plot of the particle numbers (N per cm3 of water) at the end of an ab initio emulsion polymerization of styrene as a function of the number of micelles (Nmic per cm3 of water) for sodium alkyl sulfonate surfactants with varying alkyl chain lengths between C10 and C18T and a concentration of 60 mM. Particle numbers are from Ref. 87 and micelle number was calculated with data from Ref. 90. Polymerization recipe: 80 mL of styrene, 200 mL of water, 12 mL of 0.1 M sodium hydroxide solution, 0.424 g of potassium peroxodisulfate, 60⬚C.

plausible explanation of these results is that after particles have been formed the stabilizing power of the surfactant is responsible for the observed effects in the sense that the higher the chain length the stronger the adsorption and consequently the better the stability and the larger the surface area or the higher the number of particles that can be stabilized. Finally, a higher number of particles leads to a higher rate of polymerization. With the CNT it is possible to answer the question of how a surfactant assists with nucleation. A centerpiece of a model for particle nucleation based on the CNT is a free energy equation for the nucleus formation (⌬GN) [Eq. (2)]. ⌬GN = (⫺c1m ln S ⫹ c2 (mj)2/3␥21 ⫹ gedl)ghet

(2)

where m is the number of chains forming a nucleus and j is their chain length, S is the supersaturation, c1 and c2 are constants [92], ␥21 is the interfacial tension between the nucleus and the dispersion medium, gedl is the contribution of the electrical double layer [93], and ghet is the heterogeneous contribution due to the presence of substrates with interfaces [94]. As the dispersion medium in water, it is always necessary to consider the influence of charges. The gedl can be expressed as gedl = ⫺c3␴⌿0(mj)2/3 where c3 is a constant, ␴ is the surface charge density, and ⌿0 is the surface potential.

FIG. 5 (a) Dependence of the particle numbers (N per cm3 of water) at the end of an ab initio emulsion polymerization of styrene on the logarithm of the critical micelle concentration for sodium alkyl sulfonate surfactants with varying alkyl chain lengths between C10 and C18. Particle numbers are from Ref. 87 and the critical micelle concentrations are from Ref. 90. (b) Dependence of the particle numbers (N per cm3 of water) at the end of an ab initio emulsion polymerization of styrene on the absorption energy (⌬G ads 0 ) of sodium alkyl sulfonate surfactants with varying alkyl chain lengths between C10 and C18. Particle numbers are from Ref. 87 and the adsorption energies are from Ref. 91.

Furthermore, gedl depends on the ionic strength, the dielectric constant of the dispersion medium, the size of the nucleus, and the temperature. The ghet can be expressed in a simple way as ghet = (2 ⫹ ␣c)(1 ⫺ ␣c)2/4, where ␣c is obtained with Young’s equation as function of the contact angle (⌰) at which the nucleus makes contact with the substrate ␣c = cos ⌰ = (␥31 ⫺ ␥32)/␥21. The interfacial tensions ␥31 and ␥32 denote the tensions between the substrate and the dispersion medium and between the nucleus and the substrate, respectively. With the approximations gedl = 0 and ghet = 1, Eq. (2) can be used easily together with the radical polymerization kinetics and Flory-Huggins solution theory to model particle nucleation as described [74,92].

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FIG. 6 Schematic drawing of the course of the free energy (⌬G) during nucleation and its dependence on the number of molecules (m) forming a nucleus. ⌬G#, free energy of activation of nucleation; m*, number of molecules forming the critical nucleus.

An important difference between the aggregation nucleation model and the micellar and precipitation nucleation models is the occurrence of an activation energy. Figure 6 shows schematically the change of ⌬G with dependence on m. The oligomers have to form a nucleus of a critical size (m*) to surmount the energy barrier (⌬G#). Nuclei with a size smaller than m* are unstable and dissolve, whereas nuclei with a size larger than m* survive and continue to grow. As the rate of nucleation is an exponential function of ⌬G#, the nucleation process is very sensitive to small changes in the conditions and to impurities. Essential features of the aggregation nucleation model based on the CNT have been verified experimentally in a qualitative way in the case of styrene emulsion polymerization [74,80,95]. Consequently, the

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sketch in Fig. 7 reflects the course of a surfactant-free styrene emulsion polymerization. After the initiation, the reaction starts in the aqueous phase with the formation of water-soluble oligomers (prenucleation period). When a critical supersaturation is reached, nucleation occurs. The real nucleation process is very fast: in a time period of less than 1 s a huge number of particles is formed. The fate of the particles after their nucleation depends on the particular conditions. A decrease in the particle number as shown in Fig. 7 due to a coalescence process was observed in the case of a surfactant-free polymerization. Note that this is qualitatively the same development of N with the polymerization time as predicted by Priest [85] for the much more water soluble vinyl acetate. At an SDS concentration higher than the cmc, after the jump during the nucleation step a further increase in N was observed [96]. In the case of the nonionic surfactant Antarox CO880 the particle number remained unchanged after the nucleation. In that case it was possible to use conductivity measurements to detect the onset of nucleation. An almost linear decrease in the duration of the prenucleation period was measured with increasing Antarox CO880 concentration, spanning a range from below to above the cmc [74]. This is exactly the way a surfactant contributes specifically to nucleation. A surfactant can lower ␥21 and in this way influence the free energy of nucleation. Ionic surfactants have an additional influence on nucleation as they may also change gedl. It was shown that the nucleation process in emulsion polymerization is influenced by the reactor material and hence the nucleation is heterogeneous [11]. Consequently, ghet is of some importance. If ⌰ is zero degrees, then ghet is zero and hence nucleation takes place

FIG. 7 Schematic drawing of the development of the particle number during a surfactant-free ab initio emulsion polymerization.


as soon as supersaturation is reached (S ⱖ 1). On the other hand, if ⌰ is 180 degrees ghet is 1 and the nucleation is homogeneous, which means that interfaces or substrates have no influence. If 0 < ghet < 1, nucleation is to a certain extent heterogeneous and ⌬G# is lower than in the homogeneous case. An important quantity within the framework of the CNT is the supersaturation. S is defined as the ratio of concentration to solubility. Nucleation occurs at a critical supersaturation, which can be related to a critical nucleation concentration of oligomers in the aqueous phase (CNC). Concerning the nucleation in emulsion polymerization, these considerations lead to two important conclusions. First, for a given monomer, not only the chain length of the oligomers (j) but also the chemical nature of the end groups is important. Consequently, chemically different initiators lead to different supersaturation necessary for nucleation even for the same monomer. Furthermore, for persulfate it has been known for almost 50 years that due to its oxidizing capability, sulfate ion radicals and hydroxyl radicals are formed [97–99]. In an aqueous dispersion medium the situation is still more complicated as radicals can take part in variety of additional reactions [100]. This also seems to be true for carbon radicals [101]. It was possible to show with matrix-assisted laser desorption ionization time-of-flight mass spectroscopy that the polymer inside the particles of a styrene emulsion polymerization initiated with KPS and with 2,2⬘azobis(2-amidinopropane)dihydrochloride, respectively, has besides the expected end groups a variety of other end groups such as hydroxyl, hydrogen, and carboxylic groups [81,102,103]. These reactions are the reason that in the aforementioned case of a thermally initiated surfactant-free emulsion polymerization of styrene, the particles possess some stability. Obviously, if two oligomers have the same j but one has a hydroxyl and the other a sulfate end group, their solubilities will be different. The oligomers with the lower solubility will nucleate earlier provided the critical S is reached. Second, the surfactants and the monomers that are present in the aqueous phase also have an influence on the solubility of the oligomers. It is not only solubilization by micelles, but increased solubility is also due to the freely dissolved molecules. Before starting and during an emulsion polymerization the dispersion medium is generally not a pure aqueous phase. Under these conditions it is important that dissolved organic matter leads to an increase in the solubility of other organic compounds [104]. That this really may have an influence on nucleation was shown in the case of an aqueous phase styrene polymerization. In some cases,

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in the presence of surfactants, no particles have been detected, whereas in the corresponding surfactant-free polymerizations particles have been detected [11,12]. The conclusion is that surfactants may cause an increase in the CNC and under certain conditions, for instance monomer starvation, their presence can even prevent nucleation. Nucleation means the formation of the second reaction locus—the polymer particles. This has strong consequences with respect to the distribution of all participants in the reaction system. Surfactants, monomers, and radicals have to redistribute, and according to Eq. (1) the kinetics will change as well. C.

Swelling of Polymer Particles

Just after nucleation the polymer particles start to interact with their environment. This corresponds first and foremost to the uptake of monomer. Most monomers are good solvents for their own polymer but the polymer particles in an aqueous dispersion are not dissolved by the monomer. This phenomenon resembles the behavior of macroscopic gels, which also do not dissolve upon interacting even with a good solvent. Hence, the technical term swelling is used in both cases. Note that swelling of macroscopic gels is an original topic of colloid science [105,106]. It is necessary to come back to this analogy later. The understanding of the swelling behavior of latex particles is important for several reasons: 1.

2. 3. 4. 5. 6. 7.

To verify the mechanism of emulsion polymerization with the monomer swollen polymer particles as the main reaction locus [30–32,107–110] To control the monomer concentration at the main reaction locus [111–113] To control the copolymer composition in the case of more than one monomer [114–116] Because it determines the viscosity inside the particles and hence influences the kinetics [48] For the preparation of large monodisperse particles [117–123] For controlling particle morphology and structure [124–136] For controlling and reducing the residual monomer concentration during the high conversion period of the polymerization [48,137]

Different methods have been applied to investigate the swelling of latex particles. Most popular are methods based on vapor pressure measurements to investigate both the swelling kinetics and equilibrium swelling [113,138–141]. But other methods have also been

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employed such as conductivity measurements [142]; scanning angle reflectometry, which allows direct observation of the uptake of the swelling agent by the particles [143]; and density measurements for investigating the equilibrium swelling [144]. Note that swelling experiments require extremely stable latexes as swelling leads to conditions favoring latex instability (increase in surface area and decrease in internal viscosity). Furthermore, as pointed out by LaMer and Gruen, investigating the swelling by means of size measurements leads to unambiguous and useful results only if the initial system is monodisperse. For polydisperse systems, the Laplace or Kelvin effect causes an increase in the polydispersity [145]. An important topic that is discussed from time to time is whether swelling leads to a homogeneous or heterogeneous distribution of the swelling agent inside the latex particles. A heterogeneous morphology is discussed for the particles in a styrene emulsion polymerization that consist of a polymer-rich core and a monomer-rich shell. The controversial discussion at the beginning of the 1970s can be followed in Refs. 146 and 147 with arguments supporting a core-shell structure and in Refs. 148 and 149 with arguments favoring a homogeneous morphology. In the middle of the 1990s, spatial inhomogeneities in poly(methyl methacrylate) latexes swollen with methyl methacrylate under equilibrium conditions were deduced from smallangle x-ray scattering data [150]. The authors concluded that there was a depletion of the polymer chains near the particle surface due to the wall repulsion effect and estimated a thickness of approximately 2 nm for the outer shell where the monomer is enriched. The answer to whether swelling leads to homogeneous particles is not easy to find. First of all it is necessary to distinguish between dynamic swelling during the polymerization and equilibrium swelling in nonpolymerizing systems. In the first case, monomer diffusion from the droplets or the gas phase has to compete with the monomer consumption due to polymerization. The rate of monomer diffusion through the aqueous phase is normally higher than the polymerization rate [111]. But there is some evidence that diffusion through the particle-water interface is hindered [111,113]. This is probably due to condensed surfactant layers. If mass transfer resistance is high, it can, of course, influence a homogeneous monomer distribution throughout the particle during polymerization. An inhomogeneous monomer distribution throughout a polymerizing particle may also occur for larger particles with higher n¯ values. In the case of equilibrium swelling, however, an inhomogeneous monomer distribution is not easy to

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understand. A possible explanation will be given in the following. Morton et al. [109] calculated the change in the chemical potential during swelling of latex particles [Eq. (3)]. Here the Flory-Rehner term [151] (last term in the brackets on the right-hand side) for cross-linking is added in order to be more general.

冉冊 2␥ r

冋

V1 = ⫺ ln(1 ⫺ ␾2) ⫹ (1 ⫺ 1/j)␾2 RT V1␳2 ⫹ ␹␾22 ⫹ ¯ (␾ 21/3 ⫺ ␾2/2) MC

册

(3)

In Eq. (3) ␥ is the interfacial tension between particle and dispersion medium, r is the swollen particle radius, V1 is the molar volume of the swelling agent, RT is the thermal energy, ␾2 is the polymer volume fraction at equilibrium, ␹ is the Flory-Huggins interaction param¯ C is the average moeter, ␳2 is the polymer density, M lecular weight between two cross-links in the network. ¯ C ⇒ ⬁), Eq. If the latex particle is not cross-linked (M (3) is identical to the Morton-Kaizerman-Altier (MKA) equation [109]. Figure 8 compares measured monomer volume fraction (␾1)–particle size (D) curves with predictions using Eq. (3), where ␾1 = 1 ⫺ ␾2 is valid. Between ␾1 and CM the relation ␾1 = CMVmon holds, where Vmon is the molecular volume of the monomer. Note that D is

FIG. 8 Change of the monomer volume fraction inside the latex particles (␾1) with the swollen particle size (D) at equilibrium swelling for polystyrene particles swollen with styrene ( j = ⬁). The open symbols are calculated data according to Eq. (3) with ␹ = 0.45, 25⬚C and ␥ = 3 mN m⫺1 for (䡩), ␥ = 30 mN m⫺1 for (▫), and ␥ = 70 mN m⫺1 for (䉭). The experimental data are from Ref. 107 for (●) and from Ref. 142 for (䡲) and (䊱). (●) Polystyrene latex in the presence of free potassium laurate; (䡲) cleansed polystyrene latex with covalently bound sulfonate groups; (䊱) cleansed polystyrene latex with covalently bound gluconosiloxane groups.


the swollen particle diameter, which is related to the unswollen size (D0) according to (D/D0)3 = 1/␾2. The common feature of the experimental data is the increase in ␾1 with D. As this increase is perceptible up to particle sizes over 200 nm, some doubts arise regarding the assumption of a constant monomer concentration in the particles during interval II. A quantitative comparison of the data presented in Fig. 8 shows that at the same particle size the experimental monomer volume fraction differs up to a factor of 3. This illustrates the additional importance of parameters other than particle size and chemical nature of the polymer. The samples for series 2 and 3 were prepared with reactive surfactants and extensively cleaned to remove all residual recipe components as well as oligomers formed during the polymerization [144]. These latexes represent extremely stable neat polystyrene spheres with covalently bound stabilizing groups. In contrast, the latexes of series 1 contain such amounts of free potassium laurate emulsifier that the surface is still completely saturated at the swelling equilibrium [109]. This means that swollen micelles as well as adsolubilized swelling agent in the surfactant layer at the particle water interface lead to that high ␾1 values [109,152]. It was shown that the apparently increased swelling of a poly(vinyl acetate) latex with increasing emulsifier concentration was due to a specific interaction of vinyl acetate monomer with the ethoxylated nonyl phenol surfactant [153]. The vinyl acetate monomer was enriched in the surfactant layer. The swelling agent should also be enriched at the particle-water interface for entropic reasons in the presence of adsorbed surfactant. Hence, the adsorbed surfactant is probably responsible for the observed inhomogeneous particle structure at equilibrium swelling [150]. Figure 8 shows that ␥ is an important parameter to shift the calculated curves in the vicinity of the experimental data. This is almost perfectly possible for series 1 but not so good for series 2 and 3. Furthermore, a curve through the experimental data of series 2 and 3 will reach the origin only if the dependence of ␾1 on D is changed for smaller diameters. Note that the ␥ values needed for series 2 and 3 are much too high. For neat polystyrene surfaces the interfacial tension with respect to water is 32.7 mN m⫺1 at 20⬚C [154]. Even a value of 30 mN m⫺1 is much too high as the latexes of series 2 are stabilized with sulfonate groups. According to Eq. (3), it is possible to estimate ␥ and ␹ values by plotting [⫺ln(1 ⫺ ␾2) ⫹ ␾2]/␾22 against 1/(r␾22). For series 1 this leads to reasonable values (␥ = 2.2 mN m⫺1 and ␹ = 0.474), whereas for series 2 and 3 much higher ␥ values and unrealistic ␹ parameters [96] are obtained.

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In conclusion, the MKA equation with reasonable values for ␥ and ␹ in the case of neat polystyrene latexes stabilized with covalently bound sulfonate and gluconosiloxane surfactants predicts much higher monomer volume fractions than are measured. In contrast, in the case of polystyrene latexes in the presence of excess potassium laurate, where the micelles and the surfactant layer at the particle-water interface mainly contribute to swelling, the agreement between theory and experiment is excellent. A possible solution of this problem requires a modification of the MKA equation in such a way that the contribution of the polymer core to swelling is considered in greater detail. The basic assumption of the MKA equation that only the change in the interfacial free energy counterbalances the swelling force is questionable. The crucial point is that a polymer latex particle behaves differently compared with a solvent droplet or a gas bubble or a micelle of the same size. The difference is an attractive force between the polymer chains that, in addition to the interfacial free energy, counteracts swelling. This attractive force between polymeric chain segments has been proved for a variety of polymers in semidilute solutions by osmotic compressibility measurements [155]. It is worth noting that upon dilution, the attractive force is reversed in a repulsion between the chains. A swollen latex particle represents a highly concentrated polymer solution (at ␾1 = 0.5 the concentration is higher than 1 g per cm3 swelling agent) and thus attractive forces exist between the polymer segments. Consequently, calculating the change in the chemical potential during swelling of latex particles needs an additional term to resist swelling. The simplest possibility is the introduction of P dV, the volume work, where P is a pressure and V the particle volume. The same procedure as used by Morton et al. [109] leads to Eq. (4).

冉

冊

2␥ ⫹P r

冋

V1 = ⫺ ln(1 ⫺ ␾2) ⫹ (1 ⫺ 1/j)␾2 RT V1␳2 ⫹ ␹␾22 ⫹ ¯ (␾21/3 ⫺ ␾2/2) MC

册

(4)

where P can be regarded as swelling pressure similar to that for the swelling of macroscopic gels. In order to reach an equilibrium with the swelling agent, if the gel is not maximally swollen, a pressure must act on the gel, otherwise it would try to reach the maximum swelling. This pressure is called swelling pressure and is identical to the osmotic pressure of a solution in considering the gel as membrane [106]. In the case of latex particle swelling, the surface tension pressure

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(␥/r) and the swelling pressure together balance the chemical potential. The limiting cases of Eq. (4) regarding r → ⬁ and ␾2 → 0 are the osmotic pressure or swelling pressure equation and the Young-Laplace equation, respectively. This seems to be very reasonable as it is an expression for the position of polymer colloids between colloid and polymer chemistry. The results depicted in Fig. 9 prove that the consideration of an additional resistance to swelling is very satisfying. The theoretical curves are shifted with surface tensions of 7 and 14 mN m⫺1 in the range of the experimental data for series 2 and 3, respectively. The grading in the ␥ values between all series seems to be reasonable. Compared with the experiments of series 2 and 3, where the aqueous phase is pure, the experiments of series 1 contain several organic solutes leading to a decrease in ␥. The difference in ␥ between series 2 and 3 is due to the fact that the latexes of series 2 have sulfonate groups whereas those of series 3 are sterically stabilized by gluconosiloxane groups. A first way to solve the problem regarding the change in the size dependence of ␾1 that still exists has been proposed in Refs. 144 and 156. Concerning the influence of surfactants, the swelling experiments described in these papers are unique, as for the first time latexes in

FIG. 9 Change of the monomer volume fraction inside the latex particles (␾1) with the swollen particle size (D) at equilibrium swelling for polystyrene particles swollen with styrene taking into account a swelling pressure (j = ⬁). The open symbols are calculated data according to Eq. (4) with ␹ = 0.45, 25⬚C and ␥ = 3 mN m⫺1 and P = 0 for (䡩), ␥ = 7 mN m⫺1 and P = 1.5 ⫻ 106 N m⫺2 for (▫), ␥ = 14 mN m⫺1 and P = 2.5 ⫻ 106 N m⫺2 for (䉭). The experimental data are from Ref. 107 for (●) and from Ref. 142 for (䡲) and (䊱). (●) Polystyrene latex in the presence of free potassium laurate; (䡲) cleansed polystyrene latex with covalently bound sulfonate groups; (䊱) cleansed polystyrene latex with covalently bound gluconosiloxane groups.

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the absence of free or adsorbed surfactants have been investigated. If surfactants are present, their specific contribution to swelling has to be taken into account. Besides the particle size, the interfacial tension, and surfactants, the Flory-Huggins interaction parameter, the cross-linking of the core, and the degree of polymerization also influence the swelling of latex particles. The influence of both cross-linking and ␹ is straightforward as the better the solubility of the polymer, the better the swelling. Hence, cross-linked particles swell less than un-cross-linked particles and monomer-polymer combinations with high ␹ values swell less [vinyl chloride and poly(vinyl chloride) with ␹ ⬇ 0.9, for example] than systems with ␹ values ⱕ 0.5, which is the case for many monomer-polymer combinations. The Flory-Huggins theory predicts that the solubility of a polymer depends on its chain length. Consequently, this is also the case for the swelling of polymer latex particles as illustrated in Fig. 10. The effect that the swelling is better the shorter the chains has an important influence during emulsion polymerization as it counteracts the low swelling tendency of the small particles just after nucleation. Furthermore, the uptake of monomer leads to an increase in the mobility of the chains and hence is a prerequisite for the formation of spherical particles if the glass transition temperature of the polymer is higher than the polymerization temperature. Figure 11 shows that well-defined polystyrene oligomers prepared by anionic polymerization terminated with sulfonate groups form nonspherical particles

FIG. 10 Change of the monomer volume fraction inside the latex particles (␾1) with the swollen particle size (D) at equilibrium swelling for polystyrene particles swollen with styrene for variation in the polymer chain length j. The open symbols are calculated data according to Eq. (4) with P = 0; ␹ = 0.45; 25⬚C; ␥ = 5 mN m⫺1; and j = 2 for (䡩), j = 5 for (▫), j = 12 for (䉭), and j = 103 for (䉮).


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ing promoter is to use a monomer emulsion of a slightly water-soluble monomer with a droplet size smaller than the size of the seed particles [121]. These monomer droplets are diffusion unstable in the presence of polymer particles and dissolve by diffusion into the polymeric seed particles. This process is similar to Ostwald ripening, where smaller particles dissolve due to the higher Laplace pressure (2␥/r) and the larger particles grow. A very interesting modification that avoids the emulsification process is the dynamic swelling method developed by Okubo and coworkers [123]. The principle of this method is that a monomer solution is treated in the presence of polymer particles in such a way that the conditions for the monomer to stay in solution become worse and tiny droplets are formed that are diffusion unstable according the principles mentioned earlier. Swelling of colloid polymer particles is a fascinating field of colloid chemistry. Although many achievements have been made, a general description of latex particle swelling during emulsion polymerization is lacking. For instance, problems with the application of Eqs. (3) and (4) to model the swelling behavior may arise because of the assumption that ␥ remains unchanged upon swelling and the limitations for most of the polymer solvent systems regarding the validity of the Flory-Huggins theory. Furthermore, the quantification of the emulsifier influence that is present during the polymerization is still an open question. FIG. 11 Transmission electron microscopy (TEM) pictures of aqueous dispersions of chemically well-defined polystyrene oligomers with sulfonate end groups (average degree of polymerization 12). (a) Original dispersion; (b) dispersion swollen with toluene. Bars indicate 1 ␮m.

with a crystalline-like appearance (see Fig. 11a) upon dispersion in water [81]. Upon swelling with tetrahydrofuran, the swollen particles have a spherical shape that corresponds to the minimum free interfacial energy (see Fig. 11b). Furthermore, the j dependence of particle swelling was successfully employed to develop methods for the preparation of large monodisperse particles by Ugelstad and coworkers [117–120]. They used a low-molecularweight compound inside the particles (an agent promoting swelling) that is insoluble in water so that it cannot diffuse through the aqueous phase into the monomer droplets. Another way to enhance the swelling capacity of latex particle in the absence of a swell-

D.

Particle Growth

After discussing particle formation and particle swelling, the parameter that remains for further discussion according to Eq. (1) is n¯ . There is no doubt that particle growth takes place via polymerization of the monomer inside the monomer swollen particles. Hence, besides swelling, particle growth requires the presence of growing radicals inside the particles. As mentioned earlier, the famous Smith-Ewart recursion formula describes in a generally valid way the population of radicals among the particles during an emulsion polymerization [Eq. (5)]. According to Smith and Ewart [32], the population of radicals inside the particles (n) is influenced by three reactions: entry [dn/ dt = ␳⬘/N], exit [dn/dt = ⫺k0a(n/v)], and termination inside the particles [dn/dt = ⫺2kt n((n ⫺ 1)/v)], where v and a are the volume and the surface of the particles, respectively, ␳⬘ is the overall entry rate into all particles, and k0 and kt are the exit and termination rate constants, respectively. Note that the reaction rate constants are defined per volume of the average particle.

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For these three reactions, the steady-state condition for the particle concentration containing n radicals is given by Nn⫺1 (␳⬘/N) ⫹ Nn⫹1 k0a((n ⫹ 1)/v) ⫹ Nn⫹2 kt ((n ⫹ 2)⭈(n ⫹ 1)/v) = Nn{(␳⬘/N) ⫹ k0a(n/v) ⫹ kt n((n ⫺ 1)/v)}

(5)

The left-hand side of Eq. (5) describes the formation of particles with n radicals and the right-hand side describes their disappearance. As 兺⬁n=1 nN corresponds to the total radical concentration inside particles, the average number of radicals per particle is n¯ =

1 N

冘 ⬁

nN

n=1

Besides the mathematical problems associated with finding an analytical solution to the recursion formula, the individual entry, exit, and termination reactions represent very complex problems. For an overview regarding the state of the art, the reader is referred to Refs. 56 and 57. Equation (5) contains more problems than mentioned explicitly. For instance, radical exit has to be treated self-consistently with chain transfer reactions occurring inside the particles, as the small radicals formed diffuse much faster through the particle and their exit is more probable compared with growing radicals. If these radicals react with monomer in the aqueous phase, the oligomers should have different properties than oligomers formed from primary initiator radicals. Consequently, one may speculate whether both types of oligomers enter the particles at the same rate. If a radical enters a growing particle, instantaneous termination takes place provided the particle is not too large. In larger particles more radicals can grow independently of each other. So the question arises whether the termination depends on both particle size and number of growing radicals per particle. The influence of recipe components and latex properties on the average number of radicals per particle can be summarized as n¯ ⬀ N ⫺x1, CTA⫺x2, Dx3, I x4 where CTA means chain transfer agent and I is the initiator concentration. The exponents x1, x2, x3, and x4 mean a certain power of the particular dependence, which is very likely not unity. The dependence of n¯ on the emulsifier concentration is not so easy to predict as it depends on whether the particle number or the particle diameter is more affected by changing the emulsifier concentration. Stabilizers may also influence n¯ by obstructing entry of radicals by forming a condensed or a hairy layer surrounding the particle core. The reaction rate profiles depicted in Fig. 12 give an impression of

FIG. 12 Heat flow–time curves (reaction rate profiles) for ab initio emulsion polymerizations of styrene at 82⬚C with different stabilizer-initiator systems leading to differently decorated particles. ⌬R indicates the thickness of the hairy layer. For the detailed polymerization procedure see Ref. 183. Calorimeter RM2-S (ChemiSens, Lund, Sweden). (a) SDS as initiator and a symmetrical poly(ethylene glycol) azo initiator with a molecular weight of the poly(ethylene glycol) of 200 g mol⫺1 (PEGA200). (b) Poly(styrene sulfonate)-b-poly(ethylethylene) blockcopolymer with a degree of sulfonation of almost 52% and 233 styrene sulfonate units, 215 styrene units, and 42 ethyl ethylene units as stabilizer (1-H52). (c) Poly(styrene sulfonate)-b-poly(ethylethylene) blockcopolymer with a degree of sulfonation of almost 100% and 448 styrene sulfonate untis and 42 ethyl ethylene units as stabilizer (1-H100) and PEGA200. (d) Poly(styrene sulfonate)-bpoly(ethylethylene) blockcopolymer with a degree of sulfonation of almost 100% and 448 styrene sulfonate units and 42 ethyl ethylene units as stabilizer and KPS as initiator.

the influence of the hydrodynamic layer thickness formed by different stabilizers on the kinetics of an emulsion polymerization. Although there is a distinct difference between curves c and d, the general kinetics seem to be almost independent of whether the primary radicals have the same charge sign as the stabilizer layer or are uncharged. The thickness of the stabilizer layer has a dominating influence on the entry and exit processes and thus on the reaction rate profile. Monomer consumption inside the particles leads to volume growth of the individual latex particles. However, with beginning of the monomer starvation— when the continuous flow of monomer into the particles decreases—the swollen particles in the reactor


start to shrink. The shrinkage is stronger the larger the density difference between monomer and polymer. Growth by monomer consumption is in most cases the desired growth mechanism as the aim of emulsion polymerization is the conversion of monomer into polymer. But note that a particle can also grow in volume by coagulation or coalescence processes with other particles. This may happen during the polymerization as the system tries to reduce its free interfacial energy or may be done intentionally to achieve some special application properties [157]. In both cases it is important to control stability and to avoid a catastrophic coagulation. The former case frequently occurs during emulsifier-free polymerizations after nucleation as mentioned before but was also observed in apparently well-stabilized systems with emulsifier concentrations well above the cmc. For instance, a continuous decrease in the particle concentration was observed during the whole course of an ab initio vinyl chloride emulsion polymerization [158,159]. Figure 13 illustrates particle coalescence by means of an N-time curve and by a plot of the particle size versus the cubic root of the conversion (X). The decrease in N is almost over one order of magnitude, and the D-X 1/3 plot deviates from the straight line that it should follow if N is constant during the particle growth. This deviation occurs in a direction indicating stronger particle growth than by monomer consumption

FIG. 13 Plots of the particle number (N) versus time (t) and the particle diameter (D) versus the cubic root of the conversion (X 1/3) for an ab initio emulsion polymerization of vinyl chloride at 50⬚C. For a description of the polymerization procedure see Ref. 156. Recipe: 4 g SDS and 1.6 g KPS per liter of water, 500 g of monomer, 690 g of water.

445

alone. The decrease in N occurred only in the polymerizing system. As soon as the polymerization was stopped either by the addition of radical scavengers or by turning off the monomer feed, the decrease in N stopped, too [158]. After restarting the polymerization, the particle concentration continued to decrease. This effect was called reaction-induced particle coalescence and could be modeled with the assumption that the exit of a radical is the coalescence rate-determining step [160]. It turned out that the reaction-induced particle coalescence is a special feature of vinyl chloride emulsion polymerization. A vinyl chloride polymerization is characterized by a high chain transfer constant to the monomer, and hence radical exit frequently occurs leading to local destruction of the stabilizer layer, thus lightening particle coalescence. Well-balanced stabilization is also required during the particle growth period, just as in the case of particle swelling, as the total interfacial area increases. An increasing particle surface results in a decreasing degree of coverage of the particle interface with emulsifier (ES). Figure 14 shows such a development in the case of an ab initio vinyl chloride polymerization in which ES decreases to less than 10%. This result proves the schematic drawing in Fig. 1 regarding the change of ␥ in the course of an ab initio emulsion polymerization as a decrease in ES also means a decrease in the concentration of the free surfactant in the aqueous phase due to the adsorption equilibrium and hence an increase in ␥.

FIG. 14 Change of the total particle water interfacial area (AP) measured as cm2 of particle surface per cm3 of water and of the degree of coverage of the particle surface with emulsifier during an ab initio emulsion polymerization of vinyl chloride at 50⬚C. For a description of the polymerization procedure see Ref. 156. Recipe: 4 g SDS and 1.6 g KPS per liter of water, 500 g of monomer, 690 g of water.

446

IV.

Tauer

TECHNICAL REALIZATIONS

Compared with condensation polymerizations or bulk polymerizations, the technical realization of emulsion polymerizations on both laboratory and industrial scales is easy. The minimum equipment needed is a container that can be closed and that is resistant to water and the monomers. In the case of gaseous monomers, the container must withstand the corresponding vapor pressure. This type of reactor, for instance, beverage bottles of different styles with crown caps or caps with a septum to allow sampling, was employed for many investigations during the early days of emulsion polymerization [161]. These so-called bottle reactors were fixed to a rotating shaft and immersed in a thermostated bath. With more than 100 bottles per shaft, it was possible to investigate many recipe variations simultaneously or to acquire conversion time data with sampling volumes large enough for the necessary latex and polymer characterizations. Nowadays for laboratory investigations stirred vessels with heating and cooling jackets are widely used, although, especially if larger sampling volumes are desired, the bottle reactors still have some advantages. In industrial processes, stirred reactors with numerous technical variations are mainly used. Besides jacket cooling, the heat of polymerization can be removed by various techniques such as hot cooling or internal fittings inside the reactor. Reactors for commercial processes have a size between 10 and 200 m3 and are pressure proof up to 2000 atm if necessary [4]. The most important procedures for effecting polymer dispersions on a technical scale are semibatch or feed processes, which are very flexible regarding product properties. Depending on the required properties with respect to particle size distribution, molecular weight distribution, chemical composition in the case of copolymerization, and particle morphology, numerous feeding policies have been developed. A variety of emulsion polymerizations [for example poly(vinyl chloride) and rubber production] are carried out continuously mainly in continuous stirred tank reactors (CSTRs) or in a series consisting of up to eight CSTRs. In the latter case, intermediate feed streams are frequently applied to control copolymer composition and particle morphology. A specific and very exciting feature of continuous processes in stirred tank reactors is the occurrence of damped or sustained oscillations even at the steady state. Besides CSTRs, continuous loop reactors are used because of greater reactor productivity. For instance, a 5 m3 batch CSTR can be replaced by a 0.05 m3 continuous loop reactor [162]. For more

detailed information concerning emulsion polymerization in continuous reactors see reviews in Refs. 163– 166. Today, from a commercial point of view, pure batch processes play only a minor role. In large-scale technical reactors it is much more necessary to attach importance to the hydrodynamic conditions than in laboratory-scale reactors. If the stirring conditions are not optimized, problems can arise regarding the homogeneity of the reaction mixture as well as the heat removal in the case of insufficient mixing. In contrast, if the shear forces are too high the latex may become unstable with respect to coagulation [4]. Is there an influence of the hydrodynamic conditions or of the stirrer speed on the kinetics besides the effect that any dispersion has only a limited shear stability. It is generally assumed that agitation has no effect and this topic is ignored in almost all textbooks. However a few published results indicate an influence if the inert gas for purging contains traces of oxygen as well as if a chain transfer agent has to diffuse out of the monomer droplets into the particles [35], if the monomer diffusion to the reaction loci is influenced [167], or if the emulsifier distribution between the interfaces is changed considerably [168]. All these investigations have been carried out by increasing the stirrer speed starting from well-mixed conditions. Recently, drastic changes in both the kinetics and the polymer and particle properties have been reported when the stirrer speed is increased starting from values so low that a bulky free monomer phase still exists on top of the reactor [11,12]. Increasing the stirrer speed leads to an increase in the polymerization rate, the particle size, and the molecular weight. The particle diameters and the number average molecular weights increased from about 10 to 20 nm and from about 8 ⫻ 103 to 4 ⫻ 104 g mol⫺1, respectively, when the stirrer speed was increased by a factor of 8. Under the same conditions, the polymerization time was reduced by a factor of 6. This was observed for a styrene emulsion polymerization (recipe: 125 g of H2O, 1.5 g of styrene, 0.5 g of SDS, 0.2 g of KPS, 70⬚C) in a reaction calorimeter RM200S (ChemiSens, Lund, Sweden). In conclusion, many different technical realizations exist to prepare polymer dispersions ranging from biosynthesis in many plants over bottle reactors up to high-tech and computer-controlled production systems. For completeness, it is necessary to mention that emulsion polymerizations have also been carried out in space under conditions of zero gravity during two Columbia missions in 1982 [169] under the supervision of the Lehigh Emulsion Polymers Institute.


V.

ROLE OF SURFACTANTS DURING EMULSION POLYMERIZATION

There is a very special connection between emulsion polymerization and emulsifiers originating from the fact that emulsifiers have a direct influence on the course of the polymerization, the properties of the dispersions, and the properties during the final applications. Consequently, one of the most common problems in the industrial world of emulsion polymerizations is that of matching a polymer dispersion formulation by making a proper choice of surfactant or surfactant combination to obtain a required end effect. This has been known in industry since the 1930s [29], and dealing with surfactants plays a major role in the industrial preparation of polymer dispersions. The application of surfactants in polymer dispersions has a bivalent character as the demands upon the surfactants during the polymerization and during the application are contradictory. All advantages of the emulsion polymerization techniques are directly connected with the dispersed state and hence with the colloidal stability and the stabilizing system. Some important advantages are [170]: The existence of a thermodynamically stable large interfacial area in an aqueous environment allows easy removal of the polymerization heat. The viscosity of the dispersion medium is low and independent of the degree of polymerization of the polymer formed. The monomer consumption takes place outside the monomer phase, thus allowing feed procedures and hot cooling as result of which control of the polymerization is possible. Control of the monomer concentration at the main reaction locus is possible in such a way that the reactor can operate constantly at the maximum rate of polymerization. It is possible to carry out with comparably little technical effort batch, semibatch, and continuous polymerizations in which the feed of any additional components is possible. The particle size and the size distribution can be tailored in a desired range between 50 nm and 10 ␮m. The use of emulsifiers, water-soluble polymers, or other auxiliary materials offers further possibilities to modify the product properties. Surfactants distribute in all phases and hence they act in all phases. In the aqueous phase they form micelles and lead to increasing solubility of organic com-

447

pounds in water. As neat colloidally dispersed systems with hydrophobic interfaces attracting each other unscreened with a rate that is given by the fast coagulation kinetics first considered by von Smoluchowski [171], the most important aspect of surfactants is, however, their ability to adsorb at interfaces. Thus, they lower the interfacial tension and impart stability to particles, droplets, and bubbles. The latter may lead to foaming, which must be suppressed by the addition of defoamers. In technical polymerizations the stability is mainly endangered by electrolytes [172]. Furthermore, surfactants may interact in very specific ways with all kinds of water-soluble polymers [173]. The way stabilizers impart stability depends on the particular stabilizing system. Ionic stabilizers lead to an electrostatic repulsion between the particles, nonionic emulsifiers stabilize via a steric mechanism, and polyelectrolyte block copolymers act, for instance, as electrosteric stabilizers. Naturally occurring polymers were the first substances used to impart stability in emulsion polymerization. Subsequently, a variety of synthetic polymers were developed for applications in emulsion polymerization [174,175]. Stabilizers based on poly(ethylene glycol) (PEG) as hydrophilic blocks are widely used [175–178]. In this case the distribution of the emulsifiers between all phases may considerably influence the kinetics. Poly(ethylene glycol) is soluble in water and in many organic solvents, including many monomers, and excludes other polymers from its aqueous solutions [179]. At the elevated temperatures at which the polymerizations are carried out, it is more soluble in the monomer phase than in the aqueous phase. Consequently, it redistributes with increasing conversion more and more into the aqueous phase and hence may lead to the stabilization of a second particle generation [180,181] or to a special particle morphology as shown for PEG-b-polystyrene and PEG-bpoly(methyl methacrylate) block copolymer particles [72]. Stabilization of colloids is a large area in its own right, and for detailed and comprehensive information the reader is referred to Refs. 157 and 174. As a rule, stability against electrolytes and freeze-thaw stability are increased by nonionic stabilizers and/or polymeric stabilizers. In industrial emulsion polymerizations a few percent of an ionic comonomer is frequently employed in order to form a polymeric stabilizer during the polymerization, thus imparting additional stability. As a new class of polymeric stabilizers, polyelectrolyte block copolymers are worthy of brief mention. If the polyelectrolyte block is long and stretched into the aqueous phase, as in the case of curves c and d of Fig.

448

11, where the layer thickness is about 60 nm, the particles possess extraordinary salt stability [182]. For instance, these particles are stable over months in the presence of 3 M sodium chloride. In contrast to the preparation of polymer dispersions, for most of their applications, colloidal instability is required at a certain moment during the application as in the case of film formation. In a coating the surfactants can migrate through the polymer layer and assemble in hydrophilic domains, leading to enhanced water uptake and subsequently to blooming or blushing [183,184]. For most applications it would be very useful if the stabilizers, which have to contain hydrophilic parts as long as the polymer is dispersed in the aqueous environment, would lose these parts and hence their hydrophilicity together with the evaporating water during the application. A possible way to avoid this drawback of surfactants during the application is to fix them in place. This may be done by using either reactive surfactants that are covalently bound to the polymer chains (see Chapter 28) or high-molecular-weight surfactants that are unable to migrate considerably. For instance, a polystyrene with a molecular weight of 4 ⫻ 104 g mol⫺1 and subsequently sulfonated to a degree of about 50% acts as a good stabilizer in emulsion polymerization [185]. It forms no extended hydrodynamic layer because of multiple adsorption points along the chain and results in a reaction rate profile similar to that in the case of SDS as emulsifier (see Fig. 11, curves a and b). A problem that is inherent in commercial surfactants is the extreme difficulty of preparing these surfactants in a chemically pure form. Some of the main sources of the imperfections are homologues as well as isomers of the main components, isomers with respect to the placement of the hydrophilic groups, oversubstitution of hydrophilic groups, inorganic electrolytes as impurities, and hydroperoxidation of alkyl or alkyl ether chains. Fluctuations of the composition are sometimes observed between batches made by the same producer and certainly between samples supplied by different producers. These fluctuations are a serious source of problems regarding reproducibility but also regarding the comparability of nominal identical polymerizations in different laboratories. In conclusion, any new surfactant for an emulsion polymerization is faced with the problem that it is only an auxiliary agent that has to meet strict cost requirements and has to improve existing solutions in two contradictory fields (polymerization and application), but this is also a challenge for further research.

Tauer

VI.

OPEN PROBLEMS AND FUTURE DEVELOPMENTS

Over the past 90 years, enormous knowledge has been accumulated on emulsion polymerization resulting in an extremely wide variety of products for very different applications. Sophisticated models have been developed that require knowledge of almost 50 basic kinetic and thermodynamic constants [160,186–188] because of the complex heterogeneous nature of the process, of which only a few are known precisely. Some problems in the case of modeling co- and terpolymerizations have been discussed [189]. A summary of on-line techniques suited for emulsion polymerizations can be found in Refs. 190–193. Procedures are also available for the control of copolymer composition and to avoid a composition drift [194–196]. Improvement with regard to process analysis and control can be expected with the development and application as much as possible of on-line sensors in combination with reaction calorimeters. It would be advantageous to be able to control online the level of free surfactant during an emulsion polymerization. Surface tension measurements have been carried out quasi–on line by bypassing the reaction mixture through a bubble tensiometer [197,198]. On-line measurements of surface tension directly inside stirred reactors have been reported at elevated temperatures [199]. This now allows control of the level of free surfactant as well as determination of surfactant properties directly under reaction conditions. Almost all the quantitative data characterizing surfactant properties used today for modeling have not been determined by polymerization temperatures. As the surface tension shows a distinct temperature dependence, improvements can be expected [200,201] if surfactant data obtained at the polymerization temperature become available. A great deal of work is going on regarding the adaptation of controlled radical polymerization processes to emulsion polymerization. All modes of controlled radical polymerization techniques are investigated, as it is promising to combine the advantages of emulsion polymerization with the possibilities of controlling the molecular weight and preparing well-defined block copolymers [202–213]. Besides the almost continuous development of new products and the improvement of existing products, several attempts have been made to use other polymerization mechanisms in aqueous emulsion polymerization. The goal is to develop initiator systems allowing stereospecific emulsion polymerization and hence control of the molecular structure (modes of addition


of the monomer molecules, branching, and isomerism). This has been an ongoing research topic since the 1960s, when dienes were polymerized with rhodium and palladium salts [214–216]. Recently, the emulsion polymerization of ethylene with organonickel metal complexes was reported for the first time [217]. Even more exciting is the cationic polymerization of 1,3,5,7tetramethylcyclotetrasiloxane [218] and p-methoxystyrene (controlled cationic polymerization) in aqueous emulsion [219]. Without any doubt, the meaning of emulsion polymerization as an environmentally friendly aqueous reaction system will continue to increase in the future. It is a field with growing attraction for scientists from different disciplines, reflecting its enormous potential as well as its multidisciplinary character.

449 15. 16. 17. 18. 19. 20. 21. 22.

23. 24.

REFERENCES 1.

2.

3.

4.

5. 6. 7. 8. 9. 10. 11.

12. 13. 14.

D. Distler, in Wa¨ßrige Polymerdispersionen: Synthese, Eigenschaften, Anwendungen (D. Distler, ed.), WileyVCH, Weinheim, 1999, pp. 1–12. D. Distler, Wa¨ßrige Polymerdispersionen: Synthese, Eigenschaften, Anwendungen, Wiley-VCH, Weinheim, 1999. A. J. DeFusco, K. C. Sehgal, and D. R. Bassett, in Polymeric Dispersions: Principles and Applications (J. M. Asua, ed.), Kluwer Academic Publishers, Dordrecht, 1997, pp. 379–396. D. Distler, in Wa¨ßrige Polymerdispersionen: Synthese, Eigenschaften, Anwendungen (D. Distler, ed.), WileyVCH, Weinheim, 1999, pp. 13–21. J. H. Baxendale, M. G. Evams, and G. S. Park, Trans. Faraday Soc. 42:155–169 (1946). J. H. Baxendale, M. G. Evams, and G. S. Park, Trans. Faraday Soc. 42:668–684 (1946). V. J. Frilette and W. P. Hohenstein, J. Polym. Sci. III: 22–31 (1948). F. A. Bovey and I. M. Kolthoff, J. Polym. Sci. V:487– 504 (1950). R. M. Fitch, M. B. Prenosil, and K. J. Sprick, J. Polym. Sci. Part C 27:95–118 (1969). R. M. Fitch and C. Tsai, Polym. Lett. 8:703–710 (1970). K. Tauer and C. Schellenberg, Nucleation in heterogeneous polymerization, Proceedings of International Symposium on Polymers in Dispersed Media, Lyon, 1999, pp. 6–10. K. Tauer, C. Schellenberg, and A. Zimmermann, Macromol. Symp. 150:1–12 (2000). G. S. Whitbey and M. Katz, Ind. Eng. Chem. 25: 1204–1211 (1933). G. S. Whitbey and M. Katz, Ind. Eng. Chem. 25: 1338–1348 (1933).

25. 26. 27. 28. 29. 30. 31. 32. 33. 34. 35. 36. 37. 38. 39. 40. 41. 42. 43. 44.

W. P. Hohenstein and H. Mark, J. Polym. Sci. 1:127– 145 (1946). W. P. Hohenstein and H. Mark, J. Polym. Sci. 1:549– 580 (1946). F. Hofmann and K. Delbru¨ck, German Patent 250.690 to Farbenfabriken Bayer (1909). H. Fikentscher, H. Gerrens, and H. Schuller, Angew Chem. 72:856–867 (1960). M. Luther and C. Heuck, German Patent 558.890 to IG Farbenindustrie (1927). R. P. Dinsmore, U.S. Patent 1.732.795 to Goodyear Company (1927). Mod. Plast. 23:153–220 (1946). F. A. Bovey, I. M. Kolthoff, A. I. Medalia, and E. J. Meehan, Emulsion Polymerization, Interscience, New York, 1955, pp. 1–25. K. Meisenburg, DRP 568.907 to IG Farbenindustrie (1930). K. Meisenburg, DRP 573.648 to IG Farbenindustrie (1930). H. Fikentscher and C. Heuk, DRP 654.989 to IG Farbenindustrie (1930). W. Starck and H. Freudenberger, DRP 727.995 to IG Farbenindustrie (1934). H. Mark, H. Fikentscher, J. Hengstenberg, and G. von Susich, U.S. Patent 2.068,424 (1932). E. Scharf and H. Fikentscher, DRP 615.219 to IG Farbenindustrie (1931). H. Fikentscher, Angew. Chem. 51:433 (1938). W. D. Harkins, J. Am. Chem. Soc. 69:1428–1444 (1947). W. D. Harkins, J. Polym. Sci. V:217–251 (1950). W. V. Smith and R. H. Ewart, J. Chem. Phys. 16:592– 599 (1948). E. Bartholome´, H. Gerrens, R. Herbeck, and H. M. Weitz, Z. Elektrochem. 60:334–348 (1956). F. K. Hansen and J. Ugelstad, J. Polym. Sci. Polym. Chem. Ed. 17:3047–3067 (1979). H. Gerrens, Fortschr. Hochpol. Forsch. 1:234–328 (1959). H. Fikentscher, H. Gerrens, and H. Schuller, Angew. Chem. 72:856–864 (1960). H. Gerrens, Dechema Monogr. 49:53–73 (1964). H. Gerrens, K. Kuchner, and G. Ley, Chem. Ing. Tech. 43:693–698 (1971). G. Ley and H. Gerrens, Makromol. Chem. 175:563– 581 (1974). R. M. Fitch and C. H. Tsai, Polym. Lett. 8:703–710 (1970). R. M. Fitch and C. H. Tsai, in Polymer Colloids (R. M. Fitch, ed.), Plenum, New York, 1971, pp. 73–102. R. M. Fitch, Br. Polym. J. 5:467–483 (1973). R. M. Fitch, Off. Dig. J. Paint Technol. Eng. 37:32– 48 (1965). F. K. Hansen and J. Ugelstad, J. Polym. Sci. Polym. Chem. Ed. 16:1953–1979 (1978).

450 45. 46. 47. 48.

49.

50. 51.

52.

53.

54. 55. 56. 57. 58.

59.

60.

61. 62. 63.

64. 65.

66.

Tauer F. K. Hansen and J. Ugelstad, J. Polym. Sci. Polym. Chem. Ed. 17:3033–3045 (1979). J. Ugelstad and F. K. Hansen, Rubber Chem. Technol. 49:536–556 (1976). G. Lichti, R. G. Gilbert, and D. H. Napper, J. Polym. Sci. Polym. Chem. Ed. 21:269–291 (1983). R. G. Gilbert, Emulsion Polymerization: A Mechanistic Approach, Academic Press, New York, 1995, pp. 78–140. M. S. El-Aasser and C. M. Miller, in Polymeric Dispersions: Principles and Applications (J. M. Asua, ed.), Kluwer Academic Publishers, Dordrecht, 1997, pp. 109–126. J. Ugelstad, M. S. El-Aasser, and J. W. Vanderhoff, J. Polym. Sci. Polym. Lett. Ed. 11:503–513 (1973). J. Ugelstad, P. Stenstad, L. Kilaas, W. S. Prestvik, A. Rian, K. Nustad, R. Herje, and A. Berge, Macromol. Symp. 101:491–500 (1996). V. L. Dimonie, E. S. Daniels, O. L. Shaffer, and M. S. El-Aasser, in Emulsion Polymerization and Emulsion Polymers (P. A. Lovell and M. S. El-Aasser, eds.), Wiley, New York, 1997, pp. 293–326. F. A. Bovey, I. M. Kolthoff, A. I. Medalia, and E. J. Meehan, Emulsion Polymerization, Interscience, New York, 1955. D. C. Blackley, Emulsion Polymerisation Theory and Practice, Applied Science Publishers, London, 1975. V. I. Eliseeva, Polimernije Dispersii (Russ.), Chimija, Moscow, 1980. R. G. Gilbert, Emulsion Polymerization A Mechanistic Approach, Academic Press, New York, 1995. R. M. Fitch, Polymer Colloids: A Comprehensive Introduction, Academic Press, New York, 1997. J. M. Asua, ed., Polymeric Dispersions: Principles and Applications, Kluwer Academic Publishers, Dordrecht, 1997. A. M. van Herk, in Polymeric Dispersions: Principles and Applications (J. M. Asua, ed.), Kluwer Academic Publishers, Dordrecht, 1997, pp. 17–30. P. A. Lovell and M. S. El-Aasser, eds., Emulsion Polymerization and Emulsion Polymers, John Wiley, New York, 1997. R. G. W. Norrish and R. R. Smith, Nature 150:336– 337 (1942). E. Trommsdorff, H. Ko¨hle, and P. Lagally, Makromol. Chem. 1:169–198 (1947). L. V. De La Rosa, E. D. Sudol, and M. S. EL-Aasser, J. Polym. Sci. Part A Polym. Chem. 34:461–473 (1996). R. S. Corley, in Monomers (E. R. Blout and H. Mark, eds.), Interscience, New York, 1951. A. L. Ward and W. J. Roberts, in Monomers (E. R. Blout and H. Mark, eds.), Interscience, New York, 1951. K. Tauer, H. Mu¨ller, C. Schellenberg, and L. Rosengarten, Colloids Surf. A Physicochem. Eng. Asp. 153: 137–142 (1999).

67.

68. 69.

70.

71.

72. 73. 74.

75. 76. 77. 78. 79. 80. 81. 82. 83. 84. 85. 86.

87. 88.

89. 90.

91.

G. Fevotte, T. F. McKenna, S. Othman, and A. M. Santos, Comput. Chem. Eng. 22(Suppl):S443–S449 (1998). L. Jansson, H. Nilsson, C. Silvergren, and B. To¨rnell, Thermochim. Acta 118:97–105 (1987). ¨ zdeger, E. D. Sudol, M. S. El-Aasser, and A. E. O Klein, J. Polym. Sci. Part A Polym. Chem. 35:3813– 3825 (1997). ¨ zdeger, E. D. Sudol, M. S. El-Aasser, and A. E. O Klein, J. Polym. Sci. Part A Polym. Chem. 35:3827– 3835 (1997). ¨ zdeger, E. D. Sudol, M. S. El-Aasser, and A. E. O Klein, J. Polym. Sci. Part A Polym. Chem. 35:3837– 3846 (1997). K. Tauer, M. Antonietti, L. Rosengarten, and H. Mu¨ller, Macromol. Chem. Phys. 199:897–908 (1998). H.-Y. Parker, D. G. Westmoreland, and H.-R. Chang, Macromolecules 29:5119–5127 (1996). K. Tauer and I. Ku¨hn, in Polymeric Dispersions: Principles and Applications (J. M. Asua, ed.), Kluwer Academic Publishers, Dordrecht, 1997, pp. 49–65. M. Vollmer and A. Weber, Z. Phys. Chem. 119:277– 301 (1925). R. Becker and W. Do¨ring, Ann. Phys. 24:719–752 (1935). J. Frenkel, J. Chem. Phys. 7:538–547 (1939). K. E. J. Barrett, Dispersion Polymerization in Organic Media, John Wiley & Sons, New York, 1975. V. K. LaMer and R. H. Dinegar, J. Am. Chem. Soc. 72:4847–4854 (1950). I. Ku¨hn and K. Tauer, Macromolecules 28:8122–8128 (1995). K. Tauer, R. Deckwer, I. Ku¨hn, and C. Schellenberg, Colloid Polym. Sci. 277:607–626 (1999). C. P. Roe, Ind. Eng. Chem. 60:20–33 (1968). J. J. P. Staudinger, Chem. Ind. (Lond.) 67:563–568 (1948). I. D. Robb, J. Polym. Sci. Part A-1 7:417–427 (1969). W. J. Priest, J. Phys. Chem. 26:1077–1082 (1952). N. M. van Os, J. R. Haak, and L. A. M. Rupert, Physico-chemical Properties of Selected Anionic, Cationic and Nonionic Surfactants, Elsevier, Amsterdam, 1983, pp. 1–107. W.-A. G. R. Al-Shahib and A. S. Dunn, J. Polym. Sci. Polym. Chem. Ed. 16:677–684 (1978). A. S. Dunn and W. A. Al-Shahib, in Polymer Colloids II (R. M. Fitch, ed.), Plenum, New York, 1980, pp. 619–628. A. S. Dunn, in Emulsion Polymerization (I. Piirma, ed.), Academic Press, New York, 1982, pp. 221–245. E. A. G. Amiansson, S. N. Wall, M. Almgren, H. Hoffmann, I. Kielmann, W. Ulbricht, R. Zana, J. Lang, and C. Tonore, J. Phys. Chem. 80:905–922 (1976). K. Lunkenheimer, G. Czichocki, R. Hirte, and W. Barzyk, Colloids Surf. A Physicochem. Eng. Asp. 101: 187–197 (1995).

Emulsion Polymerization 92. 93. 94. 95.

96. 97. 98. 99. 100.

101. 102. 103.

104.

105. 106. 107. 108. 109. 110. 111. 112.

113. 114.

115. 116. 117.

K. Tauer and I. Ku¨hn, Macromolecules 28:2236–2239 (1995). W. Wu and G. H. Nancollas, J. Colloid Interface Sci. 182:365–373 (1996). A. Laaksonen, V. Talanquer, and D. W. Oxtoby, Annu. Rev. Phys. Chem. 46:489–524 (1995). I. Ku¨hn, Untersuchungen zum Mechanismus der Teilchenbildung wa¨hrend der Emulsionspolymerisation, University Potsdam, Potsdam, Germany, 1996. K. Tauer, I. Ku¨hn, and H. Kaspar, Prog. Colloid Polym. Sci. 101:30–37 (1996). I. M. Kolthoff and I. K. Miller, J. Am. Chem. Soc. 73: 3055–3059 (1951). D. A. House, Chem. Rev. 62:185–203 (1962). E. J. Behrman and J. O. Edwards, Rev. Inorg. Chem. 2:179–206 (1980). G. V. Buxton, C. L. Greenstock, W. P. Helman, and A. B. Ross, J. Phys. Chem. Ref. Data 17:513–886 (1988). K. Tauer, Polym. Adv. Technol. 6:435–440 (1995). K. Tauer and R. Deckwer, Acta Polym. 49:411–416 (1998). R. Deckwer, Oligomere in der Emulsionspolymerisation von Styrol—Eigenschaften und Charakterisierung, Ph.D. dissertation, University Potsdam, Potsdam, Germany, 1999. W. J. Lyman, in Handbook of Chemical Property Estimation Methods—Environmental Behavior of Organic Compounds (W. J. Lyman, W. F. Reehl, and D. H. Rosenblatt, eds.), American Chemical Society, Washington, DC, 1996, pp. 2-1–2-52. A. Kuhn, Wo¨rterbuch der Kolloidchemie, Theodor Steinkopff, Dresden, 1932, pp. 124–128. J. Stauff, Kolloidchemie, Springer Verlag, Berlin, 1960, pp. 682–690. W. Smith, J. Am. Chem. Soc. 70:3695–3702 (1948). S. H. Herzfeld, A. Roginsky, and M. L. Corrin, J. Polym. Sci. V:207–215 (1950). M. Morton, S. Kaizerman, and M. W. Altier, J. Colloid Sci. 9:300–312 (1954). J. L. Gardon, J. Polym. Sci. Part A-1 6:2859–2879 (1968). B. W. Brooks, Br. Polym. J. 3:269–373 (1971). I. A. Maxwell, J. Kurja, G. H. J. Van Doremaele, A. L. German, and B. R. Morrison, Makromol. Chem. 193:2049–2063 (1992). J.-I. Kim, J. W. Vanderhoff, and A. Klein, J. Appl. Polym. Sci. 58:279–290 (1995). I. A. Maxwell, J. Kurja, G. H. J. Van Doremaele, and A. L. German, Makromol. Chem. 193:2065–2080 (1992). P. D. Armitage, J. C. De La Cal, and J. M. Asua, J. Appl. Polym. Sci. 51:1985–1990 (1994). Y. G. Duront and D. C. Sundberg, J. Appl. Polym. Sci. 58:1607–1618 (1995). J. Ugelstad, Makromol. Chem. 179:815–817 (1978).

451 118. 119.

120.

121. 122.

123. 124. 125.

126. 127. 128. 129. 130. 131. 132. 133. 134. 135. 136. 137. 138. 139. 140. 141. 142.

143. 144.

J. Ugelstad, K. H. Kaggerud, F. K. Hansen, and A. Berge, Makromol. Chem. 180:737–744 (1979). J. Ugelstad, K. H. Kaggerud, and R. M. Fitch, in Polymer Colloids II (R. M. Fitch, ed.), Plenum, New York, 1980, pp. 83–93. J. Ugelstad, P. C. Mork, A. Berge, T. Ellingsen, and A. A. Khan, in Emulsion Polymerization (I. Piirma, ed.), Academic Press, New York, 1982, pp. 383–413. L. H. Jansson, M. C. Wellons, and G. W. Poehlein, J. Polym. Sci. Polym. Lett. Ed. 21:937–943 (1983). J. Ugelstad, H. R. Mftuakamba, P. C. Mork, T. Ellingsen, A. Berge, R. Schmid, L. Holm, A. Jorgendal, F. K. Hansen, and K. Nustad, J. Polym. Sci. Polym. Symp. 72:225–240 (1985). M. Okubo, T. Yamashita, and M. Shiozaki, J. Appl. Polym. Sci. 60:1025–1031 (1996). D. I. Lee, Makromol. Chem. Macromol. Symp. 33: 117–131 (1990). D. C. Sundberg, A. P. Casassa, J. Pantazopoulos, M. R. Muscato, B. Kronberg, and J. Berg, J. Appl. Polym. Sci. 41:1425–1442 (1990). M. Okubo, Makromol. Chem. Macromol. Symp. 35/ 36:307–325 (1990). C. L. Winzor and D. C. Sundberg, Polymer 33:4269– 4279 (1992). Y. C. Chen, V. L. Dimonie, O. L. Shaffer, and M. S. El-Aasser, Polym. Int. 30:185–194 (1993). E. J. Sundberg and D. C. Sundberg, J. Appl. Polym. Sci. 47:1277–1294 (1993). S. Omi, T. Kohmoto, and M. Iso, Polym. Int. 30:499– 504 (1993). Y. C. Chen, V. L. Dimonie, and M. S. El-Aasser, J. Appl. Polym. Sci. 45:487–499 (1992). L. J. Gonzales-Ortiz and J. M. Asua, Macromolecules 28:3135–3145 (1995). L. J. Gonzales-Ortiz and J. M. Asua, Macromolecules 29:383–389 (1996). L. J. Gonzales-Ortiz and J. M. Asua, Macromolecules 29:4520–4527 (1996). M. Okaniwa, J. Appl. Polym. Sci. 68:185–190 (1998). X. Z. Kong and E. Ruckenstein, J. Appl. Polym. Sci. 71:1455–1460 (1999). A. R. Berens, Pure Appl. Chem. 53:365–375 (1981). E. J. Meehan, J. Am. Chem. Soc. 71:628–633 (1949). E. Vanzo, R. H. Marchessault, and V. Stannett, J. Colloid Sci. 20:62–71 (1965). H. Nilsson, C. Silvergren, and B. To¨rnell, Eur. Polym. J. 14:737–741 (1978). G. Lo¨hr, in Polymer Colloids II (R. M. Fitch, ed.), Plenum, New York, 1980, pp. 71–81. L. F. J. Noel, R. Q. F. Janssen, W. J. M. van Well, A. M. van Herk, and A. L. German, J. Colloid Interface Sci. 175:461–469 (1995). E. A. van der Zeeuw, L. M. C. Sagis, and G. J. M. Koper, Macromolecules 29:801–803 (1996). M. Antonietti, H. Kaspar, and K. Tauer, Langmuir 12: 6211–6217 (1996).

452 145. 146. 147. 148. 149. 150. 151. 152. 153. 154. 155. 156.

157.

158. 159. 160. 161.

162.

163. 164. 165. 166.

167. 168. 169.

170.

Tauer V. K. LaMer and R. Gruen, Trans. Faraday Soc. 48: 410–415 (1952). M. R. Grancio and D. J. Williams, J. Polym. Sci. Part A-1 8:2617–2629 (1970). P. Keusch and D. J. Williams, J. Polym. Sci. Polym. Chem. Ed. 11:143–162 (1973). D. H. Napper, J. Polym. Sci. A-1 9:2089–2091 (1971). J. L. Gardon, J. Polym. Sci. Polym. Chem. Ed. 11: 241–251 (1973). J. Bolze and M. Ballauff, Macromolecules 28:7429– 7433 (1995). P. J. Flory and J. Rehner, J. Chem. Phys. 11:521 (1943). B. Kitiyanan, J. H. Ohaver, J. H. Harwell, and S. Osuwan, Langmuir 12:2162–2168 (1996). K.-L. Gosa, J. Dispersion Sci. Technol. 17:577–589 (1996). B. R. Vijayendran, J. Appl. Polym. Sci. 23:733–742 (1979). W. Burchard, Prog. Colloid Polym. Sci. 78:63–67 (1988). H. Kaspar, Untersuchungen zur Gleichgewichtsquellung polymer Nanopartikel, Ph.D. dissertation, University Potsdam, Potsdam, Germany, 1996. R. H. Ottewill, in Polymeric Dispersions: Principles and Applications (J. M. Asua, ed.), Kluwer Academic Publishers, Dordrecht, 1997, pp. 31–48. K.-H. Goebel, H.-J. Schneider, W. Jaeger, G. Reinisch, Acta Polymerica 33:49–62, (1982). K. Tauer, B. R. Paulke, I. Mu¨ller, W. Jaeger, and G. Reinisch, Acta Polym. 33:287–298 (1982). K. Tauer, G. Reinisch, H. Gajewski, and I. Mu¨ller, J. Macromol. Chem. A28:431–460 (1991). F. A. Bovey, I. M. Kolthoff, A. I. Medalia, and E. J. Meehan, Emulsion Polymerization, Interscience, New York, 1955, pp. 271–324. C. Abad, J. C. de la Cal, and J. M. Asua, in Polymeric Dispersions: Principles and Applications (J. M. Asua, ed.), Kluwer Academic Publishers, Dordrecht, 1997, pp. 333–347. B. Jacobi, Angew. Chem. 64:539–543 (1952). G. W. Poehlein and D. J. Dougherty, Rubber Chem. Technol. 50:601–638 (1977). G. W. Poehlein, Polym. Int. 30:243–251 (1993). F. J. Schork, in Polymer Reactor Engineering (C. McGreavy, ed.), Chapman & Hall, London, 1994, pp. 148–202. K. Arai, M. Arai, S. Iwasaki, and S. Saito, J. Polym. Sci. Polym. Chem. Ed. 19:1203–1215 (1981). M. Nomura, M. Harada, W. Eguchi, and S. Nagata, J. Appl. Polym. Sci. 16:835–847 (1972). J. W. Vanderhoff, M. S. El-Aasser, F. J. Micale, E. D. Sudol, C. M. Tseng, A. Silwanowizc, D. M. Kornfeld, and F. A. Vicente, J. Dispersion Sci. Technol. 5:231– 246 (1984). G. Markert, Angew. Makromol. Chem. 123/124:285– 306 (1984).

171. 172.

173.

174. 175. 176. 177. 178. 179.

180. 181. 182.

183. 184.

185. 186. 187. 188. 189. 190.

191.

192.

193. 194.

M. von Smoluchowski, Z. Phys. Chem. 92:129 (1917). M. F. Kemmere, J. Meuldijk, A. A. H. Drinkenburg, and A. L. German, J. Appl. Polym. Sci. 69:2409–2421 (1998). B. Lindman and K. Thalberg, in Interaction of Surfactants with Polymers and Proteins (E. D. Goddard and K. P. Ananthapadmanabhan, eds.), CRC Press, Boca Raton, FL, 1993, pp. 203–276. D. H. Napper, Polymeric Stabilization of Colloidal Dispersions, Academic Press, New York, 1983. I. Piirma, Polymeric Surfactants, Marcel Dekker, New York, 1992. R. Brown, B. Stu¨tzel, and T. Sauer, Macromol. Chem. Phys. 196:2047–2064 (1995). J.-L. Mura and G. Riess, Polym. Adv. Technol. 6:497– 508 (1995). C.-S. Chern, Y.-C. Liou, and W.-Y. Tsai, J. Macromol. Sci. A33:1063–1075 (1996). J. M. Harris, in Poly(ethylene glycol) Chemistry Biotechnical and Biomedical Applications (J. M. Harris, ed.), Plenum, New York, 1992, pp. 1–14. I. Piirma and M. Chang, J. Polym. Sci. Polym. Chem. Ed. 20:489–498 (1982). I. Piirma and T. S. Maw, Polym. Bull. 11:497–504 (1984). K. Tauer, H. Mu¨ller, L. Rosengarten, and K. Riedelsberger, Colloids Surf. A Physicochem. Eng. Asp. 153: 61–74 (1999). J. Dickstein, Polym. Prepr. 27:427–428 (1986). S. Lam, A. C. Hellgren, M. Sjo¨berg, K. Holmberg, H. A. S. Schoonbrood, J. M. Asua, K. Tauer, D. C. Sherrington, and A. Montoya Goni, J. Appl. Polym. Sci. 66:187–198 (1997). H. Mu¨ller, W. Leube, K. Tauer, S. Fo¨rster, and M. Antonietti, Macromolecules 30:2288–2293 (1997). K. W. Min and W. H. Ray, J. Macromol. Sci. Rev. Macromol. Chem. C11: 177–255 (1974). C. Kiparissides, J. F. MacGregor, and A. E. Hamielec, J. Appl. Polym. Sci. 23:401–418 (1979). E. M. Coen, R. G. Gilbert, B. R. Morrison, H. Leube, and S. Peach, Polymer 39:7099–7112 (1998). A. M. van Herk and A. L. German, Macromol. Theory Simul. 7:557–565 (1998). W.-D. Hergeth, in Polymeric Dispersions: Principles and Applications (J. M. Asua, ed.), Kluwer Academic Publishers, Dordrecht, 1997, pp. 243–256. M. Morbidelli, G. Storti, and S. Siani, in Polymeric Dispersions: Principles and Applications (J. M. Asua, ed.), Kluwer Academic Publishers, Boston, 1997, pp. 257–266. W.-D. Hergeth, in Polymeric Dispersions: Principles and Applications (J. M. Asua, ed.), Kluwer, Dordrecht, 1997, pp. 267–288. E. G. Chatzi, O. Kammona, and C. Kiparissides, J. Appl. Polym. Sci. 63:799–809 (1997). A. Urretabizkaia, E. D. Sudol, M. S. El-Aasser, and J.


195.

196.

197. 198. 199. 200. 201.

202. 203.

204. 205. 206. 207.

208.

M. Asua, J. Polym. Sci. Part A Polym. Chem. 31: 2907–2913 (1993). M. Morbidelli and G. Storti, in Polymeric Dispersions: Principles and Applications (J. M. Asua, ed.), Kluwer Academic Publishers, Dordrecht, 1997, pp. 349–361. J. R. Leiza and J. M. Asua, in Polymeric Dispersions: Principles and Applications (J. M. Asua, ed.), Kluwer Academic Publishers, Dordrecht, 1997, pp. 363–378. F. J. Schork and W. H. Ray, J. Appl. Polym. Sci. 28: 407–430 (1983). D. C. H. Chien and A. Penlidis, J. Rev. Macromol. Chem. Phys. C30:1–42 (1990). K. Tauer, C. Dessy, S. Corkery, and K.-D. Bures, Colloid Polym Sci. 277:805–811 (1999). N. B. Vargaftik, B. N. Volkov, and L. D. Voljak, J. Phys. Chem. Ref. Data 12:817–820 (1983). K. S. Birdi, in Handbook of Surface and Colloid Chemistry (K. S. Birdi, ed.), CRC Press, Boca Raton, FL, 1997, pp. 71–118. J. Krstina, C. L. Moad, G. Moad, E. Rizzardo, and C. T. Berge, Macromol. Symp. 111:13–23 (1996). M. Bouix, J. Gouzi, B. Charleux, J.-P. Vairon, and P. Guinot, Macromol. Chem. Rapid Commun. 19:209– 213 (1998). C. Marestin, C. Noel, A. Guyot, and J. Claverie, Macromolecules 31:4041–4044 (1998). T. Nishikawa, M. Kamigaito, and M. Sawamoto, Macromolecules 32:2204–2209 (1999). J. Qui, S. G. Gaynor, and K. Matyjaszewski, Macromolecules 32:2872–2875 (1999). T. Prodpran, V. L. Dimonie, E. D. Sudol, and M. S. El-Aasser, Nitroxide-mediated living free radical miniemulsion polymerization, Proceedings of the ACS PMSE (Vol. 80) Spring Meeting, Anaheim, CA, 1999, pp. 534–535. S. G. Gaynor, J. Qui, and K. Matyjaszewski, Controlled/‘‘living’’ radical polymerization applied to water-borne system, Proceedings of the ACS PMSE

453

209.

210.

211.

212.

213.

214. 215.

216. 217.

218. 219.

(Vol. 80) Spring Meeting, Anaheim, CA 1999, pp. 536–537. Y. G. Duront, Miniemulsion polymerization applications and continuous processes, Proceedings of the ACS PMSE (Vol. 80) Spring Meeting, Anaheim, CA, 1999, pp. 538–540. D. Charmot, P. Corpart, H. Adam, S. Zard, and T. Biadatti, Controlled radical polymerization in dispersed media, Proceedings of International Symposium on Polymers in Dispersed Media, Lyon, 1999, pp. 15–16. J. Claverie, S. Kanagasabapathy, and D. Christie, Living radical polymerization in emulsion, Proceedings of International Symposium on Polymers in Dispersed Media, Lyon, 1999, pp. 17–18. M. Lansalot, B. Charleux, J.-P. Vairon, R. Pirri, and P. Tordo, Nitroxide-mediated controlled radical polymerization of styrene in aqueous dispersed media, Proceedings of International Symposium on Polymers in Dispersed Media, Lyon, 1999, pp. 19–20. B. Charleux, Controlled radical polymerization in dispersed media, Proceedings of EPF Workshop on Controlled Radical Polymerization, Paris, 1999, p. L5. R. E. Rinehart, H. P. Smith, H. S. Witt, and H. Romeyn, Jr., J. Am. Chem. Soc. 83:4864–4865 (1961). R. E. Rinehart, H. P. Smith, H. S. Witt, and H. Romeyn, Jr., J. Am. Chem. Soc. 84:4145–4147 (1962). A. J. Canale and W. A. Hewett, Polym. Lett. 2:1041– 1045 (1964). A. Tomov, J. P. Broyer, and R. Spitz, Emulsion polymerization of ethylene in water medium catalyzed by organotransition metal complexes, Proceedings of International Symposium on Polymers in Dispersed Media, Lyon, 1999, p. 36. S. Maisonnier, J. C. Favier, M. Masure, and P. Hemery, Polym. Int. 48:159–164 (1999). K. Satoh, M. Kamingaito, and M. Sawamoto, Macromolecules 32:3827–3832 (1999).

22 Free Radical Polymerization in Microemulsions CARLOS C. CO, RENKO DE VRIES,* and ERIC W. KALER Newark, Delaware

I.

INTRODUCTION

University of Delaware,

usually too weak to suppress microstructural changes caused by the differences in physical properties between the monomer and polymer. Numerous review articles [1–3] (see the companion chapters in Part 3 of this volume) discussing the polymerization in self-assembled structures are available, and no attempt is made here to review comprehensively polymerizations in all types of microstructures. Instead, this chapter focuses on the latest developments in the quantitative modeling of free radical polymerizations of oil-in-water microemulsions containing droplet microstructures. A detailed understanding of polymerizations in this simpler geometry should be useful in developing quantitative models for polymerizations in bicontinuous phases, vesicles, and liquid crystalline phases.

Microemulsions are thermodynamically stable onephase solutions of immiscible substances such as water (or another polar component, e.g., formamide) and oil (hydrocarbon, fluorocarbon, or silicone) that self-assemble in the presence of one or more surfactants into a wide range of microstructures. Depending on the temperature, composition, molecular architecture, and hydrophobicity or hydrophilicity of these components, various microstructures can exist. As the oil-to-water ratio is increased, a progression of microstructures, ranging from oil-swollen micelles dispersed in water to bicontinuous structures and finally to water-swollen micelles dispersed in oil, is typically observed. Furthermore, the oil- or water-swollen micelles can adopt spherical, ellipsoidal, or rodlike geometries. With some exceptions, microemulsions are optically transparent because the length scales of the oil and water domains are usually less than 10 nm. The rich variety of microstructures possible within microemulsions have made them the subject of great scientific and practical interest. The substitution of the oil by monomers or the addition of water-soluble monomers followed by subsequent polymerization has been attempted for essentially all possible types of microstructures. However, in many cases, the original microstructure is not preserved because of the rapid diffusion of the monomer to the localized regions where polymerization is taking place. In addition, the forces that govern self-assembly are

A.

Why Study Microemulsion Polymerization?

The free radical polymerization of microemulsions containing droplet microstructures provides a route for the synthesis of latex particles as small as 5 nm in radius that are difficult to prepare via emulsion polymerization [4]. These small latex nanoparticles are useful for coating the internal surfaces of microporous materials and can also be used as seed particles for emulsion polymerizations. For larger latex particles (⬃15 nm in radius), the molecular weights of the polymers formed are extraordinarily high (>20 million daltons) because a particle typically contains only one polymer chain. The synthesis of such high-molecularweight polymers within these nanoparticles leads to polymers with increased stereoregularity [5] and, possibly, chain knotting.

*Current affiliation: Wageningen University, Wageningen, The Netherlands. 455

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Differences Between Microemulsion and Emulsion Polymerizations

The preparation of latexes via emulsion polymerization is a large-scale commercial process that is very well understood. Gilbert [6] provides a comprehensive experimental and theoretical review of emulsion polymerization. The following brief and qualitative summary of emulsion polymerization serves only to highlight the differences between microemulsion and emulsion polymerization processes. In typical nonseeded emulsion polymerizations, monomer is dispersed by surfactant stabilization and vigorous stirring to form large monomer droplets (1 to 10 ␮m) and smaller monomer-swollen micelles (⬃3 nm). During the first interval of emulsion polymerization, surface-active oligomeric free radicals, generated by the reaction between initiator-derived radicals and monomer partitioned in the aqueous phase, nucleate the swollen micelles to form polymer particles. Typically, the concentration of surfactant is such that when 0 to 10% of the monomer has been converted, all the surfactant becomes adsorbed on the polymer particles. At this point, monomer-swollen micelles disappear and particle nucleation ceases. In contrast, as monomer is added to a surfactant solution to form a microemulsion, equilibrium microstructure forms without stirring. All the monomer in a microemulsion exists within monomer-swollen micelles and no large droplets are present. Microemulsions typically have higher surfactant concentrations than used to form emulsions, so usually the amount of surfactant that adsorbs on the polymer particles is negligible. Consequently, monomer-swollen micelles are present throughout the polymerization and particle nucleation ceases only when all the monomer has been consumed. The rate at which nucleated particles grow is directly proportional to the concentration of monomer at the locus of polymerization within the polymer particles. The concentrations of monomer with the polymer particles during microemulsion and emulsion polymerizations are controlled by different mechanisms. The large monomer droplets in emulsions constitute a separate thermodynamic phase wherein the chemical potential of monomer is essentially constant. Thus, for emulsion polymerizations, the concentration of monomer within the polymer particles is set by a balance between surface and monomer-polymer interaction free energies [7,8]. Typical monomers are good solvents for their polymers. Hence, the interaction between monomer and polymer would result in polymer particles that

are highly swollen with monomer. In this case, the extent to which the polymer particles are swollen by monomer is limited only by interfacial tension and the availability of monomer. A key feature that differentiates microemulsion from emulsion polymerizations is the absence of large monomer droplets. In the absence of a separate monomer phase, the chemical potential of the monomer within the swollen micelles is set primarily by the curvature elastic properties of the surfactant monolayers and can change as the polymerization proceeds (C. C. Co et al., submitted). Thus, in contrast to emulsion polymerizations, the concentration of monomer within the polymer particles is governed by a balance between the curvature energy of the micelles and monomer-polymer interaction free energy. This theory qualitatively implies that the monomer-swollen micelles have an optimal radius of curvature that corresponds to the radius of the micelles at the solubilization limit. As the amount of monomer is progressively reduced, the micelles compete more effectively with the polymer particles for monomer. This effect underscores the essential interplay of phase behavior and microstructure in quantitatively modeling microemulsion polymerizations.

II.

POLYMERIZABLE MICROEMULSIONS

A.

Phase Behavior

The literature abounds with papers on microemulsion polymerization. However, the majority of these studies tend to focus on the polymerization aspects and the preparation of materials with unique morphologies. This approach results in rather limited phase behavior studies for a large variety of polymerizable microemulsions, so it is difficult to construct a unified view of the situation. A powerful general approach for studying the phase behavior of oil/water/surfactant systems has been presented by Kahlweit et al. [9,10]. This approach entails mapping out the phase behavior on vertical sections of the Gibbs phase prism. This systematic approach has been applied by O. Lade (submitted) in an exhaustive phase behavior study of methacrylates with nonionic ethoxylated alkyl surfactants in water. The phase behavior of ionic surfactants is usually insensitive to changes in temperature. Hence, mixtures of ionic surfactants are often used to improve their usefulness and flexibility because mixing provides additional degrees of freedom in phase space. A useful example of this approach toward using ionic surfactants

Free Radical Polymerization in Microemulsions

was described by Lusvardi et al. [11,12], who studied the phase behavior of methacrylates using a mixture of dodecyltrimethylammonium bromide (DTAB) and didodecyldimethylammonium bromide (DDAB) surfactants. The molecular architecture of DTAB favors the formation of oil-in-water (o/w) microemulsions, whereas the twin hydrocarbon tails of DDAB favor inverse w/o microemulsions. On mixing these two surfactants, a one-phase channel forms in the appropriate phase prism and it becomes possible to form microemulsions with an arbitrary water-to-oil ratio. Systematic phase behavior studies make it possible to choose the most efficient surfactants and compositions for a microemulsion polymerizing a given monomer. In addition, mapping out the phase behavior thoroughly makes it possible to choose polymerization conditions that permit a systematic study. For example, by first mapping out the phase behavior of a series of methacrylates in mixtures of DTAB, DDAB, and water, one can find a common set of conditions under which each of the methacrylates forms a one-phase microemulsion [12]. By polymerizing these methacrylate microemulsions under similar conditions, the effect of differences in monomer properties on the kinetics and polymer properties can be elucidated. The primary information from these phase behavior studies that is needed to model monomer partitioning is the location of the phase boundary, i.e., the maximum amount of monomer that can be microemulsified (␣max) under the polymerization conditions. In Section IV.D we discuss how the monomer concentration at the locus of polymerization depends on the difference between the amount of monomer in the microemulsion (␣) and ␣max. The primary experimental technique for measuring monomer partitioning is small-angle neutron scattering (SANS), which is a quantitative probe of the microstructure of these microemulsions. B.

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example, it is not possibly to establish bicontinuity using SAS; instead self-diffusion nuclear magnetic resonance (NMR) is the most reliable technique. Similarly, the GIFT method for analyzing SAS data is not applicable to all systems, such as polymerized microemulsions containing both latex particles and micelles. Consequently, analysis of SAS spectra of microemulsions containing monomer-swollen micelles and their polymerized counterparts is best done by fitting SAS spectra calculated by assuming certain geometric models for the micelles and polymer particles. Excellent reviews of these SAS analysis techniques are available [14–17]. Therefore, the following discussion presents only a brief introduction to some specific approaches used to analyze the SAS spectra to measure structure and even to record the evolution of the microstructure during microemulsion polymerization. Figure 1 shows the calculated scattering spectra for a dilute solution of monodisperse latex particles. The scattering intensity [I(q)] can be interpreted in terms of the scattering contribution from each particle [P(q)],

Microstructure and Characterization

The microstructural length scales present within microemulsions range from 1 to more than 100 nm, so small-angle x-ray scattering (SAXS) and SANS are the methods of choice for quantitative structural investigations. Analysis of small-angle scattering (SAS) spectra using Glatter’s generalized indirect Fourier transform (GIFT) technique permits almost unmistakable assignment of spherical, cylindrical, or planar geometries as well as accurate estimates of their dimensions [13]. Direct imaging using electron microscopy on vitrified samples provides further verification of these results. Nevertheless, SAS is not without limitations. For

FIG. 1 Variation of the form factor [P(q)] for monodisperse ˚ . Sharp minima in P(q) hard spheres with a radius of 150 A are smeared out by polydispersity in the particle size distribution. For a dilute solution of such particles (1 vol%), the structure factor [S(q)] is approximately unity and the smooth I(q) curve results if the latex particles have a 10% size polydispersity.

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scaled for the number density (n) of particles, and corrected for their nonrandom positioning due to interparticle interactions [S(q)]. I(q) = nP(q)S(q)

(1)

The form factor [P(q)] depends on the size, shape, and composition of the individual latex particles. In the simplest case where the particles are modeled as monodisperse spheres of radius, R, and volume, V, with a uniform scattering contrast relative to the solvent (⌬␳), P(q) =

冉

3(⌬␳)V

冊

sin(qR) ⫺ qR cos(qR) (qR)3

2

(2)

For qR < 1, P(q) varies little and is approximately equal to (V⌬␳)2. At qR = 4.5, P(q) goes through the first of an infinite number of sharp minima. However, these sharp minima are typically smeared or smoothed out by polydispersity in the particle size distribution as shown in Fig. 1. In general, form factors can be calculated for any particular structure. The structure factor [S(q)] accounts for the nonrandom positioning of the scattering centers due to interactions between the scattering objects. The arrangement of particles or micelles depends on their potential of mean force, and reliable descriptions of this potential exist for colloidal structures. The potential of mean force yields S(q) via application of one of a family of well-studied liquid-state models, and computationally convenient methods exist to aid in data fitting [18–20]. For dilute solutions of weakly interacting particles, such as a dilute solution of latex particles, the structure factor correction is approximately unity and can often be neglected. However, for microemulsions consisting of micelles made up of ionic surfactants, the structure factor contribution is a critical component of the scattering intensity. Figure 2 shows the calculated scattering spectra for a hypothetical microemulsion consisting of monodisperse micelles made up of ionic surfactants. The peak in the scattering intensity is due to the periodic variation of the structure factor, and its position is an indication of the relative distance between the micelles. The sharp minima in the form factor and scattering intensity are seldom observed because of polydispersity in the size and shape of the micelles as well as background scattering. Polydispersity in the size or shape of the micelles and polymer particles can be taken into account approximately by decoupling the correlation between position and size or orientation [21]. However, for highly polydisperse or bidisperse samples, e.g., polymerized microemulsions containing both micelles and particles,

FIG. 2 Variation of the form factor [P(q)], structure factor [S(q)], and scattering intensity [I(q)] for a hypothetical microemulsion consisting of monodisperse spherical micelles ˚ and a volume fraction of 0.15. The with a radius of 25 A structure factor is calculated using the Percus-Yevick closure [19,20] and assuming that the micelles interact via an effec˚. tive hard-sphere radius of 35 A

more rigorous approaches are necessary. In the case of hard-sphere systems, Vrij [22] has derived an analytical result for the scattering intensity that is particularly convenient for model fitting SAS spectra. For more complex pair interaction potentials, the partial structure factors between individual components of the mixture must be numerically calculated to obtain the total scattering intensity [18]. III.

EXPERIMENTAL TECHNIQUES

A.

Kinetics

For the most accurate kinetic studies, inhibitors must be completely removed from the monomer and this typically requires vacuum distillation. Oxygen must be completely removed from the water and the reactor must be kept at a positive pressure of nitrogen or argon. Higher purity grades of nitrogen or argon are recommended, especially for kinetic studies at low initiator concentrations. However, the sensitivity of these reactions to oxygen can be used advantageously as a means

Free Radical Polymerization in Microemulsions

of quenching the reaction rapidly as samples are taken from the reactor. The monomer content in polymerizable microemulsions with droplet-type microstructures is typically only a few percent and rarely exceeds 10%. Accurately measuring the polymerization kinetics in a mixture of monomer, polymer, surfactant, and water presents significant analytical challenges. The accuracy of most spectroscopic techniques is significantly reduced by the need to correct for the increasing turbidity of the samples as the concentration of latex particles increases. Chromatographic techniques are complicated by the presence of polymer, surfactant, and water. Gas chromatography may be feasible for volatile and less reactive monomers with thermally stable surfactants but is not generally applicable. Because of the low concentration of analyte, bulk techniques to reduce interferences due to either polymer, surfactant, or water often lead to large errors in conversion measurement (>5%). Titration of the monomer double bonds by bromination, hydrogenation, ozonolysis, and other rapid chemical reactions may be possible, but side reactions involving the surfactant and water are often problematic. The most reliable and general techniques for measuring the polymerization kinetics are densimetry, calorimetry, and a gravimetric technique we use in our laboratory. It is routinely possible to measure the density of liquids to five significant digits by measuring the frequency of vibration of a U-tube filled with the sample; such is the principle of operation of Anton Paar densimeters. Although the relationship between measured density and conversion is often highly linear, it is prudent to confirm this by gravimetry. The accuracy of these U-tube densimeters can be seriously compromised by gradual phase separation of the sample or changes in the viscosity of the samples. Under optimal conditions, conversion measurements with less than ⫾1% error can be achieved. Reaction calorimeters, e.g., the Mettler RC1, typically have adequate sensitivity to monitor polymerization kinetics provided that the reactor head is heated to prevent condensation. The accuracy of this technique is relatively poor (⫾5%) if it is necessary to relate conversion to the heat generated on an absolute scale. The accuracy of the technique is significantly improved if the final conversion can be determined independently using a different technique such as gravimetry. Accurate gravimetric measurement of the polymer formed is possible if the monomer is adequately volatile. This technique is typically feasible only for monomers with volatilities at least equal to that of n-hexyl

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methacrylate (boiling point 90⬚C at 14 mm Hg). Surfactants with very low but nonnegligible volatility such as ethoxylated alkyl surfactants are incompatible with this technique. In this procedure, approximately 5-mL samples are extracted from the reactor directly into preweighed 20-mL ampules, sealed with a septum, then frozen in liquid nitrogen. Condensate from the ampules is washed off with acetone, and then the amount of sample in the ampules is measured by difference. The water and monomer are then evaporated by positioning the ampules horizontally overnight under a gently blowing air stream. A volatile solvent (e.g., acetone) in which the surfactant is insoluble is used to extract residual volatiles from the cake, and the ampules are air dried again after rotating them 180⬚ in the rack. After thorough air drying, the samples are dried further in a vacuum oven initially kept at 30⬚C for 12 h and then ramped up to 60⬚C for 6 h. The samples are cooled to ambient temperature and then reweighed. The precision of the 30 to 40 conversion measurements obtained for each reaction is routinely better than ⫾0.5% provided the weighings are performed carefully on an analytical balance. Note that the buildup of static electricity on the thoroughly dried glass ampules can seriously affect the accuracy of digital balances and care should be taken to minimize frictional contact. The accuracy of these measurements is within ⫾1% and is limited by the accuracy in preparing the original microemulsion. The most reliable way to obtain rates of polymerization is by differentiating accurate conversion versus time data using the cross-validation smoothing spline algorithm developed by Craven and Wahba [23]. Statistical validity is then examined by using a bootstrapping algorithm [24] to account for errors in measuring the conversion and time. B.

Molecular Weight Distribution

Accurate measurement of the molecular weight distribution of polymers prepared by microemulsion polymerization has been hampered by their very high molecular weights. Because of the unique morphology of polymers prepared by microemulsion polymerization and the relatively low quality of high-molecular-weight commercial standards, absolute molecular weight determination using light scattering detectors is required. However, columns capable of separating high-molecular-weight polymers typically shed and interfere with light scattering detectors. Only with the advent of nonshedding columns for high-molecular-weight separations from Polymer Laboratories has it been possible to perform these measurements properly. Even then, the

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high molecular weight of these polymers frequently results in overloaded columns, and it is necessary to work at very low concentrations such that the concentration of polymer is less than 10 ppm at the peak. Careful static light scattering measurements on the original unfiltered samples give molecular weights that are consistent with those obtained chromatographically, so shear degradation during the chromatographic separation is minimal. C.

Particle Size Distribution

Numerous experimental techniques exist for measuring particle size. For polydisperse samples, fractionation techniques, e.g., field flow fractionation (FFF), capillary hydrodynamic chromatography, or centrifugation, are typically necessary for accurate estimation of the particle size distribution. However, the very small particles prepared by microemulsion polymerization may cause difficulties in applying these fractionation techniques. Direct imaging by transmission electron microscopy (TEM) gives an excellent indication of the particle size distribution, but care must be taken to avoid artifacts related to sample preparation and the sizing of only a small number of particles. Quasi-elastic light scattering (QLS) is a popular and relatively easy to use technique for estimating the particle size distribution of latexes prepared by microemulsion polymerization. However, particle size measurements obtained using QLS can be highly misleading and these results must be interpreted very carefully. Therefore, we discuss some of the caveats here in detail. QLS measurement must be performed in the absence of interactions between the particles. This can be ascertained by checking that no variation in the measured particle size occurs upon further dilution. A volume fraction of approximately 0.1% is an adequate starting point for these dilution studies. Destabilization of some latexes may occur if they become highly diluted with pure water. In these cases, a solution of the same surfactant used to prepare the microemulsion at a concentration slightly below the critical micelle concentration (cmc) should be used. For typical latexes, multiple scattering is no longer a concern at the dilute concentrations necessary to minimize the interactions. The light scattering intensity is, to a first approximation, proportional to the sixth power of the particle radius. Deconvoluting QLS data to yield an accurate size distribution in terms of normalized number density versus radius is often impossible. Experimental errors and the strong dependence of the scattering intensity

on radius typically result in numerical instabilities that preclude this type of analysis. Therefore, the particle size distribution measured using QLS is typically plotted as intensity versus radius. For polydisperse samples, this may result in a gross overestimation of the average particle size and underestimation of the polydispersity. Modern techniques that take advantage of the weaker scattering of large particles at larger scattering angles and simultaneously analyze QLS data obtained at multiple angles can provide better estimates [25]. Nevertheless, the use of complementary techniques such as SAS and electron microscopy is required to confirm QLS results. D.

Monomer Partitioning

The rate of polymerization is directly proportional to the monomer concentration at the locus of polymerization. Clearly, any progress in understanding the polymerization kinetics as well as the molecular weight and particle size distributions requires measurement of the monomer concentration. Traditional techniques for determining latex swelling by solvents are not applicable because it is impossible to separate the monomerswollen polymer particles and monomer-swollen micelles without affecting the partitioning of monomer. Until recently, the only independent measurements of the monomer concentration in polymer particles have been based on pulsed laser polymerization (PLP) of styrene microemulsion [26]. Unfortunately, the PLP technique is restricted to low conversions (106 g/mol) High rate of polymerization (complete conversion often within 5–40 min compared with several hours in emulsion polymerization) Low viscosity of microlatexes High stability against coagulation (on the time scale of months to years) Beside the many possibilities and advantages of microemulsion polymerization, some disadvantages also exist, which so far prevent the use of this technique in technical applications on a broader scale. The most challenging factor is the expensive formulation (relatively low monomer and high surfactant contents compared with conventional emulsion polymerization).

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New approaches have been developed to overcome these problems through improving our understanding of polymerization mechanisms. The current literature is providing fascinating examples of the versatility of inverse microemulsion polymerization in the synthesis of new materials, nanocomposites, and catalysts. 1.

Surfactants for Inverse Microemulsion Polymerization In contrast to normal microemulsions, which contain the monomer as dispersed oil nanodroplets in a continuous polar phase (e.g., water or formamide [80]), in inverse microemulsions nanodroplets of aqueous monomer solution are dispersed in a continuous oil phase. The function of the surfactant is the formation of the microemulsion by decreasing the interfacial tension and the solubilization of the monomer solution. Furthermore, the surfactant has to stabilize the system throughout the polymerization process to prevent phase separation, gel formation, and coagulation. Often cosurfactants are used, such as aliphatic alcohols with short hydrocarbon chains (e.g., 2-propanol or octanol), to achieve the formation of a single-phase microemulsion. The cosurfactant interacts with the surfactant at the interface, penetrates the surfactant monolayer [81], and affects the partitioning of the monomer in the continuous phase [82]. Also, the water-soluble monomers themselves usually act as cosurfactants, as they consist of a polymerizable hydrophobic vinyl group and a polar group. 1 H and 13C spectra were used to study environmental changes and surfactant transitions in acrylamide-water/ bis(2-ethylhexyl)sulfosuccinate (AOT)/toluene microemulsions [83] due to monomer addition. The monomers increase the flexibility and fluidity of the interface [83]. This leads to an extension of the single-phase microemulsion domain in the phase diagram. Carver et al. [43] hypothesized that added acrylamide facilitates attractive interactions between particles, increases the contact time of such particles during collisions, and increases interfacial flexibility with concomitant transitory pore opening. The existence of an acrylamiderich region in the shell of the water pool was documented by Candau et al. [77]. The following are general guidelines for the formulation of inverse microemulsions for free radical polymerizations: Chemical compatibility (in terms of solubility parameters and molar volume) between oils and the hydrophobic moieties of the surfactant improves microemulsion formation.

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Good solubility of the polymer and the cosurfactant leads to higher microlatex stability. Addition of cosolvent to the polymer enhances microlatex stability (water usually acts as cosolvent in inverse systems of liquid monomers, e.g., acrylic acid). In cases of thermal initiation of nonionically stabilized microemulsions, stable systems exist only well below the cloud point of the surfactant. The influence of electrolytes can play an important role in microemulsion formulation [84–86]. The phase behavior of nonionic surfactants is generally more temperature dependent and less dependent on the electrolyte concentration than that of ionic surfactants. But even for nonionically stabilized microemulsions, addition of electrolyte causes salting-in and salting-out effects, which reduce or enhance the stability of the microemulsion [39]. Addition of electrolyte also affects the structure of the water. Two types of water, namely interfacial and bulklike, were detected by Fourier transform infrared (FTIR) spectroscopy, nuclear magnetic resonance (NMR) spectroscopy, electron spin resonance (ESR), and near infrared spectroscopy [87]. The relative amounts were found to depend on the waterto-surfactant ratio and also on the nature of the organic solvent. The interactions between the water and polar groups of the surfactant (AOT) change with the addition of electrolyte [88]. Nowadays, inverse microemulsions typically contain about 10–15 wt% of their total mass as surfactant (occasionally up to 30 wt%), compared with 2–4 wt% surfactant in inverse emulsion formulations. However, one has to consider that the monomer content in inverse microemulsions is quite low, typically about 15 wt% compared with 30–60 wt% in conventional emulsions. Therefore, a systematical approach to optimization of microemulsion formulations is necessary to improve the efficiency, especially for industrial applications on a broader scale. The most systematic approach to optimize the formulation of inverse microemulsions for polymerizations was achieved by Candau, Pabon, and Antquetil [42]. By blending surfactants with different HLB values, the HLB value of the surfactant mixture can be adjusted. The modified cohesive energy ratio (CER) model was used for the calculation of the required HLB value of the surfactant mixture for a given continuous oil phase to find the optimal surfactant mixture. The calculation of the HLB value neglected the effect of monomer on the HLB and the interfacial properties, which was thoroughly investigated for acrylamide [16,89] and MADQUAT [35,90]. Nevertheless,

Landfester and Hentze

the surfactant content could be drastically reduced from about 10 to 5.5 wt%. Increasing the monomer content to 22 wt% leads automatically to a transition to a bicontinuous microemulsion, as the monomer amount increases the flexibility and decreases the curvature of the interface. It can be anticipated that future studies will also improve the efficiency of globular microemulsion polymerization formulations by using this concept. The first inverse microemulsion systems for polymerizations contained up to 10 times more surfactant and cosurfactant than monomer [52]. The cosurfactants were alcohols (2-propanol, cyclohexanol, and octanol) [48], which are also radical transfer agents. They decrease the molecular weight and thereby often decrease the end-use efficiency of the resulting polymer. These first formulations were improved by the use of mixtures of AOT and nonionic surfactants or nonionic surfactant blends (e.g., of sorbitan ester). The efficiency increased, less surfactant was necessary for stabilization, and radical transfer by the cosurfactant was avoided by banishing alcohols as cosurfactants. In the following, a variety of examples of formulations for inverse microemulsion polymerization are given. The first polymeric stabilizer used for inverse microemulsion polymerization was a polystyrene-copoly(ethylene oxide) copolymer [63]. The steric stabilization by polymeric surfactants was investigated by Hernandez-Barajaz and Hunkeler [91]. Cationic surfactants have also been used for inverse microemulsion polymerization: Yan et al. [92] reported the polymerization of acrylamide in hexadecyltrimethylammonium bromide (CTAB)/hexanol-stabilized inverse microemulsions. Barton and Stillhammerova [51] reported the use of a mixture of two anionic surfactants. The more hydrophilic sodium dodecyl sulfate (SDS) and the more hydrophobic AOT were utilized as surfactants for the polymerization of acrylamide initiated by dibenzoyl peroxide. The presence of SDS increases the one-phase microemulsion phase region and decreases the acrylamide polymerization rate and the resulting particle size. In the case of the polymerization of the cationic monomer MADQUAT, it was shown [35,90] that the application of a blend of sorbitan sesquiolate (Arlacel 83, HLB = 3.7) and a sorbitan monooleate with 20 ethylene oxide units (Tween 80, HLB = 15) was well adapted to the microemulsification of the aqueous monomer solution in cyclohexane. For the copolymerization of particles of acrylamide with acrylates in microemulsions, an emulsifier blend (HLB = 9.30) of sesquiolate sorbitan (Arlacel 83, HLB = 3.7) and a polyoxyethylene sorbitol hexaoleate with 40 ethylene

Heterophase Polymerization in Inverse Systems

oxide residues (GG 1086, HLB = 10.2) was successfully employed [34]. For the use of microlatexes in biomedical applications, lecithin-stabilized biocompatible, nontoxic microlatexes were prepared in normal microemulsions [93]. Inverse microemulsions can also be formed with lecithin [94–96]. However, to our knowledge these systems have so far not been applied to inverse microemulsion polymerization. The use of polymerizable surfactants is a special case of polymerizations in inverse systems. Using surfactants that form inverse micelles and that have a polymerizable double bond in the polar headgroup [97–99] results in particles about 60 nm in diameter. Nagai et al. [100] reported the polymerization of sodium(10-undecenyl)sulfosuccinate (DUSS) with the electron-accepting monomer diethyl fumarate (EF). The copolymerization in the reverse micellar system was greatly accelerated by solubilization of water. The use of a surfactant with a polymerizable counterion (didecyldimethylammonium methacrylate, DMAMA) resulted in extremely small 2- to 5-nm particles consisting of polyelectrolyte-surfactant complexes [68]. By using this surfactant for copolymerization with sodium methacrylate (NaMA), latex particles 12 nm in size were obtained [69]. 2.

Thermodynamics, Kinetics, and Mechanism Because of their thermodynamic stability, microemulsions form spontaneously. Before polymerization the systems are clear and transparent. During the course of reaction they usually turn into translucent to opaque dispersions. The observed polymer particle size is typically bigger (20–120 nm) than the primary microdroplet size (90%) are reached in a short period of time, often within 5–40 min. The number of particles and the particle size increase during the polymerization process. A qualitative model that describes the scenario of inverse microemulsion polymerization schematically is the CLF model (Fig. 1), established by Candau, Leong, and Fitch [44]. At the beginning of the polymerization the aqueous monomer solution is homogeneously dispersed within the nonpolar continuous phase (Fig. 1a). The kinetics of the microemulsion formation cause fluctuations of the nanodroplets around their equilibrium size. The initiation occurs by entry of radicals inside the primary microemulsion droplets or by homonucleation. In a second step, particle growth takes place by diffusion of monomer through the continuous phase (primary growth) and by particle collision (secondary growth) during the polymerization process (Fig. 1b). Besides polymer particles, empty micelles are formed that can serve as reservoirs for the continuous nucleation of new latex particles. At the end of the polymerization, micelles and latex particles coexist (Fig. 1c). The size of the particles is typically much larger and their number much lower than those of the primary microdroplets.

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FIG. 1 Schematic representation of inverse microemulsion polymerizaion. (a) At the beginning of the polymerization, the aqueous monomer solution is homogeneously dispersed within the unpolar continuous phase. (b) In a second step, particle growth takes place by diffusion of monomer through the continuous phase and by particle collision during the polymerization process. (c) At the end of the polymerization, micelles and latex particles coexist. The size of the particles is typically much larger and their number much lower than those of the primary microdroplets.

Most quantitative models for microemulsion polymerization were developed for normal o/w microemulsions (see Chapter 22) [103–106]. A mathematical model for inverse microemulsion polymerization was presented [107]. Assuming pseudo-steady-state conditions, the parameters taken into account were the balance of monomer concentration and initiator concentration; the balance of the particle population and the radicals; the partitioning of monomer, oil, and surfactant; the number of micelles; and the balance of the growing polymer chains’ molecular weight. The predictions of the resulting particle size and the time dependence of the conversion were compared with experimental data for the photoinitiated polymerization of 2-methacryloyl oxyethyl trimethylammonium chloride (MADQUAT) stabilized by a blend of nonionic emulsifiers [108]. On the whole, a good fit of predicted and experimental data was achieved. Applying this model to other systems will broaden the data basis and provide deeper insights. The use of fluorescence spectroscopy facilitates the investigation of molecular changes in the interior of particles during polymerization [109,110]. It was shown that the decrease of acrylamide during polymerization is monotonic regardless of the fluorescent probe localization. Future studies will give a better understanding of the data and allow further interpretations. Other important parameters that determine mechanism and kinetics are the locus of initiation and the dynamics of the microemulsion, e.g., in terms of monomer exchange between microdroplets by percolation. (a) Locus of Initiation. The nature of the initiator determines the locus of initiation. The locus is the wa-

ter pool of inverse micelles, e.g., in the case of ammonium peroxodisulfate (APS), or the continuous oil phase, e.g., in the case of dibenzoyl peroxide (BPO). The partitioning of the monomer and/or free radical initiator between water and oil phases of an inverse microemulsion is very important for determining the formation and growth mechanism of polymer particles. If radical reactions are limited to only one phase in the inverse system, e.g., to the water phase, the formulation of a mechanism for the polymer particle formation is straightforward [44]. In the case of partitioning the (co)monomer and the initiator in both phases of the dispersion system, polymerization of the monomer in the oil phase contributes to the overall polymer particle formation. The decrease of the acrylamide polymerization rate observed for the APS initiator in percolating inverse microemulsion reflects the lowering of the acrylamide concentration in the main locus of propagation (alteration of the acrylamide-rich regions by the formation of water channels in percolating inverse microemulsions) [111]. On the other hand, the increased concentration of acrylamide in the water channels augments the probability of successful competition of acrylamide in the reaction with free radicals. Thus the retardation of acrylamide polymerization in the presence of Fremy’s salt is lower in percolating systems than in nonpercolating systems [112]. In the case of a continuous inverse microemulsion polymerization, it is important to work at low temperatures. Therefore, the redox system sodium metabisulfite/ammonium persulfate in a 1:1 mole ratio was used for initiation [113]. It was shown that the particle size


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is not affected by the amount of initiator. Removal of the oxygen allowed high conversion, and the molecular weight decreased with increasing amount of initiator. Another study showed that the polymerization rate of acrylamide was independent of the type of initiator [azobisisobutyronitrile (AIBN) or APS], but the initiation by an oil-soluble initiator led to a more complex mechanism [45]. The oligoacrylamide radicals and acrylamide oligomers, after reaching their limit of solubility in toluene, precipitate and are captured by AOT micelles or form aggregates that are finally also captured by inverse AOT micelles. Oligoacrylamide radicals penetrate through the interphase of the inverse micelle into the acrylamide-rich region in the surface layer of the water pool of the inverse micelle [77]. In the acrylamide-rich region, the growth of oligoacrylamide radicals continues. The locus of propagation for the polymerization of acrylamide in inverse microemulsions is thus initially the oil phase but later mainly the acrylamide-rich phase in the surface layer of the water pools. The acrylamide-rich phase as a locus of propagation is responsible for the high polymerization rates of acrylamide beyond a conversion of 10%. Fouassier et al. [52] studied the photopolymerization of acrylamide as an alternative means of initiation in inverse microemulsions. (b) Kinetics in Nonpercolating Systems. In the case of the acrylamide (AM) polymerization within an inverse microemulsion, it has been shown that the polymerization rate Rp and the number-average molecular mass Mn depend on the acrylamide concentration in the dispersed phase. For a nonpercolating inverse microemulsion the dependences are described by the equation ¯ n) ⬀ [AM]x Rp (or M

(1)

where x has a value of 1.8 for Rp and 1.4 for Mn [112]. It was found that at low emulsifier concentrations the polymerization rate depends strongly on the concentration of emulsifier, but the effect is negligible for high emulsifier concentrations. Similar behavior was observed for the particle size, namely that Rp decreased sharply at low emulsifier concentration and much more smoothly later [114]. Comparable observations have been reported by Zekhnini [115]. The dependence of the number of particles Np on the amount of emulsifier changed from Np ⬀ [emulsifier]3.2 at low emulsifier concentrations to Np ⬀ [emulsifier]0.6 at high emulsifier concentrations. The effect of the emulsifier is stronger than in normal microemulsion polymerization [116]. This suggests that the lowest emulsifier concentration

was too close to the stability limit for microemulsions and partial coagulation occurred. For the kinetics of the inverse microemulsion polymerization of MADQUAT stabilized with a blend of nonionic emulsifiers and initiated by UV irradiation, it was found that during polymerization Rp first increased, reached a maximum, and then decreased. This effect was due to the combined effect of continuous nucleation and the decrease of the concentration of the monomer in the polymer particles as the polymerization proceeded. The correlation Rp ⬀ [AIBN]0.54 was found, suggesting that a second-order process for radical loss was operative [114]. These determinations facilitated the development of this quantitative model [117]. (c) Kinetics in Percolating Systems. In percolating inverse microemulsions, inverse micelles form semipermanent aggregates. The impetus for the formation of these aggregates might be provided by the strings of connected micelles in a percolating system [43] suggested by quasi-elastic light scattering (QELS) and viscosimetry. Acrylamide at the interface induces strong interparticle attractions because the addition of acrylamide is sufficient to convert a nonpercolating (only water) to a percolating system [43]. The formation of water channels between water pools of inverse micelles in a percolating inverse microemulsion leads to an average acrylamide concentration in the dispersed water phase [118]. This process inevitably influences the location of acrylamide at the water-oil interface. As a consequence, for a given acrylamide/water mass ratio, the concentration of acrylamide at the locus of the polymerization reaction of the percolating inverse microemulsion is different from that of a nonpercolating inverse microemulsion. This situation influences both the kinetics and the molecular mass [112]. Percolation decreases the rate of polymerization of acrylamide initiated by APS [119]: ¯ n) ⬀ [AM] x Rp(or M

(2)

where for percolating inverse microemulsions the respective values of x are 1.1 and 0.4 for Rp and Mn, respectively. For the polymerization of acrylamide initiated by BPO, percolation decreases the time interval of slow oil phase polymerization. This can be ascribed to the increased rate of capturing the acrylamide oligomer radicals by inverse micelles and to efficient mass transfer between oil and water phases in percolating inverse microemulsions. 3. Characteristics of Microlatexes The properties of the resulting polymer dispersions (microlatexes) and the polymers are directly correlated

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with the mechanism of the polymerization. For polymer characterization, the latex particles are usually precipitated in a large excess of nonsolvent, purified by extraction or washing, and redissolved in a suitable solvent (e.g., water or methanol). Afterward, standard techniques of polymer characterization can be used for analysis, such as dynamic light scattering (DLS), gel permeation chromatography (GPC), viscometry, or differential scanning calorimetry (DSC). Especially in the case of cross-linking polymerizations, where the spherical structure of the polymer particle is kept by covalent bonding, transmission electron microscopy (TEM) and scanning electron microscopy (SEM) are also useful analytical tools. A brief summary of the results of polymer characterization is as follows: Decreasing particle size is achieved by increasing the surfactant/monomer ratio. The higher surfactant content enables the stabilization of the larger total interfacial area provided by smaller particles (as described in a simple geometrical model for normal microemulsion polymerization [74]). Increasing the monomer content [39] or the temperature [34] increases the resulting particle size (among other factors) by increasing the number of collisions and the diffusion rate of the monomer. Increasing the initiator concentration usually results in smaller particles [74], probably because of reduced primary particle growth in the presence of many simultaneously growing polymer chains. Comparison of the latex particle size with the gyration radius of the dispersed polymers shows that the polyacrylamide chains in microlatex particles are in a highly collapsed state [44]. The molecular weight of the polymers is typically >106 g mol⫺1 and increases with higher monomer contents, lower surfactant/monomer ratios, lower initiator concentrations, and lower temperatures (DLS, GPC, viscometry) [78]. The use of alcohols as cosurfactants and other chain transfer agents lowers the molecular weight of the polymer obtained. DSC measurements show no differences in the glass temperatures of polymers synthesized in solution, inverse emulsion, or inverse microemulsion polymerization [120]. Beside the parameters already mentioned that control particle size and molecular weight, the choice of the monomer has the greatest influence on the polymer properties. An overview of different monomers and surfactants used in inverse microemulsion polymerization


is given in Table 2. Most common is the use of acrylamide, acrylates, and MADQUAT. The polymers obtained are not only interesting model systems for the study of inverse microemulsion polymerization but also interesting candidates for applications of high-molecular-weight, water-soluble monomers of Section V. In addition to the polymerization parameters discussed in this chapter, copolymerization and functionalization can be used to control the polymer and particle characteristics of microlatexes and polymers with outstanding and fascinating properties. 4. Copolymerization and Functionalization In general, there are two different ways to achieve the functionalization of polymer latexes [121]. One is the functionalization by polymer analogue reactions; the other, more convenient and more common way, is the addition of a functionalized compound (e.g., a comonomer) in a one-step-procedure. According to the latter strategy, amine [122], carboxyl [123], hydroxyl [124], mercapto [125], and sulfonate [126] functionalized latexes have been synthesized in heterophases. Depending on the method of monomer addition (batch or feed polymerization) and the physiochemical properties of the monomers, different latex morphologies can be obtained [127]. The main advantage of copolymerization in microemulsions, compared with copolymerization in homogeneous solutions or emulsions, is the possibility of achieving very homogeneous products, even from monomers that are not suitable for copolymerization in solution or emulsion. The copolymerization parameters of monomer pairs are strongly affected by the microstructure of the reaction medium, as a comparison of reactivity ratios has shown [78]. In microemulsions the comonomers are preferably oriented toward the wateroil interface and charge effects are shielded that way. But as the kinetics of microlatex formation are also strongly affected by monomer transport through the interface, this process also has some influence on the copolymerization behavior. Principally, two different cases of copolymerizations can be distinguished, as follows. (a) Copolymerization of Hydrophilic and Hydrophilic Monomers. The most remarkable effect of copolymerizations in microemulsions is the improvement of structural homogeneity as the copolymerization parameters tend toward unit. In the case of the copolymerization of acrylamide with sodium acrylate, the acrylate content of the copolymer was varied between 10 and


55 mol% [34]. By 13C NMR studies it was shown that the monomer sequence distribution is perfectly random and obeys Bernoullian statistics [128]. The reactivity ratios are close to unity. By using biunsaturated vinyl monomers, cross-linked microlatexes or so-called microgels are obtained. One study investigated the effect of copolymerization of acrylamide with the cross-linker N,N⬘-methylenebisacrylamide (BAM) on kinetics, polymer particle size, and the degree of swellability. Among other effects, variations of conversion curves and particle sizes were found [129]. Inverse microemulsion polymerization has also been applied to the synthesis of copolymers containing both positive and negative charges along the polymer chain, i.e., polyampholytes [19,130]. The importance of structure homogeneity for the net charge distribution of linear ampholyte terpolymers based on sodium-2acrylamido-2-methylpropanesulfonate (NaAMPS), 2(methacryloyloxy)-ethyltrimethylammonium chloride (MADQUAT), and acrylamide (AM) has been demonstrated [36]. By viscometry and dynamic light scattering it was shown that quasi-neutral chains exhibited an extended conformation when they were solubilized in low-salt solutions, which hints at a low charge excess. Increasing the salt content resulted in more compact conformations. Compared with their macroscopic counterparts (polyampholyte macrogels), little attention has been paid so far to their colloidal counterparts. Cross-linking of NaAMPS, MADQUAT, and AM using N,N⬘-methylenebisacrylamide (BAM) leads to polyampholyte microgels with diameters in the range 85–116 nm. The flocculation behavior in aqueous solutions has been investigated with respect to effects of charge densities and electrolyte addition [37]. Cross-linked polyelectrolyte microgels are interesting model systems for the systematic investigation of the origin of polyelectrolyte effects due to conformational transitions [131]. (b) Copolymerization of Hydrophilic and Hydrophobic Monomers. The copolymerization of hydrophilic and hydrophobic monomers results in amphiphilic polymers. In an early study, acrylamide was copolymerized with the oil-soluble monomer methyl methacrylate (MMA) using the oil-soluble initiator AIBN. In addition to the copolymer, homopolymers of polyacrylamide (PAM) and poly(methylmethacrylate) (PMMA) were found. The total conversion of MMA was lower than 10%. The composition of the copolymer was almost independent of the comonomer ratio, probably because of a constant molar ratio of the monomers at the interface as the locus of the copolymerization [49,111].

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The locus of copolymerization and the nature of the w/o interlayer are also important factors for the copolymerization of acrylamide with styrene in the system toluene/styrene/AOT/water/acrylamide. Also in this case, copolymer and homopolymers were formed. The molar fraction of acrylamide in homopolymer compared with copolymer is about 45–55 [119]. Addition of small amounts of the polymerizable surfactant T10 [t-octylphenoxy-poly(oxyethylene) methacrylate, with 10 ethylene oxide units] to the copolymerization of AM and sodium acrylate (NaAA) resulted in hydrophobically modified, water-soluble copolymers [42]. The polymers show interesting rheological properties, e.g., shear thickening, shear thinning, and viscoelasticity. Very low amounts of hydrophobic entities in the copolymer structure (0.5 mol% T10) increase the low-shear viscosity of a 0.2 wt% solution by a factor of 1000 compared with the nonmodified copolymer. B.

Inverse (Macro)emulsion Polymerization

Vanderhoff et al. [20] developed a heterophase waterin-oil polymerization process that they termed ‘‘inverse emulsion polymerization,’’ analogous to the direct oilin-water process. Inverse emulsion polymerization comprises emulsification of a water-miscible monomer, usually in aqueous solution, in a continuous oil medium using a water-in-oil emulsifier. Stabilization was achieved sterically, and the initiating species could reside either in the dispersed water phase (in analogy to suspension polymerization) or in the continuous phase (in analogy to the classical emulsion polymerization) to give a colloidal dispersion of water-swollen polymer particles in oil. The final product is usually a colloidal dispersion of hydrophilic polymer particles in a continuous oil phase. The average particle size of inverse latexes is usually 100–1000 nm, compared with the original droplet size of 100 nm to several micrometers. In contrast to microemulsions, macroemulsions are only kinetically stable. This means that besides the formulation, other parameters such as reactor geometry and stirring speed can have a strong influence on the course of reaction and the product properties. Many of the different ways of performing polymerizations in direct emulsions have also been established for inverse emulsion polymerization, such as batch, feed, and seeded polymerization. A list of different systems including the surfactant, the monomer, the initiator, and the continuous phase as reported in the literature is given in Table 2.

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1.

Surfactants for Inverse (Macro)emulsion Polymerization In principle, for the formulation of inverse emulsions, surfactants very similar to those known for inverse microemulsions are used, but the required amount is usually much smaller and is in the range 2–4% by weight. There are only a few papers on the use of AOT as surfactant in such systems [46]. Sorbitan esters of fatty acids such as sorbitan monooleate are common surfactants for the formulation of the inverse emulsions [24,132], even if the resulting polymerized dispersion usually shows limited stability. Dimonie et al. [55] used polyoxyethylene(8) stearic acid or polyoxyethylene(4) nonylphenol as emulsifier and potassium persulfate and sodium bisulphite as the redox initiator in an acrylamide system. Kurenkov et al. [58] used Sentamid-5 (amide of polyoxyethylated stearic acid) as emulsifier and potassium persulfate as initiator. Usually, nonionic stabilizers are blended to achieve an overall HLB value of 4–6 to better prevent particle coalescence. McKechnie [29] used a blend of Span 80 and Tween 80 as emulsifier and benzoylperoxide as initiator. He illustrated the relation between stabilization and the amount of emulsifier. The Lehigh group [57] used Tetronic 1102 (polyoxyethylene adduct of polyoxypropylene ethylene diamine) as emulsifier for the formulation of an acrylamide emulsion in o-xylene. For the inverse emulsion polymerization of aqueous acrylamide solution in toluene, a blend of a low-HLB Montane 83 and a high-HLB Montanox 85 was used in order to determine the influence of the high-HLB emulsifier on the initial polymerization rate [40]. Despite the small particles, the final dispersions with sorbitan monooleate and sorbitan sesquiolate were not very stable for long storage times. Dispersions with higher stability were obtained with the use of triblock polymeric surfactants such as polyester–polyethylene oxide–polyester (HB 239) [60,133] prepared by reacting condensed 12-hydroxystearic acid with polyethylene oxide [33,134]. Steric stabilization using these polymers is achieved when the polyethylene oxide chain is anchored to the interface and the poly(12-hydroxystearic acid) end is free to move in the continuous phase. The stabilization is enhanced relative to the low molecular fatty acid ester derivatives because of the inherent advantages of triblock surfactants as well as the larger extended length of the poly(12-hydroxy˚ compared with 20–22 A ˚ for C18 stearic acid) (115 A sorbitan esters) [135]. In another study in which small amounts of sorbitan fatty acid esters and polyethoxylated sorbitans were blended with the block copolymer,


nonsettling polymerizable inverse emulsions at low surfactant and high monomer concentrations could also be obtained [61]. Kurenkov et al. [136] investigated the emulsifierfree polymerization of acrylamide in a water-toluene medium in the absence and in the presence of ionogenic monomers (sodium or potassium styrene sulfonate). 2. Kinetics and Mechanism The level of understanding of inverse emulsion polymerization has significantly improved over the past 30 years. During the 1980s efforts were dedicated to the elucidation of the reaction mechanism, kinetic measurements, and reactor modeling of the inverse emulsion polymerization processes. Even so, the published data are often inconsistent with each other because the kinetic behavior of inverse emulsion polymerization is complex and is specific to a given monomer-emulsifierinitiator-continuous phase set. The features of the proposed mechanism are mainly based on the nature of the initiator, which controls the initiation process as well as the colloidal stability behavior of the growing polymer particles during the polymerization process. Apparently, there is a difference in the initiation process with water-soluble and oil-soluble initiators, as already seen for microemulsions. Whereas in the case of inverse microemulsions, an oil-soluble initiator leads to more complex kinetics, the water-soluble initiator does so in case of inverse emulsions. When an oil-soluble initiator is used, the kinetics of inverse emulsion polymerization seem to resemble those of a conventional emulsion polymerization process. The micellar model can be put into practice for the explanation of the polymerization mechanism only in some cases [132]. The inverse emulsion polymerization initiated by a water-soluble initiator probably takes place as a solution polymerization in a microparticle [5,137]. Other differences can cause reaction among the components of the polymerization system [44]. For example, the redox reaction between the emulsifier AOT and initiator APS strongly influences the dependence of the polymerization rate on the concentration of the emulsifier. Because of the great importance of the different methods of initiation, we will focus on this point in detail. (a) Initiation by Oil-Soluble Initiators. The kinetics and mechanism of an inverse emulsion polymerization are expected to be similar to those observed in the conventional emulsion polymerization because the initiator is dissolved in the continuous phase. There it can form radicals, followed by reaction with monomer units that


are dissolved to a low extent in the continuous phase. The macroradicals formed can enter into the micelles swollen with monomer or into the particles. One important feature is the droplet and particle size throughout the polymerization. This seems to follow a different mechanism than that in conventional emulsion polymerization. In the latter case, monomer diffuses from large monomer droplets to the particles through the water phase during the polymerization process. Contrary to that, in the case of inverse emulsion polymerization with oil-soluble initiators, the evolution of the droplet is reported to follow a balance between dispersion and coalescence of the emulsion droplets. Graillat et al. [40] showed for the system acrylamide in toluene initiated by the oil-soluble AIBN that two populations of droplets or particles existed in both the initial emulsion and the final latex. The large droplets underwent a sharp decrease in size at a certain percentage of conversion depending on the agitation. It was suggested that this results from the balance between dispersion and coalescence of the emulsion droplets. The determination of the initiation locus and the rate of polymerization is of great interest. Systems have been reported with kinetics that are close to those for conventional emulsion polymerization. Deviation from the conventional kinetics is mostly a result of the nature of the emulsifier. Kinetics similar to conventional emulsion polymerization. When an oil-soluble initiator is used, the kinetics of inverse emulsion polymerization seem to resemble those of a conventional emulsion polymerization process. This is schematically presented in Fig. 2. The initiation step (Fig. 2a) occurs in the continuous

485

phase, and radicals or macroradicals have to reach the monomer phase where the particles are nucleated. Large monomer droplets act as a monomer reservoir and monomer diffuses through the continuous phase toward the reaction locus. As the particles grow, they are stabilized by absorbing surfactant from surrounding micelles. After micelles disappear, no new polymer particles are generated and the number of particles remains constant throughout the polymerization (Fig. 2b). At the end, the monomer in the monomer droplets has been consumed and only the monomer in the monomer-swollen particles has to be polymerized to obtain the final latex (Fig. 2c). Pross et al. [138] reported that in the case of acrylamide in isooctane stabilized by a surfactant of high purity, pentaerythriolmyristate, and initiated by 2,2⬘-azobis(2,4-dimethylvaleronitril) (ADVN, Wako V-65), kinetics of the Smith-Ewart (case 2) type with an average radical number of 0.5 are found. The inverse emulsion polymerization shows the following features of a conventional emulsion polymerization: Particle nucleation and monomer consumption take place in the monomer droplets. Mass transfer of monomer and radical entry are not rate limiting [139]. The partial order of the emulsifier concentration is positive. Chain termination is predominately second order with respect to the polymer radical concentration at initiator concentrations above 0.09 mmol L⫺1. The inverse emulsion polymerization of aqueous acrylamide solution in toluene using a selected blend of emulsifiers (Montane 83 and Montanox 85) and oil-

FIG. 2 Schematic representation of inverse emulsion polymerization. (a) One starts from large monomer droplets and surfactant micelles in the water phase. The initiation step occurs in the continuous phase and radicals or macroradicals have to reach the monomer phase, where the particles are nucleated. (b) During the polymerization, the monomer diffuses through the water phase. (c) At the end, particles with a diameter usually larger than 100 nm are obtained.

486

soluble azo compounds as initiators is also found to behave, for the most part, like the conventional emulsion polymerization process. Deviation from the kinetics of conventional emulsion polymerization. Numerous papers report kinetics that are different from those of conventional emulsion polymerization. It is confusing that all three Smith-Ewart cases are reported. In one of the first papers about the kinetics of inverse emulsion polymerization, Vanderhoff et al. [20] assumed a Smith-Ewart case 1 model with an oil-soluble initiator. The average number of radicals per particle was found to be incredibly small (0.008 to 0.2). At that time it was proposed that the initiation step is due to the slightly dissolved initiator, benzoyl peroxide, inside the aqueous phase. Other authors found that the kinetics resemble a Smith-Ewart case 3 model [40,140], and Platkowski et al. [138] proposed a Smith-Ewart case 2 model. In an effort to explain this discrepancy, it was found [5] that the kinetics are strongly influenced by the nature of the surfactant. This can lead to the following unusual steps during inverse emulsion polymerization: A reaction between the macromonomers with the hydrophilic moiety of an interfacial surfactant molecule can take place. A long-chain reaction with radically active functional groups on the emulsifier has to be considered. A chain length–dependent mass transfer of primary radicals from the continuous to the disperse phase might be possible. In most of the papers in which different kinetics compared with conventional emulsion polymerization kinetics were reported, the inverse emulsion polymerization was carried out using a fatty ester of sorbitan and an aliphatic continuous phase. For example, McKechnie [29] used different blends of Span 80 and Tween 80 for the emulsion polymerization of acrylamide and reported kinetic and molecular weight data for a wide range of benzoyl concentrations. It was found that there are unusual dependences of the polymerization rate on emulsifier concentration (Rp ⬀ [E]0.2) and on the initiator concentration (Rp ⬀ [I]1.0). The rate dependence on initiator indicates that a unimolecular termination competes with bimolecular termination, and the relationship between rate and emulsifier concentration is an indirect indication of the radical activity of the surfactant molecules. Many of the studies have also shown that the use of sorbitan esters of fatty alcohols, such as sorbitan monooleate, leads to a degradative chain transfer reaction resulting in branched homo-


polymers and lower polymerization rates. Therefore, the low rates of polymerization of acrylamide in inverse emulsion polymerization with sorbitan monooleate can be explained in terms of the emulsifier’s chain transfer activity [5,23]. Sorbitan monooleate has an unsaturated carbon in the middle of its hydrophilic tail and five labile hydroxy functional groups on its surfactant head. These radically active functional groups can react with primary radicals in the continuous phase, lowering the polymerization rate and increasing the molecular weight. A systematic study has been reported by the Lehigh group [57] on an acrylamide system using a surfactant of different chemical nature, Tetronic 1102 (polyoxyethylene adduct of polyoxypropylene ethylenediamine adduct), and benzoyl peroxide as initiator. However, because of the nature of the emulsifier, the formation of multicelled emulsion droplets consisting of Tetronic emulsifier molecules surrounding aqueous acrylamide subdroplets was found to affect the polymerization kinetics. In the inverse emulsion polymerization of aqueous acrylamide solution in toluene using a selected blend of emulsifiers (Montane 83 and Montanox 85) and oilsoluble azo compounds as initiators, it was found that not only the nature of the surfactant but also the composition of different surfactants in a surfactant blend is of interest. There is a minor effect of the high-HLB emulsifier concentration on the initial polymerization rate that is reflected in the molecular weight values. The use of mercapto-acrylamide oligomers results in a lower molecular weight. It is suggested that the initiation process follows a mechanism in which the primary radicals are mainly produced in the oil phase or possibly in the interfacial layer. In the former situation, the radical or oligoradical may be captured by the monomer droplets or cause a homogeneous nucleation in the oil phase by reacting with the dissolved acrylamide molecule; in the latter case, the radicals diffuse into the interior of the monomer droplets. Other experimental data also support [141] an initiation step from radicals formed in the interfacial layer of emulsifier and captured by the droplets. The kinetics are affected not only by the chemical role of the surfactant but also by its physical role. This could be shown by inverse emulsion polymerization involving the block copolymer surfactant HB239. In this case no chemical reaction with the surfactant is expected to take place. Indeed, it was found that the rate of polymerization of acrylamide in inverse emulsion polymerization is higher when the block copolymeric surfactant is utilized in comparison with sorbitan


487

monooleate, and the rate of polymerization does not depend on the emulsifier concentration. The initial rate of polymerization of an inverse emulsion of acrylamide using HLB239 is found to be: Rp ⬀ [M]1.0[I]1.0[E]0

(3)

The first-order dependence on the initiator concentration suggests that unimolecular termination dominates. The first-order dependence with respect to the monomer implies standard free radical initiation and propagation steps. The zeroth-order dependence with respect to the emulsifier suggests a purely physical role of the emulsifier [6,60]. However, the weight average molecular weight of the resulting polymer was found to be lower because of a transfer reaction to the hydrophilic part of the emulsifier [56]. The influence of the emulsifier on the polymerization rate can be studied by comparing the systems with a system synthesized in absence of an emulsifier. In the case of emulsifier-free polymerization [136] of acrylamide in a water-toluene medium, in the absence and in the presence of ionogenic monomers (styrene sulfonate of sodium and potassium), the kinetics were found to follow a 0.46 order dependence on the initiator concentration when AIBN was used as initiator. Factors that influence the particle diameter, such as the rate of agitation and the impeller size and type, also have a minor influence on the rate of polymerization. (b) Initiation by Water-Soluble Initiators. Apparently, the inverse emulsion polymerization initiated by a water-soluble initiator is expected to take place in a microparticle and the kinetics should resemble those for a solution polymerization [5,137]. In their pioneering work on inverse emulsion polymerization of sodium p-vinylbenzene sulfonate, Vanderhoff et al. [20] investigated the effect of temperature, emulsifier concentration, type, and concentration of the emulsions. Based on TEM micrographs showing very small droplets (in the range of 20 nm), it was postulated that particle nucleation occurs in emulsion droplets as well as in monomer-swollen micelles if present. From the kinetic and molecular weight results, Vanderhoff et al. [20] assumed a Smith-Ewart case 2 model in the case of a water-soluble initiator. But the SmithEwart micellar theory cannot be used to explain the polymerization mechanism because the initiator is dissolved not in the continuous phase but in the dispersed phase. The initiation reaction starts in finely dispersed droplets of the aqueous solution of the monomer. The evolution of particle size during polymerization is of great interest for the interpretation of the mecha-

nism. Many papers do not mention the droplet size versus the particle size or the dependence of particle size on conversion. In some papers the evolution of the particle size distribution versus conversion is observed [40,54]. This is mostly in the case of oil-soluble initiators, and it was discussed with the balance between dispersion and coalescence of the emulsion droplets. Contrary to these findings, in the case of water-soluble initiation, most of the published data show that the droplet and particle size seems to remain constant throughout the conversion [28,30,33,46]. For this behavior two explanations may be discussed: The mechanism of coalescence and breakup of droplets takes place. The droplets are stable throughout the polymerization. The question of whether the identity of the droplets during polymerization is maintained also leads directly to the discussion of miniemulsion polymerization (see Section IV.C). However, carefully designed experiments in which monomer and initiator were in different droplets and therefore different droplets had to collide for polymerization to occur supported the mechanism of coalescence and breakup of droplets [59]. The largest droplets act as monomer reservoirs and their size is found to be affected by the stirring rate. The dispersion under high shear seems to be more efficient at relatively high conversions. The smaller droplets, which are insensitive to the stirring rate, are sensitive to Brownian motions and they coagulate with other polymer particles. Coalescence and breakup of aqueous droplets (see Fig. 3) take place simultaneously under continuous agitation and have a significant effect on polymerization, drop/particle size, and distribution [59]. The particle size distribution is broad for the inverse latexes. This is expected for particles produced by a breakup coalescence mechanism. However, it is interesting to note that Kriwet et al. [28] have observed that the use of water-soluble initiators leads to particles of 1–10 ␮m, whereas in the case of oil initiators, smaller particles of about 80–150 nm were formed. There are numerous studies of inverse emulsion polymerizations, some of which are discussed here. Studies of Kurenkov et al. [142] using KPS initiator and Sentamid-5 emulsifier show that the polymerization rate increased with increasing emulsifier concentration (up to 20% conversion) and then became independent of emulsifier concentration. Molecular weight was found to decrease with increasing initiator, emulsifier, and toluene concentrations. For the kinetics of acrylamide stabilized by Tetronic 1102 and initiated by KPS [141] the rate of polymerization was found to be:

488


FIG. 3 (a) Mechanism of coalescence and breakup of aqueous droplets. (b) This mechanism can lead to the same particle size as it is observed for the droplet size in the starting emulsion.

Rp ⬀ [I]0.4[M]1.0[E]0.6

(4)

Benda et al. [46] found that the kinetics of the persulfate-initiated emulsion polymerization are independent of the type of monomer: acrylamide and acrylic acid (sodium or ammonium salt) show similar kinetics and the polymerization can be described by the following equation: Rp ⬀ [I]0.5[M]1.5[E]0.1

(5)

The kinetics of the KPS-initiated inverse emulsion polymerization of aqueous sodium acrylate solutions in kerosene with Span 80 as emulsifier were studied [21]. The conversion-time curves are S shaped. The following expressions have been obtained for the maximum rate of polymerization and the molecular weight of the polymers under the experimental conditions investigated: Rmax ⬀ [KPS]0.78[M]1.5 [Span 80]0.1 ⫺0.37

¯ v ⬀ [KPS] M

2.9

⫺0.2

[M] [Span 80]

(6) (7)

Other studies show that the polymerization rate can have up to a 1.7 order dependence on the monomer concentration [137]. The rate of polymerization for an inverse emulsion photopolymerization of acrylamide using the water-soluble initiator ␣-ketoglutaric acid (␣KGA) and the emulsifier Span 80 was found to be [25]: Rmax ⬀ [Intensity of light]0.5 [I]0.5 [M]1.28 [Span 80]⫺0.42 (8) The resulting molecular weights are higher than in the case of the water-soluble 4,4⬘-azobis-4-cyanopentanoic acid (ACPD). This is due to the fact that ACPA generates single radical pairs on dissociation, whereas ␣-KGA (and ␤-KGA) gives rise to triplet pairs [143].

In conclusion, the kinetics of the inverse emulsion polymerization initiated by water-soluble initiators depends mainly on: The type and amount of the surfactant (Rp ⬀ [E]0.1–0.6) The amount of initiator (Rp ⬀ [I]0.4–0.8) The type and amount of monomer (Rp ⬀ [M]1.0–1.7) A dependence of the polymerization rate on the surfactant and initiator concentration was observed in the case of oil-soluble initiators, and it was also obtained for the inverse emulsion polymerization initiated by water-soluble initiators. This behavior was explained by reactions between the radicals and the emulsifier. However, in the case of water-soluble initiators, the dependence on the amount of initiator follows a lower order (0.4 to 0.8) than for the oil-initiated inverse emulsion polymerization. This low order is consistent with the order in emulsifier-free polymerization [136] of acrylamide in a water-toluene medium, for which in both the absence and the presence of ionogenic monomers (styrene sulfonate of sodium and potassium) a 0.5 order dependence related to the initiator is observed in the case of KPS. This deviation from the first-order rate with respect to the monomer is observed only in the case of water-initiated inverse emulsion polymerization. The deviation from the first-order rate with respect to the monomer is between 1 and 1.7 and usually has been explained by complex or cage effect theory or a hybrid of them. Hunkeler and Hamielee [137] assumed the occurrence of persulfate in three forms: dissolved, compact cage fragments, and diffuse cage fragments. The explanation of the polymerization mechanism is also connected to unusually low polymerization temperatures, and Benda et al. [46] discussed a redox reaction of AOT and APS. The initiation reaction takes


489

place in the water phase and was found to go over the complex stage. The ammonium persulfate and acrylamide complex decomposes into two unpaired radicals capable of propagation. This suggestion is supported by the almost sesquimolecular rate order with respect to the monomer for acrylamide and acrylic acid. Formation of the complex accounts for the enhanced decay of ammonium persulfate at low temperatures. The initiation can also be performed using watersoluble redox initiators [56,144,145]. In inverse emulsion polymerization using water-soluble initiators, the two components of a redox pair have to be introduced separately. Usually, the oxidizing part is dissolved in the aqueous monomer, which is then dispersed in an oil stabilized with surfactant, and the reducing part is then added to start polymerization. An alternative is that both oxidant and reductant are added separately to the emulsion of aqueous monomer in an agitated oil phase. Therefore, the polymerization system may consist of either two or three different droplets and the distribution of initiator(s) is heterogeneous in nature. This also supports the mechanism of coalescence and breakup of aqueous droplets [59,146,147]. The initial polymerization rate in an inverse emulsion polymerization of acrylic acid in Isopar-M and N,N-bishydroxyethyl tall oil amide as surfactant was found to be: Rp ⬀ [AA]2.01[Na2S2O5 ]0.70 [KBrO3 ]0.76 [E]⫺0.47

(9)

A combination of bimolecular and monomolecular termination modes, a chain transfer of the surfactant, and an oxidizing role for the oxygen molecules were suggested [147]. This complicated mechanism has to be considered because a coalesced aqueous drop might undergo further coalescence and breakup. Modeling of inverse emulsion polymerization applying Monte Carlo methods has also been done [148]. This permits the calculation of kinetics as well as different product distributions. This method is not restricted to a steady-state assumption, and chain length– dependent reactions, such as cross-linking and long chain branching, can easily be included. (c) Initiation by Radiation. The initiation of polymerization in inverse emulsions can also be achieved by radiation using a 60Co source [32]. In principle, in the case of radiation-initiated polymerization, kinetics close to those with the water-soluble initiator are expected because the nucleation and polymerization are limited to the monomer phase. The polymerization of vinylpyrrolidone in an isoparaffinic hydrocarbon with an emulsifier blend of Span 80 and Tween 85 results in high-molecular-weight polyvinylpyrrolidone ob-

tained at high polymerization rates (Rp ⬇ 10–35 mol L⫺1 s⫺1) to high conversions (90–95%). The particle sizes are in the range 200 nm to 2 ␮m. In the case of 60Co ␥-ray–initiated inverse emulsion polymerization of aqueous sodium acrylate solutions in kerosene with Span 80 as emulsifier, the polymerization rate was found to be: Rp ⬀ D0.9[M]1.5[E]0.4

(10)

This kinetic analysis suggests a dose rate–independent polymerization process for the system such that there was only one active passage of radiation through a droplet; e.g., all polymer radicals resulting from a radiation passage were terminated before another passage [22]. In another system, the copolymerization of (2-methacryloyloxyethyl) trimethyl ammonium chloride and acrylamide was performed in an inverse emulsion polymerization using gamma rays for initiation. The system was emulsified in kerosene with a blend of Span 80 and OP10. The rate of polymerization can be presented by: Rp ⬀ D 0.87[M]1.37[E]0.53

(11)

where D is the dose rate [30,31]. 3. Inverse Emulsion Copolymerization Copolymerization reactions allow the combination of nonionic, anionic, and cationic monomers in order to obtain polymers with new properties. Inverse emulsion copolymerization studies of acrylamide and methacrylic acid with AIBN as initiator were reported by Glukhikh et al. [41]. The kinetic behavior of the copolymerization is strongly pH dependent. This can be partly explained by the wide differences in the reactivities of MAA monomer molecules and MAA-ended macroradicals, but it is also due to the partition of the ionic comonomer between the organic and the aqueous phase of the emulsion under acidic conditions. The latex stability under acidic conditions is poor. An experimental investigation of the inverse emulsion copolymerization of acrylamide and quaternary ammonium cationic monomers, dimethylaminoethylacrylate (DMAEA), and dimethylaminoethylmethacrylate (DMAEM) has been carried out using sorbitan monooleate [23] or a block copolymeric surfactant (HB246) whose hydrophilic moiety is polyethylene oxide and whose hydrophobic moiety is poly(12-hydroxy stearic acid) [62]. The reaction was started by AIBN or KPS and the following observations were made: Nucleation and polymerization occur within the monomer droplets.

490


Heterophase diffusion-limited oligoradical precipitation is the predominant initiation reaction. Unimolecular termination with interfacial species is competitive with the bimolecular process. Propagation and termination were not found to be influenced by the nature of the polymerization system, proceeding at equal rates in solution and inverse emulsion. A kinetic expression suggested for the inverse emulsion copolymerization of (2-methacryoyloxyethyl) trimethyl ammonium chloride with acrylamide using KPS as initiator is [30]: Rp ⬀ I 0.52[M]1.50[E]0.38

(12)

NMR measurements have shown that the choice of the monomer pairs leads to different compositions. The microstructure of acryloylethyltrimethylammonium chloride turned out to be more homogeneous than the copolymer (2-methacryoyloxyethyl) trimethyl ammonium chloride with acrylamide [149]. It was also found that not only does the choice of the monomer set influence on the composition but also the surfactant has a strong influence on the quality of the copolymer produced [62]. For example, more uniform copolymers of acrylamide and DMAEA can be synthesized using the block copolymer as emulsifier at faster production rates in comparison with sorbitan monooleate when using batch reactors. But even in the first case a composition drift is observed because DMAEA reacts faster than acrylamide. By feeding the monomers, a more homogeneous composition can be obtained. In addition, artificial neural networks have been used to predict the copolymer composition as a function of reaction conditions and conversion [150].

4.

Inverse Macroemulsion Polymerization in Supercritical Carbon Dioxide as an Alternative Medium Supercritical fluids (materials at temperatures and pressures above their critical values) possess intriguing physical properties that make them interesting media in which to conduct polymerizations. For polymerization in CO2, fluorinated surfactants are required [151]. Yates et al. [152] investigated two steric stabilizers, poly(1,1-dihydroperfluorooctyl acrylate (PFOA) and a block copolymer, PS-b-PFOA. For emulsions stabilized with these polymers, the critical flocculation density (CFD) is very near the ⌰ point of the stabilizing moiety in CO2. Just below the CFD, emulsions stabilized with PFOA exhibit a sharp increase in average droplet size, followed by a sharp decrease, indicating flocculation and subsequent sedimentation [153]. Emulsions stabilized by PS-b-PFOA exhibit a lower flocculation rate below the CFD because of greater surfactant adsorption and absence of bridging flocculation. C.

Inverse Miniemulsion Polymerization

In the case of inverse miniemulsion systems, hydrophilic monomers were miniemulsified by high shear in a nonpolar medium, e.g., cyclohexane or hexadecane containing a surfactant suitable for inverse emulsions (see Fig. 4a). In order to provide osmotically stabilized droplets, water or a salt was added as a ‘‘lipophobe’’ to the monomer phase. Polymerization in carefully prepared miniemulsions should result in latex particles of about the same size as the initial droplets, and a virtually 1:1 copying of the droplets to the particles with respect to their sizes can be obtained (see Fig. 4b and c) [154], as shown for direct systems by a combination

FIG. 4 Schematic representation of inverse miniemulsion polymerization. (a and b) In a first step, relatively stable oil droplets with interfacial tensions larger than zero and droplet sizes within the range 50 to 500 nm are prepared by shearing a system containing oil, water, surfactant, and a water-insoluble hydrophobe. (c) These minidroplets can be polymerized to polymer latex particles, ideally in a 1 : 1 copying process.


of SANS, surface tension measurements, and conductometry [155]. It was found that inverse systems exhibit characteristics similar to those of direct (oil-in-water) miniemulsions (K. Landfester et al., Ref. 66a): The formation of a miniemulsion requires high mechanical agitation to reach a steady state given by a rate equilibrium of droplet fission and fusion. The dispersed miniemulsions are osmotically stable but critically stabilized with respect to colloidal stability. The interface energy between the oil and water phase is greater than zero. The surface coverage of the miniemulsion phases by surfactant molecules is not complete. The osmotic stability of miniemulsion droplets results from an osmotic pressure in the droplets that controls the solvent or monomer evaporation. The osmotic pressure results from the addition of a lipophobe, which has extremely low solubility in the continuous phase. During the polymerization in miniemulsions the growth of particles can be suppressed. The monomer diffusion is balanced by a high osmotic background of the lipophile, which makes the influence of the polymer less serious. The amount of surfactant required to form a polymerizable miniemulsion with surfactant was 0.015 < S < 0.25 (where S is the mass ratio of surfactant to monomer) and covers the whole range from inverse suspension to inverse microemulsion polymerization. Inverse miniemulsions were generated with the polar monomers acrylic acid, hydroxyethyl methacrylate, and acrylamide in cyclohexane or hexadecane as an unpolar continuous phase, and the miniemulsions were polymerized to latexes (K. Landfester et al., Ref. 66a). Rather small and narrowly distributed latexes in a size range 50 nm < d < 200 nm were made of acrylic acid, acrylamide, and hydroxyethylacrylate. Nonionic amphiphilic block copolymers with poly(ethylene-co-butylene) tails turned out to be very efficient stabilizers. Depending on the system, the surfactant loads can be as low as 1.5 wt% per monomer, which is very low for an inverse polymerization reaction and clearly underlines the applicability. It was found that with increasing amount of emulsifier, the particle size decreases as expected. But as already seen for direct miniemulsions, the demand of surface per surfactant molecule increases with decreasing particle size. This means that the smaller the particles are, the higher the coverage of the particles with surfactants is in order to obtain stable latex particles.

491

It might be possible that some of the inverse emulsion polymerization processes with water-soluble initiators are very close to miniemulsions because in some cases the droplet and particle size seems to be constant throughout the polymerization. Especially in the case of copolymeric emulsifier [33], high stability of the droplets is expected. The ionic initiator can overtake the function of the osmotic agent because it is not soluble in the continuous phase. However, the use of high shear to obtain defined starting conditions would be important to ensure a well-defined droplet size with a small distribution. D.

Inverse Suspension Polymerization

Inverse suspension polymerization involves the dispersion of a water-soluble monomer in a continuous organic phase. The rather low consumption of surfactant, the very low amount of coagulum, and the ease of recovery of the polymer from the reaction medium are important advantages of this type of polymerization. Emulsifier levels are typically very low with 2–5% of the organic phase and are below the critical micelle concentration. Inverse micelles have not been detected during nucleation, and the polymerization proceeds in the monomer droplets. The dispersion is thermodynamically unstable and requires both continuous vigorous agitation and the addition of a low-HLB steric stabilizer. This forms a condensed electrically neutral interfacial layer and prevents coalescence. The monomer droplets are typically between 1 and 200 ␮m in diameter and are controlled by the Weber number of the mixture. A scheme for inverse suspension polymerization is presented in Fig. 5. 1.

Surfactants for Suspension Polymerization Sorbitan monooleate, Span 80, has also been reported as a suitable surfactant for polymerization in inverse suspension polymerization [27]. If the dispersion is stabilized by a mixture of the low-molecular-weight surfactant Span 80 and macromolecular emulsifier ethyl cellulose (degree of substitution 2.42 to 2.53, N type of Hercules), better control of the size and the morphology is obtained. Polyoxyethylene(4) nonylphenol has also been used as a effective surfactant for inverse suspension polymerization [56]. 2. Kinetics and Mechanism The initiation and polymerization of an inverse suspension should take place only in the droplets. Because of the large size of the droplets and therefore contrary to inverse emulsion polymerization initiated by water-sol-

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FIG. 5 Schematic representation of inverse suspension polymerization. (a) It involves the dispersion of a water-soluble monomer in a continuous organic phase; the initiator is dissolved in the monomer droplets. (b) After polymerization, large polymer particles (1–200 ␮m) are obtained.

uble initiator, the polymerization is not affected by the interfacial layer formed by emulsifier molecules. Omidian et al. [156] reported the preparation of superabsorbent polymers by inverse suspension polymerization using different acrylic acid/sodium acrylate compositions and different amounts of cross-linking agents. The particle size distribution was narrow (300–400 ␮m). Partially substituting the ionic monomers with nonionic acrylamide broadened the distribution considerably. Large superabsorbent polymers based on acrylic acid with sizes of about 200 ␮m and with undefined morphology have been synthesized by using Span 80 and toluene [27]. Toluene as the continuous phase was heated with sorbitan monooleate. The monomer blend was then added dropwise under constant agitation. The monomer droplet size was inversely related to the emulsifier level. The suspension polymerization took place with a high polymerization rate, reached the maximum conversion, and resulted in a linear (gel-free) polyacrylamide characterized by a high molecular weight of 106 to 107 [27]. If the dispersion was stabilized by a mixture of low-molecular-weight surfactant Span 80 and macromolecular ethyl cellulose emulsifiers (degree of substitution 2.42 to 2.53, N type of Hercules), better control of the size and the morphology was obtained. Dimonie et al. [55] investigated the persulfate-initiated polymerization of acrylamide in the presence of a low emulsifier concentration. They proposed an inverse suspension process with the following reaction steps: starting with a water-in oil dispersion of aqueous monomer droplets, which are very instable, the addition of K2S2O8 rapidly causes an increase in viscosity, followed by gel formation and subsequently phase inversion. As the polymerization proceeds and enough polymer is formed, the gel is broken into smaller particles

by stirring. This mechanism emphasizes the important roles of the emulsifier type and concentration, salt concentration, reaction temperature, and stirring intensity in the physicochemical interfacial behavior during polymerization. It is reported that acrylamide polymerization by inverse suspension differs from the widely accepted model for suspension polymerization of vinyl monomers [56]. The similarities between these two processes are conventional ones, and they concern mainly the shape and size of particles obtained at the end of the polymerization. The changes of topochemistry were shown by an inverse suspension polymerization carried out by dispersing the concentrated solution of acrylamide in cyclohexane containing ethoxylated nonylphenol ethers [EO(4)NP] and using a redox initiator (NaHSO3K2S2O8). Several distinct stages were found: coarse water-in-oil dispersion, concentrated oil-in-water emulsion, bicontinuous system, and coarse polymer-water dispersion in oil. The main reaction, which determines the limitation of the molecular weight, was the chain transfer with the emulsifier EO(4)NP. E.

Inverse Dispersion Polymerization

Water-soluble polymers also include the preparation of a nonaqueous dispersions in which a water-immiscible monomer in organic solvent solution is polymerized using an oil-soluble initiator, so that the polymer precipitates as it is formed. In the presence of a suitable oil-in-oil emulsifier, spherical particles 100 nm to 10 ␮m in diameter are formed from the precipitating polymer. Thus, these polymerizations begin as precipitation polymerizations but become emulsion polymerizations upon stabilization of the polymer particles. A scheme for inverse dispersion polymerization is presented in Fig. 6.


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FIG. 6 Schematic representation of inverse dispersion polymerization. (a) Water-immiscible monomer is dissolved in an organic solvent in the presence of a water-in-oil emulsifier; the polymer precipitates as it is formed. (b) Spherical particles 100 nm to 10 ␮m in diameter are formed from the precipitating polymer. The particles still grow by diffusion of monomer, and (c) after consumption of the monomer, polymer particles are obtained.

1. Surfactants for Dispersion Polymerization For the process of dispersion polymerization, polyacrylic particles were stabilized by block copolymers (polystyrene-b-polyethylenoxide). The use of this stabilizing system enables the production of polyacrylate particles with particle size ranging from 50 to 300 nm depending on the composition of the surfactant (block length) and its concentration [64]. Ray and Mandal [66] carried out dispersion polymerization of acrylamide using poly(vinyl methyl ether) (PVME) as the polymeric stabilizer. 2. Kinetics and Mechanism Baade and Reichert [132] suggested a dispersion polymerization model for the acrylamide system using different nonionic emulsifiers (sorbitan derivatives) in two oil phases (isoparaffinic mixture and toluene). One starts from a solution of acrylic acid in toluene, and during the course of polymerization, the polymer precipitates and is stabilized by emulsifiers. Their model revealed that radicals from the oil phase diffused into the hydrophilic phase in which polymerization took place when the oil-soluble initiator (azodimethylvaleronitrile or AIBN) was used. In this case, they reported a kinetic expression for the polymerization rate (Rp) that is initiator concentration dependent (1.0 order) and emulsifier and emulsifier concentration dependent (⫺0.2 order), instead of the 0.5 order dependence related to the initiator concentration in the case of a water-soluble initiator. The mass transfer of primary radicals from the oil into the water phase is considered to be the rate-determining step of the reaction [157]. The rate of polymerization in an acrylic system showed strong autocatalytic behavior. The maximum of the polymerization

rate and the corresponding time of appearance depend strongly on the water content. Because the polymerization started in the continuous phase and no micelles of the block copolymer were detected, a homogeneous nucleation process was proposed [158]. Using dicarboxylic dichloride or diglycidyl ether as cross-linking agent for polyacrylic acid particles synthesized by inverse dispersion polymerization, the particles can be linked with each other and a gel with three-dimensional network structure can be formed [159,160]. Ray and Mandal [66] carried out dispersion polymerization of acrylamide using poly(vinyl methyl ether) (PVME) as the polymeric stabilizer, KPS as the initiator, and various alcohols or their mixtures with water as the polymerization medium. Polydisperse spherical as well as oval particles are formed. The simultaneous presence of both species suggests the coalescence of particles of similar size leading to polydispersity. The increase of stabilizer concentration leads to a decrease in the particle size and a decrease of the molecular weight. The particle size also decreases with increasing t-butyl alcohol (TBA) concentration in the TBA-water mixture. TBA-water mixtures exhibit cosolvency toward PVME, the solvency becoming highest at about 70 vol% TBA. Very similar to dispersion polymerization is precipitation polymerization. In this case, the polymer formed is usually not stabilized by a surfactant. Precipitation polymerization of acrylamide and N,N⬘-methylbisacrylamide (MBA) was carried out in alcohols [71]. Large, bulky, and porous particles were formed by the polymerization. On the contrary, copolymerization of acrylamide and MBA with a certain amount of methacrylic acid resulted in the formation of fine monodisperse hydrogel microspheres. This resembles a dispersion poly-

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merization process. This result was attributed to the contribution of methacrylic acid units to the stabilization of particles formed at the initial stage of polymerization and the enhancement of swelling of the particles by monomer and alcohol. It could be shown that the size of the microspheres varied from 0.2 to 1.3 ␮m as a function of the solubility parameter of the dispersant [161]. F.

Mixed Cases of Inverse Heterophase Polymerization

Since their respective inventions by Vanderhoff et al. [20] and Leong and Candau [48], inverse emulsion and inverse microemulsion polymerizations have shared the common objectives of synthesizing high-molecularweight homo- and copolymers with controlled properties. However, both have unique advantages and disadvantages. For example, the lower emulsifier level required for inverse emulsions led to earlier and more extensive commercialization. However, these latexes are thermodynamically unstable. Furthermore, process improvements that have been implemented to enhance the colloidal stability, such as the addition of cosurfactants, have generally decreased the molecular weight of the resulting product and the end-use efficiency. One approach has been discussed in which a thermodynamically unstable inverse macroemulsion is transformed into a thermodynamically stable inverse microemulsion [33]. Heterophase water-in-oil polymerizations of acrylamide were performed in the presence of blends of nonionic stabilizers at 20% monomer concentration. The initial monomeric system is located outside the inverse microemulsion domain, yet close to the inverse macroemulsion/inverse microemulsion phase boundary. A turbid, viscous, and unstable dispersion is produced at the outset and during the conversions. This evolves to an inviscid and nonsettling system at high conversions. Transparent inverse latexes can also be produced provided that the polymerizations are conducted semiadiabatically. Independent of the conversion, the particles were found to be 150 nm. The system follows an inverse macroemulsion–like mechanism. The hybrid inverse microemulsion/inverse macroemulsion polyacrylamides produced herein have a smaller diameter in the aqueous phase than those produced by either solution polymerization or true inverse emulsion polymerization. This is probably due to a large number of intermolecular interactions, such as hydrogen bonds, which are induced by the collapsed nature of the polymer chains in the inverse microemulsion droplets. The

molecular weight and the diameter of the final latex are independent of the polymerization conditions such as initiator level, the hydrophilic-lipophilic balance, the temperature, and physical changes occurring during the polymerization. From the kinetic point of view, the molecular weights of these systems are controlled by the transfer to monomer, and transfer to interfacial emulsifier is the polymerization rate-controlling step. The polymerization process produces final latexes that are transparent and nonsettling with particle sizes smaller than 150 nm. V.

APPLICATIONS

The production of water-soluble polymers in the United States is a multibillion dollar industry, and polyacrylamide and its copolymers constitute the majority of this market. Typical applications are flocculants for wastewater treatment, paper manufacturing, superadsorber, coatings, flotation aids, and aqueous viscosity modifiers in enhanced oil recovery and latex paint systems [33,162–164]. Polyacrylamide and its anionic and cationic copolymers are also applied as coagulants and flocculants in waste and potable wastewater treatment applications, as pushing fluids in enhanced oil recovery, as drag reduction agents and drilling fluids, and for process water clarification in industries such as mining and papermaking [165]. A.

Latexes Obtained by Inverse Microemulsion Polymerization

Polymers synthesized in inverse microemulsions are interesting candidates for all applications of water-soluble polymers. As microlatexes combine high molecular weights with small particle sizes, they show some advantages compared with conventional polymers, such as low viscosities and higher surface areas. Some copolymers can be obtained only by microemulsion polymerization, especially amphiphilic copolymers of water- and oil-soluble monomers. Because of the huge surface area of microlatex particles in the dispersion (⬃100–300 m2 g⫺1), they are outstanding adsorbents, e.g., for proteins, enzymes, and for the immobilization of antibodies [166]. Therefore one important field of application is targeted drug delivery systems [167,168]. The functionalized small microlatexes can pass the blood-brain barrier and have longer circulation times in the body [169] compared with functionalized emulsion latexes (typically 100 nm to 10 ␮m in diameter). Gan et al. [67] reported the polymerization of aniline in inverse emulsion polymerization. Because polyani-


line is a conducting material, there might be a potential for this kind of particle. Besides the listed applications, many new applications will arise from the use of functionalization techniques, e.g., applications of nanohybrids for materials science, reactive particles, and catalysis. This will enable the synthesis of new materials with outstanding properties. One example is the synthesis of superparamagnetic hydrogel particles [170]. In a single microemulsion, magnetite nanoparticles were prepared and then coated by copolymerization of methacrylic acid (MAA) and hydroxyethyl methacrylate (HEMA). The size of the hybrid particles varied between 160 and 320 nm depending on the surfactant/monomer ratio. In a similar approach, superparamagnetic colloids were generated within a continuous hydrogel, which was synthesized in a bicontinuous microemulsion [171]. Silica particles prepared in an inverse microemulsion can be encapsulated, e.g., by a semicontinuous emulsion polymerization of ethyl acrylate (EA) [172]. All these examples show how different properties of inorganic and organic compounds can be combined within nanostructured hybrid materials. The synthesis of reactive, functionalized microgels by immobilization of enzymes can be achieved in a twostep procedure [50]. The copolymerization of acrylamide (AM) and N,N⬘-methylene bisacrylamide (BAM) with N-acryloyl-1,6-diaminohexane or acrylic acid resulted in amine- or carboxylic acid–functionalized microgels. In a second step, alkaline phosphatase was physically entrapped by adsorption at the particle surface. The functionalized particles show enzymatic activity toward the hydrolysis of p-nitrophenylphosphate. Using cross-linked microgels of poly-MADQUAT or sulfonated microgels as exotemplates for the controlled growth of noble metal colloids results in metal-polymer modules that can act as endotemplates for the synthesis of functionalized mesoporous silica supports [173]. The metal-polymer nanoparticles generate the porosity of the silica matrix (by calcination) in which the noble metal colloids (e.g., rhodium, platinum, palladium) are entrapped. The functionalized silica shows catalytic activity in the hydrogenation of dehydrolinalol. These are only a few examples, which were chosen to demonstrate the versatility and the huge impact for materials science provided by inverse microemulsion polymerization. B.

Latexes Obtained by (Macro)emulsion Polymerization

The inverse emulsion polymerization process can also be used for the encapsulation of polypyrrole particles

495

of about 100 nm by acrylamide. The encapsulation increases the processability of the conducting particles by preventing reagglomeration of the particles. It also improves the electrical stability of the particles because the shell of insulating polymer can act as a physical barrier against the dedoping effect [174]. Xie et al. [175] reported the synthesis in inverse emulsion polymerization of poly(lithium acrylate), which can be used as an electrorheological fluid. Such a dispersion can undergo changes in rheological properties, such as development of a yield stress and increased viscosity upon application of kV mm⫺1 electric fields [176]. Because poly(acrylic acid) micro- and nanoparticles yielded excellent bioadhesive properties in an in vitro assay, they may be suitable for the encapsulation of peptides and other hydrophilic drugs [28]. C.

Latexes Obtained by Suspension Polymerization

By utilizing the suspension polymerization technique on water-soluble monomers such as acrylic acid, hydrogels with a high capacity for retaining water can be obtained. For some fields of application, such as agricultural and horticultural use, the exact particle size distribution is of minor importance because superadsorbent unmodified systems can be used. But for medical and hygienic uses such as sanitary napkins and baby diapers, some modification of size is necessary. Such particles can be achieved by the use of macromolecular stabilizers [27]. To obtain superadsorbers with a high capacity for adsorption and desirable kinetics, some optimization (chiefly in terms of neutralization degree, type and amount of the cross-linking agent, and monomer concentration) must be made [26]. VI.

CONCLUSION AND OUTLOOK

The main aim of this chapter was to review critically the current literature in the fascinating field of inverse heterophase polymerization. The main interest is in carrying out the process in order to obtain stable latexes of water-soluble monomers with high molecular weight at low surfactant content. To understand the underlying kinetics thoroughly, the mutual interplay of monomer, surfactant, initiator, and the continuous phase is of high interest. The challenge for the future is to combine the advantages of the different types of inverse heterophase polymerization. In particular, high stabilities such as those of inverse microemulsions are desired for sys-

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tems with low surfactant content as is usual for the other types of inverse heterophase polymerization. Homogeneous functionalization of the particles can potentially be used to create complex polymer superstructures for different applications such as catalysis, selective ionic binding, and detoxification. Incorporation of inorganic material within water-soluble latex particles with well-defined structures will be the focus of future research. Polymerization in inverse heterophases is a rapidly developing field in which major scientific breakthroughs are to be expected. The numerous possible applications testify that the tool of modern heterophase polymerization is very powerful. We are standing at the beginning of fascinating developments for industry and fundamental research.

14. 15. 16. 17. 18.

19. 20.

21.

ACKNOWLEDGMENTS

22.

We especially thank Markus Antonietti for his great support, his advice, and his help. Financial support by the Fonds der Chemischen Industrie, the DAAD, and the Max Planck Society is gratefully acknowledged.

23. 24. 25.

REFERENCES 1.

2.

3. 4. 5. 6. 7. 8. 9. 10. 11. 12. 13.

D. Hunkeler, F. Candau, C. Pichot, A. E. Hamielec, T. Y. Xie, J. Barton, V. Vaskova, J. Guillot, M. V. Dimonie, and K. H. Reichert, Adv. Polym. Sci. 123:115– 133 (1994). E. D. Sudol and M. S. El-Aasser, in Emulsion Polymerization and Emulsion Polymers (P. A. Lovell and M. S. El-Aasser, eds.), Wiley, Chichester, 1997, p. 699. K. Landfester, N. Bechthold, F. Tiarks, and M. Antonietti, Macromolecules 32:5222–5228 (1999). D. Hunkeler and A. E. Hamielec, ACS Symp. Ser. 480:24–41 (1992). D. Hunkeler, A. E. Hamielec, and W. Baade, Polymer 30:127–142 (1989). J. Hernandez-Barajas and D. Hunkeler, Polymer 38: 437–447 (1997). W. D. Bancroft, J. Phys. Chem. 17:501–519 (1913). W. C. Griffin, Soc. Cosmet. Chem. 1:311 (1949); W. C. Griffin, Soc. Cosmet. Chem. 5:249 (1954). J. T. Davies, Int. Congr. Surface Activity 2nd, London, 1957, 1:426. I. J. Lin and P. Somsundaran, J. Colloid Interface Sci. 37:731–743 (1971). I. J. Lin, J. P. Friend, and Y. Zimmeles, J. Colloid Interface Sci. 45:378–385 (1973). P. Sherman, in Emulsion Science (P. Sherman, ed.), Academic Press, New York, 1968, chapter 3. J. Boyd, G. Parldnson, and P. Sherman, J. Colloid Interface Sci. 41:359–370 (1972).

26. 27. 28. 29. 30. 31. 32. 33. 34. 35. 36.

37. 38. 39.

K. Shinoda, Proc. Int. Congr. Surface Activity 5th, 1969, 2:275. R. E. Ford, L. Ford, and C. G. Furmidge, J. Colloid Interface Sci. 22:331–341 (1966). C. Holtzscherer and F. Candau, Colloids Surf. 29:411– 423 (1988). H. Ni and D. Hunkeler, J. Dispersion Sci. Technol. 19: 551–569 (1998). A. Beerbower and H. W. Hill, McCutcheon’s Detergents and Emulsifiers Annual, Allured Publishing Co. Ridgewood, NJ, 1971, p. 223. J. M. Corpart and F. Candau, Colloid Polym. Sci. 271: 1055–1067 (1993). J. W. Vanderhoff, E. B. Bradford, M. L. Tarkowski, J. B. Shaffer, and R. M. Wiley, Adv. Chem. Ser. 34:32 (1962). P.-Y. Jiang, Z.-C. Zhang, and M.-W. Zhang, J. Polym. Sci. Polymn. Chem. 34:695–699 (1996). P.-Y. Jiang, Z.-C. Zhang, and M.-W. Zhang, Macromolecules 29:6710–6716 (1996). D. J. Hunkeler and A. E. Hamielec, Polymer 32:2626– 2640 (1991). K. H. Reichert and W. Baade, Angew. Makromol. Chem. 124/125:361–381 (1984). S. K. Ghosh, M. Nazimuddin, and B. M. Mandal, Makromol. Chem. Rapid Commun. 13:583–586 (1992). H. Omidian, S. A. Hashemi, F. Askari, and S. Nafisi, J. Appl. Polym. Sci. 54:241–249 (1994). F. Askari, S. Nafisi, H. Omidian, and S. A. Hashemi, J. Appl. Polym. Sci. 50:1851–1855 (1993). B. Kriwet, E. Walter, and T. Kissel, J. Controlled Release 56:149–158 (1998). M. T. McKechnie, Proc. Conf. Emulsion Polym., London, June 1982, paper 3. X. Ge, Q. Ye, Z. Zhang, and G. Chu, J. Appl. Polym. Sci. 67:1005–1010 (1998). X. Ge, Q. Ye, X. Xu, Z. Zhang, and Q. Sun, Radiat. Phys. Chem. 50:253–258 (1997). M. B. Taylor, R. D. Gilbert, V. T. Stannett, and J. L. Williams, J. Appl. Polym. Sci. 53:1385–1390 (1994). J. Hernandez-Barajas and D. Hunkeler, Polymer 38: 5623–5641 (1997). F. Candau, Z. Zekhnini, F. Heatley, and E. Franta, Colloid Polym. Sci. 264:676–682 (1986). P. Buchert and F. Candau, J. Colloid Interface Sci. 136:527–540 (1990). A. Ohlemacher, F. Candau, J. P. Munch, and S. J. Candau, J. Polym. Sci. Polym. Phys. 34:2747–2757 (1996). S. Neyret and B. Vincent, Polymer 38:6129–6134 (1997). F. Candau, Z. Zekhnini, and J. Durand, Colloid Polym. Sci. 264:676–682 (1986). C. Holtzscherer, J. P. Durand, and F. Candau, Colloid Polym. Sci. 265:1067–1074 (1987).

Heterophase Polymerization in Inverse Systems 40. 41. 42. 43. 44. 45. 46. 47. 48. 49. 50. 51. 52. 53. 54. 55.

56.

57.

58.

59. 60. 61. 62. 63. 64. 65.

C. Graillat, C. Pichot, A. Guyot, and M. S. El-Aasser, J. Polym. Sci. Polym. Chem. 24:427–449 (1986). V. Glukhikh, C. Graillat, and C. Pichot, J. Polym. Sci. Polym. Chem. 25:1127–1161 (1987). F. Candau, M. Pabon, and J. Y. Anquetil, Colloid Surf. A Physicochem. Eng. Asp. 153:47–59 (1999). M. T. Carver, E. Hirsch, J. C. Wittmann, R. M. Fitch, and F. Candau, J. Phys. Chem. 93:4867–4873 (1989). F. Candau, Y. S. Leong, and R. M. Fitch, J. Polym. Sci. Polym. Chem. Ed. 23:193–214 (1985). J. Barton, Makromol. Chem. Rapid Commun. 12:675– 679 (1991). D. Benda, J. Snuparek, and V. Cermak, Eur. Polym. J. 33:1345–1352 (1997). P. A. Dresco, V. S. Zaitsev, R. J. Gambino, and B. Chu, Langmuir 15:1945–1951 (1999). Y. S. Leong and F. Candau, J. Phys. Chem. 86:2269– 2271 (1982). V. Vaskova, V. Juranicova, and J. Barton, Makromol. Chem. 191:717–723 (1990). C. Daubresse, C. Grandfils, R. Jerome, and P. Teyssie, Colloid Polym. Sci. 274:482–489 (1996). J. Barton and M. Stillhammerova, Angew. Chem. 237: 113–122 (1996). J. P. Fouassier, D. J. Lougnot, and I. Zuchowicz, Eur. Polym. J. 22:933–938 (1986). F. Yan, C. Zheng, X. Zhai, and D. Zhao, J. Appl. Polym. Sci. 63:747–754 (1998). A. Pross, K. Platkowski, and K.-H. Reichert, Polym. Int. 45:22–26 (1998). M. V. Dimonie, C. M. Boghina, N. N. Marinescu, M. M. Marinescu, C. I. Cincu, and C. E. Oprescu, Eur. Polym. J. 18:639–645 (1982). M. Dimonie, N. Marinescu, D. S. Vasilescu, O. Shaffer, H. Caldarar, A. Caragheorgheopol, and J. Languri, J. Macromol. Sci. Pure Appl. Chem. A29:277–296 (1992). J. W. Vanderhoff, F. V. Ditefano, M. S. El-Aasser, R. O’Leary, O. M. Shaffer, and D. G. Visioli, J. Dispersion Sci. Technol. 5:323–363 (1984). V. F. Kurenkov, T. M. Osipova, E. V. Kuznetsov, and V. A. Mtagchenkov, Vysokomol Soedin Ser. B 20: 647–650 (1978). Z. Liu and B. W. Brooks, J. Appl. Polym. Sci. 66: 2191–2197 (1997). J. Hernandez-Barajas and D. Hunkeler, Polym. Adv. Technol. 6:509–517 (1995). H. Ni and D. Hunkeler, J. Dispersion Sci. Techn. 18: 123–160 (1996). J. Hernandez-Barajas and D. J. Hunkeler, Polymer 38: 449–458 (1997). Y. S. Leong, G. Riess, and F. Candau, J. Chim. Phys. 78:279–284 (1981). S. Fengler and K.-H. Reichert, Angew. Makromol. Chem. 225:139–152 (1995). M. Dauben, K. H. Reichert, P. Huang, and J. Fock, Polymer 37:2827–2830 (1996).

497 66. 66a. 67. 68. 69. 70. 71. 72. 73. 74. 75. 76. 77. 78.

79. 80. 81. 82.

83. 84. 85. 86. 87. 88. 89. 90. 91.

B. Ray and B. M. Mandal, Langmuir 13:2191–2196 (1997). K. Landfester, M. Willert, M. Antonietti, Macromolecules 33:2370–2376 (2000). L. M. Gan, C. H. Chew, H. S. O. Chan, and L. Ma, Polym. Bull. 31:347–350 (1993). A. Hammouda, T. Gulik, and M. P. Pileni, Langmuir 11:3656–3659 (1995). N. Moumen, M. P. Pileni, and R. A. Mackay, Colloids Surf. A Physicochem. Eng. Asp. 151:409–417 (1999). K. Nagai, H. Satoh, and N. Kramoto, Polymer 34: 4969–4973 (1993). H. Kawaguchi, Y. Yamada, S. Kataoka, Y. Morita, and Y. Oktsuka, Polym. J. 23:955–962 (1991). J. P. Hoar and J. H. Schulman, Nature 152:102–104 (1943). J. H. Schulman, W. Stoeckenhuis, and L. Prince, J. Phys. Chem. 63:1677–1680 (1959). M. Antonietti, R. Basten, and S. Lohmann, Macromol. Chem. 196:441–466 (1995). J. O. Stoffer and T. Bone, J. Dispersion Sci. Technol. 1:37–54 (1980). J. O. Stoffer and T. Bone, J. Polym. Sci. Polym. Chem. Ed. 18:2641–2648 (1980). F. Candau, Y. S. Leong, G. Pouyet, and S. Candau, J. Colloid Interface Sci. 101:167–183 (1984). F. Candau, in Polymerization in Organized Media (C. Paleos, ed.), Gordon & Breach, Philadelphia, 1992, pp. 215–282. J. Sjoblom, R. Lindberg, and S. E. Friberg, Adv. Colloid Polym. Sci. 65:125–287 (1996). K. M. Lusvardi, K. V. Schubert, and E. W. Kaler, Ber. Bunsenges. Phys. Chem. 100:373–379 (1996). R. Strey and M. Jonstromer, J. Phys. Chem. 96:4537– 4542 (1992). J. S. Guo, E. D. Sudol, J. W. Vanderhoff, H. J. Yue, and M. S. El-Aasser, J. Colloid Interface Sci. 149: 184–196 (1992). B. Antalek, A. J. Williams, E. Garcia, and J. Texter, Langmuir 10:4459–4467 (1994). P. Becher, J. Colloid Interface Sci. 17:325–333 (1962). M. Schick, J. Colloid Interface Sci. 17:801–813 (1962). H. Schott, J. Colloid Interface Sci. 43:150–155 (1973). T. Kawai, K. Hamada, N. Shindo, and K. Kon-No, Bull. Chem. Soc. Jpn. 65:2715–2719 (1992). H. MacDonald, B. Bedwell, and E. Gulari, Langmuir 2:704–708 (1986). C. Holtzscherer and F. Candau, J. Colloid Interface Sci. 125:97–110 (1988). F. Candau and P. Buchert, Colloids Surf. 48:107–122 (1990). J. Hernandez-Barajaz and D. J. Hunkeler, Abstracts of Papers of the American Chemical Society 1993, 206: 127.

498 92. 93. 94. 95. 96. 97. 98. 99. 100. 101.

102. 103.

104.

105. 106. 107. 108.

109. 110. 111.

112. 113. 114.

115. 116. 117.

Landfester and Hentze F. Yan, C. Zheng, X. Zhai, and D. Zhao, J. Appl. Polym. Sci. 67:747–754 (1998). M. Antonietti, R. Basten, and F. Grohn, Langmuir 10: 2498–2500 (1994). S. Avramoitis, A. Xenakis, and P. Lianos, Prog. Colloid Polym. Sci. 100:286–289 (1996). S. Avramiotis, V. Bekiari, P. Lianos, and A. Xenakis, J. Colloid Interface Sci. 194:326–331 (1997). S. Backlund, M. Rantala, and O. Molander, Colloid Polym. Sci. 273:293–297 (1995). G. Voortmans, C. Jackers, and F. De Schryver, Macromolecules 21:1977–1980 (1988). C. A. Parker, Proc. R. Soc. A220:104 (1953). C. G. Hatchard and C. Parker, Proc. R. Soc. A235:516 (1956). K. Nagai, H. Satoh, and N. Kramoto, Polymer 34: 4969–4973 (1993). A. P. Full, J. E. Puig, L. U. Gron, E. W. Kaler, J. R. Minter, T. H. Mourey, and J. Texter, Macromolecules 25:5157–5164 (1992). L. M. Gan, C. H. Chew, S. C. Ng, and S. E. Loh, Langmuir 9:2799–2803 (1993). J. S. Guo, E. D. Sudol, J. W. Vanderhoff, and M. S. El-Aasser, J. Polym. Sci. Polym. Chem. 30:691–702 (1992). J. S. Guo, E. D. Sudol, J. W. Vanderhoff, and M. S. El-Aasser, J. Polym. Sci. Polym. Chem. 30:703–712 (1992). J. D. Morgan and E. W. Kaler, Macromolecules 31: 3197–3202 (1998). J. D. Morgan, K. M. Lusvardi, and E. W. Kaler, Macromolecules 30:1897–1905 (1997). A. Saenz de Buruaga, J. C. de la Cal, and J. M. Asua, J. Polym. Sci. Polym. Chem. 37:2167–2178 (1999). A. Saenz de Buruga, I. Capek, J. C. de la Cal, and J. M. Asua, J. Polym. Sci. Polym. Chem. 36:737–748 (1998). M. A. Chung, J. Adams, and J. Fuhrmann, Polym. Bull. 40:195–202 (1998). I. Lacik, J. Barton, and G. G. Warr, Macromol. Chem. Phys. 196:2223–2236 (1995). V. Vaskova, Z. Hlouskova, V. Juranikova, and J. Barton, Makromol. Chem. Macromol. Chem. Phys. 193: 1445–1449 (1992). J. Barton, J. Tino, Z. Hlouskova, and M. Stillhammerova, Polym. Int. 34:89–96 (1994). A. Saenz de Buruaga, J. de la Cal, and J. M. Asua, J. Appl. Polym. Sci. 72:1341–1348 (1999). A. Saenz de Buruga, I. Capek, J. C. de la Cal, and J. M. Asua, J. Polym. Sci. Polym. Chem. 36:737–748 (1998). Z. Zekhnini, Ph.D. thesis, Strasbourg University, 1986. I. Capek and P. Potisk, J. Polym. Sci. Polym. Chem. 33:1675–1683 (1995). A. Saenz de Buruaga, J. C. de la Cal, and J. M. Asua, J. Polym. Sci. Polym. Chem. 37:2167–2178 (1999).

118. 119. 120.

121. 122. 123. 124. 125. 126.

127.

128. 129. 130. 131. 132. 133. 134. 135.

136.

137. 138. 139.

140. 141. 142.

J. Barton, Polym. Int. 30:151–156 (1993). J. Barton, Makromol. Chem. Macromol. Symp. 53: 289–306 (1992). I. Janigova, K. Csomorova, M. Stillhammerova, and J. Barton, Macromol. Chem. Phys. 195:3609–3614 (1994). C. Pichot, Makromol. Chem. Macromol. Symp. 35/36: 327–347 (1990). K. Sakota and T. Okaya, J. Appl. Polym. Sci. 20: 1725–1733 (1976). R. S. Molday, W. J. Dreyer, A. Rembaum, and S. P. S. Yen, J. Cell Biol. 64:75–88 (1975). H. Tamai, M. Hasegawa, and T. Suzawa, J. Appl. Polym. Sci. 38:403–412 (1989). K. G. I. Nilsson, J. Immunol. Methods 122:273–277 (1989). J. H. Kim, M. Chainey, M. S. El-Aasser, and J. W. Vanderhoff, J. Polym. Sci. Polym. Chem. Ed. 27: 3187–3199 (1989). S. Kirsch, A. Doerk, E. Bartsch, H. Sillescu, K. Landfester, H. W. Spiess, and W. Maechtle, Macromolecules 32:4508–4518 (1999). F. Candau, Z. Zekhnini, and F. Heatley, Macromolecules 19:1895–1902 (1986). V. Vaskova, M. Stillhammerova, and J. Barton, Chem. Pap. Chem. Zvesti 48:355–361 (1994). J. M. Corpart, J. Selb, and F. Candau, Makromol. Chem. Macromol. Symp. 53:253–265 (1992). M. Antonietti, A. Briel, and S. Fo¨rster, J. Chem. Phys. 105:7795–7807 (1996). W. Baade and K. H. Reichert, Eur. Polym. J. 20:505– 512 (1984). J. Hernandez-Barajas and D. J. Hunkeler, Polymer 38: 437–447 (1997). N. O’Connor, L. J. Barker, and G. Ryles, U.S. Patent 5,200,448 (1993). G. Bognolo, in Industrial Applications of Surfactants (R. Karsa, ed.), Royal Society of Chemistry, Cambridge, 1990. V. F. Kurenkov, A. S. Verizhnikova, E. V. Kuznetsov, and V. A. Myagchenkkov, Izv. Vuz. Khim. Kh. Tekh. 25:221–226 (1982). D. Hunkeler and A. E. Hamielec, ACS Symp. Ser. 467:82–104 (1991). K. Platkowski, A. Pross, and K.-H. Reichert, Polym. Int. 45:229–238 (1998). W. Huebinger and K. H. Reichert, Polymer Reaction Engineering (K. H. Reichert and W. Geiseler, eds.), VCH, Berlin, 1989, p. 207. W. Baade and K. H. Reichert, Makromol. Chem. Rapid. Commun. 7:235–241 (1986). G. Visioli, Ph.D. thesis, Lehigh University, Bethlehem, PA, 1984. V. F. Kurenkov, T. M. Osipova, E. V. Kuznetsov, and V. A. Myagchenkow, Vysokomol. Soedin Ser. B20: 647–650 (1978).

Heterophase Polymerization in Inverse Systems 143. 144. 145. 146. 147. 148. 149. 150. 151. 152.

153. 154.

155. 156. 157. 158. 159.

S. K. Gosh and B. M. Mandal, Polymer 34:4287–4290 (1993). V. F. Kurenkov, Izv. Vuz. Khim. Technol. 29:92–95 (1986). J. Texter, L. E. Oppenheimer, and J. R. Minter, Polym. Bull. 27:487–494 (1992). Z. Liu and B. W. Brooks, Polymer 40:2181–2188 (1999). Z. Liu and B. W. Brooks, J. Polym. Sci. Polym. Chem. 37:313–324 (1999). K. Platkowski and K.-H. Reichert, Polymer 40:1057– 1066 (1999). C. Vu and J. Cabestany, J. Appl. Polym. Sci. 42:2857– 2869 (1991). H. Ni and D. Hunkeler, Polymer 38:667–675 (1997). F. A. Adamsky and E. J. Beckmann, Macromolecules 27:312–314 (1994). M. Z. Yates, M. L. O’Neill, K. P. Johnston, S. Webber, D. A. Canelas, D. E. Betts, and J. M. DeSimone, Macromolecules 30:5060–5067 (1997). S. R. Reddy, D. H. Melik, and H. S. Fogler, J. Colloid Interface Sci. 82:116–127 (1981). C. M. Miller, E. D. Sudol, C. A. Silebi, and M. S. ElAasser, J. Polym. Sci. Polym. Chem. Ed. 33:1391– 1408 (1995). K. Landfester, N. Bechthold, S. Fo¨rster, and M. Antonietti, Macromol. Rapid Commun. 20:81–84 (1999). H. Omidian, S. A. Hashemi, P. G. Sammes, and I. Meldrum, Polymer 40:1753–1761 (1999). K. H. Reichert and W. Baade, Angew. Macromol. Chem. 123/124:361–380 (1984). S. Fengler and K.-H. Reichert, Angew. Makromol. Chem. 225:139–152 (1995). M. Dauben, K. Patkowski, and K.-H. Reichert, Angew. Makromol. Chem. 250:67–83 (1997).

499 160. 161. 162. 163. 164. 165.

166. 167. 168.

169. 170. 171.

172. 173. 174. 175. 176.

M. Dauben, K. H. Reichert, P. Huang, and J. Fock, Polymer 37:2827–2830 (1996). H. Kawaguchi, K. Fujimoto, M. Saito, T. Kawasaki, and Y. Urakami, Polym. Int. 30:225–231 (1993). M. J. Snowden, P. Thomas, and B. Vincent, Analyst 118:1367 (1993). M. S. Wolfe, Polym. Mater. Sci. Eng. 61:398 (1989). S. Evani and G. D. Rose, Polym. Mater. Sci. Eng. 57: 477 (1987). D. Hunkeler and J. Hernandez-Barajas, in Polymeric Materials Encyclopedia (J. C. Salamone, ed.), Vol. 9, CRC Press, New York, 1996, pp. 3322–3333. S. Slomkowski, Prog. Polym. Sci. 23:815–874 (1998). C. Larpent and T. F. Tadros, Colloid Polym. Sci. 269: 1171–1183 (1991). C. Vauthier-Holtzscherer, S. Benabbou, G. Spenlehauer, M. Veillard, and P. Couvreur, S.T.P. Pharma. Sci. 1:109 (1991). E. Allemann, G. Gurney, and E. Doelker, Eur. J. Pharm. Biopharm. 39:173–191 (1993). P. A. Dresco, V. S. Zaitsev, R. J. Gambino, and B. Chu, Langmuir 15:1945–1951 (1999). M. Breulmann, H. Co¨lfen, H. P. Hentze, M. Antonietti, D. Walsh, and S. Mann, Adv. Mater. 10:237–241 (1998). P. Espiard, A. Revillon, A. Guyot, and J. E. Mark, ACS Symp. Ser. 492:387–404 (1992). N. T. Whilton, B. Berton, L. Bronstein, H. P. Hentze, and M. Antonietti, Adv. Mater. 11:1014–1018 (1999). P. Degobert and F. Henry, Polym. Adv. Technol. 6: 362–370 (1994). H.-Q. Xie, D. Tian, P. He, and J. Guo, J. Appl. Polym. Sci. 68:2169–2174 (1998). W. M. Winslow, J. Appl. Phys. 20:1137–1140 (1949).

24 Vesicular Polymerization JUTTA HOTZ and WOLFGANG MEIER

I.

University of Basel, Basel, Switzerland

INTRODUCTION

oration, or spontaneously, just by mixing micellar solutions of oppositely charged surfactants [7], to mention only the most common methods [6]. The amphiphilic molecules of the lipid bilayer of the vesicles or liposomes can be in a gel (or solidlike) phase or in a liquid crystalline (or fluid) state. In the low-temperature gel phase the individual molecules usually show orientational and positional ordering with, for example, good packing of the hydrocarbon chains, typically in an all-trans conformation. This phase melts at the phase transition temperature Tc into the less ordered liquid crystalline phase, with disordered hydrocarbon chains. This different degree of order has direct consequences for the mobility of the lipid molecules within the bilayer: it typically differs by about two orders of magnitude for the two different phases, e.g., the later diffusion coefficient being about 10⫺10 cm2 s⫺1 in the gel phase and about 10⫺8 cm2 s⫺1 in the liquid crystalline phase [8]. The dynamics of the lipid molecules in the bilayer and their phase behavior have, for example, a direct influence on the stability of the whole vesicle or the permeability of the lipid membrane [6]. The self-closed bilayer structure of vesicles can be regarded as a simple model for biological membranes that, similarly to the natural prototype, can serve as a permeability barrier to shield the aqueous core from the surrounding medium or can be used as a support matrix to embed membrane proteins. Moreover, vesicles or liposomes can also be loaded with various polar and nonpolar substances and used as a vehicle able to transport the entrapped substances across membranes and other hydrophobic barriers or even to perform targeted delivery. These unique properties have led to a multi-

Vesicles or liposomes are spherically closed lipid bilayers that enclose an aqueous core and are dispersed in water or an aqueous buffer (see Fig. 1 for a schematic representation). The bilayer is composed of individual lipid molecules, which typically consist of a water-soluble headgroup covalently attached to hydrophobic hydrocarbon chains. Because of this amphiphilic nature, the molecules form aggregates in water in which their hydrophobic tails are shielded as far as possible by the hydrophilic headgroups from the surrounding aqueous environment. Typically, lipid molecules show very low solubility in aqueous media, which—together with their molecular geometry— forces them into bilayer aggregates [1]. Usually phospholipids are the most common constituent of vesicles or liposomes. However, Kunitake and Okahata discovered in 1977 [2] that synthetic amphiphiles are also able to form bilayer membrane structures, and synthetic compounds, such as long-chain quaternary ammonium salts or even block copolymers, are finding increasing interest [3–5]. There exist many different methods for the preparation of vesicles and liposomes. The interested reader may find more details of the preparation of vesicles, for example, in Ref. 6, where this topic has been extensively reviewed. Vesicles can be formed, for example, by hydration of thin lipid films, extrusion of extended bilayer structures through pores of defined width, ultrasonification of lipid dispersions, detergent dialysis of lipid-detergent mixed micelles, injection of organic lipid solutions into water, reverse phase evap501

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Schematic presentation of an unilamellar vesicle.

tude of applications of vesicles and liposomes in various fields of science and technology, reaching from their use in basic studies on the shape of biological cells, membrane and membrane protein function [7], and chemical catalysis [9] or even as templates in biomimetic materials chemistry [10] to applications as drug delivery systems, medical diagnostics, transfection vectors, new hydrogels in cosmetics [11], or selfhealing paints [6]. However, the usually only very limited stability of the vesicles frequently represents a serious problem, especially for applications. It is well known that their stability can be significantly enhanced using their interactions with polymers [12] (see Fig. 2). In this context, so-called hydrophobically modified water-soluble polymers are of special interest. These polymers carry a low fraction of hydrophobic anchor groups along their hydrophilic polymer backbone. These anchor groups can, for example, be inserted into the lipid membrane of vesicles, thus immobilizing the polymer chains at the surface of the vesicle and leading to steric stabilization [13]. The so-called ‘‘Stealth liposomes’’ are perhaps the most famous example and have found applications as drug carriers in pharmacy [6,13]. Another possibility to stabilize lipid membranes and, in addition, to control the physical properties or the morphology of the vesicular system is their polymerization. This can be realized by modifying the membrane-forming lipids with polymerizable groups [12] or by dissolving conventional hydrophobic monomers in the lipid bilayer of the vesicle [14–19]. Beyond this, such polymerization in a two-dimensional fluid is also interesting from a theoretical point of view, e.g., the scaling behavior of the newly formed polymer chains within the restricted environment in the two-dimensional membrane [20,21], and can be used to prepare polymer particles with unusual structures and mor-

FIG. 2 Schematic presentation of several methods for stabilizing lipid vesicles. (From Ref. 12.)

phologies, such as polymer hollow spheres or quasitwo-dimensional polymers [19]. Studies of polymerized vesicles derived from polymerizable lipids were pioneered in the late 1970s and early 1980s [22–25], and this is still an active field of research. Polymerization of conventional hydrophilic or hydrophobic monomers in vesicle dispersions has attracted less attention, although their polymerization leads to interesting new materials with exceptional structures [19]. However, it is well known that hydrophobic substances can be solubilized to a certain degree in the hydrophobic part of lipid bilayers [26]. It is therefore probable that hydrophobic monomers can be polymerized in the interior of the lipid bilayer. In this case, the vesicle serves only as a template, determining the structure of the newly formed polymer, e.g., eventually a two-dimensional polymer which provides an internal scaffold of the bilayer membrane without being covalently attached to the lipid molecules. In this chapter we review the developments in the area of polymerization in vesicular structures. Because several reviews of the polymerization of reactive lipids in vesicles and liposomes have already appeared [12,27–32], we will focus mainly on some materials and polymer chemical aspects. We summarize the polymerization of polymerizable lipids and that of conventional monomers in vesicles separately to put some emphasis on the recent revival of the latter method.

Vesicular Polymerization

II.

POLYMERIZATION OF REACTIVE LIPIDS IN VESICLES

A.

General Aspects

Since the end of the 1970s and beginning of the 1980s [22–25] it has been well known that polymerizable groups can be incorporated in bilayer-forming lipids. Up to now, the polymerization of such reactive amphiphiles has been the most common method in the field of polymerization of vesicular structures. Synthetic procedures have been developed to prepare such amphiphilic monomers derived from nearly every naturally occurring or synthetic lipid. The polymerizable moiety can be localized anywhere along the molecular unit of the lipid, i.e., along the tail groups or attached to the hydrophilic headgroup [12] (see Fig. 3). For the headgroup-functionalized lipids the polymerizable group can be bound covalently or electrostatically as a counterion. The latter, i.e., the polymerization of reactive counterions, can be regarded as an interfacial polymerization whereby the vesicle surface serves as a template for the newly formed polyelectrolyte [33]. Some aspects of such systems (which can be regarded as intermediate between the vesicular polymerization of reactive lipids and that of conventional monomers) are discussed at the end of this section. Derivatization of lipids has been reported with a great variety of polymerizable groups, such as butadiene, styryl, diacetylene, vinyl, acryloyl, methacryloyl, or sorbyl, just to mention those most commonly used [12] (see Fig. 4). After formation of the vesicles, free radical polymerization is usually used to convert the reactive lipids into the corresponding polymers. The polymer chain reaction in the lipid bilayer of vesicles can be initiated using thermal, UV irradiation–mediated, or redox chemical generation of radical species [32]. Although the free radical polymerization is constrained to two dimensions because of the organized structure of the bilayer, the rather high mobility of the individual lipid molecules, especially in the liquid crystalline phase, permits the monomers to diffuse to the growing chain ends [8]. However, other polymerization reactions in vesicles have been performed. This is especially interesting in the context of the preparation of biodegradable polymerized vesicles that could be useful as drug carrier systems. Typical examples are the pH-triggered ring opening polymerization of lipoyl-functionalized lipids, which proceeds via S — S linkages [34] and the polycondensation of long-chain ␣-amino acid esters to polypeptide vesicles [35,36]. Interestingly, the bulk

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FIG. 3 Schematic presentation of the different locations of polymerizable groups in reactive lipids.

polymerization of ␣-amino acid esters is not possible. Obviously, the organized structure of the lipid bilayer leads to a rather high density of well-aligned reactive groups, which seems to be a basic requirement for polypeptide formation. Another case where the alignment of the polymerizable groups is also of crucial importance is the poly-

FIG. 4 Some representative examples of polymerizable groups that have been introduced in reactive lipids.

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merization of diacetylene lipids [25]. Whereas the free radical polymerization of the most reactive groups is possible in both the fluid, liquid crystalline phase and the solid-analogous gel phase of the bilayer structure, diacetylene lipids can be polymerized efficiently only in the higher ordered gel phase because of the wellknown topochemically controlled nature of the polymerization [37]. B.

Free Radical Polymerization of Reactive Lipids

To learn more about the mechanism of the polymerization in vesicles, it is necessary to perform kinetic studies and, hence, to investigate the influence of the monomer and the initiator concentration on the reaction kinetics. However, one essential point of polymerization in vesicular structures is that the monomers and the initiator (e.g., in the case of the hydrophobic AIBN) are constrained within the lipid bilayer and are not homogeneously distributed in the bulk, as in conventional solution polymerization. The polymerization occurs within the individual vesicles, which are essentially isolated from each other on the time scale of the experiment; i.e., molecular exchange does not play a role [38]. Variation of the monomer concentration within the vesicles can, therefore, be achieved only by incorporating nonpolymerizable, conventional lipids in the bilayers. The relative fraction of polymerizable lipid in the resulting two-dimensional solution can be used as a measure for the monomer concentration, which enters into the kinetics of the polymerization [38,39]. It has been shown that for low conversions the rate of polymerization shows the same concentration dependence as a conventional solution radical chain reaction, i.e., rp ⬀ [M][I]0.5. However, at higher conversion ratios, this kinetic behavior changes, leading to an rp ⬀ [M]2 relation and becoming independent of [I] [38]. This change has been attributed to a reduced termination rate relative to the propagation rate because of the reduced mobility of the growing polymer chains within the constrained environment of the bilayer. This can be expected to increase the lifetime of the reactive chain ends of the growing polymers, thereby lowering the probability for termination by bimolecular recombination or disproportionation of chains. The diffusion of the small initiator radical fragments within the bilayer is less hindered and, therefore, primary termination (i.e., the reaction of initiator fragments with the active chain ends) becomes more likely. In conventional solution polymerization in isotropic media, pri-

mary termination usually occurs at high initiator concentrations and/or in highly viscous solvents. This termination mechanism in the bilayers is also reflected in the observed dependence of the degree of polymerization on the monomer and initiator concentration. Whereas at low conversions the kinetic chain length depends on [M] and [I]⫺0.5 as in common solution polymerization, at high conversion ratios a molecular weight dependence scaling with [M]2 and [I]⫺1 has been reported [39]. The average degree of polymerization depends, as in conventional solution polymerization, on the relative stability of the propagating species. Degrees of polymerization ranging from 2 up to about 104 have been reported, depending on the mode of initiation, the phase structure of the bilayer, the type and location of the reactive group, and others [27–32]. In the case of photoinduced polymerization using short-wavelength UV light, a significant dependence of the polymer chain length on the irradiation time has been observed: polymer chain degradation is in competition with chain growth, leading to lower degrees of polymerization for longer irradiation times [40]. The overall rate of a thermally initiated free radical polymerization of the monomeric lipids has been shown to be quite similar to that of solution polymerization of the respective underlying conventional monomers [38]. However, the difference in the reactivity of different polymerziable groups, such as acryloyl and methacryloyl groups, seems to be ‘‘squeezed out’’ [38]. The highly ordered state in the bilayer has a major influence and minimizes the reactivity difference between the monomers. The influence of the state of order in the bilayer on the rate of polymerization is also reflected in investigations of the temperature dependence of the kinetics of a redox-initiated free radical polymerization [41]. Interestingly, despite the different mobility of the monomeric lipid molecules in the solidlike gel phase and the liquid crystalline phase of the lipid bilayer, only a very moderate difference in both the overall rate of polymerization and the degree of polymerization has been found for the respective phase structures [41]. Obviously, the lower mobility of the monomeric lipids in the gel phase compared with the liquid crystalline phase can be partly compensated. The reason may be that the all-trans conformation of the lipid tails in the gel phase leads to a more favorable orientation of the reactive groups with respect to the propagation reaction compared with the liquid crystalline phase. The polymerization of monomeric lipids in vesicles can also be performed in a cross-linking manner, de-


pending on the number of polymerziable groups per monomeric lipid [42]. Whereas the polymerization of lipids containing only one single reactive moiety typically leads to the formation of linear polymer chains, lipids bearing more than one reactive group generally yield covalently cross-linked polymer network structures. As a result of such a cross-linking polymerization, the whole vesicle or at least each half of the lipid bilayer of the vesicle is one single molecule, thus locking in the structure and the shape of the aggregate existing during the cross-linking reaction [30]. This leads to significantly different physical properties of the whole vesicle compared with linearly polymerized lipids. Such covalently cross-linked structures show stability of shape, solid-state properties such as elasticity, increased chemical stability, or drastically lowered solubility [30]. In isotropic cross-linking polymerizations, usually mixtures of mono- and bi- or higher functional monomers are used to prepare the three-dimensional polymer network structures. Usually only a very small fraction (often below 1 mol% in the monomer mixture) of the cross-linking agent is necessary to exceed the gel point, i.e., to form a system (vesicle)-spanning covalently cross-linked polymer network structure. In contrast to such monomers in isotropic media, the lipid monomers in a vesicle are confined to the quasi-two-dimensional fluid of the lipid bilayer. As a consequence, the crosslinking polymerization leads to a two-dimensional network structure. However, the geometric restrictions within the bilayer can be expected to have a significant influence on the cross-linking reaction. Indeed, investigations with mixtures of polymerizable lipids bearing one and two reactive groups at the end of their hydrophobic tails revealed that a substantially higher mole fraction of bifunctional monomer, i.e., about 30 mol%, is necessary to reach the gel point within the bilayer of the vesicles [43]. This inefficiency of the cross-linking reaction could be proved using different methods that are sensitive to the changes in the physical properties associated with the onset of gelation, e.g., the lateral diffusion behavior of a small molecule probe in the bilayer or the detergent solubilization of the vesicles [43] (see Fig. 5). The low effectiveness of the cross-linking reaction has been attributed to the preferred conformation of the lipid chains in the bilayer structure, which may favor side reactions such as intramolecular cyclization leading to network defects. Indeed, this seems to be supported by the fact that locating the reactive groups closer to the hydrophilic headgroups (which reduces the probability for such side reactions) increases sig-

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nificantly the efficiency of the cross-linking reaction; i.e., only about 10 mol% of the cross-linking agent is required for gelation [32]. C.

Properties of Polymerized Vesicles

An interesting aspect of the polymerization of reactive lipids in the bilayers of vesicles is that this method generally offers the possibility to engineer various physical properties of the whole vesicular systems. One example, is the aforementioned stabilization effect. The stability and flexibility of biological cell membranes usually arise from the coupling between the lipid bilayer and biopolymer networks, for example, the cytoskeleton [44], the spectrin network of erythrocytes [45,46], or the murein network of gram-negative bacteria [47,48]. In some sense, the polymerized lipids can be considered to mimic the role of such polymeric scaffolds, thereby stabilizing the synthetic membrane structure. Indeed, polymerized vesicles remain stable for months and are usually not destroyed by the addition of detergents or a few percent of an organic solvent (e.g., alcohol). In this context, vesicles stabilized by a cross-linking polymerization are an especially telling example: the cross-linked polymer network structure allows the vesicles to preserve their spherical shape, even in the absence of water [30]. In contrast to that, the lipid polymerization can also be used to produce controlled labile domains in the lipid membrane. This can be realized, for example, by polymerization of vesicle bilayers constituted from lipid mixtures consisting of reactive lipids and nonpolymerizable lipids. It is well known that such polymerizations may cause phase separation phenomena in the membrane; i.e., separation of the polymerized and the nonpolymerized lipids into enriched domains [30]. The more labile, nonpolymerized domains of such partially polymerized vesicles can be ‘‘uncorked’’ using detergents, solvent, or even enzymatic lysis to yield skeletonized vesicles consisting of a spherically closed polymerized bilayer with multiple holes [12] (Fig. 6). If such vesicular skeletons are charged and the holes are small enough, they can be plugged or unplugged with suitable ions upon variation of the pH. Such vesicles with a switchable permeability should be valuable systems for controlled release of trapped molecules [12,30]. Typically, polymerization of the lipids in the bilayer causes changes in both the bilayer fluidity and permeability and the phase behavior of the whole lipid membrane [12]. Whereas linear polymerization usually

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FIG. 5 Lateral diffusion coefficient in polymerized mixed mono- and bis-substituted lipid bilayers as a function of the mole fraction of bis-substituted lipid. (From Ref. 43.)

causes only quite moderate changes, the formation of a cross-linked polymer network structure leads to dramatic changes. For example, the lateral diffusion of low molecular bilayer components is substantially retarded by the cross-linking polymerization of reactive lipids. The bilayer permeability decreases upon formation of linear polymers in the membrane by a factor of about 2–5, and the formation of a two-dimensional polymer network structure decreases the permeability by at least two orders of magnitude [49,50].

FIG. 6 Raster electron micrograph of a skeletonized vesicle with multiple holes. (From Ref. 12.)

This allows, for example, maintaining a pH gradient of several units across completely polymerized vesicles [51], although protons or hydroxide ions are usually able to permeate almost instantaneously through conventional (unpolymerized) bilayer membranes [7]. Similarly, polymerization via the hydrophobic tails of the lipids normally changes the thermotropic phase behavior of the membranes. The bilayers often lose their fluid phase behavior upon polymerization because of the covalent linkage of the lipid tails. Polymerization via the hydrophilic headgroups generally leads to lower conformative restrictions for the lipid tails; consequently, in this case the gel-to-liquid crystalline phase transition of the bilayer is preserved [12]. An extremely interesting example of polymerization via the hydrophilic headgroups is the polymerization of reactive counterions. This polymerization can also be regarded as a ‘‘template polymerization’’ occurring at the interface of the vesicles, whereby the shape and dimensions of the vesicles are imprinted on the newly formed polymer [33]. The resulting polyelectrolytes are attached via electrostatic interactions to the vesicle surface, which led to the term ‘‘liposomes in a net’’ [12]. The polyelectrolyte chains (or the covalently crosslinked polyelectrolyte network structure) can be attached to the inner and outer surface of the vesicles or to one of these surfaces. The latter can be achieved, for


example, by ion exchanging the outer counterions with charged, polymerizable counterions and subsequently polymerizing them [12]. A similar polymerization of only the inner leaflet of the vesicle bilayer, but using covalently attached polymerizable moieties, has also been performed using ␤-nitrostyrene as the reactive group [52]. Interestingly, the permeability of polyelectrolyte-stabilized vesicles has been shown to be identical to those of the monomeric vesicles [12]. Consequently, the polymer provides in this case—similarly to the spectrin network in erythrocytes—just the physical stability of the membrane while the permeability behavior is determined by the lipid bilayer. As with the cross-linking polymerization of the reactive lipids themselves, it is possible to produce a twodimensional polymeric network at the surface of the vesicles using mixtures of reactive counterions bearing one or more than one polymerizable groups. Because of their cross-linked polymer network structure, these polymer particles are also able to retain their hollow sphere morphology even after removal of the vesicleforming lipid molecules [53]. The resulting so-called ghost vesicles are promising systems that could, eventually, serve as responsive nanocapsules for the encapsulation of pharmaceutically active substances. One interesting point in this context is that the mesh size of the polymer network structure controls the porosity of the polymeric membrane. Molecules having dimensions smaller than this mesh size should be able to pass the shell of the polymer particles without hindrance; molecules bigger than this mesh size should not be able to permeate through the polymer network.

III.

POLYMERIZATION OF CONVENTIONAL MONOMERS IN VESICLES

A.

General Aspects

In the first part, we have summarized some aspects of the polymerization of reactive lipids in vesicular structures. Characteristic of these systems is that the newly formed polymer chains or polymer network structures are usually covalently attached to the lipid bilayer. It is obvious that the covalent coupling must dramatically influence the structure and dynamics of the whole membrane. As already mentioned, this influence can be reduced to some extent if the polymer is attached via electrostatic interactions to the bilayer structure [12]. However, still another possibility is to produce conventional hydrophilic or hydrophobic polymers in the respective domains of the vesicles, which are bound to

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the vesicular structure simply by steric constraints and/ or hydrophobic interactions. Up to now, there exist only a few studies dealing with such polymerization of hydrophilic or hydrophobic monomers to the respective polymer structures within the hydrophilic or hydrophobic parts of lipid vesicles [14–19,54]. As mentioned before, vesicles or liposomes are able to solubilize hydrophobic substances to a certain degree [26]. Such compounds are usually dissolved in the hydrophobic part of the lipid bilayer. If such substances also carry polymerizable groups, their subsequent polymerization should lead to the formation of polymer chains entrapped in the interior of the membrane. In contrast to polymerizable lipids, the polymer chains are now simply dissolved within the alkane part of the bilayer forming lipids, and, hence, they have a minor influence on the overall physical properties of the membranes. Similarly, hydrophilic substances can be encapsulated in the aqueous core of vesicles [54]. Subsequent polymerization leads to the formation of hydrophilic polymer chains whose dimensions are directly determined by the monomer concentration and the dimensions of the enclosed water pool of the vesicles. This geometrical restriction is a direct consequence of the very low permeability of the lipid bilayer against the hydrophilic monomers, which prevents an intervesicular exchange of monomers on the time scale of the experiment. A cross-linking polymerization of, for example, a mixture of acrylamide and N,N⬘-methylenediacrylamide can be used to produce a hydrophilic polymer gel in the interior of the vesicle, similar to the cytoskeleton of biological cells [44]. The resulting polymer particles are a direct cast of the aqueous core of the vesicle and are able to preserve their shape and dimensions even after their isolation from the vesicles [54]. One special feature of vesicular polymerization of conventional hydrophilic or hydrophobic monomers is that the different compartments provided by the selfassembly of the lipid molecules generally serve only as a template that determine size and shape of the resulting polymers. Hence, it is possible to use nearly every natural or synthetic lipid without any modification. In most reported studies of vesicular polymerization of conventional monomers, usually synthetic lipids such as dioctadecyl dimethylammonium chloride (DODAC) or bromide (DODAB), sodium di-2-ethylhexyl phosphate (SEHP), or even spontaneously formed vesicles, prepared from mixtures of cationic and anionic surfactants [14–19], have been used (perhaps primarily for budget reasons). Also, any natural

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lipid would provide a suitable matrix. Moreover, a combination of polymerziable lipids and conventional monomers could be incorporated in the templating vesicles to yield hybrids with interesting new polymer structures (J. Hotz and W. Meier, to be published). B.

Swelling of Lipid Bilayers with Hydrophobic Monomers

In the following we will focus mainly on the polymerization of hydrophobic monomers such as styrene, divinyl benzene, or long-chain alkyl acrylates or alkyl methacrylates in vesicles. Such hydrophobic substances are usually dissolved within the hydrophobic part of the lipid bilayers. The usual polymerization procedure therefore requires, as a first step, the swelling of the vesicles with the hydrophobic monomers. This is usually performed by simply mixing an adequate amount of the water-insoluble monomer with a suspension of preformed vesicles and stirring this mixture until the monomer has dissolved [14–19]. In this context, it is, therefore, of crucial importance to know more about this swelling process. Of course, the incorporation of hydrophobic substances into lipid bilayers should not exceed a certain saturation concentration. Above this concentration the monomer is no longer homogeneously distributed within the bilayers, as has been shown for toluene in phospholipid vesicles at concentrations above the saturation value [55]. Moreover, exceeding this saturation concentration may also disrupt the whole bilayer structure, thus converting the system to a conventional emulsion or even leading to the formation of a separate monomer phase in the presence of intact vesicles. Generally, the degree of solvent uptake by the vesicles is restricted by the interfacial free energy of the bilayers. This has been shown by using a thermodynamic model based on classical Flory-Huggins theory, which allows the description of the equilibrium partitioning of hydrophobic solvents between water and phospholipid vesicles [56]. Although these findings provide a theoretical basis for the understanding of bilayer swelling and may even allow certain predictions concerning the saturation concentration of individual substances, experimental investigations are also required to provide information about the local distribution of monomers within the bilayers and the resulting physical properties of swollen lipid membranes. In this context, investigations of not only vesicles or freestanding lipid membranes (so-called black lipid membranes) [57] but also lyotropic liquid crystalline phases

[58] or even microemulsions [59,60] may yield valuable information. The swelling of the lipid bilayers can be expected to influence the phase behavior and the ultrastructure of the lipid membrane. It has been shown that, for example, long-chain alkanes are preferentially oriented parallel to the palisade layer of the lipid alkyl chains within the bilayer, thereby increasing the gel-to-liquid crystalline phase transition temperature [58]. In contrast, short-chain alkanes are accumulated in the central part, in the region between the two underlying lipid monolayers, thereby disturbing the alkyl chain orientation of the lipid molecules. This leads to a decrease of the phase transition temperature of the membrane [58]. Moreover, this difference in the locus of solubilization for long- and short-chain alkanes also provides an explanation for the decreasing saturation concentration of alkanes with increasing chain length [58]. It is obvious that the overall thickness of the lipid membranes has to increase upon solubilization of hydrophobic substances. However, the maximum swelling of the membrane typically leads to an increase from about 3 nm to about 5 nm [57,58]. This is, however, a negligible effect compared with the overall diameter of typical small unilamellar vesicles, which is about 100 nm. Usually, therefore, no dimensional changes of the underlying vesicles can, as long as the monomer concentration stays below the saturation concentration in the membranes, be detected upon swelling of such vesicles with monomer [14–19]. C.

Polymerization of Hydrophobic Monomers in Lipid Bilayers

The free radical polymerization of the hydrophobic monomers incorporated in the lipid membranes of vesicles can be initiated, similarly to the polymerization of reactive lipids, by ultraviolet (UV) irradiation or thermal or redox chemical radical generation. Like emulsion or microemulsion polymerization systems, these systems consist of at least three components, water, monomer, and surfactant or lipid. However, in vesicular systems, in contrast to the emulsions and microemulsions, no influence of the polymerization rate on the nature of the initiating species, e.g, hydrophilic or hydrophobic, has been detected [16]. The local monomer concentration is always very high in the interior of the vesicles because of the restricted volume within the hydrophobic part of the lipid bilayers. Moreover, the mobility of the individual monomer molecules is rather high compared with the alkyl chains of the lipid molecules, and obviously the


anisotropic environment within the bilayer induces a preferred molecular orientation of the monomers (and simultaneously of the reactive groups) that favors the polymerization reaction. As a consequence, the overall rate of polymerization has been shown always to be very high in vesicular polymerization [14,16]. The conversion from monomer to polymer can be followed, for example, by 1H nuclear magnetic resonance (NMR) or UV spectroscopy, depending on the monomer. The kinetics have been found to be similar to those of a homogeneous phase of polymerization or the polymerization of reactive lipids in vesicles with a rate dependence of rp ⬀ [M][I]0.5, whatever the initiating species is [16]. Obviously, in contrast to emulsion and microemulsion polymerization, in vesicular polymerization the intervesicular exchange (which would lead to a different dependence of the polymerization rate) plays only a minor role on the time scale of the reaction. This is also reflected in the observation that each vesicle contains only one polymer particle, whose size is directly related to that of vesicle [18,19]. Because of the rather low reaction volume in the compartmentalized structure of the system, the number of radical species entering the bilayer per time unit is quite low. As a result, the time for chain growth is rather high until termination occurs; i.e., polymers with a degree of polymerization of about 104 are typically found and the conversion of the chain reaction is always relatively high, always above 90% [14] (Fig. 7). Like the polymerization of reactive lipids carrying more than one polymerizable group, the polymerization of hydrophobic monomers in the lipid membrane can

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also be performed in a cross-linking manner. In contrast to the very inefficient cross-linking reaction to polymerizable lipids (see earlier), for the hydrophobic monomers in vesicle bilayers about 0.1 mol% of a bifunctional monomer is enough to exceed the gel point in the interior of the bilayer [19]. This can be shown, for example, by isolation of the resulting polymer particles from the lipid bilayer. Hence, the fraction of cross-linking agent necessary for gelation is quite similar to that of an isotropic cross-linking reaction [19]. In contrast to linear polymerization, which simply results in a hydrophobic polymer chain dissolved in a quasi-two-dimensional liquid, the cross-linking polymerization can be expected to lead to a polymer particle consisting of one single polymer molecule with the shape of a hollow sphere whose the inner and outer shape is directly controlled by the underlying vesicle (see Fig. 8 for a schematic representation). D.

Properties of Lipid Membranes with a Hydrophobic Polymer Scaffold

Because of the nearly two-dimensional geometry of the whole lipid bilayer, it is extremely difficult to visualize directly such a homogeneous polymer shell enclosed in the interior of the membrane and, hence, to get information about the localization of the newly formed polymer particles. However, electron microscopy and light scattering experiments on polymerized vesicle dispersions clearly show that the size and shape of the vesicles are not altered upon polymerization. Moreover, there are no separate polymer particles present in the

FIG. 7 Conversion of isodecyl acrylate during vesicular polymerization at 60⬚C. (From Ref. 16, reprinted by permission of John Wiley & Sons, Inc.)

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FIG. 8 Schematic presentation of the polymer hollow sphere formed upon cross-linking vesicular polymerization of hydrophobic monomers. The hollow sphere morphology is preserved even after extraction of the lipid.

system and the polymerized vesicles show a significantly increased lifetime and have been found to be stable against detergent lysis [14–19]. Taking into account all of these findings, they can be explained only by the fact that the newly formed hydrophobic polymer is indeed incorporated in the interior of the lipid bilayer. As already mentioned, one essential point of such systems is that the lipid molecules are not covalently attached to this polymer scaffold. As a result, their lateral mobility [14], the phase behavior [14], and even the permeability of the polymer-containing membranes [14,15] have been shown to undergo no significant changes compared with the polymer-free reference systems. This holds for both linear polymer chains and cross-linked polymer network structures [14], at least as long as the cross-linking density of the network structure is not too high, i.e., the mesh size of the network is large enough. The mechanical stabilization of the polymer scaffold containing bilayers has been demonstrated using planar lipid membranes as model systems [33]. Rupture of the membranes can be induced by carefully applying single electric field pulses across the membrane. The critical voltage causing the breakdown of the membrane provides direct information about the membrane’s mechanical stability [61]. This voltage has been shown to increase by a factor of about 5 in the presence of the hydrophobic polymer scaffold, thus reflecting a considerable mechanical stabilization [33]. This stabilization is also reflected by the fact that polymer-containing vesicles could be directly visualized using atomic force microscopy in the liquid tapping mode [17]. This method can usually not be used with unpolymerized vesicles because of their high fragility.

E.

Properties of Vesicle-Templated Polymer Particles

In the context of membrane stabilization as well as with respect to possible applications of the resulting hollow polymer particles, it is essential to know more about the structure and behavior of the polymer scaffold in the membrane. Only if the quasi-two-dimensional polymer network is distributed homogeneously within the membrane of a vesicle does the cross-linking polymerization lead to a spherically closed shell. Otherwise, only fragments should be formed. However, it was shown that the structure of the polymer itself could be successfully visualized [18,19]. Whereas cryogenic transmission electron microscopy on polystyrene in DODAB vesicles clearly shows a phase separation within the lipid bilayer leading to a so-called parachute-like morphology (i.e., small spherical polymer particles linked to the vesicle bilayers [18] in the respective DODAC-alkylmethacrylate system), confocal laser scanning microscopy (CLSM) and scanning electron microscopy (SEM) investigations provide evidence for a homogeneously closed polymer hollow sphere morphology [19] (Fig. 9). The differences between these two systems probably arise from the fact that the alkyl chain milieu of the lipid bilayer represents a poor solvent for polystyrene and poly(alkyl methacrylates) show better compatibility. Moreover, styrene is a good solvent for poly(styrene), and hence the monomer can be expected to be taken up by the nascent polymer particles. In contrast, alkyl methacrylates are a poor solvent for their corresponding polymers and consequently the growing polymer will preferentially form a compact polymer core in the center of the monomer-swollen hydrophobic part of the lipid


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FIG. 9 Confocal laser scanning micrograph of a polymer hollow sphere prepared in a giant vesicle. (From Ref. 19.)

bilayer. Similar arguments have been successfully applied to model the chain length and particle size distribution of styrene and alkyl methacrylate microemulsion polymerization [59,60]. Another difference between the two systems arises from the relative monomer concentrations. Whereas a polymer hollow sphere morphology of poly(alkyl methacrylates) was reported for molar ratios of monomer to lipid smaller than 1 [19], in the styrene-DODAB system this ratio was 2 [18]. This is also supported by the observation of phase separation within the lipid bilayers upon solubilization of high concentrations of toluene in dipalmitoylphosphatidylcholine vesicles, which led to morphologies very similar to that of the vesicular parachutes [55] (Fig. 10). An interesting aspect of the formation of especially cross-linked polymer particles in vesicular dispersions arises from the fact that—in contrast to linear polymers—they should be able to retain their structure even after their isolation from the lipid matrix. This has been shown for cross-linked poly(alkyl methacrylates) by CLSM, SEM, and light scattering investigations [19]. Although the particles contract considerably after their isolation from the lipid membrane, they preserve their spherical shape. Their dimensions remain, however, always directly proportional to those of the underlying vesicles [19] (Fig. 11). This is not surprising because the polymer chains can be expected to be forced into a nearly two-dimensional conformation in

FIG. 10 Micrograph (obtained by combined phase contrast and fluorescence microscopy) of the phase separation induced by polymerization of styrene/divinyl benzene (molar ratio 1:1) in a giant dimyristoyl phosphatidylcholine (DMPC) vesicle. The bright spots in the membrane region are the phase-separated polymer particles. (Courtesy of E. Bru¨ckner and H. Rehage.)

FIG. 11 Radius of polymer particles Rpolymer as a function of the radius of the templating vesicles Rvesicle-polymer. (From Ref. 19.)

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the interior of the lipid membrane. After their liberation from the membrane, the polymer chains can gain entrophy by adopting a three-dimensional conformation. To do this, such spherically closed polymer shells have to shrink and the thickness of their shells increases. Up to now it has, however, not been fully clarified why the polymers retain their spherical shape (without collapsing) even in the dry state. However, similar observations with polymerized liposomes [62] and the results of computer simulations on two-dimensional polymers [21] (where it has been shown that the socalled flat phase is the stable state of such polymers) seem to support these observations. Polarizing microscopy investigations of polymer particles obtained by polymerization in giant vesicles show that the shells of these polymer hollow spheres are birefringent in the dry state. This birefringence vanishes upon swelling the polymer with organic solvents such as toluene. Obviously, the polymer backbone of the pure polymer adopts an ordered conformation. One possibility would be an accordion-like folding of the polymer chains normal to the surface of the sphere (J. Hotz and W. Meier, to be published). The extent of the observed contraction of the particles depends sensitively on the cross-linking density of the polymer network structure. The contraction increases with increasing cross-linking density, showing the same scaling behavior as branched polymers upon variation of their number of branches [19]. For the highest cross-linking densities the particles contract to about 1/10 of the original size of the templating vesicles. Consequently, the overall shell thickness of the pure polymer hollow spheres increases by a factor of up to about 100. Detailed light scattering investigations of the behavior of such polymer hollow spheres in solution seem to reflect a transition from the hollow spheres to the behavior of branched polymers with decreasing cross-linking density (J. Hotz and W. Meier, to be published). Although size and shape of the resulting polymer particles are directly determined by the templating vesicles, the polymer scaffold can be modified rather easily using conventional chemical reactions. It has been shown, for example, that polymer hollow spheres made from poly(styrene) can be converted into water-soluble polyelectrolyte hollow spheres by sulfonation (polyanionic hollow spheres) or by reaction with chloro-dimethyl ether and subsequent quaternization with trimethyl amine (polycationic hollow spheres). Similarly, the saponification of poly-tert-butylacrylate leads to (also polyanionic) poly(acrylic acid) hollow spheres or polymerization of N-isopropylacrylamide in vesicles

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to poly(N-isopropylacrylamide) (PNIPAM) hollow spheres [63]. An extremely interesting aspect that all of the preceding examples of such water-soluble hollow spheres have in common arises from their reversible pH-, electrolyte concentration–, or temperature-dependent swelling. The dimensions of poly(acrylic acid) hollow spheres, for example, change considerably with variation of the pH of the solution, analogous to the coil extension observed for linear poly(acrylic acid) chains or poly(acrylic acid)-based gels [63,64]. At low pH (3 M NaCl). The hydrodynamic layer thickness (␦) scales with the electrolyte concentration (cs): ␦ ⬀ c⫺s␣. According to a theory of Pincus [93], the exponent ␣ is 1/5 provided that ␦ is much larger than the particle radius (R). In a series of experiments with polystyrene model latexes it was found [20,208,209] that ␣ depends on the ratio ␦/R. For ␦/R > 0.7 the theoretically predicted value 1/5 for ␣ was determined. For larger particles (␦/R < 0.7), ␣ values of 1/10 were obtained [209]. If the degree of sulfonation of the polyelectrolyte block is about 50%, the adsorption pattern changes completely. The polymer is still water soluble and a very efficient stabilizer because of multiple adsorption points leading to so-called ringlet adsorption patterns [208]. However, if the stabilizer concentration is higher than a critical value the hydrophobic points along one chain can adsorb on different particles, leading to aggregate formation [20] and bridging flocculation. In contrast to the porcupine particles, the ringlet particles are very sensitive to added electrolyte. The coagulation concentration with NaCl is in the range of some 10 mM, and consequently it is advisable to use nonionic initiators during the polymerization. It is noteworthy that it is possible to achieve a ringlet adsorption behavior with any kind of a statistical copolymer consisting of hydrophilic and hydrophobic segments. Thus, a partly sulfonated polystyrene [20], a partly quaternized poly(4-vinyl pyridine) [209], and a partly sulfonated poly(butadiene) or poly(isoprene) (K. Tauer et al., submitted) are very efficient stabilizers in emulsion polymerization as long as nonionic initiators are used. Partly sulfonated poly(butadiene) and poly(isoprene) represent reactive polymeric surfactants as they will be grafted to the particles via the remaining double bonds. Furthermore, the hydrophobic parts of these reactive polymeric surfactants can easily find the equilibrium configuration in the adsorbed state because of the low glass transition temperature. Note that the stabilizing efficiency of the ringlet-type polymeric surfactants per surfactant weight is as high as for conventional lowmolecular-weight, ionic surfactants. Of course, the efficiency per stabilizer molecule is much higher. A single molecule of a 50% sulfonated polystyrene with a number average molecular weight of 40,000 g mol⫺1 (before the sulfonation) is able to stabilize a polystyrene particle about 15 nm in diameter [209].

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The synthesis and application as stabilizer in emulsion polymerization of styrene initiated with KPS of a poly(styrene sulfonate)-b-polystyrene are described in Ref. 210. The block copolymer was prepared by nitroxide-mediated controlled radical polymerization and had a composition of 11–12 styrene units and 30–31 styrene sulfonate units. The same controlled radical polymerization method was used to prepare cationic amphiphilic block copolymers starting from poly(vinyl benzyl chloride)-b-polystyrene and subsequent quaternization with trimethyl alkyl amine [211]. Latexes with high surface charge densities have been prepared by batch emulsion polymerization of styrene initiated with H2O2. Depending on the amount of block copolymer stabilizer, a surface charge density of up to 161 ␮C cm⫺2 has been obtained for 16.6% stabilizer relative to the monomer weight. The particle size is smaller the higher the stabilizer concentration and the smaller the number of styrene units in the stabilizer for a given cationic block length. The lowest stabilizer concentration reported is 5% relative to the monomer weight and hence much higher than in the case of the poly(ethyl ethylene)-bpoly(styrene sulfonate) stabilizers [20,208]. By copolymerization of vinyl acetate and N-vinyl formamide and subsequent two-step hydrolysis, a PVAL-co-poly(vinyl amine) was prepared and used as stabilizer for styrene emulsion polymerization [212]. The resulting latexes have a cationic net charge although the polymerization was started with persulfate initiator. A further class of polymeric stabilizers comprises polymers prepared from surface-active monomers by either homopolymerization or copolymerization leading to so-called polysoaps. With the keyword ‘‘polysoap’’ numerous papers can be found in the scientific literature over the last 5 years [77,213–235], but only two (to the best of our knowledge) deal with the utilization of polysoaps as stabilizers in emulsion polymerization [17,235]. In a comprehensive study, different cationic polysoaps have been employed in a semibatch styrene emulsion polymerization started either with a cationic initiator (2,2⬘-dimethyl-2,2⬘-axo-Nbenzylpropionamidine) hydrochloride or with KPS [17]. Compared with the cationic initiator, KPS can lead to some trouble during the polymerization due to electrostatic interactions. The following polysoaps have been investigated: a homopolymer of poly(((methacryloyloxy)undecyl)-N,N⬘-dimethylamino-N-2-hydroxyethyl ammonium bromide), a copolymer of ((methacryloyloxy)ethyl)-N,N⬘-dimethyl-N-decyl ammonium bromide, and ((methacryloyloxy)ethyl)trimethyl ammonium bro-

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mide, a copolymer of ((methacryloyloxy)ethyl)-N,N⬘dimethyl-N-undecyl ammonium bromide and ((methacryloyloxy)ethyl)trimethyl ammonium bromide. The copolymers investigated were different with respect to the hydrophobic-hydrophilic composition. If the hydrophilic-hydrophobic balance in the polysoap molecule is in a proper range (i.e., the content of the hydrophobic component is higher than a certain critical value), emulsion polymerization results in stable latexes with a much higher surface tension compared with the case with classical low-molecular-weight surfactants.

IV.

CONCLUSIONS

Many studies have been made of synthesis of polymerizable surfactants as well as their use in various processes of heterophase polymerization (chiefly emulsion polymerization). Recent studies have stressed the associated benefits. The latexes produced are more stable with electrolyte addition, they are more stable under shear, and they are more robust after being subjected to freezing. Further, when used in the preparation of film-forming latexes, polymerizable surfactants yield various improvements in the film properties (mainly the blocking properties) and in the behavior of the films in the presence of water. This last benefit seems to be a very constant property of the introduction of reactive surfactants in the polymerization recipes. A further example of this property is shown in Fig. 6 of Ref. 1, where film samples, aged for 30 days, were immersed in water for 50 days. Films produced using styrenic polymerizable block copolymer surfactants maintain their dimension (length) much better than those derived from similar but nonreactive dispersants. In addition, the former films remain more cohesive than the latter, which are very fragile after the immersion treatment. However, an explanation of these improved properties is far from complete, and much more work is needed. A study of the concentration profile of surfactant within such films should be a great help in explaining the beneficial behavior in the presence of water. It will be useful to determine whether there are hydrophilic domains within such films and whether there is a trend for migration of the surfactant toward the film surface. Such migration might interfere with the adhesive properties of the surface. It is known that the latex stability is very dependent on the structure of the polymerizable surfactant (HLB balance, reactivity of the polymerizable group), but systematic analysis of these structural features has not yet been carried out. Finally, the optimization of a rec-

ipe using surfmers for a particular application remains a very empirical task, and that may explain why this class of surfactants has not yet been used for any important market, even if a few products can be obtained on a commercial basis. Polymeric surfactants are a fascinating class of stabilizers, as they combine different stabilization mechanisms in one molecule, such as electrostatic and steric or electrostatic, steric, and depletion. Besides variations in the chemistry of the hydrophobic and hydrophilic parts, the arrangement of these segments along the polymeric chain, the degree of polymerization, and the molecular weight distribution offer additional possibilities for fine tuning various properties. The different examples illustrate the enormous versatility of applications of polymeric surfactants and illustrate the potential of this class of stabilizers. Nevertheless, one may get the impression that especially for emulsion polymerization, the application of polymeric stabilizers, chiefly in the case of polymers with charged blocks, is just in an initial stage of basic research. The authors believe that the potential of polymeric stabilizers is today far from being completely explored or understood, as almost each day modern chemical methods allow access to new structures with improved performance and the possibilities to create polymers with new structures are almost unlimited.

REFERENCES 1.

2. 3. 4. 5. 6. 7. 8. 9. 10. 11. 12.

Q. Soula, A. Guyot, N. Williams, J. Grade, and T. Blease, J. Polym. Sci. A Polym. Chem. 37:4205 (1999). A. Guyot and A. Goux, J. Appl. Polym. Sci. 65:2289 (1997). S. Onodera, S. Yamamoto, T. Tamai, and H. Takahashi, Jpn. Patent 06239908 (1994). R. H. Tang and P. M. Chakrabarti, U.S. Patent 5296627 (1994). K. Yokota, A. Ishihara, and H. Shinike, U.S. Patent 5324862 (1994). K. Kinoshita, Jpn. Patent 94/49108 (1994). S. Usai, Jpn. Patent 94/65551 (1994). J. Biale, U.S. Patent 5326814 to Rhom & Haas (1994). D.E. Patent 3239527 to Rhom GmBh (1984). G.B. Patent 1427789 to Bayer AG (1982). I. M. Kusters, R. H. Napper, R. G. Gilbert, and A. L. German, Macromolecules 25:7043 (1992). A. Guyot, K. Tauer, J. M. Asua, S. Van Es, C. Gauthier, A. C. Helgren, D. C. Sherrington, A. MontoyaGoni, M. Sjo¨berg, O. Sindt, F. Vidal, M. Unzue´, H. A. S. Schoonbrood, E. Schipper, and P. Lacroix-Desmazes, Acta Polym. 50:57 (1999).

Polymerizable and Polymeric Surfactants 13. 14. 15. 16. 17. 18. 19.

20. 21. 22. 23. 24.

25. 26.

27. 28. 29. 30. 31.

32.

33. 34. 35.

36.

37.

C. C. Fifield, Ph.D. thesis, University of Connecticut, Univ. Microfilms Int. 5869, Ann Arbor MI, 1992. F. Vidal, J. Guillot, and A. Guyot, Colloid Polym. Sci. 273:999 (1995). F. Vidal and A. Guyot, New J. Chem. 19:1081 (1995). E. Rizzardo, G. F. Meijs, and S. H. Thang, U.S. Patent 5.385.996 (1995). D. Cochin, A. Lawschewski, and F. Nallet, Macromolecules 30:2278 (1997). I. Pirma and J. R. Lenzotti, British Polymer J. 21:45 (1989). I. Pirma, Polymer surfactants and polymer colloid stabilization, in The Polymeric Materials Encyclopedia, CRC, New York, cd rom, 1996. K. Tauer, M. Antonietti, L Rosengarten, and H. Muller, Macromol. Chem. Phys. 199:897–908 (1998). A. Guyot and K. Tauer, Adv. Polym. Sci. 111:45 (1994). K. Tauer, Polym. News 20:342 (1995). A. Guyot, Curr. Opin. Colloid Interface Sci. 1:580 (1996). K. Tauer, in Polymeric dispersions: Principles and Applications (J. M. Asua, ed.), Kluwer Academic Publishers, Dordrecht, 1997. J. M. Asua and H. A. S. Schoonbrood, Acta Polym. 49:671 (1998). A. Guyot, in Novel Surfactants (K. Holmberg, ed.), Surface Science Series, Vol. 74, Marcel Dekker, New York, 1998. B. W. Greene and D. P. Sheetz, J. Colloid Interface Sci. 32:90, 96 (1970). B. W. Greene and F. L. Saunders, J. Colloid Interface Sci. 33:393 (1970). S. L. Tsaur and R. M. Fitch, J. Colloid Interface Sci. 115:450 (1987). J. L. Guillaume, C. Pichot, and J. Guillot, J. Polym. Sci. A Polym. Chem. 28:137 (1990). M. B. Urquiola, V. L. Dimonie, E. D. Sudol, and M. S. El Aasser, J. Polym. Sci. A Polym. Chem. 30:2619, 2631 (1992). M. B. Urquiola, E. D. Sudol, V. L. Dimonie, and M. S. El Aasser, J. Polym. Sci. A Polym. Chem. 31:1403 (1993). R. H. Ottewill and R. Satguranathan, Colloid Polym. Sci. 265:845 (1987). R. H. Ottewill and R. Satguranathan, Colloid Polym. Sci. 266:547 (1988). A. L. Palluel, M. J. Westby, C. W. Bromley, S. P. Davies, and A. J. Backhouse, Makromol. Chem. Macromol. Symp. 35/36:509 (1990). H. A. S. Schoonbrood, M. J. Unzue´, O. J. Beck, J. M. Asua, A. Montoya-Goni, and D. C. Sherrington, Macromolecules 30:6024 (1997). H. A. S. Schoonbrood, M. J. Unzue´, J. I. Amalvy, and J. M. Asua, J. Polym. Sci. A Polym. Chem. 35:2561 (1997).

571 38. 39. 40. 41. 42. 43. 44. 45. 46. 47. 48. 49.

50. 51. 52.

53.

54. 55. 56. 57. 58. 59. 60. 61. 62. 63. 64. 65.

K. H. Goebel and K. Sta¨lher, Polym. Adv. Technol. 6: 452 (1994). H. A. S. Schoonbrood and J. M. Asua, Macromolecules 30:6034 (1997). R. H. Ottewill and R. Satguranathan, Colloid Polym. Sci. 273:379 (1995). F. Thenoz, O. Soula, and A. Guyot, J. Polym. Sci. A Polym. Chem. 37:2251 (1999). T. Hamaide, A. Zicmanis, C. Monnet, and A. Guyot, Polym. Bull. 33:133 (1994). O. Sindt, C. Gauthier, T. Hamaida, and A. Guyot, J. Applied Polymer Sci. 77:2768 (2000). S. Abele, C. Graillat, A. Zicmanis, and A. Guyot, Polym. Adv. Technol. 10:301 (1999). S. Abele, A. Zicmanis, C. Graillat, C. Monnet, and A. Guyot, Langmuir 15:1033, 1045 (1999). S. Abele, C. Gauthier, C. Graillat, and A. Guyot, Polymer. 41:1147 (2000). O. Soula and A. Guyot, Langmuir 15:7956 (1999). O. Soula, R. Petiaud, M. F. Llauro, and A. Guyot, Macromolecules 32:6938 (1999). S. Braun, H. O. Kalinowski, and S. Berger, 100 and More Basic Experiments, VCH, New York, 1996, pp. 170, 173, 390. B. Charleux and C. Pichot, Polymer 34:195 (1993). B. Charleux, C. Pichot, and M. F. Llauro, Polymer 34: 4353 (1993). M. T. Charreyre, P. Boulanger, C. Pichot, B. Mandrand, and M. F. Llauro, Makromol. Chem. 194:117 (1993). M. T. Charreyre, P. Boulanger, T. Delair, B. Mandrand, and C. Pichot, Colloid Polym. Sci. 271:668 (1993). J. Revilla, A. ElAı¨ssari, C. Pichot, and B. Gallot, Polym. Adv. Technol. 6:455 (1994). K. Nagai, T. Ohashi, R. Kaneko, and T. Tanigushi, Colloid Surf. Phys. Chem. Asp. 153:133 (1999). M. Dreja and B. Tieke, Macromol. Rapid Commun. 17:825 (1996). M. Dreja, W. Pickout-Hintzen, and B. Tieke, Macromolecules 31:272 (1998). C. Larpent, E. Bernard, J. Richard, and S. Vaslin, Macromolecules 30:354 (1997). C. Favero, C. Graillat, and A. Guyot, Macromol. Symp. 150:235 (2000). C. S. Chem and T. J. Chen, Colloid Polym. Sci. 275: 546, 1060 (1997). K. E. J. Barrett (ed.), Dispersion Polymerization in Organic Media, Wiley, New York, 1975. C. K. Ober, Makromol. Chem. Macromol. Symp. 35/ 36:87 (1990). Y. Almog, S. Reich, and M. Levy, Br. Polym. J. 131 (1982). S. Chen, E. D. Sudol, and M. S. ElAasser, J. Polym. Sci. Polym. Chem. 32:1087 (1994). S. Kobayashi, H. Uyama, J. H. Choi, and Y. Matsumoto, Polym. Int. 30:265 (1993).

572 66. 67. 68. 69. 70. 71. 72. 73. 74. 75.

76. 77. 78. 79. 80. 81.

82.

83. 84. 85.

86. 87. 88. 89. 90. 91. 92. 93.

Guyot and Tauer S. Kobayashi, H. Uyama, S. W. Lee, and Y. Matsumoto, J. Polym. Sci. A Polym. Chem. 31:3133 (1993). S. Kawaguchi, M. A. Winnik, and K. Ito, Macromolecules 28:1159 (1995). A. J. Paine, Macromolecules 23:3109 (1990). P. Lacroix-Desmazes and A. Guyot, Polm. Bull. 37: 183 (1996). P. Lacroix-Desmazes and A. Guyot, Colloid Polym. Sci. 274:1129 (1996). D. A. Canelas, D. E. Betts, and J. M. De Simone, ACS Polym. Preprints 35:628 (1997). D. Cochin, R. Zana, and F. Candau, Macromolecules 26:5755, 5765 (1993). F. Candau and R. Zana, Encycl. Polym. Mater. 6:4287 (1996). V. Vaskova, D. Renoux, M. Bernard, J. Selb, and F. Candau, Polym. Adv. Technol. 6:441 (1995). J. Selb and F. Candau, Association Polymers in Aqueous Solution, ACS Symp. Ser. (J. E. Glass, ed.), 765, 2000, p. 95–108. K. Sta¨hler, J. Selb, P. Barthelemy, B. Pucci, and F. Candau, Langmuir 14:4765 (1998). K. Sta¨hler, J. Selb, and F. Candau, Colloid Polym. Sci. 276:860 (1998). K. Sta¨hler, J. Selb, and F. Candau, Langmuir, 15:7565 (1999). D. H. Napper, Polymeric Stabilization of Colloidal Dispersions, Academic Press, London, 1983. A. Bringer, E. Eisenriegler, F. Schlesener, and A. Hanke, Eur. Phys. J. B 11:101–109 (1999). J. W. Goodwin, in Colloid Science (D. H. Everett, ed.), Vol. 2, The Chemical Society, London, 1976, pp. 246– 293. R. H. Ottewill, in Emulsion Polymerization and Emulsion Polymers (P. A. Lovell and M. S. El-Aasser, eds.), Wiley, New York, 1976, pp. 59–121. F. Caruso, H. Lichtenfeld, E. Donath, and H. Mo¨hwald, Macromolecules 32:2317–2328 (1999). F. Caruso, E. Donath, and H. Mo¨hwald, J. Phys. Chem. B 102:2011–2016 (1998). E. Donath, G. B. Sukhorukov, F. Caruso, S. A. Davis, and H. Mo¨hwald, Angew. Chem. Int. Ed. 37:2201– 2205 (1998). F. Caruso, R. A. Caruso, and H. Mo¨hwald, Science 282:1111–1114 (1998). D. G. Kurth, F. Caruso, and C. Schu¨ler, Chem. Commun. 1579–1580 (1999). F. Caruso and H. Mo¨hwald. J. Am. Chem. Soc. 121: 6039–6046 (1999). F. Caruso, Chem. A Eur. J. 6:413–416 (2000). F. Lux, Synth. Met. 102:1190–1193 (1999). S. Creutz and R. Jerome, Langmuir 15:7145–7156 (1999). I. Piirma, Polymeric Surfactants, Marcel Dekker, New York, 1992. P. Pincus, Macromolecules 24:2912–2919 (1991).

94.

95.

96. 97. 98. 99. 100. 101. 102. 103. 104.

105. 106. 107. 108. 109. 110. 111.

112.

113. 114. 115. 116. 117. 118. 119. 120.

E. A. Grulke, in Encyclopedia of Polymer Science and Engineering (J. I. Kroschwitz, exec. ed.) Vol. 16, New York, 1989, pp. 443–473. H. G. Yuan, G. Kalfas, and W. H. Ray, J. Macromol. Sci. Rev. Macromol. Chem. Phys. C31:215–299 (1991). V. Macho, M. Fabini, M. Rusina, S. Bobula, and M. Harustiak, Polymer 35:5773–5777 (1994). V. Macho, M. Fabini, M. Rusina, S. Bobula, and M. Harustiak, Chem. Pap. Chem. Zv. 49:102–105 (1995). M. Zerfa and B. W. Brooks, J. Appl. Polym. Sci. 60: 2077–2086 (1996). M. Zerfa and B. W. Brooks, J. Appl. Polym. Sci. 65: 127–134 (1997). K. D. Prince, Plast. Rubber Compos. 28:105–108 (1999). D. H. Lee, J. Chem. Eng. Jpn. 32:97–103 (1999). F. Lerner and S. Nemet, Plast. Rubber Compos. 28: 100–104 (1999). E. Vivaldolima, P. E. Wood, A. E. Hamielec, and A. Penlidis, Ind. Eng. Chem. Res. 36:939–965 (1997). R. Olayo, E. Garcia, B. Garciacorichi, L. Sanchezvazquez, and J. Alvarez, J. Appl. Polym. Sci. 67:71–77 (1998). H. K. Mahabadi, T. H. Ng, and H. S. Tan, J. Microencap. 13:559–573 (1996). G. Polacco, M. Palla, and D. Semino, Polym. Int. 48: 392–397 (1999). D. W. Zhu, Macromolecules 29:2813–2817 (1996). G. Scmidt-Naake, M. Drache, and C. Taube, Angew. Makromol. Chem. 265:62–68 (1999). T. Nishikawa, M. Kamigaito, and M. Sawamoto, Macromolecules 32:2204–2209 (1999). H. Fischer, J. Polym. Sci. A Polym. Chem. 37:1885– 1901 (1999). E. D. Sudol, in Polymeric Dispersions: Principles and Applications (J. M. Asua, ed.), Kluwer Academic Publishers, Boston, 1997, pp. 109–126. J. L. Cawse, in Emulsion Polymerization and Emulsion Polymers (P. A. Lovell and M. S. El-Aasser, eds.), Wiley, New York, 1976, pp. 743–761. T. K. Mandal and B. M. Mandal, Polymer 36:1911– 1913 (1995). T. K. Mandal and B. M. Mandal, J. Polym. Sci. Polym. Chem. 37:3723–3729 (1999). P. Banerjee and B. M. Mandal, Macromolecules 28: 3940–3943 (1995). H. Uyama, H. Kurioka, and S. Kobayashi, Chem. Lett. 795–796 (1995). H. Kurioka, H. Uyama, and S. Kobayashi, Polym. J. 30:526–529 (1998). H. Uyama, H. Kurioka, and S. Kobayashi, Colloids Surf. A Physicochem. Eng. Asp. 153:189–194 (1999). D. Chattopadhyay and B. M. Mandal, Langmuir 12: 1585–1588 (1996). J. Stejskal, P. Kratochvil, and M. Helmstedt, Langmuir 12:3389–3392 (1996).

Polymerizable and Polymeric Surfactants 121. 122. 123.

124. 125. 126. 127.

128.

129. 130. 131.

132. 133. 134. 135. 136. 137. 138. 139.

140. 141. 142. 143.

144. 145.

M. Okubo, T. Masuda, and T. Mukai, Colloid Polym. Sci. 276:96–99 (1998). D. Chattopadhyay, S. Banerjee, D. Chakravorty, and B. M. Mandal, Langmuir 1544–1547 (1998). M. T. Gill, S. E. Chapman, C. L. Dearmitt, F. L. Baines, C. M. Dadswell, J. G. Stamper, G. A. Lawless, N. C. Billingham, and S. P. Armes, Synth. Met. 93: 227–233 (1998). P. Banerjee, Eur. Polym. J. 34:841–847 (1998). Y. L. Hsiao, E. E. Maury, S. Mawson, and K. P. Johnston, Macromolecules 28:8159–8166 (1995). Y. L. Hsiao and J. M. DeSimone. J. Polym. Sci. A Polym. Chem. 35:2009–2013 (1997). M. L. O’Neill, M. Z. Yates, K. P. Johnston, C. D. Smith, and S. P. Wilkinson, Macromolecules 31:2848– 2856 (1998). M. L. O’Neill, M. Z. Yates, K. P. Johnston, C. D. Smith, and S. P. Wilkinson, Macromolecules 31:2838– 2847 (1998). A. I. Cooper, W. P. Hems, and A. B. Holmes, Macromolecules 32:2156–2166 (1999). H. Shiho and J. M. DeSimone, J. Polym. Chem. A Polym. Chem. 37:2429–2437 (1999). J. H. Xia, T. Johnson, S. G. Gaynor, K. Matyjaszewski, and J. M. DeSimone, Macromolecules 32: 4802–4805 (1999). X. H. Li and Z. G. Sun, J. Appl. Polym. Sci. 58:1991– 1997 (1995). E. Bourgeat-Lami and J. Lang, J. Colloid Interface Sci. 197:293–308 (1998). E. Bourgeat-Lami and J. Lang. J. Colloid Interface Sci. 210:281–289 (1999). X. B. Ding, Z. H. Sun, G. X. Wan, and Y. Y. Jiang, Chin. J. Polym. Sci. 17:129–134 (1999). E. Bourgeat-Lami and A. Guyot, Polym Bull 35:691– 696 (1995). E. Bourgeat-Lami and A. Guyot, Colloid Polym. Sci. 275:716–729 (1997). K. Ishizu and N. Tahara, Polymer 37:1729–1734 (1996). H. Miyazaki, K. Terada, T. Sato, H. Maruyama, and T. Okaya, J. Appl. Polym. Sci. 60:2149–2157 (1996). P. Lacroix-Desmazes and A. Guyot, Macromolecules 29:4508–4515 (1996). P. Lacroix-Desmazes and A. Guyot, Polym. Adv. Technol. 8:608–615 (1997). K. Ishizu, M. Yamashita, and A. Ichimura, Polymer 38:5471–5474 (1997). J. Liu, L. M. Gan, C. H. Chew, C. H. Queck, H. Gong, and L. H. Gan, J. Polym. Sci. A Polym. Chem. 35: 3575–3583 (1997). J. Liu, C. H. Chew, S. Y. Wong, L. M. Gan, J. Lin, and K. L. Tan, Polymer 39:283–289 (1998). M. Q. Chen, T. Serizawa, and M. Akashi, Polym. Adv. Technol. 10:120–126 (1999).

573 146.

147. 148. 149. 150. 151.

152. 153. 154. 155. 156. 157. 158. 159. 160. 161. 162. 163. 164. 165. 166. 167. 168. 169. 170. 171. 172. 173.

S. F. Lascelles, F. Malet, R. Mayada, N. C. Billingham, and S. P. Armes, Macromolecules 32:2462– 2471 (1999). D. Donescu, M. Teodorescu, L. Fusulan, and C. Petcu, J. Dispersion Sci. Technol. 20:1085–1096 (1999). B. Moustafa and A. Faizalla, J. Appl. Polym. Sci. 73: 1793–1798 (1999). M. A. Awan, V. L. Dimonie, and M. S. El-Aasser, J. Polym. Sci. A Polym. Chem. 34:2633–2649 (1996). M. A. Awan, V. L. Dimonie, and M. S. El-Aasser, J. Polym. Sci. A Polym. Chem. 34:2651–2664 (1996). J. Kim, S. Y. Jeong, K. U. Kim, Y. H. Ahn, and R. P. Quirk, J. Polym. Sci. A Polym. Chem. 34:3277–3288 (1996). J. V. Dawkins, D. J. Neep, and P. L. Shaw, Polymer 35:5366–5368 (1994). R. Hu, V. L. Dimonie, E. D. Sudol, and M. S. ElAasser, J. Appl. Polym. Sci. 55:1411–1415 (1995). A. Tuncel, H. Cicek, M. Hayran, and E. Piskin, J. Biomed. Mater. Res. 29:721–728 (1995). E. Piskin, K. Kesenci, N. Satiroglu, and O. Genc, J. Appl. Polym. Sci. 59:109–117 (1996). O. Pekcan, Eur. Polym. J. 32:117–124 (1996). V. Bulmus, A. Tuncel, and E. Piskin, J. Appl. Polym. Sci. 60:697–704 (1996). M. Laus, C. Dinnella, G. Lanzarini, and A. Casagrande, Polymer 37:343–347 (1996). C. Dinnella, M. Doria, M. Laus, and G. Lanzarini, Biotechnol. Appl. Biochem. 23:133–140 (1996). F. L. Baines, S. Dionisio, N. C. Billingham, and S. P. Armes, Macromolecules 29:3096–3102 (1996). H. Bamnolker and S. Margel, J. Polym. Sci. A Polym. Chem. 34:1857–1871 (1996). M. Laus, M. Lelli, and A. Casagrande, J. Polym. Sci. A Polym. Chem. 35:681–688 (1997). V. Bulmus, H. Ayhan, and E. Piskin, Chem. Eng. J. 65:71–76 (1997). T. Yamashita and M. Okubo, Colloid Polym. Sci. 275: 214–219 (1997). B. Ray and B. M. Mandal, Langmuir 13:2191–2196 (1997). K. Takahashi, S. Miyamori, H. Uyama, and S. Kobayashi, Macromol. Rapid. Commun. 18:471–475 (1997). M. Bayham and A. Tuncel, J. Appl. Polym. Sci. 67: 1127–1139 (1998). K. Takahashi, H. Uyama, and S. Kobayashi, J. Macromol. Sci. Pure Appl. Chem. A35:1473–1487 (1998). J. W. Kim and K. D. Suh, Colloid Polym. Sci. 276: 870–878 (1998). B. Ray and B. M. Mandal, J. Polym. Sci. A Polym. Chem. 37:493–499 (1999). D. Horak, M. Karpisek, J. Turkova, and M. Benes, Biotechnol. Prog. 15:208–215 (1999). D. Horak, J. Polym. Sci. A Polym. Chem. 15:3785– 3792 (1999). W. Yang, J. Hu, Z. Tao, L. Li, C. Wang, and S. Fu, Colloid Polym. Sci. 277:446–451 (1999).

574 174.

175. 176. 177. 178. 179.

180. 181. 182. 183. 184. 185.

186. 187.

188. 189. 190. 191. 192. 193. 194.

195.

196.

197. 198.

Guyot and Tauer K. Nakamura, K. Fujimoto, and H. Kawaguchi, Colloid Surf. A Physicochem. Eng. Asp. 153:195–201 (1999). B. Thomson, A. Rudin, and G. Lajoie, J. Polym. Sci. A Polym. Chem. 33:345–357 (1995). I. Capek, Radical Polymerization Polyelectrolytes 145 PG: 1–55, 1999. J. M. Harris, in Poly(ethylene glycol) Chemistry (J. M. Harris, ed.), Plenum, New York, 1992, pp. 1–14. I. Piirma, Polymeric Surfactants, Marcel Dekker, New York, 1992, pp. 127–164. V. M. Nace, ed., Nonionic Surfactants—Polyxyalkylene Block Copolymers, Marcel Dekker, New York, 1996. R. Brown, B. Stutzel, and T. Sauer, Macromol. Chem. Phys. 196:2047–2064 (1995). R. Walz, B. Bo¨mer, and W. Heitz, Makromol. Chem. 178:2527–2534 (1977). O. Nuyken and R. Weidener, Adv. Polym. Sci. 73/74: 145–199 (1986). R. G. Santos, J. G. Zilliox, J. E. Herz, and G. J. Beinert, Eur. Polym. J. 28:233–242 (1992). I. Cakmak, Macrmol. Rep. A31(Suppl. 3 and 4):333– 337 (1994). Y. Haneda, H. Terada, M. Yoshida, A. Ueda, and S. Nagai, J. Polym. Sci. A Polym. Chem. 32:2641–2652 (1994). H. Terada, Y. Haneda, A. Ueda, and S. Nagai, Macromol. Rep. (Suppl. 1 and 2):173–178 (1994). C. I. Simionescu, G. David, A. Ioanid, V. Paraschiv, G. Riess, and B. C. Simionescu, J. Polym. Sci. A Polym. Chem. 32:3123–3132 (1994). H. Kitano and J. Kawabata, Macromol. Chem. Phys. 197:1721–1729 (1996). H. Kitano and J. Kawabata, Macromol. Chem. Phys. 197:3657–3666 (1996). K. Tauer, Polym. Adv. Technol. 6:435–440 (1995). T. Nagamune, A. Ueda, and S. Nagai, J. Appl. Polym. Sci. 62:359–365 (1996). K. Tauer, M. Antonietti, L. Rosengarten, and H. Mu¨ller, Macromol. Chem. Phys. 199:897–908 (1998). V. N. Kislenko, Colloid Surf. A Physicochem. Eng. Asp. 152:199–203 (1999). M. S. El-Aasser and J. W. Vanderhoff, eds., Emulsion Polymerization of Vinyl Acetate, Applied Science Publishers, London, 1981. G. S. M. Gonzales, V. L. Dimonie, E. D. Sudol, H. J. Yue, A. Klein, and M. S. El-Aasser, J. Polym. Sci. A Polym. Chem. 34:849–862 (1996). H. Murakami, Y. Kawashima, T. Niwa, T. Hino, H. Takeuchi, and M. Kobayashi, Int. J. Pharm. 149:43– 49 (1997). H. Zeh and H. Baumgartl, JOCCA Surf. Coat. Int. 78: 132–138 (1995). H. Warson, in Emulsion Polymerization of Vinyl Acetate (M. S. El-Aasser and J. W. Vanderhoff, eds.), Applied Science Publishers, London, 1981, pp. 1–10.

199.

200.

201. 202. 203. 204.

205. 206. 207.

208. 209.

210.

211. 212. 213. 214. 215. 216. 217. 218. 219. 220. 221. 222.

D. Donescu, K. Gosa, I. Diaconescu, M. Mazare, and N. Carp, in Emulsion Polymerization of Vinyl Acetate (M. S. El-Aasser and J. W. Vanderhoff, eds.), Applied Science Publishers, London, 1981, pp. 203–214. W. E. Daniels, J. W. Vanderhoff, C. T. Enos, J. G. Iacoviello, S. M. Ahmed, and J. Frost, in Emulsion Polymerization of Vinyl Acetate (M. S. El-Aasser and J. W. Vanderhoff, eds.), Applied Science, London, 1981, pp. 191–202. E. M. Coen, R. A. Lyons, and R. G. Gilbert, Macromolecules 29:5128–5135 (1996). T. Cao, W. P. Yin, and S. E. Webber, Macromolecules 27:7459–7464 (1994). M. Antonietti and M. C. Weißenberger, Macromol. Rapid Commun. 18:295–302 (1997). D. de Wet-Roos, J. H. Knoetze, B. Cooray, and R. D. Sanderson, J. Appl. Polym. Sci. 71:1347–1360 (1999). G. Riess, Colloid Surf. A Physicochem. Eng. Asp. 153:99–110 (1999). L. Leemans, R. Fayt, Ph. Teyssie´, and N. C. de Jaeger, Macromolecules 24:5922–5925 (1991). K. Tauer, H. Mu¨ller, L. Rosengarten, and K. Riedelsberger, Colloid Surf. A Physicochem. Eng. Asp. 153: 75–88 (1999). K. Tauer, M. Antonietti, H. Mu¨ller, and L. Vorwerg, Pitture Vrnici—Paints Varnishes 73:31–46 (1997). H. Mu¨ller, Polymere Stabilisatoren in der Emulsionspolymerization, Ph.D. dissertation, Universita¨t Potsdam, Germany, 1997. M. Bouix, J. Gouzi, B. Charleux, J. P. Vairon, and P. Guinot, Macromol. Rapid Commun. 19:209–213 (1998). W. Jaeger, U. Wendler, A. Lieske, and J. Bohrisch, Langmuir 15:4026–4032 (1999). K. D. Campbell, D. J. Sagl, and J. W. Vanderhoff, J. Dispersion Sci. Technol. 19:785–804 (1998). S. E. Friberg, T. Moaddel, and E. D. Sprague, J. Phys. Chem. 98:13414–13417 (1994). J. Kevelam and J. B. F. N. Engberts, Langmuir 11: 793–797 (1995). G. J. Wang and J. B. F. N. Engberts, Eur. Polym. J. 31:409–417 (1995). G. J. Wang and J. B. F. N. Engberts, J. Org. Chem. 60:4030–4038 (1995). A. Laschewsky, Adv. Polym. Sci. 124:1–86 (1995). Y. Hu, M. C. Kramer, C. J. Bourdeaux, and C. L. McCormick, Macromolecules 28:7100–7106 (1995). O. Anthony and R. Zana, Langmuir, 12:3590–3597 (1996). Y. X. Hu, R. S. Armentraut, and C. L. McCormick, Macromolecules 30:3538–3546 (1997). Y. X. Hu, G. L. Smith, M. F. Richardson, and C. L. McCormick, Macromolecules 30:3526–3527 (1997). Y. Rouault and C. Marques, J. Phys. II 7:903–911 (1997).

Polymerizable and Polymeric Surfactants 223.

224. 225.

226.

227. 228.

V. G. Babak, M. Rinaudo, J. Desbrieres, G. A. Vikhoreva, and M. C. Michalski, Mendeleev Commun. 4:149–151 (1997). V. S. Zdanowicz and U. P. Strauss, J. Phys. Chem. B 102:40–43 (1998). T. Sata, K. Mine, Y. Tagami, M. Higa, and K. Matsusaki, J. Chem. Soc. Faraday Trans. 94:147–153 (1998). Y. Yang, R. Prudhomme, K. M. McGrath, P. Richetti, and C. M. Marques, Phys. Rev. Lett. 80:2729–2732 (1998). I. Iliopoulos, Curr. Opin. Colloid Interface Sci. 3:493– 498 (1998). T. Sata, Y. Tagami, and K. Matsusaki, J. Phys. Chem. B 102:8473–8479 (1998).

575 229.

230. 231. 232. 233. 234. 235.

V. Babak, I. Lukina, G. Vikhoreva, J. Desbrieres, and M. Rinaudo, Colloids Surf. A Physicochem. Eng. Asp. 147:139–148 (1999). D. Cochin and A. Laschewsky, Macromol. Chem. Phys. 200:609–615 (1999). A. Benjelloun, P. Lochon, and A. Brembilla, J. Mol. Catal. A Chem. 140:215–223 (1999). S. Bayoudh, A. Laschewsky, and E. Wischerhoff, Colloid Polym. Sci. 277:519–527 (1999). A. Lieske and W. Jaeger, Tenside Surfactants Deterg. 36:155–161 (1999). M. R. Anklam, D. A. Saville, and R. K. Prud’homme, Langmuir 15:7299–7307 (1999). W. Jaeger, U. Wendler, A. Lieske, J. Bohrisch, and C. Wandrey, Macromol. Symp. in press.

29 Organic Particle Precipitation JOHN TEXTER

I.

Strider Research Corporation, Rochester, New York

A.

INTRODUCTION

Physical State

The production of well-characterized and monodisperse organic particles by precipitation is much less developed than inorganic particle precipitation. This is mainly due to the high number of internal degrees of freedom in typical organic molecules of interest in comparison with inorganic solids often derived from relatively simple salts or oxides. Large numbers of internal degrees of freedom such as chiral centers and rotational degrees of freedom make for the occurrence of a plethora of polymorphs, when crystallization can be achieved, and make amorphous states of condensation the most easily obtained in rapid precipitation processes. Organic precipitation of dyes and pigments to produce press cakes suitable for purification and storage but requiring further treatment (typically comminution) for particle size reduction is well-established art [4]. Emphasis in such processes is often on how to promote particle growth so that crystals can be washed and filtered expeditiously and without clogging. Both amorphous and crystalline physical states can be advantageous under certain conditions. One or the other type of physical state may have a preferred property, especially with respect to color or ultraviolet (UV)-visible spectrum. Amorphous physical states can lead to untoward behavior, such as unwanted crystallization and concomitant changes in other physical properties. Transmission electron micrographs (TEMs) of various crystalline Color Index pigments [5] are il-

This chapter addresses precipitation and condensation processes for forming organic particulates in homogeneous solutions and in multiphase fluids. Both soft and hard particles are discussed. Soft particles such as micelles and microemulsion droplets sometimes have only fleeting dynamical lifetimes, but they provide nanoscale compartmentalization that is useful, sometimes, for templating other particulates. Other soft particles, such as emulsion droplets of oil in water, can be used to template the growth of larger droplets [1], they can provide micrometer-scale compartmentalization for forming relatively large droplets and beads [2], and they can be used to compartmentalize condensation of solid amorphous and crystalline organic materials (see Section II). Comminution and related grinding and fluid-energy milling processes are widely used industrially for preparing micrometer-scale and submicrometer-sized powders and dispersions of organic materials [3]. However, such methods are not very applicable to organic solids that are soft or waxy or solids that are explosive. Also, such processes often do not yield particle sizes appropriate for a particular application. Dissolution or vaporization followed by condensation, precipitation, or recrystallization represents a diverse class of processes for producing small-particle organic formulations with sizes ranging from a few nanometers to tens or hundreds of micrometers and with physical states ranging from liquid to amorphous solid to crystalline.

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FIG. 1 Transmission electron micrographs of crystalline organic pigments: (a,b) Blue 15 : 3; (c) Red 57 : 1; (d) Violet 19; (e) Yellow 110. (From Ref. 6.)

lustrated in Fig. 1 [6]. Dispersions of the pigments illustrated in Fig. 1 are routinely achieved by comminution processing to create a stable suspension. A challenge before us is to learn how to precipitate various organic pigments and materials as small particles of controlled size in a crystalline state with well-defined habit. A further challenge is to learn to do so while obtaining a colloidally stable dispersion, where viscosity and particle-particle interactions are minimized. B.

Compartmentalization

Particle size during precipitation can usually be controlled by some sort of compartmentalization. In cases relating to condensation from supersaturated solutions, particle size is essentially a kinetic or diffusion-controlled process wherein a de facto reaction field or region of significant concentration gradient directs the flux of condensing species at a growing particle. Such compartments may be thought of as reaction or diffusion-limited condensation zones. Alternatively, physical or interfacial boundaries may serve to define na-

noreactors or microreactors that limit the size of particles formed therein. Such cases are easier to visualize conceptually and include precipitation within emulsion droplets and aerosol droplets as well as within hollow capsules (see Section IX.B). C. 1.

Driving Forces

Free Energy Within Single Phase Domains An important class of organic particles are those that form spontaneously because of chemical free energy driving forces. This class comprises micelles, microemulsions, reverse micelles, reverse microemulsions, and some vesicles [7]. In such systems one needs only to bring the various chemical components into physical contact and thermodynamic evolution will drive codissolution and mixing until a thermodynamically isotropic solution is formed. The supramolecular particles formed therein from amphiphilic molecules are in a dynamic equilibrium with the rest of the solution phase. The use of such particles may be quite limited, as

Organic Particle Precipitation

changes in intensive variables such as temperature and concentration often cause transformation or loss of the particles of interest or the formation of multiple-phase domains. However, such thermodynamically stable particles can serve as useful templates from which kinetically stabilized (thermodynamically unstable) particles can be formed. 2. Supersaturation and Nucleation If S⬁ is the solubility of a material having an infinite radius of curvature, or in simpler terms the macroscopic equilibrium solubility, the supersaturation is defined as [S/S⬁ ⫺ 1], where S is the local solubility. The greater the degree to which a condensation volume element is devoid of heterogeneous nucleation material (seed nuclei, dust, etc.), the higher the supersaturation has to be in order to induce nucleation. An in-depth discussion of nucleation theory is beyond the scope of this chapter; see Refs. 8 and 9 for reviews. However, several qualitatively useful generalizations should be noted. As more nuclei are formed, smaller particle sizes usually obtain because a given amount of mass is distributed over a greater number of centers. This effect also often leads to slightly to dramatically increased viscosity because as particles decrease in size the average separation distance decreases and interparticle interactions increase. The faster a given supersaturation is reached, the greater will be the number of nuclei formed. Nuclei tend to dissolve at a given supersaturation, and this instability becomes more severe as the size of nuclei decreases. This effect is described by the wellknown Gibbs-Thompson (Ostwald-Freundlich) equation [10]. This equation, kT ln

Sr 2␥ u¯ = S⬁ r

relates the solubility Sr of a particle of radius r to that of a macroscopic particle, S⬁, the particle-continuous phase interfacial free energy, ␥, and the molecular volume, u¯ , of the organic species. This equation shows that the propensity for dissolution (or increase in solubility) is inversely proportional to the particle’s radius. This effect gives rise to the ever present driving force for particle growth by Ostwald ripening, where small particles (nuclei) dissolve and reprecipitate or condense on larger particles. 3.

Metastable Two-Phase Boundary Formation Most organic particles when condensed quickly from a multicomponent liquid adopt a spherical morphology.

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This result is a consequence of surface free energy minimization, where the interfacial free energy per unit volume is a minimum, because spheres yield the lowest surface-to-volume ratio. This driving force is also prevalent even in the precipitation of nanoparticulate inorganics, including metals and diverse oxides. Subsequently, however, further free energy may be given up by crystallization into one or more polymorphs accessible to the material. These transformations lead to the development of particular facets at the particle surface, characteristic of crystalline habits.

II.

DISPERSIONS FROM EMULSIONS

A.

General Preparative Methods

1. Emulsification of Organics A widely applicable technique for preparing amorphous organic nanoparticulates is to dissolve the water-insoluble organic substrate in a water-immiscible solvent having a relatively high vapor pressure (e.g., ethyl acetate) in order to form an ‘‘oil phase’’ containing the substrate. Such water-immiscible solvents are often known as ‘‘auxiliary’’ solvents. This dissolution step is often aided by heating. The amount of heating (temperature of dissolution) is determined by the thermal stability of the organic substrate, the viscosity required during emulsification, and the amount of auxiliary solvent utilized. It is sometimes possible to omit the auxiliary solvent, or nearly so, when the melting point of the organic substrate is not too high. It is generally desired to obtain dissolution of the organic substrate using the least amount of auxiliary solvent necessary so as to minimize the amount of auxiliary solvent (VOCs, volatile organic components) that must subsequently be removed. This organic solution is then emulsified with an aqueous solution containing stabilizers such as surfactant and polymeric dispersants (e.g., gelatin, polyvinyl alcohol, polyvinylpyrrolidone). Generally, increasing surfactant levels lead to decreasing particle sizes, as the specific surface area stabilized increases in direct proportion to the surfactant added. Charged surfactants provide charge stabilization. Nonionic surfactants and polymeric stabilizers provide steric stabilization. All of the surfactants when adsorbed to the aqueous-oil interface lower the interfacial tension and facilitate smaller droplet production with a given amount of input shear energy. Many high-shear methods for achieving emulsification are available. The available shear methods in decreasing order of effectiveness are high-pressure ho-

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mogenization, colloid milling with rotor-stator devices, ultrasonic mixing, and very high speed stirring. 2.

Transformation of Emulsions to Dispersions The final steps center around removal of the auxiliary solvent. Two methods are used in practice, evaporation and washing. (a) Evaporation. On the laboratory scale, evaporation is easily done using a rotovap apparatus. The emulsion is circulated over a large surface area under reduced pressure and the water-immiscible solvent gradually diffuses out of the emulsion into the vapor phase, where it is vented or condensed for recycling. Larger scale industrially practical flow systems generally condense the auxiliary solvent for recycling. These techniques are practical only for certain classes of solvents, as the auxiliary solvents must exhibit a sufficiently high vapor pressure. Ethyl acetate and cyclohexanone are two examples of auxiliary solvents well suited for evaporative removal. There are, however, several limitations of evaporative solvent removal. One limitation is that evaporation may be too slow at the desired processing temperature. Another is that the amorphous physical state of the organic substrate may be too unstable at the processing temperature and untoward physical ripening, particle growth, or crystallization may occur. (b) Washing. Although the auxiliary solvents are water immiscible, they usually have finite water solubility. It is sometimes preferred to use countercurrent washing techniques to remove unwanted auxiliary solvent. If the emulsion is not gelled, then constant-volume dialysis or ultrafiltration can be used effectively to wash out the auxiliary solvent. If the emulsion gels, as is easily obtained when using gelatin or some other gelling polymeric stabilizer, one can chill (causing gelation) and then chunk the emulsion to produce a high surface area. This gelled emulsion is then repeatedly washed with a stream of wash water (containing an appropriate electrolyte to control swelling) to remove the auxiliary solvent. (c) Condensation. As the auxiliary solvent is removed and the temperature of the emulsion cools, the solubility of the organic substrate decreases. After the auxiliary solvent is gone, one usually obtains an amorphous (solid) state for the organic substrate. In some cases, particularly when the substrate has few degrees of internal freedom, intraemulsion particle crystallization may occur. However, for most organics having molecular weights >300 or so, condensation into an

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amorphous solid state is the rule rather than the exception. Low-vapor-pressure organic solvents or plasticizers can be included in such dispersion formulations for various chemical and physical reasons. Such solvents, plasticizers, and additives typically do not very effectively solubilize the substrate. Sufficient water-insoluble solvent, dramatically less water miscible than auxiliary solvents, can be included to prevent condensation of the organic substrate and to keep the substrate in a solution state. B.

Applications

Such methods have been in use on an industrial scale for many decades in the manufacture of photographic papers and films. Applications to pharmaceutical preparation have begun and are currently a focus area where current research is being done. Other diverse applications of this condensation approach include non-crosslinked polymer bead production. 1. Photographic Applications Image dye formation in most color films and papers occurs via coupling with oxidized color developers [11]. The couplers that form dye upon reaction with oxidized developer are generally only sparingly soluble in water and are incorporated into particular layers of photographic elements as submicrometer particles prepared by emulsification techniques [12]. Typical examples of such couplers are illustrated in Table 1. The coupler dispersion particles are usually in the size range 50–300 nm. Particle size is an important physical parameter, particularly with respect to its influence on the kinetic reactivity and dye-forming efficiency of such dispersions [13,14]. Such couplers are often formulated with a low-vapor-pressure organic solvent in order to modify coupling reactivity or dye hue. High-vapor-pressure auxiliary solvents, such as ethyl acetate and cyclohexanone, are often used temporarily to facilitate dissolution of coupler at a given processing temperature. In formulations using auxiliary solvent, 1 part coupler, 1/4 to 2 parts low-vapor-pressure plasticizer or coupler solvent, and 4–6 parts auxiliary solvent are combined with mild heating and low-shear mixing in order to effect dissolution. Such a solution is typically termed the ‘‘oil’’ phase. In parallel, an aqueous solution containing dispersing aids such as surfactant and gelatin is prepared, and this solution is typically referred to as the ‘‘aqueous’’ phase. These oil and aqueous phases are then mixed under mild shear to effect crude emulsification, and then this emulsion is passed through high

Organic Particle Precipitation TABLE 1

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Amphiphilic Color-Forming Photographic Couplers

shear to produce a submicrometer-sized emulsion. Colloid mills and diverse types of homogenizers are widely used in the art to effect such emulsification. When gelatin has been included as a dispersing aid (it is a good steric stabilizer and binder), it is often convenient to chill the emulsion to effect gelation, then chunk it to produce a high surface area, and then subject the emulsion in this state to washing processes to remove the auxiliary solvent. As an alternative to chilling and gelling, the auxiliary solvent may be removed by evaporation under reduced pressure. After this stage of auxiliary solvent removal, the oil-in-water emulsion has been thereby transformed into a dispersion comprising amorphous coupler-coupler solvent particles. Only rarely are such couplers significantly soluble in their respective coupler solvents. Two general modifications of these processing steps are encountered in industrial applications. (a) NS Dispersions. One modification simply omits the use of coupler solvents (low-vapor-pressure organic solvents or plasticizers). Such omission is most often made in connection with couplers that have sufficient reactivity without added solvent. Auxiliary solvents are still often used, but after their removal, such dispersions are often termed ‘‘NS’’ dispersions (no solvent). (b) Direct Dispersions. Another important modification in such formulations is the omission of auxiliary solvents. The driving force for formulating without auxiliary solvents is that one avoids the expense of the

auxiliary solvent removal steps. However, the price that must be paid, typically, is that the oil phase must be heated to a much higher temperature than is necessary when formulating without auxiliary solvents. The organic composition to be dispersed is simply heated to a suitable liquidus temperature and then emulsified or homogenized to form an emulsion. The primary concern is the thermal stability of the substance being liquefied and dispersed. With couplers that are sensitive to aerial oxidation, such elevated heating is often done under a nitrogen blanket. (c) Examples. Examples of such coupler dispersions are illustrated in the TEMs of Fig. 2. All of the formulations illustrated used aqueous phases that comprised gelatin and Alkanol-XC (Du Pont) as dispersing aids (Structure 1). The dispersion of coupler I illustrated in Fig. 2a was formulated 1:1 (w/w) with di-nbutylphthalate and utilized ethyl acetate as auxiliary solvent, and this auxiliary solvent was removed by evaporation. The amorphous particles obtained are nearly spherical, and the particle size distribution is polydisperse, ranging from 50 to 400 nm in diameter. An NS dispersion of coupler II is illustrated in Fig. 2b. The carboxy functionalty of this coupler makes it highly surface active, so that no added coupler solvent is necessary to achieve efficient coupling. Again, ethyl acetate was used as auxiliary solvent to facilitate emulsification. A very fine particle size dispersion was obtained after removal of the auxiliary solvent. Particles

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FIG. 2 Transmission electron micrographs of coupler dispersions prepared by emulsification (homogenization): (a) coupler I formulated 1 : 1 (w/w) with di-n-butylphthalate; (b) coupler II formulated without added plasticizer; (c) coupler III formulated 1 : 1/2 with tricresylphosphate; (d) coupler IV formulated 1 : 1/4 with di-n-butylphthalate. (Adapted from Ref. 12.)

in the range 50–300 nm are evident in Fig. 2b. Coupler III was formulated 1: 1/2 with tricresyl phosphate as coupler solvent and emulsified by colloid milling, and the ethyl acetate auxiliary solvent was removed by evaporation. The resulting dispersion particles are illustrated in Fig. 2c, where it is seen clearly that the dispersion particles are not homogeneous. The shadowing shows that while these dispersion particles are probably spherical in the bulk, they are sufficiently soft to deform on the TEM grids. Moreover, the deformations appear to be conelike, as is evident from the shadows. Figure 2d shows a dispersion of yellow dye forming coupler IV formulated 1: 1/4 with di-n-butylphthalate. This dispersion was prepared without the use of auxiliary solvent, and emulsification was done using high-pressure homogenization. Such oil phases are typically fairly viscous during homogenization, and a consequence of this viscosity is a broader particle size distribution. The particles illustrated in Fig. 2d span a range of 50–500 nm in diameter. 2. Pharmaceutical Applications Homogenization is becoming more prevalent in the pharmaceutical literature as a means for preparing amorphous and crystalline dispersions of active drug substances and of excipients. Nearly all of the problems currently being encountered in formulation work have been encountered (and overcome) much earlier in the

photographic technology literature. A prime example is illustrated by the so-called hot homogenization technique. (a) Hot Homogenization. A schematic of the hot homogenization process is illustrated in Fig. 3. This method is essentially isomorphic to the direct dispersion process described above for dispersing couplers without auxiliary solvent. The overarching goal is to produce fine-particle crystallites of pharmaceutical agent, encapsulated and stabilized by an immiscible coating of lecithin. The lecithin and agent are heated to dissolution and then emulsified, typically by homogenization, with a hot aqueous phase to produce an emulsion [15]. This emulsion is then cooled, during which process (it is hoped that) the liquid disperse phase solidifies and crystallizes to produce a fine particle dispersion. During this crystallization, the pharmaceutical agent and stabilizer (lecithin) phase sepa-

STRUCTURE 1

XC (Alkanol-XC).


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FIG. 3 Hot homogenization process for dispersing pharmaceutical agents. Liquification of drug compound and stabilizer, followed by (hot) homogenization, yields emulsion droplets pictured on left. Subsequent cooling leads to solidification of core drug compound surrounded by stabilizer (right). (Adapted from Ref. 15.)

spontaneously wets the amorphous or crystalline surfaces and facets of the model compound once the compound solidifies upon cooling. In addition, it is difficult to control exactly when a liquid disperse phase will crystallize. Although cooling is sufficient to produce an amorphous solid phase, the free energy of such phases is generally higher than that of a crystalline phase. Such particles are in a supercooled physical state and have an effectively higher solubility than lower free energy crystallites have. Such dispersions are therefore primed for untoward crystal growth by Ostwald ripening, in which large (lower free energy) crystallites are formed from metastable, amorphous solid dispersion particles. In such cases, monomer transport is by diffusion, and binary particle collisions are not required for transport, although such collisions can provide the necessary activation for nucleation of a crystalline phase.

rate, with the latter forming a stabilizing coating around the former. Severe crystallization problems can be encountered in such processes, especially since lecithins are not particularly well suited as stabilizers and, furthermore, particularly because it is difficult to control when and how the liquid agent phase will crystallize after cooling. As an example, consider the hot homogenization of a model pharmaceutical agent where lecithin is used as the stabilizer. A composition of model compound and lecithin was heated to effect liquefaction of the organic phase, and then this phase was emulsified in water using homogenization. Particle size analysis soon after emulsification showed that a submicrometer dispersion was obtained. However, after 5 days of storage, particle size analysis revealed that in addition to the submicrometer mode corresponding to the original dispersion, a second significant mode in the 10–20 ␮m range had appeared, suggesting that a major portion of the mass had been transformed into large microcrystallites. This untoward crystallization was the natural consequence of several features. First, there was no matrix stabilization, so dispersion particles were free to undergo binary collisions during storage. Such collisions can activate and nucleate crystallization processes. Furthermore, lecithin itself is not an ideal stabilizer, in general. Because it was believed that the lecithin and model compound were immiscible at storage temperature, it is presumed that phase separation drives these two components apart. It is unknown whether lecithin

(b) Cholesteryl Acetate. A general flowchart illustrating dissolution, homogenization, precipitation, auxiliary solvent extraction, and recycling is shown in Fig. 4. Application of this process to produce cholesteryl acetate (CholA) (Structure 2) particles under various auxiliary solvent evaporation regimes consistently resulted in amorphous CholA particles [16]. Particle sizes obtained were insensitive to the conditions of auxiliary solvent removal and were mainly controlled by the emulsion droplet sizes following homogenization. When toluene was used as the auxiliary solvent and removed by evaporation and POE-(20)-sorbitan monoleate was used as emulsifier, particle sizes in the 300– 500 nm range were obtained using 3% (w/w) emulsifier and in the 100–150 nm range at 10% (w/w) emulsifier, as a function of the disperse phase of the emulsion. Particle sizes correlated very strongly with starting emulsion droplet sizes, even though the auxiliary solvent was removed by dramatically different processes. A summary of these results is given in Table 2. The final dispersion sizes are fairly uniform no matter how the auxiliary solvent was removed, whether by evaporation or by washing (dialysis). Perhaps more surprising is the close correspondence between the dispersion sizes and the starting emulsion droplet sizes, even though the toluene has been removed. At the highest CholA loading, 50% (w/w), there was essentially no difference in size upon solvent removal. At only 5% loading, the final dispersion sizes were still 75% of the starting emulsion sizes. A detailed analysis of this surprising result is not yet available, but several factors probably contribute. First, there is probably some incorporation of water during the evaporation and wash-

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FIG. 4 Cyclic process for producing organic dispersions by emulsification. The active component is dissolved in an auxiliary solvent and combined with an aqueous emulsifier solution. This two-phase mixture is then homogenized to produce an emulsion. The auxiliary solvent is then removed by evaporation (or other means) and recycled. (From Ref. 16.)

ing steps to remove the auxiliary solvent. Cholesteryl derivatives are known to form hydrates. Second, the direct evidence indicated that the resulting dispersion particles were amorphous and therefore solidified in a sort of diffusion-limited aggregation sense that preserved volume and retarded compaction and densification during condensation. Third, the emulsifier most likely intercalated to some degree in the periphery of the dispersion particles and provides a significant shell volume, especially due to the 20-unit poly(oxyethylene) hydrophilic part of the headgroup, which amounts to 20–30% of the particle diameters. 3. Polymeric Bead Formation A particularly straightforward path for producing polymeric beads from polymer produced in melt or solution polymerization is to dissolve the polymer in an auxiliary solvent, emulsify this polymer solution, and then

remove the auxiliary solvent to leave polymer beads in suspension. As the auxiliary solvent is removed, the supersaturated polymer condenses to form a bead. Of course, beads may be produced using many different polymerization pathways, as discussed in several other chapters in this volume (see Part 3). This approach to bead formation has several advantages. First, all of the technologies available for controlling particle size in emulsification are applicable. For example, the controlled production of large (1 ␮m diameter and larger) beads by using limited coalescence [17] is available. The production of beads having mixtures of various polymers and polymer fractions essentially requires only that all of the ultimate components be soluble in the same auxiliary solvent. Whether microscopic phase segregation occurs during condensation or subsequently is another matter, however.

III.

STRUCTURE 2

CholA.

PRECIPITATION BY SOLVENT SHIFTING

Changes in solubility resulting from physical modification of a solvent’s ability to dissolve an organic substrate are central to nearly all of the precipitation processes discussed in this chapter, as well as the condensation processes discussed in the previous section. Solvation power changes dramatically with most intensive variables, including volume fraction, mole fraction, temperature, and concentrations of additives,


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TABLE 2 Correlation of Particle Sizes of CholA Dispersions, Prepared According to Different Regimes of Auxiliary Solvent (Toluene) Removal, with Starting Emulsion Droplet Particle Sizes Mean particle size (nm) CholA [% (w/w)] 5 10 50

Emulsion droplet

Evaporation at 100 mbar

Evaporation at 1 bar

Washing by dialyis

157 149 193

108 127 193

108 133 195

117 140 197

salts, and binding and nucleation sites. In this section we focus upon the controlled dissolution of substrate in a ‘‘good’’ solvent (sufficient to produce a singlephase solution), followed by mixing with a miscible but poor solvent (typically water). A poor solvent can also be constructed by having sufficient components that diminish solvent quality toward certain substrates, such as certain salts. A.

Flow Systems

Solvent shifting processes are often done in batch mode, and such methods are standard in bulk precipitation and crystallization. However, batch solvent shifting processes generally do not yield very uniform particle size distributions; continuous flow systems are better suited for producing good particle uniformity. Tee-mixing comprising two axially opposing flow streams, such as pictured in Fig. 5, is very effective and various sizes are available to accommodate flows of varying volume. Subsequent mixing downstream may or may not be utilized and can consist of flow

FIG. 5 Simple tee-mixing head fashioned for small-scale manufacturing by solvent shifting. Such a mixing head is easily machined from plastics, and even simpler mixing heads can be fashioned from tee-pipe and tubing fittings. Opposing reactant flows enter through 19 and 20; the mixed flow exits through 12.

Dialysis with toluene-saturated water 111 197

ultrasonication, high-energy milling, and static mixing. Turbulent flow usually suffices. B.

Salting Out

Some organic pigments may be precipitated from solution by so-called salting out procedures. A solution of the pigment is prepared and then salt, often containing a metal ion that interacts (binds) specifically with the dye anion, is added. When the solubility product of the metal ion complex of the dye is low, the metallized dye or pigment precipitates. Such metallized pigments and dyes are known as ‘‘lakes.’’ Production of lakes by encapsulating inorganic pigment particles with organic dyes and pigments is an important process for producing specialized colorful and pearlescent pigments, and these processes are discussed further in Section IX. 1. Organic-Inorganic Composites Wu and Matijevic´ [18] demonstrated the importance of agitation and surfactant level in controlling particle size and particle aggregation in BaCl2-induced precipitations of Red Dye No. 6 (V) (Structure 3) to produce the so-called barium lake of V. Precipitation of dye solutions (0.024 M) with aqueous BaCl2 (0.02 M) produced thin needles typically of the order of 1.5 ␮m in length and 100 nm in diameter. These needles were not primary single crystals but comprised many smaller nanosize subunits. When precipitation was done in the presence of a commercial surfactant, Daxad 11G, primary subunits about 30–40 nm in largest dimension

STRUCTURE 3

V (Red dye No. 6).

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were formed. These nanoparticles were amorphous by x-ray diffraction and were negatively charged, due to the adsorbed anionic surfactant, with an electrophoretic mobility of about ⫺0.8 ␮m s⫺1 V⫺1. Such surfactantaided precipitations produced stabilized nanodispersions with much improved optical covering power and dramatically decreased scattering in the long-wavelength region of the visible spectrum. Another example consists of coprecipitation of the anionic dye 3 Mordent Blue (3MB, Table 3) with aluminum sulfate to produce fairly monodisperse particles in the 200–300 nm diameter range comprising Al/dye ratios of 1:0.001 to 1:0.1 [19]. Such composite precipitated particles are produced by a hydrothermal process, and good size monodispersity arises as a result of kinetically controlled chemistry to produce hydrous oxides. The aluminum sulfate and dye solutions are aged at elevated temperatures. The aluminum hydrolyzes water to produce aluminum hydroxide and coprecipitation occurs with the anionic dye. An alternative form of composite pigment has been described by Wu et al. [20]. Nanoparticulate silica (Ludox CL), 5–12 nm in diameter, was surface treated to produce an alumina-type surface with resultant particles about 13–20 nm in diameter. These particles were then reacted with various organic dyes, including Red

Dye No. 6 (V), Acid Yellow 1, Acid Blue 25, and Guinea Green B (Table 3) to form inorganic (core)organic (shell) composite pigment particles. The amount of V incorporated ranged from 12 to 30% (w/ w) relative to the inorganic weight and increased with specific surface area of the inorganic core. Inorganic cores 15 nm in diameter supported saturation organic shells of 30, 19, 70, and 60% (w/w), for Red Dye No. 6, Acid Yellow 1, Acid Blue, and Guinea Green B, respectively. Such coating is analogous to the formation of so-called aluminum lakes. 2. Protein Coacervation Submicrometer-sized gliaden particles, derived from wheat gluten, have been produced [21] by precipitation from nonsolvent mixtures and are potential excipients for delivery of pharmaceutically active compounds such as trans-retinoic acid [22]. An aqueous ethanol solution of gliadin is infused with an aqueous saline solution that induces, by salting out, protein coacervation and particle formation. Ethanol evaporation (rotary evaporator) expedites the coacervation. Particles are isolated by centrifugation, resuspended, and optionally cross-linked with glutaraldehyde. Various aqueous ethanol, aqueous ethylene glycol, and aqueous propylene glycol mixtures were examined from a solubility

TABLE 3 Dye Structures for Forming Inorganic-Organic Core-Shell Composite Pigments


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parameter perspective in examining solvent and processing effects on particle size. C.

Miscible Solvent Mixing

A practical development scale flow system is illustrated in Fig. 6 for the case of dispersing organic pigments as submicrometer dispersion particles. The pigment is dissolved in a suitable water-miscible solvent and fed into the reactor in a shear field. As droplets of the pigment solution are formed in the nonsolvent, water, counterdiffusion flows of water into the particles and solvent out of the droplets occur, leading to supersaturation of the pigment, followed by nucleation and growth. 1. Carotenoids The precipitation of ␤-carotenoids in aqueous gelatin solutions by solvent shifting has been studied by Horn and coworkers [23,24]. The carotenoid is first dissolved in a water-miscible solvent such as an alcohol or ketone at an elevated temperature. This solution is then pumped into a mixing chamber, where it is mixed with an aqueous gelatin solution. The temperature drop and lower solubility in water induce precipitation to produce nanosize particles sterically stabilized by the gelatin. The presence of a surfactant, ascorbylpalmitate (AscP) (Structure 4), in the aqueous gelatin solution yields smaller particles than obtained otherwise. Results are summarized in Table 4. Gelatin is well known as an excellent steric stabilizer. It is also surface active and has been used for decades in photographic dispersion technology in the preparation of emulsions and dispersions as described in Section II. The results in Table 4 were obtained using two separate types of gelatins. Type A had a molecular weight of 240,000 and type B had a molecular weight of 300,000. The isoelectric point (IEP) of type A gelatin was determined to be 9.5, while that of type B gelatin was 5. The isoelectric points of the precipitated particles depend on the IEP of the type of gelatin used but do not depend on the surfactant, AscP. The surfactant will be either nonionic (in ring-closed form) or anionic at pH above 5 or so if the carboxylate group is activated by ring opening. The surfactant has a significant effect on particle size for both types of gelatins. 2. Color Instant Image Dyes The production of 100–200 nm diameter dispersions of organic pigments for color instant photographic applications by solvent shifting was well demonstrated by Gutoff and Swank [25]. Two pigments, one yellow (Yel) (Structure 5) and one cyan (Cyan) (Structure 6),

FIG. 6 Miscible solvent shifting reactor illustrating organic pigment solution fed into reactor containing aqueous stabilizers. The shear field in the reactor produces droplets of feed solution that immediately begin to undergo countercurrent solvent exchange, with water diffusing into the droplets and organic solvent diffusing out of the droplets. All of these processes lead to supersaturation with respect to the organic pigment and subsequently to homogeneous nucleation of pigment particles. (Courtesy of M. C. Brick, H. J. Palmer, and T. J. Whitesides, to be published.)

STRUCTURE 4

AscP.

TABLE 4 Precipitated ␤-Carotenoid Nanoparticle Properties Gelatin type A A B B

Weight % surfactant

Particle diameter (nm)

Isoelectric point (pH)

0 8 0 8

346 262 327 157

6.0 6.8 4.8 4.7

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STRUCTURE 5

STRUCTURE 7

Yel.

were dissolved in water-miscible solvent (acetone/isopropanol and acetone, respectively) and fed into an aqueous stabilizer solution in a tee-mixer to produce submicrometer amorphous pigment particles. Both surfactants (Tamol 731) and polymeric dispersants (polyvinylpyrrolidone, PVP) were used to provide stabilization of the resulting dispersions. After precipitation, the auxiliary solvent was removed in a sieve tray column. The essentially auxiliary solvent–free dispersion was cycled in a reboiler at the bottom of the column, and the residence time in this reboiler was correlated with final average particle size and was shown to be an effective means for growing particles to an aim size. 3. Photographic Couplers and Pigments Solvent shifting to prepare a very small particle size dispersion of amphiphilic couplers is a well-established photographic art. Godowsky and Duane [26] disclosed water-miscible solvent shifting to disperse molecular couplers and polymeric couplers. The couplers were typically fairly amphiphilic, owing to carboxy, sulfonic acid, and methyl ester substituents. Recent work has demonstrated homogeneous nucleation in miscible solvent shifting for the yellow organic

YPG.

pigment YPG (Stucture 7) precipitated out of various solvents (dimethylacetamide, methyl pyrrolidone, dimethyl sulfoxide, and acetonitrile). Using an aqueous phase containing both a surfactant, sodium dodecyl sulfate (SDS), and a polymeric stabilizer, PVP, Brick et al. (M. C. Brick et al., to be published) have shown that submicrometer particles such as those illustrated in Fig. 7a can be generated. Nucleation rates as a function of supersaturation ratio are illustrated in Fig. 7b. The four different water-miscible solvents all yield about the same power law correlation between nucleation rate and the supersaturation ratio over a range in ratio from 500 to 105. 4. Pharmaceutical Dispersions Specialized batch precipitations for pharmaceutical preparations have been demonstrated by Violante and coworkers [27–29] for a variety of organic materials. A general flow diagram is illustrated in Fig. 8. A basic limitation of this process is the need to use preparative centrifugation to isolate suitable size fractions of the drug dispersions. The water-insoluble pharmaceutical is dissolved in a water-miscible solvent and is precipitated by infusion of an aqueous or nonaqueous precipitating liquid (miscible with the original solvent). Or-

STRUCTURE 6

Cyan.


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FIG. 7 (a) Scanning electron micrograph of organic pigment YPG particles made by miscible solvent shifting; (b) correlation of nucleation rate with supersaturation ratio for YPG precipitation out of various organic solvents using SDS and PVP as particle stabilizers; units of dN/dt are particle per second. DMA, dimethylacetamide; MP, methylpyrrolidone; DMSO, dimethyl sulfoxide; AN, acetonitrile. (Courtesy of M. C. Brick, H. J. Palmer, and T. J. Whitesides, to be published.)

ganic solvent removal is done by washing and centrifugation, and particles ranging in size from 10 nm to 5 ␮m can be obtained depending on formulation and process parameters. For example, the image contrast agent iodipamide ethyl ester (IEE) (Structure 8) can be precipitated as 100 nm to 2 ␮m particles from 1:2 dimethyl sulfoxide (DMSO)/ethanol by 5% (w/w) aqueous PVP, where average size can be controlled by the aqueous dispersant infusion rate. Increasing infusion rate of nonsolvent produces smaller particles. In-

creasing temperature produces larger particles. Another example is provided by 2,2⬘,4,4⬘-tetrahydroxybenzophenone (THBP) (Structure 9) precipitated from DMSO by an aqueous serum albumin solution to produce 500-nm-diameter particles. Frank et al. [30] have reported a particularly simple solvent process to produce 2-␮m particles of probucol (PBCOL) (Structure 10) stabilized by SDS and PVP. An ethanol solution of probucol is dispersed into aqueous stabilizer solution with moderate shear. Counter-

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FIG. 8 Batch solvent shifting precipitation process for producing pharmaceutical dispersions suitable for intravenous injection. Nonsolvents bring the organic solution close to saturation or place the solution into a supersaturated state and often include solvents such as lower alcohols, e.g., ethanol. (From Ref. 27.)

diffusion leads to supersaturation and precipitation of the PBCOL particles. 5.

STRUCTURE 8

STRUCTURE 9

STRUCTURE 10

IEE.

Block Copolymer Self-Assembled Particles A very interesting class of spherical and vesicular particles in the micrometer size range has been discovered by Jenekhe and Chen [31,32] based on block copolymer self-assembly. The block copolymers are derived from rigid rods of poly(phenylquinoline) and random coils of polystyrene (PPQ-b-PS) (Structure 11). Morphology control is achieved by using different solvent combinations that are good solvents or nonsolvents for

THBP.

PBCOL.

STRUCTURE 11

PPQ-b-PS.


591

one or the other of these two block materials. For example, trifluoroacetic acid and dichloromethane and toluene are good solvents for the PPQ rod blocks, but the PS coils are insoluble in these solvents. Such diblocks then tend to form bilayer structures and upon solvent evaporation yield various vesicular morphologies (spherical, ellipsoidal). Particles having largest dimensions on the order of ␮m were obtained, depending on evaporation rate and solvent mixture proportions. These are remarkably large size dimensions to obtain by self-assembly. Such particles have also been prepared in fullerene suspensions in such a way that the interior of the particles was filled with fullerenes [32]. IV.

SUPERCRITICAL FLUID METHODS

A variety of supercritical and near-critical fluid processes have been introduced in the past 20 years for small particle precipitation. Most of these techniques combine aspects of aerosol particle formation with solvent shifting aspects, where the critical or near-critical fluid may function as the primary solvent for the organic principal compound or as an antisolvent. Such fluids are of interest for several reasons. A primary motivation is that a variety of useful solvents can be made critical at rather moderate temperatures. A summary of critical temperatures and pressures for some useful fluids is given in Table 5. Carbon dioxide is the most favored supercritical fluid because it is inexpensive, has low critical conditions (pressure and temperature), is not flammable, and is environmentally ‘‘green’’ and nontoxic. Carbon dioxide is particularly favored for pharmaceutical formulations. Processes using supercritical fluids usually can be very easily ‘‘dried’’ because such fluids quickly vaporize upon venting at atmospheric pressure. A.

Rapid Expansions of Supercritical Fluids

The most broadly studied process termed rapid expansion of supercritical solutions (RESS) involves the dis-

TABLE 5

Critical Values for Supercritical Fluids

Solvent Carbon dioxide Nitrous oxide Ethylene Trifluoromethane Chlorotrifluoromethane

Pc (atm)

Tc (⬚C)

74 72 51 47 39

31 36 10 26 29

solution of the organic principal compound in nearcritical or supercritical solvent followed by controlled expansion of the solution at reduced pressure. This expansion is very analogous to aerosol processes for producing droplets. In RESS processes, however, there is no significant heat transfer problem to be overcome during the expansion and ‘‘evaporation’’ stage. As the supercritical solvent expands, its solubilizing power decreases, and the organic solute becomes supersaturated and condenses into either an amorphous solid state or a crystalline morphology. This kind of solvent shifting may be thought of as one-dimensional solvent shifting, as there is typically only one solvent component, the supercritical (or near-critical fluid). A laboratory-scale RESS system is illustrated in Fig. 9 [33]. The process is direct and simple. Dissolution of the organic in the near-critical or supercritical fluid occurs in the extraction chamber. Expansion with concomitant precipitation occurs in the next stage, the Utubes in this instance. Early applications of this process [33] to dodecanolactam (DL), ␤-estradiol, lecithin (Lec), and a blue azo-type pigment (Azo) demonstrated some of the potential of this technology. See Table 6 for structures. All of these organics were extracted (dissolved) at 55⬚C and 5000 psi in supercritical carbon dioxide, where the flow rate was maintained at 5–10 standard liters per minute, and were collected in the sequential U-tubes as illustrated in Fig. 6. Dodecanolactam polymerizes to form Nylon 12 and was available as a powder of irregular particles 5–10 ␮m in largest dimension. Under the operating conditions just described it is soluble at about 15% (w/w). Precipitation in this RESS system produced primary particles that were needles in the range of 10–30 ␮m in length and less than 1 ␮m in diameter. ␤-Estradiol was initially available as a polydisperse powder with largest dimensions in the range of micrometers to hundreds of micrometers. Reprecipitation in this RESS process produced particles uniformly less than 1 ␮m in largest dimension. Lecithin (Lec) is an important stabilizer and excipient in pharmaceutical formulations, and it often comes with many impurities such as phosphatidylinositol and phosphatidylenthanolamine, so that it is often soft and gummy and difficult to disperse by comminution processing. The Lec examined in this process consisted of large particles hundreds of micrometers in diameter. Application of the RESS process produced a very fine powder with primary particle sizes ranging up to several micrometers. A blue pigment, Navy Blue (Azo), was obtained as particulates in the range of 50–150 ␮m in largest dimension. This material was transformed into a fine powder having particle

592

Texter

FIG. 9 RESS flow system for precipitation of organic particulates from supercritical solutions. PC, pressure controller; P, pressure guage; TC, temperature controller; T, thermocouple. (From Ref. 33.)

sizes in the range of a few micrometers. The RESS process was also applied to polypropylene (PP) (Structure 12), although instead of carbon dioxide, supercritical propylene (140⬚C, 3500 psi) was used. The as supplied material consisted of large clumps scores of micrometers in diameter. The supercritical reprecipitated powder comprised very small particles (a few micrometers and smaller) that formed linear strings or linear clusters up to 50 ␮m in length. The morphology and size yielded by the RESS process vary dramatically with the target organic species. Solubility in the supercritical fluid, and how this solubility changes (decreases) as fluid density decreases, is a key parameter in modifying resulting particle size (growth) and how primary particles might tend to congeal during the process. Application of additional chemical components as stabilizers is an area that has not yet been very broadly investigated. B.

Gas Antisolvent Process

Another important supercritical process is the gas antisolvent (GAS) process. This process requires that the solute be essentially insoluble in the supercritical fluid and soluble in an auxiliary solvent. The auxiliary solvent will generally have at least limited miscibility with the supercritical fluid. The organic solute is dissolved in the auxiliary solvent to produce a solution. The supercritical fluid is then introduced into this solution, causing it to expand and causing, by ‘‘two-dimensional’’ solvent shifting (shifting the balance from predominantly one solvent component to another), the organic solute to precipitate as small particles. It is

important that the organic substrate be soluble in the auxiliary solvent and that the gas antisolvent (supercritical fluid) have finite solubility in the auxiliary solvent as well. This last requirement is necessary in order to be certain that the supercritical fluid will effectively expand the auxiliary solvent. In the absence of such mutual solubility, the injected supercritical fluid will tend not to ‘‘take the auxiliary solvent with it’’ while it expands, and two-phase separation at the outset will render the process relatively ineffective. It is also important that the organic substrate not be too soluble in the supercritical fluid, as the goal is to create a supersaturated solution during expansion from which the substrate will condense or precipitate. If the substrate has appreciable solubility in the gas antisolvent, then a much narrower window of pressure and temperature will be available for creating supersaturation. Gas antisolvent injection rates and extents of expansion are two control variables that can effectively be used to control particle size and polydispersity. A range of expansion ‘‘paths’’ is illustrated in Fig. 10. Curve A represents a long-time and low-expansion extreme case. The degree of expansion corresponds to the threshold pressure (THP), where weak turbidity corresponding to the first visual detection of precipitating particles is visually evident. Curve B represents a path that yields a continuously varying particle size distribution. The step-shaped path C yields a polydisperse distribution with discrete particle size modes generated during each plateau period. Stepping to a higher plateau induces secondary (and tertiary) nucleation and the growth of smaller particles. Path D yields small monodisperse particles.

Organic Particle Precipitation TABLE 6

593

Structures of Organics Reprecipitated by Supercritical Processing

This GAS process has been applied [34] to nitroguanidine (NG) (Structure 13) dissolved in dimethylformamide (DMF), an explosive that is not a prime candidate for comminution processing. The initial material consisted of crystalline needles in the range of 100 ␮m in length and about 5 ␮m in diameter. Using very rapid expansion paths, fine NG particles in the 3 ␮m range were obtained. Similar results were obtained using carbon dioxide and expanding rapidly (5 s) a

12% (w/w) solution of NG in DMF to 750 psi at 20⬚C or by rapidly expanding a 10% solution in critical chlorodifluoromethane to 75 psi at 20⬚C. When very slow (30 min) expansion was done at the threshold pressure (80 psi at 22⬚C) of a 5% NG solution in DMF using chlorodifluoromethane injection, quite large spheres in the range of 30–60 ␮m in diameter were obtained. When intermediate rates of expansion or paths were used, intermediate particle sizes were obtained. C.

STRUCTURE 12

PP.

Solution Enhanced Dispersion by Supercritical Fluids

An alternative process is the so-called solution enhanced dispersion by supercritical fluids, SEDS, pro-

594

Texter

(300 bar, 35⬚C) yielded crystalline particles of 7.5 ␮m median spherical diameter. Flow rates and working pressures could be used as control variables to modify particle sizes. V.

FIG. 10 Expansion paths for antisolvent (supercritical fluid) addition. THP denotes the threshold pressure for the onset of particle precipitation. Path A yields large, monodisperse particles. Path B yields polydisperse particles. Path C yields polydisperse particles, with discrete modes evident. Path D yields small monodisperse particles.

STRUCTURE 13

NG.

Weak acids such as pharmaceuticals, organic pigments, and dyes are often precipitated by acidifying a concentrated solution of a soluble anionic form. The in situ precipitation of such species to produce controlled submicrometer particle sizes while maintaining viscosity at a sufficiently low level to facilitate convective mixing and transport is often a challenge. This is because condensing organics readily form amorphous states and aggregate in almost a diffusion-limited fashion, leading to network and gel structures. We stress that pH shifting is a specialized example of solvent shifting. A.

cess. It is a solvent shifting process somewhat similar to the GAS process. However, in the SEDS process, the supercritical fluid and a solution of the organic principal compound in an auxiliary solvent are introduced into the expansion chamber simultaneously through a coaxial nozzle assembly [35,36]. This coaxial flow produces a dispersion of the two fluid phases. The auxiliary solvent is extracted into the supercritical fluid. This extraction leads to supersaturation of the organic principal and subsequent precipitation as small particles. Application of this SEDS process to salmeterol xinafoate (SX) (Structure 14) using acetone as auxiliary solvent (0.5% w/v) and supercritical carbon dioxide

PRECIPITATION BY pH SHIFTING

Organic Pigments

The nanoprecipitation of methine oxonol pigments of the general structure MO5 (Structure 15) by pH shifting has been described for mono-, tri-, and pentamethine (n = 1, 2, and 3, respectively) oxonols [37–39]. Such pigments have a variety of useful functions in various kinds of conventional photographic products, including microfilm, movie film, and reversal films. Such pigments are easily dissolved in dilute alkali because of the weakly acidic carboxylic acid groups and because of the fairly acidic oxonol proton. Note that two resonance forms for delocalization along the oxonol backbone can be written; this contributes to the acidity of these hydroxyl protons. Subsequent precipitation by

STRUCTURE 14

STRUCTURE 15

SX.

MO5.


acidification in the presence of various dispersing aids can produce very fine particle sizes and domain lengths at weight concentrations of up to 1%. Because of the carboxyl bifunctionality, such species tend locally to form hydrogen bonds that can yield lengthy nematic strings in one dimension but quite nanoscale cross sections normal to the nematic vector. An ultrafine dispersion of MO5 was prepared using a double-jet acid precipitation procedure [37,38] in which the pH was kept constant at 5.2 during precipitation. The pigment feed solution at 0.073 M was prepared by dissolution at pH 9 with dilute 2 N NaOH. The reactor was initially charged with water, gelatin, and Alkanol-XC (sodium di- and triisopropyl naphthalene sulfonate in about equal molar proportions). The pigment solution was fed into the reactor at a constant rate, and 2 N aqueous H2SO4 was added under feedback control in order to maintain a set pH (5.2). The amorphous precipitated particulates exhibited a nematic-type structure as revealed by cryo-TEM. The proton uptake at completion corresponded to only approximately 64%, so the balance of the sites was neutralized with sodium ions. The peculiar physical state obtained had serendipitous optical effects, as illustrated in Fig. 11. There one can see that an optical absorption envelope is obtained that is dramatically different from that obtained by comminution of the fully protonated pigment. Thus, we see that such a precipitation regimen yields a different physical state than obtained by presscake precipitation. Similar long-wavelength absorption envelopes have been produced for trimethine and monomethine analogues of MO5.

595

STRUCTURE 16

VI.

Some organic precipitations can yield crystalline habits. An example is given by pigment VI (Structure 16) precipitated similarly to the process just described for MO5 [39]. A slightly alkaline feedstock solution of VI, 1.9% by weight, was prepared by dissolving the pigment with 2 N NaOH at pH 7.5. Double-jet precipitation at pH 5 was done at 24⬚C using polyvinyl alcohol (molecular weight 15,000 to 30,000) in this reactor as a stabilizer. The precipitation yielded moderate-sized (up to several micrometers in largest dimension) microcrystallites. A comparison microcrystalline dispersion of VI was prepared by comminution and yielded comparably sized microcrystallites as determined by optical microscopic analysis. Thin-film coatings of these dispersions yielded the absorption spectra illustrated in Fig. 12. These spectra are essentially indistinguishable, as would be expected for comparably sized pigment particles in the same crystalline physical state. Thus, there are some organics that do crystallize relatively rapidly. B.

Pharmaceuticals

Smaller molecular weight weak acids are conventionally precipitated by acid-base techniques. Precipitation

FIG. 11 Visible absorption spectrum (curve 1) of MO5 dispersion coated at 108 mg/m2 in a thin film using gelatin (1.61 g/ m2) as a binder. Curve 2 is for a fully protonated counterpart of MO5 prepared by comminution processing and coated at 69 mg/m2 similarly with gelatin.

596

FIG. 12 Visible absorption spectrum (curve 1) of precipitated VI dispersion coated at 107 mg/m2 in a thin film using gelatin (1.61 g/m2) as a binder. Curve 2 is a comparison dispersion prepared by comminution processing and coated at 320 mg/m2 similarly with gelatin.

conditions affect particle size and physical state; often various polymorphs are accessible, depending on the precipitation process. A good example is the precipitation of phenobarbitone (PB, phenobarbital) (Structure 17). Thirteen polymorphs have been reported under various conditions. Generally increasing particle size is obtained [40] as the precipitating acid solution is made more dilute. This trend is consistent with elementary nucleation concepts in that the more slowly nucleation is induced, the fewer nuclei are created. This leads to larger crystals. Precipitation temperature was also observed to affect size, as well as polymorph form. Over the 10–50⬚C interval, form VIII of PB was produced and particle size increased with increasing temperature, from about 3 to 9 ␮m in largest dimension. As the temperature was increased further, form II of PB was produced and the size dropped below 3 ␮m. Form VIII is a monohydrate [40]. Direct precipitation of the triiodobenzoate ester IA (Structure 18), a radiographic contrast agent, was shown to be a reasonable direct alternative to comminution techniques for preparing aqueous dispersions [41]. An aqueous solution was prepared using 5 g of IA, 5 g of water, and 11.15 g of 20% aqueous NaOH. This mixture was heated to 56⬚C and then cooled to room temperature to yield a transparent solution. An aqueous stabilizer solution was prepared using 2.1 g of 60% Polystep B23 (Stephan) and 0.1 g of Aerosol OT in 125 g of water. These two solutions were then combined and neutralized using 75 mL of 15% propionic acid. The resulting dispersion was dialyzed to remove salts. The average particle size was about 250 nm in

Texter

STRUCTURE 17

PB.

STRUCTURE 18

IA.

largest dimension. Upon autoclaving, the average size increased to about 350 nm. A similar process was disclosed, but with the substrate molecule used to derive an aqueous stabilizer [42]. The benzoate derivative, DA (sodium diatrazoate) (Structure 19), was prepared to serve as a surface-active species with high affinity for IA surfaces. A dispersion was formulated using 20 g IA, 20 g of water, and 45 g of 20% aqueous NaOH. This mixture was dissolved by heating to 75⬚C and cooling to room temperature. The aqueous stabilizer solution was prepared using 0.4 g DA, 6.5 g Tetronic T-908, 500 g water, and 1 g 20% aqueous NaOH. These two solutions were combined and then neutralized with 300 g of 15% propionic acid to form IA particles about 230 nm in size. A further important variation of such precipitation processes is to use structurally similar materials to restrain particle growth. Such materials are known as crystal growth modifiers. When effective, they serve to restrain growth, thereby producing smaller particles (and a higher number density of particles per unit volume). One approach to designing such growth modifiers is to model them upon the substrate molecular structure but to alter the structure sufficiently that appreciable solid-state mutual solubility is avoided, while

STRUCTURE 19

DA.


597

B.

STRUCTURE 20

CGM.

intense surface activity, through structural correspondence, is achieved. An example applied to the precipitation of IA [43] is the modifier CGM (Structure 20). A mixture of 4 g IA, 1 g CGM, and 5 g water was dissolved using 11.5 g 20% aqueous NaOH and by heating to 55⬚C. After cooling, this solution was combined with aqueous stabilizer comprising 125 g water, 1.165 g Tetronic T-908, and 0.1 g Aerosol OT. This alkaline solution was then neutralized with 75 mL of 15% propionic acid to produce a dispersion, and this dispersion was then dialyzed to remove salt. The resulting particle size was about 194 nm. The size was dramatically smaller than the 274 nm obtained when another gram of IA was substituted for the CGM in this formulation.

VI.

MICELLES AND RELATED SYSTEMS

Micelles are thermodynamically stable nanoparticles that provide important templates for various kinds of materials, including thermodynamically metastable particles as discussed in Section B. Excellent discussions of the thermodynamic driving forces for forming micelles [44] and for forming mixed micelles [45] are available, so these topics will not be elaborated here. A.

Effects of Solvent and pH Shifting on Solubility

Solvent shifting is a process by which the solubility of a component is altered by changing the composition of the solvent. High solubility in one solvent can be mitigated by addition of another solvent in which the soluble component is much less or only sparingly soluble. Similarly, high solubility can often be obtained by ionizing an organic species, such as a weak carboxylic acid, in dilute alkali solution. Subsequent neutralization by pH shifting, or dropping the pH through the pK of the acid, generally yields a significant drop in solubility and is often accompanied by precipitation of the weak acid component.

pH Shifting Method of Priest

1. Dissolution and Micellization The use of pH shifting to utilize mixed micelle formation of alkali-soluble hydrophobic organic compounds and to stabilize such mixed micelles kinetically appears to have been disclosed first by Priest [46]. Such organic compounds have some weak acid functionality, such as — COOH, — OH, — SO2NH — R, and the like, that can be ionized at sufficiently high pH. Technologically useful candidates for such processes are colorforming couplers used to form indoaniline image dyes in photographic films and papers. Typical examples include structures VII to XI in Table 7. Ionization generally increases solubility in aqueous or an aqueous water-miscible solvent system to about 0.5% (w/w) or more. When ionized, these compounds are surface active and form micelles and mixed micelles with other surfactant or amphiphilic compounds. Upon lowering the pH by addition of mineral or organic acid, the solubility of these compounds decreases dramatically, and if the micelles in which these compounds reside are not kinetically stabilized, macroscopic crystals of the protonated species can readily form or other untoward effects may occur. 2. Stabilization Once the pH has been lowered and the amphiphilic ionized molecules have been reprotonated, one can no longer rely upon chemical free energy forces for stabilization because the most stable states have shifted to multiphase crystalline states. The kinetic stabilization of such reprotonated species can be achieved by more or less standard methods, such as charge, steric, and matrix stabilization techniques. (a) Charge Stabilization. The use of ionic surfactants, such as anionic and cationic surfactants having charged groups that remain charged at pH >1, is advantageous in producing mixed micelles with the weakly acidic organic compounds. After acidification and reprotonation of the weakly acidic organic compounds, the ionic surfactants remain charged and provide charge stabilization as long as the ionic strength of the suspension is suitably low and the charged groups are not excessively shielded by counterions. (b) Steric Stabilization. The use of nonionic surfactants and polymeric stabilizers (nonionic and polyelectrolytes) can provide effective stabilization of the reprotonated particles. Such use of polymeric stabilizers in conjunction with surfactants is illustrated in Fig. 13, where interfacial tension at the air-water or hydrocarbon-water interface is illustrated as a function of sur-

598

Texter TABLE 7

Amphiphilic Color-Forming Photographic Couplers

FIG. 13 Schematic for surface tension lowering as a function of surfactant concentration with and without added polymeric stabilizer that interacts with the surfactant. The full line corresponds to the case of no polymer, and the dashed curve indicates aggregation processes occurring in the presence of polymer. (Reproduced by permission from Ref. 47; copyright American Chemical Society.)


factant concentration [47]. The self-assembly of surfactant and polymeric stabilizer in the bulk and at the interface is illustrated by cartoons in five different regimes of surfactant concentration (a–e). In the low surfactant concentration limit (region a) the polymeric stabilizer adsorbs at the interface and little complexation between surfactant and polymer occurs in the bulk. At higher concentration (region b) the situation in bulk solution has not changed much, but surfactant adsorbs to the interface. As the concentration rises further (region c), the polymer nucleates surfactant aggregation in the bulk. The surfactant concentration at point T1 is the so-called critical aggregation concentration. At higher concentration (region d), polymer desorbs (at concentration C*) from the interface in order to bind to aggregates in the bulk. In the highest concentration region (e) all of the polymer is involved in aggregates and then conventional surfactant micelles form. In the absence of polymer the surfactant critical micelle concentration (cmc) is found as illustrated by the solid line in Fig. 13.

599

identifying stability domains for the organic amphiphiles of interest. 3. Examples Coupler VII (200 mg) and 100 mg of N,N,N⬘,N⬘-tetraethylphthalamide dissolved in diethoxymethane were mixed with 1.5 mL of 0.4 N KOH. The dimethoxymethane was removed in a nitrogen stream to yield a clear micellar solution. About 3 mL of 10% (w/w) type V gelatin was added and the pH was adjusted to 10. Butyrolactone (0.12 mL) was added to protonate the coupler and to lower the pH. The dispersion that formed also gelled and imparted matrix stabilization. The dispersion was stable for more than a month at room temperature and could be melted easily by moderate heating. A flowchart of this assisted micellization approach is detailed in Fig. 14. Surfactant and substrate (coupler) solutions are combined under appropriate pH and sol-

(c) Matrix Stabilization. Organic particulates are stabilized against collision-based aggregation and growth processes when the viscosity of the continuous phase is increased to the point where particle diffusion is shut down or dramatically retarded. Such ‘‘matrix’’ stabilization can be achieved by using thickeners or associative thickeners to increase viscosity. Another very effective approach is to use a polymeric solution in the continuous phase that forms a gel network. Upon gelation, the mobility of particles therein is effectively quenched. (d) Chemical Stabilization. Most complex organic molecules that are greater than a few hundred daltons in molecular mass and that are amphiphilic and have hydrolyzable linkages are susceptible to a variety of hydrolysis reactions and are pH sensitive. The rigors of dissolution through ionization can also lead to untoward chemical decomposition, as increasing pH leads to increasing rates of nucleophilic attack by hydroxyl ion and concomitant hydrolysis chemistry. The susceptibility of alkali-soluble hydrophobic organic compounds to such hydrolysis chemistry varies widely with the particular structure and species. The pH range and electrolyte composition during the dissolution and micellization processes must therefore be controlled in order not to induce significant decomposition during the initial stages of particle preparation. Often water-miscible solvents must be chosen to aid dissolution while permitting lower alkali levels to be used [48,49]. Phase diagrams can be particularly useful in such cases in

FIG. 14 Schematic block diagram of nanoparticle precipitation using pH shifting in mixed micellar systems. Mixed micelles of surfactant and amphiphilic coupler (or other amphiphilic organic compound containing weak acid groups) are formed using chemical free energy. The mixed micelles are reacted with acid in a controlled manner in order to reprotonate the amphiphilic coupler and to lock in the nanoscale structure. Excess salt is then removed by ultrafiltration. (From Ref. 48.)

600

vent conditions to form a mixed micellar solution. This solution is fed into a reactor, where the substrate species are reprotonated under controlled conditions, thereby creating metastable nanoparticles of substrate and surfactant. The dispersion so produced is then subjected to washing by ultrafiltration or other dialysis means in order to remove unwanted salts and/or solvents. A major limitation that applies to such alkali-assisted dissolution techniques, especially for multifunctional organic molecules, is untoward decomposition and hydrolysis. For example, the coupler X (Table 7) is not stable in aqueous alkali when dissolved. However, mixtures with n-propanol are stable for appreciable times. A ternary stability diagram is illustrated in Fig. 15. This diagram illustrates a composition regime in which X is stable for longer than it takes to undergo the dissolution-reprotonation process illustrated in Fig. 14. The dispersion process involved preparing a Dupanol ME surfactant solution comprising 900 g surfactant, 4.1 kg PVP, and 329 kg water, and a solution of X (8.2 kg) also comprising 18.1 kg n-propanol and 13.7 kg of 1 M aqueous NaOH, both at 25⬚C. In less than 20 min these two solutions were mixed as shown in Fig. 14, metered into a continuous stirred tank reactor (CSTR) at 18.4 kg/min, and mixed with a 15% (w/w)

Texter

STRUCTURE 21

acetic acid solution metered at 300 g/min. The resulting dispersion was washed for three turnovers at constant volume, pH adjusted to 5.2, and concentrated by ultrafiltration to 5.5% X. This dispersion was optically transparent and was stable for more than 3 weeks [49]. A newer approach to drug delivery is the combination of linking chemistry with amphiphilic water-insoluble carriers developed for photographic applications. The various technologies useful for dispersing photographically useful compounds can then be brought to bear on preparing nanosize dispersions of pharmaceutically useful compounds that are linked to photographically useful carrier species. For example [50], consider PL-IA (Structure 21), which contains a triiodo group, thus qualifying as an image contrast agent (for radiography). A substrate solution of 5 g PL-IA, 5 g npropanol, and 20% aqueous NaOH was prepared, heated to 55⬚C, and cooled to room temperature. This solution was combined with 125 g water and 45 g of 33% aerosol A102 and then neutralized with 15 g of 15% propionic acid. The dispersion was then dialyzed to remove salts. The average particle size obtained was only 12 nm. The bioavailability of such formulations is extremely high. C.

FIG. 15 Stability diagram for coupler X in mixtures of npropanol and aqueous 1 M NaOH. The region of stability is given on the left by the noncrosshatched region. (From Ref. 48.)

PL-IA.

Stabilization by Polymerization

Kline [51] has illustrated the stabilization of micelles by polymerizing polymerizable counterions in the headgroup region. The system studied comprised rodlike micelles of cetyltrimethylammonium 4-vinylbenzoate (CTVB) (Structure 22). Highly viscous solutions of CTVB are formed at millimolar concentration and ˚ comprise highly entangled rodlike micelles about 40 A in diameter. After free radical polymerization of the 4˚ vinylbenzoate counterion, cylindrical rods about 400 A in length were formed from micellar solutions 0.1% and 1.0% in CTVB. The initial viscosities of these solutions were quite different, but essentially identical reaction products were obtained after polymerization.


601

STRUCTURE 22

While the entangled micelles in the highly viscous CTVB solutions may be branched, the rodlike micelles ˚) stabilized by the polymerization appear shorter (400 A and behave in some respects as uncharged rods. These micelles with their linear polymer coating appear stable for times in excess of a year. These suspensions may be dried and then redispersed in water; the rods retain their dimensionality. These suspensions can also be put through freeze-thaw cycles without including surfactant crystallization. On the whole, this approach appears an effective exoskeletal way to stabilize soft micellar structures. D.

Vesicles

Vesicles and liposomes are important particulate objects for many reasons, particularly with respect to drug delivery, and are extensively reviewed [52,53]. The production of vesicles is usually by some shear-assisted means, and such approaches fall outside the scope of our present chapter. However, an important exception is a class of thermodynamically stable micelles discovered by the Kaler-Zasadzinski collaboration [54,55]. Isotropic micellar solution domains in ternary water, cationic surfactant, anionic surfactant systems were discovered that contained thermodynamically stable vesicles. The first report [54] used cetyltrimethylammonium tosylate (CTAT) and sodium dodecylbenzene sulfonate (SDBS). One domain in which vesicles formed spontaneously was characterized as being primarily cationic surfactant, with less than a stoichiometric ratio of anionic, and another domain comprised mainly anionic surfactant, with a smaller amount of cationic. At stoichiometric equivalence, the surface-active ions precipitate to form an insoluble double tail salt, so excess population by one of the species is necessary to obtain stability and curvature. It is believed that the ratios of different surfactants vary among the inner and outer halves of the bilayer membrane. Recent work has shown that unilamellar and double lamellar vesicles may be spontaneously formed (E. W. Kaler and J. A. Zasadzinski, private communication, 1999).

STRUCTURE 23

MyrA.

E.

CTVB.

Nanodiscs

As a logical extension of the formation of thermodynamically stable vesicles, the controlled use of mixtures of cationic and anionic surfactants (catanionic solutions) has produced thermodynamically stable nanodiscs of essentially bilayer thickness and diameters ranging from tens of nanometers to several micrometers [56]. A key limitation in the stabilization of thermodynamically stable structures deriving from catanionic solutions is the electrostatic screening length dictated by the associated ionic strength. A 5% (w/w) catanionic solution may have an electrolyte concentration of about 0.1 M from the counterion salts formed. Such electrostatic screening promotes the formation of closed vesicles over discs. In this preparation of nanodiscs the catanionic solutions were prepared from myristic acid (MyrA) (Structure 23) and cetyltrimethylammonium hydroxide (CTAOH) (Structure 24). Solutions were purged with nitrogen to eliminate carbonate. The protons and hydroxyl ions combine to form water, so the net ionic contributions to ionic strength emanate from the hydroxyl ions associated with the excess cationic surfactant level. Such steps helped maintain the ionic strength close to 10 ␮M and the conductivity at about 10 ␮S cm⫺1. A screening length of about 100 nm was obtained, rather than a legnth of about 10 nm if alkali and halide counterions had been used. The cationic excess results in excess hydroxyl species, and pH varied between 7 and 13, depending on the degree of excess. The physical properties of the nanodiscs obtained vary with the compositional variables in this pseudoternary system (water, myristic acid, and CTAOH). The total amount of surfactant is denoted c (wt%) and the mole fraction of myristic acid to total surfactant is denoted r. A single-phase region (U⫹) in the water-rich corner yielded stable nanodiscs. In the presence of atmospheric CO2, this region U⫹ is bounded from above by c = 0.1%. In the presence of atmospheric CO2, nanodiscs are found in a two-phase region with a lamellar phase. Herein disc diameters vary from 30 nm to sev-

STRUCTURE 24

CTAOH.

602

Texter

eral micrometers. A schematic cross-sectional view of such discs is shown in Fig. 16. VII. A. FIG. 16 Perspective cross-section view of nanodisc particles synthesized from mixtures of anionic and cationic surfactants. The particle surfaces comprise ion pairs (de facto double-tail zwitterionic surfactants) and the rounded edges comprise an excess of cationic surfactant. The central layer of the nanodisc comprises hydrocarbon chains that appear to adopt a near-crystalline packing arrangement. (Courtesy of Professor Thomas Zemb.)

STRUCTURE 25

AOT.

Summary of Phase Diagrams

Microemulsions are thermodynamically stable micellar emulsions of two immiscible liquids stabilized by a third chemical component, a surfactant. A typical ternary phase diagram is illustrated in Fig. 17. There are usually two isotropic microemulsion domains in such systems [57]: an L1 domain, corresponding to a nominally oil-in-water droplet structure, and an L2 domain, corresponding to a water-in-oil droplet structure. Reverse microemulsions comprising water cores surrounded by a surfactant layer have become increasingly used as nanoreactors for exploring various kinds of chemistries, including inorganic precipitations [59], inorganic polymerizations [60], organic polymerizations [61], and enzymatic catalysis [62]. Until recently, there had been no reports of organic precipitations of nanoparticles in such microemulsion media. B.

FIG. 17 Ternary phase diagram of surfactant, oil, water microemulsion. Isotropic single-phase oil-in-water (L1) and water-in-oil (L2) microemulsion domains are illustrated. In some systems, or with variation in some field variable (temperature, fourth chemical component concentration), these L1 and L2 domains may become simply connected, as illustrated by the dotted lines. In such circumstances an irregular bicontinuous microemulsion comprising interdigitated oil and water domains connects these L1 and L2 domains.

MICROEMULSIONS

Solvent Shifting

The first example of precipitating organics in a reverse microemulsion has been described [63], and these processes are described more fully in Chapter 30 and in some recent manuscripts (F. Debuigne, L. Jeunieau, M. Wiame, and J. B.Nagy, submitted). The reverse microemulsion system was a water-in-heptane microemulsion prepared with Aerosol OT (AOT) (Structure 25). The organic substrates, rhodiarome (RhoD) (Structure 26) and rhovanil (Rhov) (Structure 27), were dis-

STRUCTURE 26

RhoD.

STRUCTURE 27

RhoV.


solved in water-miscible solvents such as acetone, ether, and ethanol and then added dropwise to the reverse microemulsion system. The weight of added active solution was generally equal to the weight of water solubilized in the microemulsion. Substrate concentrations were varied over the 50 to 400 g/L range, but this concentration did not affect particle size much. Average particle diameters in the range of 5–7 nm were obtained. These examples illustrate compartmentalization by the water pools in the microemulsions. The auxiliary solvent solution of the organic principal is directed to the microemulsion droplets where precipitation occurs. The same process has been used to produce nanocrystallites of cholesterol (F. Debuigne et al., submitted). VIII.

GAS CONDENSATION

The formation of inorganic ultrafine particles by gas evaporation, gas condensation, and related vacuum– gas phase processing methods has been very well developed for producing nanoparticulate metals, oxides, and ceramic precursors [64–66]. Such methods have been successfully extended to certain organic particulates. Such techniques use one method or another to vaporize the organic compounds, often into a low pressure or partially evacuated chamber. In the gas phase, collisions among molecules lead to condensation of clusters and particles, which may aggregate further with one another before adhering to a solid collection device or filter. Such techniques are limited to organic materials that will vaporize with heating without decomposing. A purported advantage of this gas condensation method is that the resulting particles have a more narrow particle size distribution than obtained, for example, by standard comminution methods. Another is that such fine particulates can be readily dispersed in water, even though the underlying organic material may be hydrophobic. This gas condensation method has been successfully applied [67] to relatively low molecular weight compounds such as anthrahacene, carbazole, ␤-carotene, chloramphenicol, cortisone acetate, phthalocyanine, and pyrene. It has also been applied to some polymers, including polyethylene, polyvinyl alcohol, polyvinyl chloride, and polystyrene. Particle size can be controlled by temperature and pressure, particularly the partial pressure of added inert noble gases. Figure 18 shows a fluorescence micrograph of pyrene particles produced by vapor phase condensation. The nominally 100-nm particles in Fig. 18a were produced at 150⬚C in a 0.1 torr helium background. The pyrene was heated in a crucible about 20 cm away from the target sub-

603

strate (glass). The 3-␮m-diameter particles of Fig. 18b were obtained similarly, except a helium gas pressure of 5 torr was used. Identical conditions except for a lower partial pressure of helium (0.1 torr) yield pyrene particles about 100 nm in diameter. An important difference for most organics precipitated in this way is that they do not tend to form fractal aggregates as readily as metals and ceramic precursors produced by such methods. IX.

ENCAPSULATION METHODS

A particularly effective way to stabilize organic particles is to precipitate them inside a matrix (matrix stabilization) or inside a hollow particle or cavity. The particle or cavity wall (shell) effectively prevents organic nuclei from coming in contact with other cores by virtue of a (steric) ‘‘cell wall.’’ An alternative approach would be to precipitate an organic particle by means such as detailed earlier and then encapsulate by one or more mechanisms of microencapsulation, such as coacervate formation, or by some condensation type of polymerization [68]. The use of preformed hollow capsules or hollow particles provides very effective limitations on the size of the resulting precipitated particles because of the compartmentalization of the precipitation chemistry. An alternative encapsulation approach to having the organic precipitated particle in the core region of an encapsulated composite particle is to layer the precipitated organic material on the exterior of a templating core material. Yet another approach is to produce composite particles by precipitating organic materials in a matrix that forms disperse particles. A.

Precipitation in Reverse Emulsions

Precipitation in so-called liquid membranes or multiple reverse emulsions offers a convenient approach to selective extractions for analytical and preparative purposes. For example [69], the selective removal of cupric ions from commercial acid leach solutions containing copper sulfate and contaminating ions such as ferric, ferrous, and nickel ions can be accomplished by combining ion-specific ligands with an organic precipitating species, such as oxalate. The acid oxalate precipitating aqueous solution is dispersed as a water-inoil emulsion, such as kerosene, using an oil-soluble surfactant, such as Span 20 (sorbitan laurate). A ligand specific for cupric ion, such as 2-hydroxy-5-nonylacetophenone, is included in the oil phase. This waterin-oil emulsion is then crudely emulsified with the

604

Texter

FIG. 18 Fluorescence micrographs of pyrene produced by a gas condensation process. (a) 100-nm-diameter particles produced at 0.1 torr helium background; (b) nominally 3-␮m-diameter particles produced at 5 torr helium background pressure. (Adapted from Ref. 68.)

aqueous metal ion solution to produce a water-in-oilin-water double emulsion. The ligand selectively transports copper across the kerosene membrane, wherein copper precipitates in the interior aqueous droplets as the oxalate. The size of such precipitates is compartmentalized by the inner water droplets and is significantly less than obtained in batch precipitations of copper and oxalate. B.

Precipitation in Encapsulating Spheres

Recently, the layer-by-layer polyelectrolyte-nanoparticle self-assembly technique has been applied to polymer particle templates as a means for producing hollow silica spheres. Such spheres may be produced over a wide range of micrometer and submicrometer inner diameters, and the thickness and permeability of the walls may be varied by proven formulation variations. Such spheres have been shown to be venues for organic

particle precipitation [70]. The spheres are suspended in a solvent for the organic solid to be precipitated, with subsequent addition of a solution of the principal compound, or alternatively they are suspended in a solution of the principal compound. The compound then permeates the sphere wall, so that the sphere is filled with a solution of the principal agent. A nonsolvent, miscible with the original solvent, is then added slowly to the suspension. The nonsolvent also permeates the sphere walls and then initiates precipitation of the principal compound inside the hollow silica spheres by a solvent shifting process. Alternatively, pH shifting may be used. Nucleation sites or other as yet not well understood factors typically induce precipitation inside the spheres prior to precipitation in the continuous phase. Thus, precipitation internally sets up radical diffusion gradients that feed more active compound into the spheres. This modified solvent shifting method pro-


605

duces encapsulated particulates for possible applications in drug delivery and in organic pigments. A variety of colloidal particles may be used for templating. For example, human erythrocytes have been templated using nine alternating layers of 4-poly (styrene sulfonate, sodium salt) and poly(allylamine hydrochloride) [70]. After wall formation, the templating erythrocyte contents were removed by oxidation with sodium hypochlorite. The weak acid 6-carboxyfluorescein (6CF; see Table 8 for structure) was solubilized at 10⫺3 M at pH 10.5 and imbibed into empty capsules. The 6CF was then precipitated by lowering the pH to 6 with addition of dilute aqueous HCl. Scanning electron microscopy images showed the nominally 5 ␮m diameter particles to make up a distinguishable core region about half the diameter of the particles. The lack of precipitate in the continuous phase points to the probable preponderance of heterogeneous nucleation sites inside the hollow particles and possibly in the alternating shell layers. Weak bases such as rhodamine 6G (6G) can also be precipitated in such hollow shells by pH shifting. Increasing pH leads to precipitation of 6G from a saturated solution in the presence of erythrocyte-templated hollow capsules. A rapid pH increase to 12 results in rodlike 6G needles in the continuous phase; a slower pH increase to 10 leads to solely intracapsule 6G rod precipitation with no ‘‘extracellular’’ material; milder and slower pH change to 8 leads to amorphous 6G precipitation in the cores. Salting out and solvent shifting have also been demonstrated in such hollow capsules for dyes such as pseudoisocyanine hexafluorophosphate (PIC) and bis(dimethylamino)heptamethine (DMHM) [70].

TABLE 8

C.

Nanocolorant Precipitation

An interesting process for dispersing organic dyes has been disclosed by BASF [71]. This process combines aspects of emulsification, precipitation, and miniemulsion polymerization in achieving small particle dispersions of organic colorants. The primary step involves being able to solubilize colorant (dye) at high load (10–20% w/w) in a polymerizable vinyl monomer, such as acrylates, styrenes, and methacrylates. In addition to the polymerizable monomer, a relatively high fraction of cross-linking monomer (bifunctional monomer) is added. A hydrophobic additive, such as hexadecane, is then added so as to osmotically stabilize the resulting miniemulsion from untoward Ostwald ripening and growth. This colorant-monomer solution is then homogenized under pressure to produce a submicrometer-sized miniemulsion, with particle sizes less than 200 nm. Suspension polymerization is then initiated using a thermal initiator or by using UV irradiation. When cross-linking is sufficiently fast and dense, the colorant is kinetically trapped within the crosslinked matrix. Full polymerization typically produces a polymeric matrix in which the colorant has low solubility, and so it condenses locally to the extent possible before further transport is impeded by the cross-linking of the polymer network. Thus nanodomains of organic colorant are encapsulated as metastable embryos within the highly cross-linked polymeric matrix. Phase separation on the mesoscale of the particle size is prevented. The phase separation that occurs on the nanoscale corresponds to domains that are nearly molecular in their electronic absorption properties, and extremely high coloring power is obtained.

Organic Dyes Precipitated in Hollow Capsules

606

Texter

ACKNOWLEDGMENTS

21.

Thanks are extended to M. Christine Brick for permission to present some of her preliminary Ph.D. thesis results, including Figs. 6 and 7, on dispersion of organic pigments by miscible solvent shifting. We are also indebted to Professor B.Nagy of Namurs and to F. Debuigne for permission to cite some of her Ph.D. research on precipitation of organics in microemulsions prior to publication.

22.

REFERENCES 1. 2. 3. 4.

5. 6.

7. 8. 9. 10. 11.

12. 13. 14. 15. 16.

17. 18. 19. 20.

B. P. Binks, J. H. Clint, P. D. I. Fletcher, and S. Rippon, Langmuir 14:5402–5411 (1998). K. Naito, K. Ohe, and N. Tsuji, U.S. Patent 4,21,862 (1980). T. C. Patton, Paint Flow and Pigment Dispersion, 2nd ed., Wiley, New York, 1979, pp. 376–512. R. B. McKay and F. M. Smith, in Dispersion of Powders in Liquids (G. D. Parfitt, ed.), 3rd ed., Applied Science Publishers, London, 1981, pp. 471–505. Society of Dyers and Colourists, Color Index, 3rd ed., 1982. R. B. McKay, in Technological Applications of Dispersions (R. B. McKay, ed.), Marcel Dekker, New York, 1994, pp. 143–176. E. W. Kaler, K. L. Herrington, A. K. Murthy, and J. N. Zasadzinski, J. Phys. Chem. 96:6698–6707 (1992). J. L. Katz and M. D. Donohue, Adv. Chem. Phys. 40: 137–155 (1979). I. Leubner, Curr. Opin. Colloid Interface Sci. 5:151– 159 (2000). J. W. Mullin, Crystallization, 3rd ed., ButterworthHeinemann, Oxford, 1993. J. Kapecki and J. Rodgers, in Kirk-Othmer Encyclopedia of Chemical Technology, 4th ed., Vol. 6, Wiley, New York, 1993, pp. 965–1002 J. Texter, J. Imag. Sci. Technol. 39:340–354 (1995). J. Texter, D. S. Ross, and T. Matsubara, J. Imag. Sci. 34:123–131 (1990). J. Texter, J. Photog. Sci. 36:14–17 (1988). C. Schwarz, W. Mehnert, J. S. Lucks, and R. H. Muller, J. Contr. Rel. 30:83–96, 1994. B. Sjo¨stro¨m, B. Bergensta˚hl, M. Lindberg, and A. C. Rasmuson, J. Dispersion Sci. Technol. 15:9–117 (1994). T. H. Whitesides and D. S. Ross, J. Colloid Interface Sci. 169:48–59 (1995). G. Wu and E. Matijevic´, J. Dispersion Sci. Technol. 19: 903–913 (1998). A. Tentoria, E. Matijevic´, and J. P. Kratohvil, J. Colloid Interface Sci. 77:418–426 (1980). G. Wu, A. Koliadima, Y.-S. Her, and E. Matijevic´, J. Colloid Interface Sci. 195:222–228 (1997).

23. 24.

25. 26. 27. 28. 29. 30. 31. 32. 33.

34.

35. 36.

37. 38. 39. 40. 41. 42. 43. 44. 45.

C. Duclairoir, E. Nakache, H. Marchais, and A.-M. Orecchioni, Colloid Polym. Sci. 276:321–327 (1998). I. Expeleta, J. M. Irache, S. Stainmesse, C. Chabenat, J. Gueguen, Y. Popineau, and A.-M. Oricchioni, Int. J. Pharm. 131:191–200 (1996). H. Auweter, V. Andre´, D. Horn, and E. Lu¨ddecke, J. Dispersion Sci. Technol. 19:163–184 (1998). D. Horn and E. Lu¨ddecke, in Fine Particles Science and Technology—From Micro to Nanoparticles (E. Pelizetti, ed.), NATO Advanced Science Institutes Series 3, Vol. 12, Kluwer Academic Publishers, Dordrecht, 1996, pp. 761–775. E. B. Gutoff and T. F. Swank, AIChE Symp. Ser. (No. 193) 76:43–51 (1980). L. Godowsky and J. J. Duane, U.S. Patent 2,870,012 (1959). M. R. Violante and R. T. Steigbigel, U.S. Patent 4,783,484 (1988). M. R. Violante and H. W. Fischer, U.S. Patent 4,826,689 (1989). M. R. Violante and H. W. Fischer, U.S. Patent 4,997,454 (1991). S. Frank, J.-E. Lo¨froth, and L. Bostanian, U.S. Patent 5,780,062 (1998). S. A. Jenekhe and X. L. Chen, Science 279:1903–1907 (1998). S. A. Jenekhe and X. L. Chen, Science 283:372–375 (1999). V. Krukonis, Supercritical fluid nucleation of difficultto-comminute solids, Proceedings 1984 Annual Meeting, AIChE, San Francisco, November 25–30, 1984, paper 140f. P. M. Gallagher, M. P. Coffey, V. J. Krukonis, and N. Klasutis, in Supercritical Fluid Science and Technology (K. P. Johnston and J. M. L. Penninger, eds.), American Chemical Society, Washington, DC, 1989, pp. 334– 354. M. H. Hanna, P. York, D. Rudd, and S. Beach, Pharm. Res. 12:S141 (1995). P. York and M. Hanna, in Respiratory Drug Delivery V (R. N. Dalby, P. R. Byron, and S. J. Farr, eds.) Interpharm Press, Buffalo Grove, IL, 1996, pp. 231–239. J. Texter, U.S. Patent 5,274,109 (1993). J. Texter, U.S. Patent 5,326,687 (1994). J. Texter, W. B. Travis, and V. J. Flow, U.S. Patent 5,624,467 (1997). G. S. Riley, SCI Monogr. 38:267–281 (1973). P. Bagchi, P. H. Karpinski, and G. L. McIntire, U.S. Patent 5,560,932 (1996). P. Bagchi, G. L. McIntire, and J. R. Minter, U.S. Patent 5,716,642 (1998). P. Bagchi, R. P. Scaringe, and H. W. Bosch, U.S. Patent 5,665,331 (1997). J. Israelachvili, Intermolecular & Surface Forces, 2nd ed., Academic Press, London, 1992, pp. 341–365. M. J. Rosen, Surfactants and Interfacial Phenomena, 2nd ed., Wiley, New York, 1989, pp. 393–418.

Organic Particle Precipitation 46. 47. 48. 49. 50. 51. 52. 53.

54. 55. 56. 57.

58. 59.

W. J. Priest, Res. Disc. (No. 16468), December 1977, pp. 75–80. K. Chari, J. Minter, N. Ferris, and P. Amato, J. Phys. Chem. 97:2640–2645 (1993). K. Chari and J. T. Beck, U.S. Patent 5,256,527 (1993). K. Chari, Chem. Technol. 29:49–55 (1999). P. Bagchi, R. C. Stewart, G. L. McIntire, and J. R. Minter, U.S. Patent 5,662,883 (1997). S. P. Kline, Langmuir 15:2726–2732 (1999). M. Rosoff, ed., Vesicles, Marcel Dekker, New York, 1996. R. Arshady, ed., Microspheres, Microcapsules and Liposomes, Vol. 1, Preparation & Chemical Applications, Citus Books, London, 1999. E. W. Kaler, A. K. Murthy, B. E. Rodriquez, and J. A. Zasadzinski, Science 245:1371–1374 (1989). L. L. Brasher and E. W. Kaler, Langmuir 12:6270– 6276 (1996). T. Zemb, M. Dubois, B. Deme, and T. Gulik-Krzywicki, Science 283:816–819 (1999). S. E. Friberg and P. Bothorel, eds., Microemulsions: Structure and Dynamics, CRC Press, Boca Raton, FL, 1987. J. Eastoe and B. Wayne, Curr. Opin. Colloid Interface Sci. 1:800–805 (1996). K. Kon-No, in Structure-Performance Relationships in Surfactants (K. Esumi and M. Ueno, eds.), Marcel Dekker, New York, 1997, pp. 551–582.

607 60.

61. 62. 63.

64. 65. 66. 67.

68. 69. 70. 71.

T. Li, J. Moon, A. A. Morrone, J. J. Mecholsky, D. R. Tallham, and J. H. Adair, Langmuir 15:4328–4334 (1999). N. Moumen, M.-P. Pileni, and R. A. Mackay, Colloids Surf. A 151:409–417 (1999). M.-P. Pileni, ed., Structure and Reactivity in Reverse Micelles, Elsevier, Amsterdam, 1989. F. Debuigne, L. Jeunieau, M. Wiame, and J. B. Nagy, The synthesis of rhodiarome nanoparticles by direct precipitation in a microemulsion, in Proceedings of the 73rd ACS Colloid and Surface Science Symposium (P. E. Laibinis and T. A. Hatton, eds.), MIT, Cambridge, 1999, paper 90. R. W. Siegel, Mater. Sci. Eng. B 19:37–43 (1993). R. W. Siegel, Sci. Am. 275:74–79 (1996). C. Hayashi, R. Uyeda, and A. Tasaki, eds., Ultra-Fine Particles, Noyes Publications, Westwood, NJ, 1997. H. Toyotama, in Ultra-Fine Particles (C. Hayashi, R. Uyeda, and A. Tasaki, eds.), Noyes Publications, Westwood, NJ, 1997, pp. 286–292. F. Lim, ed., Biomedical Applications of Microencapsulation, CRC Press, Boca Raton, FL, 1984. M. Yang, G. A. Davies, and J. Garside, Powder Technol. 65:235–242 (1991). G. Sukhorukov, L. Da¨hne, J. Hartmann, E. Donath, and H. Mo¨hwald, Adv. Mater. 12:112–115 (2000). T. Clemens, A. J. Boehm, and S. Kielhorn-Bayer, Polym. Prepr. 41:24–25 (2000).

30 Synthesis of Inorganic and Organic Nanoparticles in Microemulsions L. JEUNIEAU, F. DEBUIGNE, and JANOS B.NAGY Namur, Belgium

I.

Universitaires Notre-Dame de la Paix,

INTRODUCTION

first case the particle size varies as a function of either the size of the inner water cores or the precursor concentration in the microemulsions; in the second case the particle size is independent of these parameters.

The synthesis of monodisperse nanometer-size nanoparticles is of great technological and scientific interest. Quantum size effects are particularly of interest because they lead to interesting mechanical, chemical electrical, optical, magnetic, electro-optical, and magneto-optical properties that are quite different from those reported for bulk materials [1–4]. Nanoparticles not only are of basic physical interest but also have resulted in important technological applications, such as in catalysts, high-performance ceramic materials, microelectronic devices, and high-density magnetic recordings [5–7]. The synthesis of nanoparticles in microemulsion allows one to obtain monodisperse particle sizes. In some cases it is possible to control the size of the particles by variation of the microemulsion droplet radius and of precursor concentrations. Although the synthesis of inorganic particles in microemulsion is already widespread, only polymer nanoparticles have been synthesized in microemulsion media, as far as organic particles are concerned [8–10]. In this chapter, it will be shown that it is also possible to synthesize organic particles by precipitation in microemulsions. We emphasize some of the fundamental aspects of monodisperse nanoparticles formation. Two models are proposed for the formation of the particles: the first is based on the LaMer diagram; the second is based on the thermodynamic stabilization of the particles. In the

A.

Preparation of Nanoparticles Using Microemulsions

1. Description of the Microemulsions A water-in-oil microemulsion is a thermodynamically stable, optically transparent dispersion of two immiscible liquids stabilized by a surfactant. The important properties are governed mainly by the water-surfactant molar ratio (R = [H2O]/[surfactant]). This factor has often been linearly correlated with the size of the water droplets. Nanoparticles have been synthesized in different reverse microemulsion systems. Ternary phase diagrams for some of these are shown in Fig. 1, where the isotropic reverse microemulsion (L 2) domain boundaries are illustrated. The anionic AOT (bis(2-ethylhexyl)sodium sulfosuccinate)/heptane/water system is one of the best characterized microemulsion systems [11,12]. The cationic cetyltrimethylammonium bromide (CTAB)/hexanol/ water system contains hexanol as the organic phase; in many other formulations hexanol plays the role of cosurfactant [13]. The nonionic penta(ethylene glycol) dodecyl ether (PEGDE)/hexane/water system was studied by Friberg and Lapczynska [14]. The reverse micellar droplets have a cylindrical shape in which the 609

610

FIG. 1

Jeunieau et al.

Ternary phase diagrams for various microemulsion systems. Reverse microemulsion L2 domains are illustrated.

surfactant molecules stay parallel to each other, forming a bilayer impregnated with water. The Triton X100 (p-(1,1,3,3-tetramethylbutyl)phenyl-polyethoxyethanol)/decanol/water system has been characterized by Ekwall et al. [15,16]. 2.

Mechanism of Synthesis of Nanoparticles in Microemulsion The aqueous droplets in reverse microemulsions continuously collide, coalesce, and break apart, resulting in a continuous exchange of solution content between nanodroplets. In fact, the half-life of the exchange reaction between the droplets is of the order of 10⫺3 – 10⫺2 s [17,18]. Two models have been proposed to explain the variation of the size of the particles with the precursor concentration and with the size of the aqueous droplets.

The first is based on the LaMer diagram [19,20]. This diagram (Fig. 2) has been proposed to explain the precipitation from solution in terms of supersaturation, nucleation, and growth. It illustrates the variation of the concentration with time during a reaction of precipitation and is based on the principle that nucleation is the limiting step in the reaction of precipitation. In the first step, the concentration increases continuously with increasing time. As the concentration reaches the critical supersaturation value, nucleation occurs. This leads to a decrease of the concentration. Nucleation continues as the concentration C* max falls to C* min , at which point particle growth is presumed to replace particle nucleation. Later, the decrease of the concentration is due to the growth of the particles by diffusion. This growth occurs until the concentration reaches the equilibrium solubility value.

Synthesis of Inorganic and Organic Nanoparticles

FIG. 2

611

LaMer diagram.

This model should be applicable to microemulsion media because microemulsions are optically isotropic solutions (thermodynamically) even though they have complex microheterogeneous structure. We assume that nucleation occurs in the first part of the reaction, and later on only the growth of the particles occurs. If this model is followed, the size of the particles will increase continuously with the concentration of the precursor or a minimum in the variation of the size with the concentration can also be observed. This is because the number of nuclei at the end of the nucleation phase is assumed to remain constant and the increase of concentration (at levels less than C* min) leads to an increase in the growth of the particles. The second model we evaluate is the thermodynamic stabilization of the particles. In this model the particles are thermodynamically stabilized by the surfactant. The size of the particles stays constant when the precursor concentration and the size of the aqueous droplets vary. These two models are limiting and approximate. The diagram of LaMer does not take into account the stabilization of the particles by the surfactant, and the thermodynamic stabilization does not take into account that the nucleation of the particles is more difficult than the growth by diffusion. II.

SYNTHESIS OF INORGANIC PARTICLES

A.

Synthesis of Silver Halide Particles

Particles of silver bromide, silver chloride, and silver bromochloride have been synthesized. The method of

preparation is the following: Two microemulsions are prepared, one containing silver nitrate, the other containing potassium bromide or chloride. The two microemulsions are mixed under red light or in the dark. The principle of the formation of such AgBr particles is illustrated in Fig. 3. Dynamical droplet fusion and fission mix the reagents. Many different kinds of inorganic precipitations have been executed using this reaction approach. In addition, many reductions to produce nanoparticle metals have been done, where a reducing agent is included in one of the microemulsions being mixed. Inorganic oxides have also been synthesized using hydrothermal syntheses in reverse microemulsions. 1.

AgBr Particles in AOT/Heptane/Water Microemulsions Silver bromide particles have been synthesized [21] in the AOT/heptane/water microemulsion system. Figure 4 shows the variation of the particle size as a function of AgNO3 concentration. The particle size increases monotonously with increasing AgNO3 concentration and approaches a plateau at high concentrations. These results have been successfully interpreted by using the LaMer diagram. In fact, the nucleation occurs only at the beginning of the reaction and the other reactants are used for the growth of the particles [22–24]. These results can be rationalized by computing the number of nuclei (Nn) formed by NM inner water cores, the Poisson distribution of Ag⫹ ions in the water cores, and the sum of probabilities 兺⬁k=i pk of containing i ions or more per water core.

612

Jeunieau et al.

FIG. 3

Silver bromide precipitation in reverse microemulsions.

The number of nuclei (Nn) is computed from a simple formula taking into account the size distribution of the particles: Nn =

冘

Nop m i /Mt

i

FIG. 4 Diameter of AgBr particles as a function of AgNO3 concentration (M).

where Nop is the number of observed particles on a photomicrograph, 兺i m i is the mass of the particles (m i = dVi with dAgBr = 6.473 g cm⫺3), and Mt is the total mass of AgBr formed. The corresponding data are reported in Table 1. The average number of inner water cores is computed from the volume of AgNO3 solution in the microemulsion divided by the volume of one inner water core of radius rM:

Synthesis of Inorganic and Organic Nanoparticles TABLE 1

613

Important Parameters for the Formation of AgBr Colloidal Particles of Size d a

[AgNO3] (mol L⫺1) R=8 0.0063 0.125 0.250 0.500 R = 10 0.063 0.125 0.250 0.500 R = 12.4 0.063 0.125 0.250 0.500 R = 20 0.063 0.125

NAg⫹ /NM

冉冘冊

2

100

˚) d (A

Nn /NM

pk

F

k=i

73.8 96.1 101.8 104.3

2 3 4 8

⫻ ⫻ ⫻ ⫻

10⫺4 10⫺4 10⫺4 10⫺4

1.17 2.25 3.57 6.96

0.4756 0.8003 0.9445 0.9980

4.2 3.7 4.2 8.0

⫻ ⫻ ⫻ ⫻

10⫺4 10⫺4 10⫺4 10⫺4

62.5 73.7 103.3 119.1

7 1 8 1

⫻ ⫻ ⫻ ⫻

10⫺4 10⫺3 10⫺4 10⫺3

1.52 4.23 5.89 10.06

0.6104 0.9711 0.9945 0.9999

1.1 1.0 8.0 1.0

⫻ ⫻ ⫻ ⫻

10⫺3 10⫺3 10⫺4 10⫺3

60.4 56.1 80.8 81.7

1 8 2 6

⫻ ⫻ ⫻ ⫻

10⫺2 10⫺3 10⫺3 10⫺3

2.88 5.96 10.09 23.85

0.8909 0.9948 0.9999 1.0000

1.1 8.0 2.0 6.0

⫻ ⫻ ⫻ ⫻

10⫺2 10⫺3 10⫺3 10⫺3

65.3 61.6

5 ⫻ 10⫺3 1 ⫻ 10⫺2

11.28 17.53

1.0000 1.0000

5.0 ⫻ 10⫺3 1.0 ⫻ 10⫺2

a

Nn /NM, number of nuclei per water core; NAg⫹ /NM, mean number of silver ions per water cor; pk, Poisson distribution of silver ions; F, proportionality factor (see text).

NM =

Msol.AgNO3 /dsol.AgNO3 4 ␲r 3M 3

The rM values are computed from the relation between rM and R [25]. The densities of the aqueous solutions of AgNO3 are taken from Ref. 26. The mean number of AgNO3 units per water core (NAg⫹/NM or ␭) is then computed (Table 1). The probability of having kAg⫹ ions per water core is given by Poisson statistics: pk =

␭ke⫺␭ k!

where k is an integer. Table 1 also shows the square 100 sum of probabilities (兺k=1 pk )2 of containing one Ag⫹ ion or more per inner water core. Indeed, it can be assumed that one Ag⫹ ion can lead to the formation of one surfactant-stabilized AgBr entity, which can be considered the initialization of an embryonic AgBr particle, although such a minimal embryo is unstable. The limit of 100 was chosen instead of ⬁ because, for practical reasons, the probability of having more than 100 ions in a water core is negligible. It was proposed previously that

冘 ⬁

Nn = FNM

pk

k=1

where F is a scaling factor. This formula is valid when an aqueous solution of reactant is added to the microemulsion containing another reactant. As in the present case when two microemulsions are mixed, the correct formula is

冉冘冊 ⬁

Nn = FNM

2

pk

k=1

A constant value of F for all the experimental concentrations corresponds to a good value of i. If i is put equal to 1 or 2, the value of F is reasonably constant for R = 8 and 10 microemulsions. The F values are somewhat less scattered for i = 1 (F ⬇ 4 ⫻ 10⫺4 –1 ⫻ 10⫺3 ), and it is this value which is taken as the minimum number of AgBr units to form an (unstable) embryonic nucleus (Table 1). For microemulsions with R = 12.4 and 20, a value of 7 ⫻ 10⫺3 is more suitable for F. This rather low value of F shows that only approximately one out of every 1000 water droplets leads to the formation of a nucleus for R = 8 and 10 microemulsions and approximately one out of every 100 water droplets for the R = 12.4 microemulsion. This

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small value emphasizes the fact that nucleation occurs very early after mixing, and once the nuclei are formed they grow to yield monodisperse silver bromide particles. (a) Characterization of the Particles [27]. In the numerous studies concerning the synthesis of nanoparticles in microemulsion medium, the localization of water after the nanoparticle synthesis has never been determined. Two models can be proposed (Fig. 5). In the first one the particles are surrounded by a layer of water; in the second the surfactant molecules (the AOT are directly adsorbed on the particles and only a small amount of water is present. In order to discriminate between these two models, 2 H nuclear magnetic resonance (NMR) measurements of deuterated water in the microemulsion have been carried out. Two NMR lines were observed in the 2H NMR spectra (Fig. 6) for the various microemulsions without particles of silver bromide. If the spectrum is taken for a very low R value, such as R = 0.5 (Fig. 7), three NMR lines are observed. These lines are not due to the presence of impurities. In fact, their intensity does not decrease as the amount of water decreases, and these lines stem from different types of water molecules, as indicated by their different relaxation times T1. In fact, for R = 1 the following relaxation times T1 were obtained at 273 K: 321 ms for the broader line, 804 ms for the line situated at ⫺3.50 ppm and 1087 ms for the line situated at ⫺3.95 ppm. As the variation of relaxation time with temperature indicates that we are in a region where the relaxation time increases with decreasing temperature, these two lines correspond to water molecules less mobile and therefore more in contact with the surfactant molecules. Generally, three kinds of water may exist in a microemulsion medium: ‘‘bulk’’ water in the center of the water core; ‘‘bound’’ water, which interacts with the

FIG. 5 Two models of the nanoparticles stabilized in the microemulsion media: (a) the particle is surrounded by a layer of water; (b) AOT is directly adsorbed on the particle.

Jeunieau et al.

FIG. 6 NMR spectra of the deuterated water in the microemulsion for R = 3.1.

FIG. 7 NMR spectrum of deuterated water in AOT/heptane/water microemulsion for R = 0.5 at T = 297 K.


hydrophilic part of the surfactant molecule; and ‘‘trapped’’ water, which is trapped in the interface in the form of monomers or dimers [28]. Bulk water molecules are normally not present for R values below 6– 10, where all the water molecules are structured because of their interaction with Na⫹ counterions and the strong dipole of the AOT polar group [29]. In this case, where the ratio R = [H2O]/[AOT] is 3.1, only two kinds of water molecules should be expected. Therefore, it is assumed that the two NMR lines observed here correspond to bound water and to trapped water. In order to check this assumption, the same experiment was done for higher R values. The chemical shift increases with the R value until reaching approximately that of the pure deuterated water (used as reference) while the line width at half-height decreases with R (Fig. 8). This variation has already been observed [29] and is the result of a fast exchange (faster than 2 ⫻ 1010 s⫺1) between the bulk water and the bound water. At low R values, the observed chemical shift comes from the variation of the number of hydrogen bonds in which the water molecules are involved. In fact, the water molecules adsorbed at the interface (or solvating the Na⫹ ions) form fewer hydrogen bonds, provoking a high-field chemical shift. This decreasing number of hydrogen bonds has previously been shown by Wong et al using 1H NMR experiments [30].

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Furthermore, if the NMR spectra are recorded at lower temperatures, the NMR line corresponding to the bound water decreases because of the freezing of this kind of water (the bandwidth becomes too large to be detectable) (Fig. 6). In fact, the freezing point of bound water seems to be about 243 K inside these reverse micelles. This corresponds to a decrease of the freezing point of water with decreasing droplet size. For example, the freezing point of water in a droplet corresponding to R = 4.5 in AOT/water/2,2,4-trimethylpentane is at around 241 K [31]. On the other hand, the line corresponding to the trapped water shows no freezing and its intensity remains quasi-constant. In order to distinguish between these two models of AgBr stabilization (see earlier), the NMR experiments already mentioned have also been carried out in the presence of silver bromide nanoparticles. As the only difference between the two experiments is the presence of silver bromide particles, all observed differences must be due to the particles. In the presence of these particles, the quantity of trapped water is larger, as shown by comparison of the spectra in the presence and absence of nanoparticles (Fig. 9). It could be hypothesized that the particles repel the bound water into the interface and, as a consequence, the amount of trapped water increases. The total intensity is also greater in the presence of silver bromide particles,

FIG. 8 (a) Variation of the 2H chemical shift as a function of the R factor. (b) Variation of the line width as a function of the R factor.

616

FIG. 9 NMR spectrum of the deuterated water in the microemulsion (full line) and in presence of AgBr particles (dotted line) at 263 K.

stemming also from the greater importance of the trapped water. In fact, this water freezes at a lower temperature. Furthermore, not all the water cores of the microemulsion are occupied by a particle. Only 1 water core out of 1.3 ⫻ 104 is occupied by a particle. Hence, if the microemulsion structure stayed constant, with the same number of water molecules in each water core, no influence on the NMR spectra could be observed upon addition of AgBr. A greater amount of trapped water favors the stabilization model of Fig. 5b, where the particles are in closer contact with the interfacial layer. However, the NMR line of the adsorbed water could overlap that of the trapped water. In order to check this hypothesis, the number of water molecules per AOT has been calculated. The spectrum in Fig. 9 has been decomposed into two bands corresponding, respectively, to the bound water and to the trapped water. The difference in intensity of the two NMR lines corresponding to the trapped water in the spectra without and with AgBr particles gives the amount of water trapped or adsorbed on the particles. The number of AOT molecules per particle has been calculated by using a spherical sur˚ diameter and by using a face corresponding to a 46 A ˚ 2 for the polar part of the AOT surface area of 41 A molecule [32]. It has been computed that if all the line intensity corresponded to the trapped water, there could be 2000 water molecules per AOT molecule. As the trapped water is considered to be in the form of monomers or dimers, this value is too high to correspond only to water molecules trapped in the interface.

Jeunieau et al.

Hence, it has to be supposed that the additional water molecules so computed are adsorbed on the AgBr particles and the NMR lines of the trapped water and of the adsorbed water overlap. If it is assumed that all these additional water molecules are adsorbed on the particles, the number of water monolayers can be calculated by using the van der Waals radius of a water molecule. Approximately 1000 monolayers of water are estimated, and this number is much too high because it does not take into account that the number of trapped molecules increases by repelling the water molecules in the interface. These two arguments, the observation of an NMR line corresponding to the adsorbed water molecules and the estimation of the number of water monolayers, favor the structural model of Fig. 5a. Hence, we adopt this model. In order to quantify the amount of water adsorbed on the nanoparticles by another method, a microemulsion in which the particles sedimented has also been examined. This microemulsion was obtained by adsorption of pseudoisocyanine on the particles. This dye provokes rapid sedimentation of the particles [33], and a 2H NMR spectrum was taken after sedimentation of all the particles. From this spectrum, it has been established that 68% of the water is adsorbed on the particles. In order to visualize this result, the number of water monolayers has been estimated to correspond to about 4600 monolayers. This value is unrealistically high and would correspond to a water core diameter of 2.6 ␮m. Such cores should be highly light scattering, and as the colloidal suspension is transparent, the number of water molecules bound to the silver halide particles must be highly overestimated by this approach. Such a large amount of water in the precipitate can be explained only if the sedimented particles form a sort of gel where a large amount of water is required. This gelation was previously shown in the case of Co2B nanoparticles prepared from a microemulsion of CTAB/n-hexanol/water [34]. This great amount of adsorbed water molecules also favors the structural model of Fig. 5a. 2.

AgBr Particles in AOT/p-Xylene/Water Microemulsions Astonishingly, the average diameters of the AgBr nanoparticles prepared in microemulsions of AOT/p-xylene/ water remain quite constant, whatever the concentrations of precursor salts or the size of the water nanodroplets. Figure 10 shows the average diameters of the nanoparticles as a function of the salt concentration and the R values. All the average diameters seem


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FIG. 10 Average diameters of the AgBr nanoparticles prepared in the AOT/p-xylene/water microemulsion.

FIG. 11 Average diameter of the AgCl nanoparticles prepared in the system AOT/n-heptane/water as a function of the concentration of precursor salts and the value of R.

˚ . The reproducibility of the to lie between 33 and 43 A size measurements has been estimated to be approxi˚ . As we have not observed any correlation mately 9 A between these synthesis parameters and the average diameter of the nanoparticles, we conclude that in this microemulsion system, the nucleation and growth of the nanoparticles do not follow the LaMer diagram. The size of the particles seems to be thermodynamically stabilized by the adsorbed surfactant.

It is not astonishing that the synthesis of AgCl particles is situated between the LaMer diagram and the thermodynamic stabilization of the particles because these two models are only limiting cases.

3. Synthesis of AgCl The preparation of silver chloride nanoparticles has also been studied in the AOT/n-heptane/water microemulsion. A size dependence on the synthesis parameters has been observed (Fig. 11). The diameter seems to pass through a minimum value at around 0.125 M AgNO3. The synthesis of AgCl particles seems to follow a model between that represented by the LaMer diagram and that which we term thermodynamic stabilization. The variation of the particles size seems to correspond to the LaMer diagram, but other factors appear to favor the thermodynamic stabilization of the particles. In fact, the size of the particles (and the number of nuclei) does not vary with the contact surface between the two microemulsions during the precipitation. If the LaMer diagram were followed, the number of nuclei should increase with the contact surface between the microemulsions and the size of the particles should decrease.

4.

Ag(Cl,Br) in AOT/n-Heptane/Water Microemulsions Nanoparticles of mixed silver halides as silver chlorobromide [Ag(Cl,Br)] have been prepared in the system AOT/n-heptane/water. Figure 12 shows an interesting behavior of the size variation as a function of the percentage of chloride in the silver chlorobromide. One may notice that from 0 to 20% chloride, the diameter of the nanoparticle goes from that of pure AgBr to that of pure AgCl. This suggests that the particles are not homogeneous but that the chloride is mainly located at the surface of the particles. It may de due to faster nucleation of the silver bromide particles. In fact, the Ksp values of AgBr and AgCl are, respectively, 7.7 ⫻ 10⫺13 mol2/L2 and 1.56 ⫻ 10⫺10 mol2/L2. The nuclei of AgBr are the first ones formed and following the diagram of LaMer, the growth of the particles is made by the AgCl. The size of the particles is governed by the interaction between the AgCl and the AOT, which explains the constant size of the particles for the greater percentages of chloride. This shows that thermodynamic stabilization is involved in the synthesis of AgCl particles. If only the LaMer diagram were involved, the size of the particles should be determined by the nu-

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FIG. 12

Average diameter as a function of the percentage of chloride in the silver chlorobromide nanocrystals.

cleation and would therefore be similar to the size of the AgBr particles as the nucleation is easier for AgBr than for AgCl. One would expect to get two different populations of AgBr and AgCl, but the size distributions of these mixed silver halide particles were monodisperse. This supports the homogeneity of the Ag(Cl,Br) particle populations. B.

Metal Boride and Metal

Two different methods were used for preparing metal boride and metal nanoparticles. The two reactants were dissolved in the same microemulsion system and then mixed with vigorous stirring (scheme II in Fig. 13). This method led to the smallest size and was used whenever the aqueous solutions of the reactants were stable enough. The nanoparticles of Pt, ReO2, and PtReO2 were all prepared following scheme II. The Ni2B, Co2B, and Ni-Co-B particles were prepared by adding an aqueous solution of NaBH4 to a microemulsion containing the metal salt (scheme I in Fig. 13). Moreover, these particles were prepared in a glove box under an argon atmosphere by adding dropwise a threefold excess of aqueous NaBH4 solution at 0⬚C with vigorous stirring. The expected microemulsion composition was achieved after complete mixing of the reactants. At the end of the reaction, the temperature was raised to room temperature until complete hydrolysis of excess NaBH4 occurred.

1. Synthesis of Nickel Boride Particles Monodisperse colloidal nickel boride and cobalt boride particles are synthesized by reducing, with NaBH4, the metallic ions solubilized in the water cores of the microemulsions. The NaBH4 /MCl2 ratio was held equal to 3 because larger particles were obtained for a lower value; the particle size remained constant above that ratio [22,23,35]. The composition of the particles was determined by XPS (x-ray photoelectron spectroscopy) to be, respectively, Ni2B and Co2B. In every case, the size of particles (2.5–7.0 nm) is much smaller than that obtained by reduction of Ni(II) or Co(II) in water (300–400 nm) or in ethanol (250–300 nm), and the size distribution is quite narrow (⫾0.5 nm). Figure 14 shows the dependence of the nickel boride particle size on the water content in the microemulsion and on the Ni(II) ion concentration. The average size of the particles decreases with decreasing size of the inner water core (decreasing water content), and a complex behavior is observed as a function of the Ni(II) ion concentration. A minimum is detected at a concentration of approximately 5 ⫻ 10⫺2 M. These observations can be understood if one analyzes the nucleation and the growth processes of the particles following the LaMer diagram. (a) Quantitative Aspects of Particle Formation. The same model can be used as already described; the following equation has to be used as only the precursor salt initially stays in the microemulsion medium.


FIG. 13

Method of preparation of monodisperse particles.

冘 ⬁

Nn = FNM

pk

k=i

The diameter of the particles is systemically higher than the diameter of the inner water cores. For all the particles synthesized, we calculated the proportionality factor F by systemically varying the value of the minimum number of ions required to form a nucleus (i ). Only if i takes the value 2 is the factor F reasonably constant. This value of 2 seems logical as two atoms of nickel are needed to form a nickel boride particle. The order of magnitude of the factor F is always 10⫺3. This means that at the very beginning of the reduction,

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i.e., when the nuclei are formed, only one aggregate per thousand leads to the formation of metal boride particles. There is another indication that the nucleation occurs at the very beginning of the reduction. Indeed, the average radius of the water cores used for the calculation of the formation parameters is measured for the system containing only three quarters of the total amount of water, which is the composition of the solution before the addition of the reducing agent. If the final composition is used, however, no coherent results based on the preceding analysis can be obtained. The order of magnitude of the factor F is constant, but its value decreases with increasing water content in the microemulsion. This phenomenon can be easily understood because the rearrangement rate of the microemulsion decreases with the amount of water and hence the number of aggregates reached by the reducing agent before rearrangement decreases. As the number of nuclei formed decreases for a constant concentration of precursor ions, the particle size increases with increasing water content. The results of Table 2 also allow us to explain the minimum in the particle size as a function of the concentration of precursor ions (see Fig. 14). For a constant microemulsion composition, at low ion concentration, only a few water cores contain the minimum number of ions (two) required to form a nucleus; hence, a few nuclei are formed at the very beginning of the reduction, and the metal boride particles are relatively large. When the ion concentration increases, the number of ions per water core increases and the number of nuclei obtained by reduction increases faster than the total number of ions (Fig. 15). This results in a decrease in the particle size. When more than 80% of the water cores contain two or more ions, the number of nuclei formed remains quasi-constant with increasing ion concentration. Hence, the size of the particles increases again. Figure 14 also shows the particle size as a function of water content in the microemulsions for different Ni(II) concentrations. An increase in the average diameter is observed with increasing proportion of water. The decrease in the number of micellar aggregates (NM) with water (Table 2) is accompanied by an increase in their size. For the same Ni(II) concentration with respect to water (i.e., for the same probability of collision between the ions in the same water core), the total number of nuclei formed in the early stage of the reduction decreases with increasing water concentration, and more ions can participate in the growth process. This results in an increase in the particle size.

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˚ ) of the nickel boride particles as a function of Ni(II) ion molal concentrations FIG. 14 Variation of the average diameter (in A for different percentages in water (the indicated percentage corresponding to the composition after adding NaBH4).

(b) (Ni,Co)2B Nanoparticles. Particles of Co2B have been synthesized under the same conditions. Furthermore, mixed particles of (Ni,Co)2B have also been synthesized by using a microemulsion containing NiCl2 and CoCl2 in different proportions. Figure 16 shows the variation of the size of the particles as a function of the molar fraction in Co(II).

TABLE 2

The F values for nickel boride and cobalt boride particles are quite different. For the former the value obtained for F is 3.2 ⫻ 10⫺3 and for the latter 17.4 ⫻ 10⫺3. As for these experiments the rearrangement rate of the microemulsion system is constant in the first approximation, the difference between F values is probably due to different solvation of the two types of

Important Parameters for the Formation of Ni2B Colloidal Particles

[Ni(II)] ⫻ 10⫺2 m

rMa

˚) d (A

Nn /NMb

⌺⬁k=2 pk

F ⫻ 103 c

CTAB 18%/hexanol 70%/water 12% 1.02 1.00 1.22 2.60 1.37 5.10 1.47 7.70

44 36 32 37

8.63 7.09 2.82 3.38

⫻ ⫻ ⫻ ⫻

10⫺5 10⫺4 10⫺3 10⫺3

0.0347 0.3661 0.8713 0.9899

2.5 1.9 3.2 3.4


45 42 40 51

9.14 4.05 2.24 1.52

⫻ ⫻ ⫻ ⫻

10⫺5 10⫺4 10⫺3 10⫺3

0.0415 0.3265 0.9752 0.9964

2.2 1.2 2.3 1.8


67 49 46 49

3.31 2.83 1.51 1.78

⫻ ⫻ ⫻ ⫻

10⫺5 10⫺4 10⫺3 10⫺3

0.0589 0.3732 0.9780 0.9973

0.6 0.8 1.5 1.8

a

Values given for the system containing three quarters of the total amount of water. Values given for 1 kg of solution. c Corrections factor from Nn = FNM ⌺⬁k=2 pk. b


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FIG. 15 Variation in the number of nuclei formed per aggregate and the probability of having two or more ions per aggregate as a function of Ni(II) concentration in the microemulsion CTAB 18%/hexanol 70%/water 12%.

ions at the interface. The Co(II) ions contain, on average, one hexanol molecule in their first coordination shell, while the Ni(II) ions are multiply-coordinated with hexanol at the interface [22]. Hence, the mobility of the latter is lower, and the probability of collision between the two reduced Ni atoms required to form a

nucleus is also lower. In other words, the rate of nucleation is higher for cobalt boride than for nickel boride particles. As it has been previously shown that the formation of Ni2B and Co2B follows the LaMer diagram, it is the nucleation that plays a predominant role in the deter-

FIG. 16 Variation of the size of (Co,Ni)2B as a function of the molar fraction in Co(II). The composition of the microemulsion system is CTAB 18.0%/hexanol 70.0%/water 12.0%. The total salt concentration is 5.0 ⫻ 10⫺2 molal.

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Jeunieau et al.

mination of the particle size. As nucleation is easier for the Co2B particles, the size of the mixed particles is determined more by the cobalt ions than by the nickel ions. This is shown in Fig. 16, where, in fact, the size of the particles did not vary linearly with the molar fraction in cobalt. The particle size approaches the size of the Co2B particles more rapidly than linearly. As nucleation is easier for the Co2B particles, the number of nuclei (and consequently the size of the particles) is determined by the cobalt concentration. The nickel ions are used for the growth of the particles. This leads to the formation of inhomogeneous particles (more nickel ions are situated at the surface of the particles). 2.

Size of Platinum and Rhenium Dioxide Particles

(a) Synthesis of Platinum Particles. Platinum particles have been synthesized in different microemulsion systems. The monodisperse Pt particles prepared from H2PtCl6 dissolved in the CTAB/hexanol/water microemulsion had an average diameter of 4.0 ⫾ 0.5 nm, and their size was not dependent on the H2PtCl6 concentration (5 ⫻ 10⫺3 –2 ⫻ 10⫺2 M with respect to water) [36]. An aqueous solution of hydrazine containing a 10-fold molar excess of hydrazine with respect to H2PtCl6 had an initial pH of 10. It should be noted that the metal particle precursor is soluble in both the dis-

persed inner water core and the continuous (or hexanol) phases. The size of the particles is thus determined by the thermodynamic stabilization of the particles as no variation of the size of the particles was observed. It is interesting to note that particles of a similar size were obtained, independently of water and H2PtCl6 concentration, from the AOT/heptane/water microemulsions [37]. Colloidal Pt particles were prepared following schemes I and II of Fig. 13 in PEGDE/hexane/water microemulsions. A nonionic surfactant, PEGDE, was used to form a microemulsion of composition PEGDE 9.5%/hexane 90%/water 0.5%. Only K2PtCl4 was tested as precursor salt, however, because it is insoluble in the organic medium. Figure 17 shows the variation in the size of the Pt particles obtained following scheme I as a function of initial K2PtCl4 concentration. The standard deviation was small in all cases studied. The particle diameter increases monotonically with increasing K2PtCl4 concentration and approaches a plateau at high concentration. This variation shows that the synthesis of the Pt particles follows the LaMer diagram in this microemulsion system. If the particles are prepared following scheme II, where the two microemulsions containing the precursor K2PtCl4 and the reducing agent N2H4, respectively, are mixed together, smaller sizes are obtained. Indeed, the

FIG. 17 Variation of the Pt average diameter as a function of K2PtCl4 concentration with respect to water prepared according to scheme I of Fig. 13.


Pt particles prepared from the microemulsion with [K2PtCl4] of 0.1 M with respect to water have a diameter of 3.5 ⫾ 0.5 nm, whereas the diameter is much greater (9.0 ⫾ 1.0 nm) if scheme I is used. Figure 17 illustrates the variation of the average diameter of the Pt particles as a function of the concentration of K2PtCl4 prepared by scheme I. The average size of the Pt particles obtained by the method of scheme I can be explained in a first approximation by the diffusion of the aqueous solution through the organic phase being slower than the exchange between the water cores. Although in the PEGDE/hexane/ water microemulsion no separate spherical droplets are present, the water is probably the dispersed phase in the microemulsion. The structure of the microemulsion is better represented as a lamellar aggregate where the surfactant molecules are associated head to head along a cylinder. (b) ReO2 Particles. Monodisperse ReO2 particles were obtained by reducing NaReO4 with hydrazine in the PEGDE 9.5%/hexane 90%/water 0.5% microemulsion system following scheme I of Fig. 13. The presence of ReO2 was confirmed by XPS experiments. However, the NaReO4 is only partially reduced under these conditions. Figure 18 illustrates the variation in particle size as a function of NaReO4 concentration. Once again the size of monodisperse particles approaches a plateau for

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high NaReO4 concentrations, and this behavior is quite similar to that of the Pt particles. This indicates that the synthesis of the ReO2 particles follows the LaMer diagram. (c) Pt-ReO2 Particles. Monodisperse Pt-ReO2 particles were prepared following scheme I from the PEGDE/hexane/water microemulsion using a total ion concentration [K2PtCl4] ⫹ [NaReO4] = 0.1 molal with respect to water. Figure 19 shows the variation in the particle size as a function of the mole fraction x of K2PtCl4. It is surprising that up to x = 0.7 the diameter of the particles remains quasi-constant and is close to that of the pure ReO2 particles. For higher initial [K2PtCl4], the diameter of the particles increases monotonically to reach that of the pure Pt particles. The electrochemical ⫺ potential of PtCl2⫺ 4 and ReO4 are, respectively 0.73 and 0.51 V. Furthermore, two electrons are needed for the reduction of K2PtCl4 and three electrons for the reduction for NaReO4. The nucleation should thus be easier for the platinum particles than for the ReO2 particles. It can thus be concluded that the ReO2 is dispersed on the Pt particles. As the particles size is constant for low values of the K2PtCl4 molar fraction, it can be concluded that the size of the particles is not determined by the nucleation, as for the (Ni,Co)2B particles, but by the interaction between the ReO2 and the surfactant. This shows the importance of the thermodynamic sta-

FIG. 18 Variation of the ReO2 average diameter as a function of NaReO4 concentration with respect to water prepared according to scheme I of Fig. 13.

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FIG. 19 Variation in Pt-ReO2 particle size as a function of ratio x of K2PtCl4 ([K2PtCl4] ⫹ [NaReO4] = 0.10 molal with respect to water).

bilization in a case where the particle size seems to be determined by the LaMer diagram. A similar variation has been observed in the case of Ag(Cl,Br) particles. All these results are different from those one might expect on the basis of a mechanical mixture. Indeed, in that case a bimodal distribution would be expected, at least for x ⱖ 0.5, based on the different sizes of the separate Pt and ReO2 particles. III.

SYNTHESIS OF ORGANIC PARTICLES

A.

General Considerations

Several types of organic nanoparticles have been synthesized recently in some microemulsions. The active compounds are cholesterol, rhodiarome, and rhovanil (aroms) (Fig. 20). The microemulsions used are AOT/ heptane/water, Triton/decanol/water, and CTAB/hexanol/water. The general preparation of these organic nanoparticles has been described [38,39]. It consists of direct precipitation of the active compound in the aqueous cores of the microemulsion. After their preparation, nanoparticles are stained with iodine vapor and observed by transmission electron microscopy (Philips EM301) [40,41]. A transmission electron micrograph of rhodiarome nanoparticles is presented in Fig. 21. A hypothesis for such nanoparticle formation has been proposed [38,39,41]. This hypothesis consists of

several stages. A solution of active compound in an appropriate solvent is added to the microemulsion. The active compound goes to the aqueous cores (by diffusion) and partitions inside by crossing the interfacial film. The solvent plays a role in this transport to the aqueous cores. The active compound precipitates in the aqueous cores because of its insolubility in water, and nuclei are thus formed. These nuclei can grow because of the exchange of active compound between the aqueous cores. At the end, nanoparticles are stabilized by the surfactants. B.

Nanoparticles of Cholesterol Prepared in Different Microemulsions

Figure 22 represents the evolution of nanoparticle size as a function of R at a fixed concentration of cholesterol solution in chloroform. The cholesterol is precipitated in an AOT/heptane/water microemulsion. It has to be noted that the total amount of cholesterol added increased with increasing R, as the volume of chloroform solution was equal to that of the water in each microemulsion. The mean particle size was in the range ˚ and a minimum was observed for a certain 30–60 A R value. Although it is tempting to put forward a hypothesis for this local minimum, the overall variability does not justify a detailed discussion at this time. In these precipitations the amount of chloroform increases with R and the relative amount of chloroform in the


FIG. 20

625

Structures of the active compounds.

solvation sphere could depend on the size of the particles. In order to check the veracity of this hypothesis, another series of precipitations was done in which the same amount of cholesterol solution in chloroform (0.3 mL) was added to the various microemulsions with different R values (Fig. 23). In this case, the particle size is constant as a function of R. The size of the particles is hence controlled by the thermodynamic stabilization. But in this experiment, the amount of cholesterol was also constant. If the concentration of chloroform remains constant, the corresponding quantity of cholesterol may be sufficient to allow the thermodynamic stabilization of the particle. Figure 24 shows the variation of nanoparticle size as a function of the concentration of cholesterol in the same microemulsion system. No local minimum appears. The size of the particles is thus controlled by thermodynamic stabilization by the surfactant. A certain size is favored. In fact, in this experiment the amount of water stays constant, and it is perhaps the difference in the number of water molecules per water core that produces a difference in the nucleation.

FIG. 21 Photograph of rhodiarome nanoparticles synthesized with a solution of rhodiarome in acetone (50 g/L) in AOT/heptane/water microemulsion (scale 96,000⫻).

Nanoparticles of cholesterol have also been synthesized in two other microemulsion systems: Triton/decanol/water and CTAB/hexanol/water. Similar experiments have been carried out. In the two cases, the nanoparticle size is independent of the factor R and also of the concentration of the cholesterol solution. The particles are thus thermodynamically stabilized by the surfactants at a certain favored size. The nanoparticles are stable for months, no precipitate appears, and the final solutions are still limpid.

FIG. 22 Variation of the nanoparticle size of cholesterol as a function of R at a fixed concentration.

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FIG. 23

C.

Variation of the nanoparticle size of cholesterol as a function of R at a fixed concentration (50 g/L).

Rhodiarome (or Rhovanil) in AOT/ Heptane/Water Microemulsion

1.

Influence of the Factor R and of the Concentration of Active Compound An example is presented for the formation of nanoparticles of rhovanil. A solution of rhovanil in acetone (50 g/L) is used. Figure 25 shows the variation of the mean diameter as a function of R. The nanoparticle size is relatively constant as a function of R and ranges be˚ for the four concentrations. It is the tween 45 and 62 A same in the other cases. The nanoparticle size is independent of the factor R. The second parameter studied is the concentration of the active compound in the solvent. Figure 26 shows a certain constancy of the ˚ . In these two size, which ranges between 45 and 70 A cases, it appears the nanoparticle size is essentially determined by thermodynamic stabilization by the surfactant molecules at a certain size. 2. Influence of Stirring Figure 27 shows that the diameter of the particles synthesized using a magnetic stirrer for mixing the solutions is higher than the diameter of those synthesized in the presence of ultrasonification (especially for smaller R). The following explanation is proposed. The available energy that is required to favor the mixing of the active compound in acetone solution in the microemulsion is more important for the ultrasound bath. The active molecule is dispersed better in the micro-

emulsion in the case of ultrasound. A greater number of nuclei are formed in contact with the aqueous cores, and the size of the nanoparticles is smaller than in the case of magnetic stirring. This difference between the two methods indicates a contribution of the LaMer diagram. In fact, this indicates the importance of the nucleation and that the growth is easier than the nucleation of the particles. 3. Solubility Limitations A microemulsion formulation can accommodate only a limited quantity of active compound (solution) to form nanoparticles without macroscopic phase separation. In Table 3, for a given factor R, a certain volume of rhodiarome solution, with a constant concentration (400 g/ L), is tolerated. As the number of active compound molecules per aqueous core increases, the corresponding interaction with surfactant molecules increases at the interface. The optimal radius of curvature is perturbed and a phase separation appears (emulsion failure). Further, as the factor R increases, the tolerable quantity of rhodiarome in acetone decreases because the microemulsion with more water is a poorer solvent for the added rhodiarome-acetone solution. 4.

Effect of Principal Compound Solution Volume Figure 28 shows the variation of particle size as a function of R for two volumes (5 and 50 mL) of rhodiarome (50 g/L) in acetone. No significant difference in the diameter of monodisperse nanoparticles is observed.


FIG. 24

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Variation of the nanoparticle size of cholesterol as a function of the concentration.

Thermodynamic stabilization of the particles is suggested with a small LaMer contribution. Indeed, in a small volume, the active compound may not be uniformly dispersed in the microemulsion prior to nucleation and precipitation. Fewer nuclei are formed at the beginning of the reaction, but the greater size obtained is not very significant.

5. Influence of Auxiliary Solvents When the active compound is added as a solid phase into the microemulsion, no particles are observed because of insufficient dispersion, slow dissolution, and lack of a thermodynamic driving force for dissolution. Solvents such as acetone probably play the role of a vector because the active compound must be carried to

FIG. 25 Variation of the nanoparticle size of rhovanil as a function of R.

FIG. 26 Variation of the nanoparticle size as a function of the concentration of rhovanil in acetone (50 g/L).

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solve the active compound. There is no apparent influence of these solvents on the nanoparticle size. These auxiliary solvents can thus be vectors for the transport of the active compound toward the aqueous cores. Avoidance of such auxiliary solvents leads to poor dispersion and aggregates are observed. These auxiliary solvents do not appear to play a significant role in the precipitation, other than their role in uniformly distributing the active compound throughout the microemulsion.

FIG. 27 Variation of the nanoparticle size of rhovanil in the case of the use of a magnetic stirrer or ultrasound bath.

the aqueous cores in order to induce nanoparticulate precipitation. Two microemulsions are used in a precipitation. The first contains the active compound in solid form and the second contains the auxiliary solvent (acetone). The final solution (obtained by mixing the two solutions) is stable after treatment for 15 min with ultrasound. In this experiment, the volume is 5 mL of a solution of rhodiarome in acetone (50 g/L) in a vessel of 25 mL and the results are compared with those in the case of the use of one microemulsion (Fig. 29). ˚, The diameters obtained are between 45 and 65 A and no obvious minimum or maximum is observed. Thermodynamic stabilization of the nanoparticles appears to control in this system. Several solvents such as acetone, ethanol, or ether are used in order to disTABLE 3

6. Effects of Time Figure 30 shows no preponderant changes of nanoparticle size as a function of time. The size ranges between ˚ for the case of a rhodiarome (in acetone) 50 and 80 A precipitation. The final solutions are still stable and transparent after a long period of time. No sedimenting agglomerates appeared after more than a year, so these nanoparticles are very effectively thermodynamically stabilized. A solution of rhodiarome in acetone (100 g/L) added drop by drop into a microemulsion yielded the results shown in Fig. 31. Different samples were taken at different times after injection. The size did not significantly change as a function of time. The ultrasound treatment can thus be reduced. The particles are first formed by direct precipitation in the aqueous cores and are simultaneously thermodynamically stabilized by the surfactants. 7. Recovery of Nanoparticles Some potential pharmaceutical applications can be considered if less toxic solvents are used. Thus the residual solvents (heptane, for example) are evaporated under

The Amount of Active Compound Tolerated in Microemulsion

R

0.25 mL (0.1 g)

0.3 mL (0.12)

0.35 mL (0.14 g)

0.4 mL (0.16 g)

0.45 mL (0.18 g)

0.5 mL (0.20 g)

0.6 mL (0.24 g)

0.7 mL (0.28 g)

48 46 44 42 40 38 36 34 32 30 28 26

● 〫〫〫〫〫〫〫〫〫〫〫

● ● ● ● ● ● ● 〫〫〫〫〫

● ● ● ● ● ● ● 〫〫〫〫〫

● ● ● ● ● ● ● ● 〫〫〫〫

● ● ● ● ● ● ● ● ● ● 〫〫

● ● ● ● ● ● ● ● ● ● 〫〫

● ● ● ● ● ● ● ● ● ● 〫〫

● ● ● ● ● ● ● ● ● ● ● 〫

〫, Limpid and stable solutions. ●, Solutions with two phases.


FIG. 28 Variation of rhodiarome nanoparticle size as a function of R: influence of the volume of microemulsions.

vacuum and the nanoparticles stabilized by surfactants are recovered. These particles are reintroduced in distilled water under ultrasound in order to obtain a limpid and stable solution. Figure 32 shows the variation of the nanoparticle size as a function of R. ˚ and do not The sizes range between 57 and 63 A change after particle recovery. The nanoparticles are thus thermodynamically stabilized by the surfactants. The change of the medium does not influence the nanoparticle size. More biocompatible microemulsions have also been used in order to allow their use in drug delivery [39,41].

FIG. 30

629

FIG. 29 Variation of rhodiarome nanoparticle size as a function of R: particles synthesized in one or two microemulsions.

IV.

CONCLUSIONS

This chapter has emphasized the mechanism of formation of particles in microemulsions. Two models have been proposed: the LaMer diagram and the thermodynamic particle stabilization model. These two models are relatively simple. The LaMer diagram model is based on the separation between the nucleation and the growth stages. It is consistent with the mechanism proposed by Lo´pez-Quintela and Rivas [42] for Fe nanoparticles obtained in AOT microemul-

Evolution of particle size of rhodiarome nanoparticles as a function of time.

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FIG. 31 Variation of particle size of rhodiarome nanoparticles as a function of time after the injection of the active compound in microemulsion.

sions using a stopped-flow technique. Nucleation implies an increase in the number of scattering centers (number of particles) for a given observation window, and, therefore, it gives an increase in the scattered intensity. On the contrary, the growth of particles is associated with a decrease of the scattered intensity because the observation window corresponds to the diffraction of smaller particles that are disappearing during the growth process. The presence of this maximum (although not well defined) has also been spectrophotometrically detected by Towey et al. [43] for the formation of CdS in AOT microemulsions. This is an illustration of the LaMer diagram, as following this diagram the nucleation occurs only at the beginning of the reaction. Theoretical calculations have been done

Jeunieau et al.

by Tojo et al. [44] involving the study of the influence of the concentration and of the film flexibility and of the kinetic exchange constant between the droplets using the difference between the nucleation and the growth of the particles. Thermodynamic stabilization is less documented in the literature, but an example shows the formation of secondary monodisperse spherical particles by coagulation of the primary particles [45]. Whether the precipitation reaction follows the LaMer diagram or thermodynamic stabilization depends on the microemulsion phase diagram and on the nature of the particles synthesized. As an example, the synthesis of AgBr particles follows the LaMer diagram in the AOT/heptane/water microemulsion system, but it follows the thermodynamic stabilization model in the AOT/p-xylene/water system. The difference between the two systems can come from the adsorption of the p-xylene molecule on the particles of AgBr. In fact, the adsorption of p-xylene on the AgBr particles has been shown in the study of the adsorption of pseudoisocyanine on these particles [46]. In CTAB/hexanol/water microemulsions, the formation of Ni2B particles follows the LaMer diagram model, but that of Pt follow the thermodynamic stabilization of the particles. The difference could stem from a difference in the adsorption of the surfactant on the particles. Mixed particles have also been synthesized. Not all the particles are homogeneous and the size of these particles does not vary linearly with their composition. In the case of organic nanoparticles, all of the particle preparations seem to follow thermodynamic stabilization. However, the cholesterol synthesized in the AOT/heptane microemulsion may be an exception to this generalization. This may be due to a specific interaction of the surfactant with the particles. ACKNOWLEDGMENT L. J. thanks F.R.I.A. for financial help. REFERENCES 1. 2. 3. 4. 5.

FIG. 32 Variation of the nanoparticle size of rhodiarome as a function of R before and after nanoparticle recovery.

J. H. Fendler and F. C. Meldrum, Adv. Mater. 7:607 (1995). G. A. Ozin, A. Kuperman, and A. Stein, Angew. Chem. Int. Ed. Engl. 28:359 (1989). J. Belloni M. Mostafavi, J.-L. Marignier, and J. Amblrad, J. Imaging Sci. 35:68 (1991). A. Henglein, J. Phys. Chem. 97:5457 (1993). R. P. Andres, R. S. Averback, W. L. Brown, L. E. Brus, W. A. Goddard III, A. Kaldor, G. Louie, M. Moscovits, P. S. Peercy, S. J. Riley, R. W. Siegel, F. Spaepen, and Y. Wang, J. Mater. Res. 4:704 (1989).

Synthesis of Inorganic and Organic Nanoparticles 6. 7. 8. 9. 10. 11. 12. 13. 14. 15. 16. 17. 18. 19. 20. 21. 22.

23.

24. 25.

R. W. Siegel, MRS Bull. 15:60 (1990). Y. T. Han, MRS bull. 14:13 (1989). M. J. Lawrence, Eur. J. Drug Metab. and Pharmacokinet. 3:257 (1994). B. Sjo¨stro¨m, B. Bergenstahl, and B. Kronberg, J. Pharm. Sci. 82:584 (1993). E. Alle´mann, R. Gurny, and E. Doelker, Eur. J. Pharm. Biopharm. 39:173 (1993). J. Rouvie`re, J.-M. Couret, M. Lindheimer, J.-L. Dejardin, and R. Marrony, J. Chem Phys. 76:289 (1979). C. Cabos and P. Delord, J. Appl. Crystallogr. 12:502 (1979). S. I. Ahmad and S. Friberg, J. Am. Chem. Soc. 94:5196 (1972). S. Friberg and I. Lapczynska, Prog. Colloid Polym. Sci. 56:16 (1975). P. Ekwall, L. Mandell, and K. Fontell, J. Colloid Interface Sci. 33:215 (1970). P. Ekwall, L. Mandell, and K. Fontell, Mol. Cryst. Liq. Cryst. 8:157 (1969). P. D. I. Fletcher, A. M. Howe, and B. H. Robinson, J. Chem. Soc. Faraday Trans. 1 83:985 (1987). S. S. Atik and J. K. Thomas, Chem. Phys. Lett. 79:351 (1981). V. K. LaMer and R. H. Dinegarn, J. Am. Chem. Soc. 72:4847 (1950). T. Sugimoto, Adv. Colloid Interface Sci. 28:65 (1987). Ph. Monnoyer, A. Fonseca, and J. B.Nagy, Colloids Surf. 100:233 (1995). J. B.Nagy, E. G. Derouane, A. Gourgue, N. Lufimpadio, I. Ravet, and J. P. Verfaillie, in Surfactants in Solution (K. L. Mittal, ed.), Vol. 10, Plenum, New York, 1989, p. 1. J. B.Nagy and A. Claerbout, in Surfactants in Solution (K. L. Mittal and D. O. Shah, eds.), Vol. 11, Plenum, New York, 1991, p. 363. A. Claerbout and J. B.Nagy, Stud. Surf. Sci. Catal. 63: 705 (1991). J. Eastoe, B. H. Robinson, A. J. W. G. Visser, and D. C. Steytler, J. Chem. Soc. Faraday Trans. 87:1899 (1991).

631 26. 27. 28. 29. 30. 31. 32. 33. 34. 35. 36. 37.

38. 39. 40. 41. 42. 43. 44. 45. 46.

Handbook of Chemistry and Physics, 67th ed., CRC Press, Boca Raton, FL, 1986. L. Jeunieau, W. Verbouwe, E. Rousseau, M. Van der Auweraer, and J. B.Nagy, Langmuir, 16:1602 (2000). T. K. Jain, M. Varshney, and A. Maitra, J. Phys. Chem. 93:7409 (1989). H. Hauser, G. Haering, A. Pande, and P. L. Luisi, J. Phys. Chem. 93:7869 (1989). M. Wong, J. K. Thomas, and T. Nowak, J. Am. Chem. Soc. 99:4730 (1977). P.-O. Quist and B. Halle, J. Chem. Soc. Faraday Trans. I 84:1033 (1988). M. A. J. Rodgers and M. Da Silva, Chem. Phys. Lett. 78:256 (1974). L. Jeunieau and J. B.Nagy, Colloids Surf. 151:419 (1999). I. Ravet, Ph.D. thesis, FUNDP, 1988. J. B.Nagy, A. Gourgue, and E. G. Derouane, Stud. Surf. Sci. Catal. 16:193 (1983). A. Wathelet, Bachelor’s thesis, FUNDP, Belgium, 1984. A. Khan-Lodhi, B. H. Robinson, T. Towey, C. Herrmann, W. Knoche, and U. Thesing, in The Structure, Dynamics and Equilibrium Properties of Colloidal Systems, NATO ASI Ser C 324 (D. M. Bloor and E. WynJones, eds.), Kluwer, Dordrecht, 1990, p. 373. F. Debuigne, L. Jeunieau, M. Wiame, and J. B.Nagy, Langmuir, in press. F. Debuigne, Bachelor’s thesis, DEA, FUNDP, 1999. Electron Microscopy and Photography, A. Kodak databook. F. Debuigne, Bachelor’s thesis, FUNDP, 1997. M. A. Lo´pez-Quintela and J. Rivas, J. Colloid Interface Sci. 158:466 (1993). T. F. Towey, A. Khan-Lodhi, and B. H. Robinson, J. Chem. Soc. Faraday Trans. 86:3757 (1990). C. Tojo, M. C. Blanco, F. Ricadulla, and M. A. Lo´pezQuintela, Langmuir 13:1970 (1997). L. Lerot, F. Lefrand, and P. De Bruycker, J. Mater. Sci. 26:2353 (1991). L. Jeunieau and J. B.Nagy, Appl. Organomet. Chem. 12:341 (1998).

31 Colloidal Nanoparticles and Nanoparticulate Films Grown at the Air-Water Interface JANOS H. FENDLER

I.

Clarkson University, Potsdam, New York

INTRODUCTION

rities, and the lack of an established protocol for layering uniform two- and three-dimensional particulate networks are the disadvantages of this approach. Nature routinely performs elegant and efficient nanoparticle preparations in a more advanced manner than either physicists or chemists. Not only are the appropriate and monodisperse nanoparticles synthesized, but they are processed into higher level organizations [4]. Accomplishments of the humble magnetotactic bacterium serve to illustrate the point. The bacterium is capable of producing 20 to 25, 45 ⫾ 8 nm diameter, spherical, single-domain Fe3O4 (magnetite) particles in the cytoplasmic membrane that are nicely aligned along its body [5]. The bacterium uses these monodisperse magnetites, in connection with the magnetic field of the earth, for navigation toward warmer waters. The mimicking of biology in general, that of biomineralization and the functioning of the biological membrane in particular, has led to the development and burgeoning of bio-organic (and bioinorganic) chemistry, of biomimetic materials chemistry [4], and of the membrane mimetic approach to advanced materials preparations [6]. The membrane mimetic approach relies on the construction of templates and/or compartments in which nanoparticles are generated in situ or into which they are incorporated. The templates and compartments are designed to imitate such essential functions of the biological membrane as organization and compartmentalization in distinct microenvironments. Zeolites and related molecular sieves, pillared clays and clay organocomplexes, porous glasses,

The preparation and characterization of size-quantized nanoparticles are receiving ever increasing attention by material scientists, physicists, chemists, and biologists. Mechanical manipulation is the predominant strategy physicists have employed in their preparations of nanoparticles and nanostructured materials. At the low end of the scale, this involves the exhaustive grinding or milling of bulk materials [1]. Examples at the high technological end include single-atom transfer from one site to another, relocation of small molecular clusters from surfaces, and etching or deposition of materials in subnanometer regions [2]. Generation of atomic and molecular clusters via gas condensation in an ultrahigh vacuum [3] falls between these two extremes. In general, any nanoparticle can be fabricated by physical methods and band gap engineering permits the construction of semiconductor superlattices with any desired nanoscale architecture. The high cost involved in these methods does not, however, conveniently lend itself to the large-scale production of advanced nanoparticles and nanostructured materials. Chemists, by vocation and definition, are makers of molecules. Rather than ‘‘breaking down’’ materials, they ‘‘build them up’’ from their elements, often by innovative routes. Increasingly, chemists are turning their attention to the synthesis of molecular clusters and to the formation and stabilization of colloidal nanoparticles. Versatility and the relative ease of scale-up are the advantages of the chemical approach to nanoparticle preparations. Polydispersity, the presence of impu633

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graphite and metallic tubes, and polymeric membranes have been used as templates [7]. Monolayers, Langmuir-Blodgett (LB) films, self-assembled monolayers and multilayers, micelles, surfactant vesicles (liposomes), bilayer lipd membranes (BLMs), cast multibilayers, and polymers have been used as compartments [6]. The terms templates and compartments are somewhat arbitrary and often used interchangeably. Similarly, membrane mimetic chemistry and biomimetic materials chemistry are closely related. The latter has been used to describe biologically inspired advanced materials synthesis by molecular tectonics. The phrase molecular tectonics (Greek tekton = builder) has been coined by chemists to describe the construction of supramolecules that integrated molecular synthesis and self-assembly into larger structures. The preparation of nanoparticles and the construction of nanostructured materials by membrane mimetic approaches are the long-term research objectives in our laboratories. Advantage has been taken of membrane mimetic systems to provide chemical, spatial, and dimensionality control for the in situ generation and stabilization of ultrasmall metallic, semiconducting, and magnetic particles and particulate films [6]. In this chapter, our work on the membrane mimetic preparation of nanoparticles under monolayers and their subsequent transfer to solid substrates are surveyed. II.

FIG. 1 The experimental arrangement used for the in situ generation of nanoparticulate films from their precursors (one of them is in the subphase under the monolayer, and the other as a gas, infused through the monolayer after its injection by the syringe). The arrangement used for the in situ reflectivity measurements (P = polarizer, D = detector) is also illustrated.

silver nitrate solution) and electrical connection is made through a 20-␮m-diameter platinum electrode floated (subsequent to monolayer formation) on the water surface at the middle of the trough. Ten to 20 min after monolayer formation, a potential of 1.8–1.9 V is applied across the electrodes (keeping Pt negative) by means of a DC power supply. With time, silver particles grow concentrically, forming larger and larger circles at the monolayer-water interface. The rate of this two-dimensional growth is typically 1–2 cm2/h. No silver particles are observed upon the application of the same potential to the water surface in the absence of

EXPERIMENTAL METHODOLOGIES

Both chemical and electrochemical routes have been developed for the in situ generation of nanoparticles under monolayers [6]. The experimental setup used for the chemical generation and in situ monitoring of nanocrystalline particulate films is illustrated in Fig. 1 [8]. Typically, a surfactant monolayer is spread on an aqueous solution of the metal salt precursor of the nanoparticles and crystallization is induced by injection of the reactant gas into the closed system. Facilities are provided for determining surface pressure versus surface area and surface potential versus surface area isotherms in the film balance placed under the glass cover. Reflectivities, angle-dependent reflectivities, Brewster angle and fluorescence microscopies, and nonlinear optical parameters can also be monitored during the nanoparticle formation under the monolayer. The experimental setup used for the electrochemical generation of nanocrystalline silver particulate films is illustrated in Fig. 2 [9]. A 1.0-mm-diameter, 3-cm-long silver electrode is immersed in the subphase (aqueous

FIG. 2 Setup used for the electrochemical generation of nanocrystalline silver particulate films.

Colloidal Nanoparticles

surfactants or to monolayers prepared from positively charged surfactants. Negatively charged monolayers are essential to the electrochemically generation of silver particles; they provide binding sites for silver ions that are reduced at the cathodic surface. To date, cadmium sulfide, zinc sulfide, lead sulfide, cadmium selenide, and lead selenide semiconductor particulate and silver and gold metallic nanoparticulate films have been chemically grown, in situ, under monolayers in our laboratories [6,10]. The formation of nanoparticulate films under monolayers by similar methodologies has been reported by other research groups [11]. III.

2. 3. 4.

5. 6.

7.

MECHANISM OF PARTICLE GROWTH

Evolution of a nanocrystalline particulate film, as illustrated by the formation of sulfide semiconductor particulate films (Fig. 3), has been discussed in terms of the following steps [8]: 1.

635

Formation of metal-sulfide bonds at a large number of sites at the monolayer-aqueous interface

The presence of a monolayer with an appropriate surface charge is essential to sulfide semiconductor particulate film formation. In the absence of a monolayer, infusion of H2S over an aqueous metal ion solution results in the formation of large, irregular, and polydispersed metal sulfide particles that precipitate in the bulk solution before settling to the bottom of the trough. An important aspect of generating nanoparticles and nanoparticulate films under monolayers is that they can be transferred to substrates at any stage of their growth for ex situ characterizations and then used as devices and sensors.

IV.

FIG. 3 Proposed schematics of the initial and subsequent growth of a monolayer-supported, porous, size-quantized semiconductor particulate film (SQSPF). The dx and dy dimensions are in the plane and the dz dimension is normal to the plane; they refer to the earliest observable particles. d⬘x, d⬘y, and d⬘z are dimensions in the plane and are normal to the plane; they refer to particles that were observed at later stages of their growth.

Downward growth of well-separated nanocrystalline metal sulfide particles Coalescence of clusters into interconnected arrays of semiconductor particles Formation of the ‘‘first layer’’ of a porous sulfide semiconductor particulate film composed of 20- to ˚ -thick, 30- to 80-A ˚ -diameter particles 40-A Diffusion of fresh metal ions to the monolayer headgroup area Formation of a ‘‘second layer’’ of the porous sulfide semiconductor particulate film (by using steps 1, 2, and 3) Buildup of ‘‘subsequent layers’’ of the sulfide semiconductor particulate film (by using steps 1, ˚ for 2, and 3) up to a plateau thickness (⬃300 A ˚ CdS and ⬃3500 A for ZnS) beyond which the film cannot grow

EPITAXIAL GROWTH OF SEMICONDUCTOR NANOCRYSTALLITES

Oriented growth requires matching the crystal lattice of the surfactants, constituting the monolayers, with that of the incipient nanocrystallites. Such epitaxial matching has been achieved by growing lead sulfide [12], lead selenide [13], and cadmium sulfide [14] under monolayers prepared from arachidic acid and from mixtures of arachidic acid and octadecylamine. This approach is illustrated here by the description of the epitaxial growth of lead sulfide nanocrystallites. Exposure of an aqueous lead ion solution to hydrogen sulfide in the absence of monolayers results in the formation of large (several millimeters long) irregular cubic crystalline lead sulfide crystals. Conversely, exposing an arachidic acid monolayer–coated aqueous lead nitrate solution to hydrogen sulfide gas in the system illustrated in Fig. 1 results in the formation of well-

636

oriented, relatively monodisperse equilateral triangular lead sulfide nanocrystallites (Fig. 4). The size of the crystals is dependent on the rate of crystal growth. Infusion of H2S for only 5 min yielded crystals with sides ˚ , and a reaction time of 30 of a mean length of 297 A min produced significantly larger crystals of a mean ˚ [L]. Selected area electron difside length of 607 A fraction of the crystalline films showed ‘‘single crystal’’ patterns, indicative of an epitaxial relationship between the lead sulfide particles and the crystalline monolayer. Reciprocal lattice spots corresponding to {220}, {422}, {440}, etc. forms of planes of the cubic lead sulfide structure were identified and demonstrated that all of the crystals nucleated and grew from {111} basal planes. Lead sulfide crystals were also grown under arachidic acid monolayers that were maintained at

FIG. 4 Transmission electron micrograph of a PbS particulate film. The film was formed by the infusion of H2S to an AA monolayer, floating on an aqueous 5.0 ⫻ 10⫺4 M Pb(NO3)2 solution in a circular trough, for 45 min. The PbS particulate film was deposited on an amorphous carbon– coated, 200-mesh copper grid. The bar represents 100 nm. Inset: Electron diffraction of a PbS particulate film domain. Limiting aperture was applied to cover an area 2 ␮m in diameter.

Fendler

lower surface pressures. Even gaseous state monolayers provided a substrate for the epitaxial growth of lead sulfide. Circular domains of epitaxially oriented lead sulfide particles were located, presumably having grown from crystalline domains of arachidic acid that were surrounded by disordered molecules in the gas phase [12]. The mechanism of oriented crystal growth has been rationalized by comparison of the structures of the arachidic acid monolayer and the lead sulfide crystals. Synchrotron x-ray studies of arachidic acid monolayers in their solid states showed that they comprise fully extended molecules with a planar zigzag conformation. The arachidic acid molecules are oriented approximately normal to the liquid surface in a hexagonal close-packed array and exhibit a lattice constant of a = ˚ . An experimentally obtained lattice constant of 4.85 A arachidic acid monolayers on lead nitrate of a = 4.81 ˚ , as derived from surface pressure versus surface area A isotherms, was considered to be in good agreement with the published data and was utilized in the analysis. Lead sulfide possesses an NaCl-type cubic structure ˚ . Epitaxial with a lattice constant of a = 5.9458 A growth of lead sulfide from the {111} face resulted from the geometrical complementarity between the arachidic acid monolayer and the {111} lead sulfide face (Fig. 5). The Pb-Pb and S-S interionic distances of 4.20 ˚ in the lead sulfide {111} plane geometrically A ˚ for arachidic matched the d{100} spacing of 4.16 A acid; the spatial mismatch between the crystals is only of the order of 1%. The investigations of epitaxial lead sulfide growth were extended by doping the supporting arachidic acid monolayer with octadecylamine [15]. The size and orientation preference of lead sulfide grown under mixed arachidic acid–octadecyl amine monolayers were shown to be profoundly influenced by the arachidic acid/octadecylamine ratio and the applied surface pressure. The lead sulfide growth habit was observed to change from [111] to [001] with a reduction in the arachidic acid/octadecylamine ratio (AA/ODA) from 1:0 and 5:1 to 2:1. The II versus A isotherms were identical for these monolayer compositions, indicating maintenance of the hexagonal close-packed structure [15]. The differences in morphology (Fig. 6) between equilateral-triangular PbS-I, right-angle-triangular PbSII (epitaxially grown under monolayers, prepared from AA/ODA = 1:0 and AA/ODA = 1:1), and disk-shaped PbS-III (nonepitaxially grown under monolayers, prepared from hexadecylphosphate) manifested themselves in different spectroelectrochemical behavior

Colloidal Nanoparticles

637

FIG. 5 Schematic two-dimensional representation of the proposed overlap between Pb2⫹ ions and AA headgroups. (䡬) AA • ) Pb2⫹ and AA headgroups. A unit cell is highlighted by the dotted area enclosed by heavy lines. headgroup; (䢇) Pb2⫹; (䡬

[16]. Specifically, marked differences were observed in the potential-dependent absorption spectra of PbS-I, PbS-II, and PbS-III. Biasing the epitaxially grown PbS nanoparticulate films to negative potentials (from ⫺0.5 to ⫺1.1 V) increased the intensity of absorption in the ultraviolet region. In contrast, no change in the absorption at wavelengths longer than 700 nm was observed in the nonepitaxially grown PbS-III nanoparticulate film on changing the potential from 0 V to ⫺1.5 V. Absorption spectra of the optically transparent conductive glass (i.e., the control) remained unaltered upon biasing the potential between ⫹0.5 and ⫺1.5 V. The near-infrared absorption is likely to correspond to the spectrum of trapped charge carriers. Increase of this absorption results from the accumulation of trapped conduction-band electrons at negative bias potentials in PbS-I and PbS-II. Indeed, absorbances for PbS-II at 750 nm were found to decrease with increasing applied positive potential linearly to ⫺0.6 V, after which they remained unaltered. The point of inflection, ⫺0.50 ⫾ 0.05 V, may be taken to correspond to the flatband potential, Vfb, of the PbS-II nanoparticulate film. Marked differences between PS-I, PS-II, and PS-III also manifested themselves in capacitance versus potential and photocurrent curves. The rise of the photo-

currents at negative potentials is characteristic for ptype semiconductors. The onset of photocurrent is considered to correspond to the flatband potential. Although for PS-II it coincides with the flatband potential determined from the potential-dependent long-wavelength absorption spectra, in the absence of other evidence the onset of photocurrent cannot be meaningfully attributed to flatband potentials in the present system. Dependence of the absorbance on the applied potential, as well as the observed photocurrent and voltagedependent capacitances, reflects a complex interplay between the electron population in the electronic bands, in the traps (whose levels correspond to bulk imperfections), and in the available surface states, in addition to the ongoing interfacial electrochemical and photoelectrochemical processes. V.

CONCLUSION

Generation of nanoparticles and nanoparticulate films under monolayers has demonstrated the viability of this colloid chemical approach to advanced materials synthesis. The versatility of the approach permitted the fabrication of simple and composite nanoparticles, nanoplatelets and nanostructured films; two- and three-

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ACKNOWLEDGMENT Support of this work by the New York State Science and Technology Foundation and Clarkson University’s Center for Advanced Materials Processing (CAMP) is gratefully acknowledged. REFERENCES 1. 2.

3.

4. 5. 6.

7. 8. 9. FIG. 6 Schematics of equilateral-triangular PbS-I epitaxially grown under monolayers prepared from AA, PbS-II epitaxially grown under monolayers prepared from mixtures of AA and ODA, and PbS-III nonepitaxially grown under monolayers prepared from hexadecylphosphate.

10. 11. 12.

dimensionally size-quantized nanoparticles; and epitaxially grown nanocrystallites. The information obtained has considerably aided the design of self-assembled films potentially usable in optical, electro-optical, and electronic devices.

13. 14. 15. 16.

E. Hellstern, H. J. Fecht, Z. Fu, and W. L. Johnson, J. Appl. Phys. 65:305–312 (1998). P. Avouris, Acc. Chem. Res. 27:159–165 (1994); E. Hartmann, P. Marquardt, J. Ditterich, and H. Steinberger, Adv. Colloid Interface Sci. 46:221–262 (1993). R. W. Siegel, in Materials Science and Technology: A Comprehensive Treatment, Cluster Assembly of Nanophase Materials, VCH Publishers, Weinheim, 1991, pp. 583–614. S. Mann, Biomimetic Materials Chemistry, VCH Publishers, New York, 1996. D. A. Bazylinski, A. J. Garratt-Reed, and R. B. Frankel, Microsc. Res. Tech. 27:389–401 (1994). J. H. Fendler, Membrane-Mimetic Approach to Advanced Materials, Springer-Verlag, Berlin, 1994, pp. 1– 235. G. A. Ozin, Adv. Mater. 4:612–649 (1992); G. A. Ozin, Adv. Mater. 6:71–76 (1994). J. H. Fendler, Isr. J. Chem. 33:41–46 (1993). N. A. Kotov, E. D. Zaniquelli, F. C. Meldrum, and J. H. Fendler, Langmuir 9:3710–3716 (1993). J. H. Fendler and F. C. Meldrum, Adv. Mater. 7:607– 632 (1995). S. X. Ji, C. Y. Fan, F. Y. Ma, X. C. Chen, and L. Jiang, Thin Solid Films 242:16–20 (1994). X. K. Zhao, J. Yang, L. D. McCormick, and J. H. Fendler, J. Phys. Chem. 96:9933–9939 (1992). J. H. Fendler, Supramol. Chem. 6:209–216 (1995). J. P. Yang, F. C. Meldrum, and J. H. Fendler, J. Phys. Chem. 99:5500–5504 (1995). J. P. Yang and J. H. Fendler, J. Phys. Chem. 99:5505– 5511 (1995). X. K. Zhao, L. D. McCormick, and J. H. Fendler, Adv. Mater. 4:93–97 (1992).

32 Formation of Nanoparticles in Organized Amphiphilic Films KAREN GRIEVE and FRANZ GRIESER Victoria, Australia D. NEIL FURLONG

I.

University of Melbourne, Parkville,

RMIT University, Bundoora, Victoria, Australia

INTRODUCTION

The in situ production of particles, method 1, has most frequently been undertaken using Langmuir-Blodgett (LB) films containing metal or semiconductor particles. As the formation of particles in situ offers considerable possibilities of particle-film synergy, these films will be considered in some detail in this chapter. LB films have also been made in which particles have been introduced at the precasting (2) or postcasting (3) stage. LB films produced from Langmuir monolayers and particles formed epitaxially under them, or from expanded vesicles of nanoparticles (method 2a), also offer possible synergistic properties with the surfactant headgroup intimately associated with the particles. A major reason for the use of LB techniques to produce particle-films is the fine, molecular-level control over film thickness and particle distribution that can be achieved, especially if the particles are synthesized in situ. The technique of layer-by-layer (LbL) assembly, in which particle films are built up through electrostatic interactions, offers less precision at the assembly stage but produces more robust films with wider possible applications and will also be discussed in this chapter. The conditions required for the manufacture of these films are considerably less rigorous than those for LB films, which require absolute cleanliness and special apparatus. It is only recently that particles have been prepared in situ in these films (method 1). Before this, particles were always prepared in colloidal solution and

Thin organic films containing colloidal particles have been of interest for some time because of their possibly synergistic properties. By surrounding nanoparticles with organic/amphiphilic groups, the useful photo, electrical, or reactive properties of the particles may be enhanced, and at the same time, the organic film provides a robust, readily manipulable and transferable medium. These particle-films have been prepared in a number of ways and can be loosely classified into three groups: 1.

2.

3.

Amphiphilic or polyelectrolyte films in which metal or semiconductor particles have been prepared in situ (in the films). These usually involve the reaction of an incorporated metal ion with a selected reactant, which may be a gaseous or solution species. Films of amphiphiles/polyelectrolytes/polymers assembled with colloidal particles previously formed. The particles may be (a) Formed using the amphiphile used in film assembly as a template, as in the epitaxial formation of particles at a Langmuir monolayer, or in vesicles, or (b) Previously prepared in an unrelated solution. Films of amphiphiles into which the preprepared particles are allowed to percolate and be adsorbed.

These methods are schematically illustrated in Fig. 1. 639

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FIG. 1 Scheme of the methods for preparing amphiphilic particle-films. For an outline of the methods, refer to the text in the Introduction. Note that two types of organic precursor have been illustrated to include ordered precursors such as Langmuir monolayers and disordered precursors such as polyelectrolytes.

then assembled as part of the film. By prepreparing particles, although the possible synergic reactions between the particle surface and the amphiphile may be lost, it is possible to incorporate a larger variety of particles into films and be sure of their properties independent of the film. Both the techniques of LB and LbL films can be used to prepare extremely thin, molecularly controlled particle-films that are useful for electro-(optical) applications such as diodes and photocells. On the other hand, to test properties such as photobleaching, films with very high optical absorbance are required and it is far more convenient to use films of self-assembled polyelectrolytes, such as Nafion, in which particles have been synthesized in situ (method 1). These films can be compared with particle-films prepared by solgel technologies. Other, thicker organic particle-films usually involve the incorporation of prepared colloidal particles into the film at the film building stage (method 2). Methods include electropolymerization, optical polymerization, and spin-casting. As stated, this chapter will concentrate on the thinner sequentially assembled films produced by the LB and LbL techniques. Nanoparticles incorporated into these films include both semiconductors and metals; however, there has been considerably more research

into semiconductor particles, and this bias will be reflected here. Following a discussion of the preparation and physical characteristics of these films, an outline of the results of photoelectrochemical investigations will be presented. To emphasize the use of particlefilms as devices, photobleaching results for self-assembled films will also be described. II.

TYPES OF FILMS

A.

Langmuir-Blodgett Films

Langmuir-Blodgett (LB) films have been prepared and studied for over 70 years [1,2], but it is only in the last 25 that they have been used for the in situ synthesis of nanoparticles [3,4] and even more recently for the incorporation of premade particles [5]. They are prepared from compressed amphiphilic monolayers (Langmuir monolayers) formed at the air-water interface. The amphiphile is transferred to the substrate a monolayer at a time, in a highly controlled manner, with hydrophilic or hydrophobic attraction binding the layers. 1. Film Preparation The method of preparation is illustrated in Fig. 2, which shows the transfer of a surfactant monolayer onto a hydrophobic substrate as it passes through the

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tain a constant surface pressure, the efficiency of the transfer process can be measured. Properties of LB films are affected by factors such as the stability of the monolayer, subphase conditions including pH and the presence of electrolytes, temperature, the surface pressure of the monolayer when it is transferred (transfer pressure), and the speed at which the substrate passes through the monolayer (transfer speed). Other factors that can affect the films are the time allowed for drying between dips and the orientation of the substrate with respect to the surface. The nature of the substrate, in particular its roughness, hydrophobicity, or hydrophilicity, is also very important. Detailed information about the manufacture and properties of LB films can be found elsewhere [6–8]. (a) Nanoparticles in Langmuir-Blodgett Films. Semiconductors and metals can be produced by the reaction of a metal ion with a reacting gas such as hydrogen sulfide or a reducing gas such as hydrazine, respectively. If the reaction is carried out in the presence of a stabilizing medium, the product can be in the form of nanosized particles [9]. Equation (1a) is an example of the reaction between a divalent metal ion and a sulfide ion to produce II-VI semiconductor nanoparticles, Equation (1b) of a monovalent metal ion and hydrazine to produce metal. stabilizer

FIG. 2 The film transfer process for a hydrophobic substrate passing through a Langmuir monolayer. The formation of the first three layers of a Y-type LB film is illustrated.

air-water interface (1). The surface of the substrate becomes hydrophilic because the headgroups face outward, and so when it is passed back up through the monolayer, it may be coated with another layer of the amphiphile, this time bonding through its hydrophilic portion (2). If the substrate is hydrophilic, the first layer is transferred when the substrate leaves the subphase. By repeating this ‘‘dipping’’ process, films of a known number of bilayers can be prepared. The structure of the film may be lamellar (formed of bilayers; Y-type) or identically oriented monolayers (X- and Z-type) depending on whether transference occurs each time the substrate passes through the monolayer or only when the substrate enters or leaves the subphase, respectively. The surface pressure of the monolayer is maintained during transfer by continual reduction in the monolayer area, effectively compensating for the area of amphiphile transferred. By comparing the area of the substrate to the reduction in area necessary to main-

M2⫹ ⫹ S2⫺ → size-quantized MS stabilizer, N2H4 M⫹ → size-quantized M0

(1a) (1b)

(b) Premade Particles. Nanoparticles can be incorporated into LB films by a variety of mechanisms. Particles can be preprepared in colloidal solutions of micelles or vesicles in which a surfactant(s) or polyelectrolyte acts as the stabilizer. These can be introduced into the subphase of a Langmuir monolayer prior to film transfer. The particles become associated with the monolayer amphiphile and are transferred with it [5,10–27]. This process is an example of synthesis type 2b by the classification used in the Introduction. A further way of preparing nanoparticles is to use vesicles as the stabilizing/capping medium. Such vesicles have been shown to open up in aqueous solution to form monolayer films at the subphase surface, with the particles attached to the monolayer (type 2a) [28,29]. Stabilized particles can also be spread directly as the monolayer, either with a supporting amphiphile [30– 32] or cross-linking/binding agent [33] or, if the colloidal stabilizer has particular properties, as the sole component of the Langmuir-type monolayer (type 2b) [34–46]. These films can then be transferred using the Langmuir-Blodgett technique. A further method for in-

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troducing semiconductor nanoparticles to LB films is one developed by Fendler and coworkers whereby particles are formed epitaxially at a Langmuir monolayer prior to film transfer (type 2a) [10,28,47–52]. In all these methods the prepared nanoparticles are incorporated in the LB film as it is formed; however, it is possible that particles can be introduced after the film is formed. Both metal [53–56] and semiconductor [57] particles were found to diffuse into similar surfactant bilayer films formed by thermal evaporation (type 3). The scheme in Fig. 3 shows the various methods for the incorporation of nanoparticles in LB films. Of the methods for incorporating premade particles, those using opening vesicles or Langmuir monolayer epitaxy are most likely to involve significant nanoparticle-amphiphile interaction. One way to ensure this interaction is to form the particles in situ. (c) In Situ Formation of Nanoparticles. A method for preparing nanoparticles in situ within fatty acid LB films (type 1 in the Introduction) was developed by Barraud and coworkers in their efforts to build con-

FIG. 3

ducting layers within amphiphilic films [3,4]. The basic procedure involves the reaction of a metal ion–fatty acid LB film with a reactive species such as H2S or N2H4 as in Eqs. (1a) and (1b). As many metal ions undergo a pH-dependent exchange with the carboxylic acid proton of the fatty acid [58,59], the film is prepared by either transferring a surfactant monolayer over a subphase that contains the metal ion at an appropriate pH [60] or immersing the fatty acid film in a solution containing the metal ion (again at an appropriate pH) [3,4]. The former method is used more frequently as the metal ion in the subphase often acts to stabilize the Langmuir monolayer and facilitates high-quality film transfer [8]. To form metal nanoparticles, the metal salt fatty-acid LB film is exposed to a reducing gas such as N2H4 [3,4,61,62] or CO [63] or is photoreduced [64]. Another reductant, H2, has been used to reduce CuS particles in LB films [65]. To form chalcogenide or halide semiconductor nanoparticles, the film is exposed to an appropriate gas [H2E (E = S, Se, Te for chalcogenides) or HX (X = Cl, Br, I for halides)]. The general

A scheme of the methods that have been used to incorporate nanoparticles into LB films.


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reaction mechanism is illustrated by the reaction of a cadmium arachidate film and H2S as shown in Eq. (2a). Cd2⫹{⫺OOC(CH2)18CH3}2 ⫹ H2S(g) → CdS ⫹ 2HOOC(CH2)18CH3

(2a)

For the purposes of this chapter, the surfactant name will be abbreviated, so arachidic acid is designated ArH and cadmium arachidate CdAr2. Similar abbreviations for behenic acid (BeH), steric acid (StH), and dioctadecyl ammonium bromide/chloride (DDAB/C) and their corresponding salts will also be used. Using this nomenclature, Eq. (2a) becomes Eq. (2b): CdAr2 ⫹ H2S(g) → CdS ⫹ 2ArH

(2b)

The reaction to form particles is usually initiated in a multilayered LB film. It is possible, however, to allow the reaction to take place after each bilayer is transferred [66]. This method has been used to form different kinds of semiconductor particles in sequential layers of the film [67]. Amphiphile-stabilized, nanosized TiO2 can be made by the hydrolysis of films formed from ArH monolayers spread on subphases containing TiCl4 [68]. The pyrolysis of similar films leads to the formation of quantum-sized TiO2 particles but destroys the amphiphilic part of the film [69,70]. Palladium likewise can be formed by the thermal decomposition of palladiumcontaining films [71]. In an analogous fashion, the formation of CdO particles by the exposure of cadmiumcontaining films to ultraviolet (UV) light and ozone is accompanied by loss of the amphiphile [72,73]. The latter methods are useful for making particles but, as the amphiphilic part of the film is destroyed in the process, will not be considered further. The easiest method for establishing the size-quantized nature of the particles formed is to analyze the absorption spectra. Blue-shifted absorption spectra, such as those shown in Fig. 4, are a clear indication of size quantization [9,74,75]. The absorption edges of the CdS, CdSe, and CdTe particles in this figure are all shifted by 0.4–0.3 eV from the band gap of the bulk material. The types of nanoparticles that have been formed in LB films are listed in Table 1. It can be seen that in addition to simple metals and semiconductors, more complex particles can be made. For example, CdS-CdSe core-shell particles have been made by exposing a CdS/BeH film to H2Se [113,114,119] and Te2⫺ can replace some Se2⫺ to form CdSeTe core-shell particles [114]. For the former reaction, it has been calculated that a monolayer of CdSe is formed around the CdS core. When the subphase of the Langmuir layer

FIG. 4 Absorbance spectra of 19-layer cadmium nonacosa10,12-diyonate LB films after exposure to (a) H2S; (b) H2Se; (c) H2Te. The spectra are corrected for the absorbance of the plate and the amphiphile, and the arrows indicate the absorption onset of the spectra [114].

contains a mixture of metal ions, the effect on the formation of particles within the LB film depends on the nature of the metal ions. If the subphase contained Zn2⫹ and Cd2⫹, or Cd2⫹ and Mn2⫹, mixed semiconductors Zn1⫺y CdyS [98] and Cd1⫺x Mnx S [120,121] were formed. The metal ratio in the particles reflected that of the subphase. However, when both Hg2⫹ and Cd2⫹ are in the subphase, it has been shown by analysis of UV-visible spectra that discrete HgS and CdS particles are formed [107]. The different reaction rates of Cd2⫹ and Hg2⫹ with S2⫺ have been used to explain the result. Mixed subphases of Cd2⫹ and Pb2⫹ produced only PbSt2 films and PbS particles [98]. This may be due to the higher stability expected of PbSt2 over CdSt2. Nanoparticles are formed throughout the whole LB film and not just at the surface. This is shown by the linear relationship commonly observed between the number of layers in a film and the UV-visible (UV-vis) absorbance of the film at a particular wavelength [116,117]. An example of this relationship is shown in Fig. 5 for an ArH film containing HgS nanoparticles [107]. 2. Control of Particle Size Particle dimensions in size-quantized particles determine their optical absorption and redox characteristics, and the ability to tune these properties is fundamental to nanoparticle synthesis and application. Particle size is thought to be restricted by either or both of two processes. One process is known as chemical ‘‘capping’’ and results from interaction between a stabilizing surfactant and the surface of a nanoparticle. Examples

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TABLE 1 Semiconductor and Metal Particles That Have Been Made In Situ in LB Filmsa Particle

Amphiphile

References

CdS

ArH StH BeH other ArH NDA NDA ArH NDA StH StH ArH ArH BeH ArH BeH ArH StH BeH other ArH StH other StH StH BeH ArH DDAB ArH DDAB ArH ArH ArH StH ArH ArH ArH BeH ArH, DDAB DDAC ArH BHDB DDAB

[60,76–93] [94–103] [104–107] [94,108–117] [118] [113,114] [113,114] [119] [113] [96–98] [98] [120,121] [67] [107] [122] [106,122–124] [61] [125] [105,126] [65,96,112] [127] [96,97,101,128–133] [110,112,134] [135] [96,97,136] [105] [137] [62] [137] [62] [138–140] [140] [140] [97] [66] [68] [66] [3,4] [63] [64] [61] [65] [62]

CdSe CdTe CdS-CdSe CdS/PbS Cd-ZnS Cd-MnS CdS-PbS & MgS CdS-HgS HgS CuS

PbS

CoS ZnS PtS(2) PdS CdI2 CdCl2 CdBr2 PbI2 AgI TiO2 Ag Au Cu Pd a

The amphiphiles used have been listed, particularly straight-chain fatty acids, for comparative purposes. As there is insufficient space to list all amphiphiles, those which have been used less frequently are usually classified under ‘‘other.’’ Abbreviations: ArH, arachidic acid; StH, stearic acid; BeH, behenic acid; NDA, nanocosa-10,12-diyonic acid; DDAB, dimethyldioctadecylammonium bromide; DDAC, dimethyldioctadecylammonium chloride; BHDB, 2,4-dihydroxybenzilidine-4⬘-(hexadecylamino)benzylamine.

FIG. 5 UV-vis absorbance spectra (corrected for the absorbance of the fatty acid and the quartz substrate) of 10-, 20-, 30-, and 40-layer HgAr2 films exposed to H2S for 15 min. The number of layers is indicated on each spectrum. Inset: Absorbance as a function of layer number at 350 nm (●), 400 nm (䊱), and 600 nm (䡲) [33].

are the use of thiols [141] or phosphates [142] as stabilizers in the preparation of colloidal solutions of CdS. The other process is the purely physical confinement presented by host media such as zeolites [143] and glasses [144]. In LB films, it is likely that the growth of the particles is restricted by both the physical confines of the layers and the capping action of the surfactant molecules. The methods are effective as particles produced in LB films are usually of the order of 1–4 nm in diameter. (a) Particle Size Determination. The method most frequently used to determine the dimensions of particles in LB films involves the comparison of a feature of the UV-vis absorbance spectrum with a calibration curve relating the diameter of the particles to the chosen feature. Figure 6 is an example a calibration curve for CdS particles. The blue shift (increased energy) in the absorbance of smaller particles due to size quantization effects [9,75,145] is clearly demonstrated by this curve. The data have been taken from numerous literature sources in which the average sizes of particles in solution have been resolved by methods such as transmission electron microscopy (TEM) and x-ray diffraction (XRD), and the inflection point (minimum of the first derivative) of the absorption spectrum has also been determined. The inflection point does not represent the band gap of the average-sized particle; however, the minimum of the second derivative, which more accurately describes this band gap [145,146], can be difficult to find precisely in LB films, which often display low absorbance and significant amounts of scat-


FIG. 6 A calibration curve of inflection point wavelengths in absorbance spectra of colloidal CdS nanoparticles as a function of experimentally determined (TEM and XRD) particle sizes. The data have been collected from a large number of literature sources [249]. The solid line is a theoretical curve often used in this method of calibration [142].

ter. The curve (solid line) in Fig. 6 [147] has frequently been used to estimate particle diameters from spectra inflection points, and, as can be seen from the figure, it should provide a reasonable result. Statistical methods that have been used to determine the sizes of particles produced in LB films include TEM and atomic force microscopy (AFM). TEM images are most useful for highly contrasting metal particles such as those in Fig. 7 [62–64], but the low contrast between surfactant and particle makes analysis of semiconductor particle-films difficult. It is possible to obtain indirect estimates of the sizes of particles in films from TEM images taken when the particles have been washed from a film onto a grid [114] or when the surfactant is removed by heating under vacuum [77]. AFM measurements have also been used [61,62,79,122,137]; however, for these it is necessary to remove the surfactant in a process that tends to result in growth of the particles. The effects of removing the amphiphile will be discussed further in the next section. (b) Factors Affecting Particle Size. The size of particles formed in LB films is influenced by conditions at all stages of preparation, i.e., when the film is made, during the reaction to form the nanoparticles, and after the particles have been formed. During film preparation there are many factors that influence the size of the particles which will form, those that have received the most attention being the structure of the film and the concentration of metal ions

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FIG. 7 TEM image of gold nanoparticles in an ArH film. ArH was compressed over an [Au(en)(en-H)]2⫹ subphase and the grid was dipped through the surface three times before exposure to CO. The insert shows an HRTEM image of a ˚ [63]. gold particle with a lattice spacing of 2.3 A

in the film. Film structure can be varied simply by changing the nature of the amphiphile. More structured films, such as those prepared using calixarenes [103,117], tend to produce smaller particles than films of straight-chain amphiphiles. Straight-chain amphiphiles in turn produce smaller particles than disordered bilayer films [94]. A systmatic investigation in which hydrocarbon interaction and film stability were increased by decreasing the ratio between carboxylic acid groups and hydrocarbon chains in poly maleic acid octadecanol ester (PMAO) amphiphiles showed a similar inverse relationship between structure and size [111,134]. Another method for increasing film structure is to increase transfer pressure. When higher transfer pressures were used in the formation of Cd, Cu, and Zn behenate films, smaller particles resulted [105]. It is possible that the higher degree of structure brought about by the various means discussed above creates films with less flexibility. Thermodynamic considerations would favor the creation of more, smaller particles with less disruption of the film structure. The effect of film structure is not simple, however, as altering the amphiphile or transfer pressure may also alter the particle concentration in the film, and as will be discussed next, this too is an important factor in determining the size of particles formed.

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The metal ion/amphiphile ratio in an LB film can be altered by varying the subphase pH and therefore the proportion of metal ions exchanged [103]. The metal ion concentration/area ratio can readily be altered by changing the molecular area of the surfactant [94] and the concentration of carboxylate functions in the amphiphile [134]. In both these instances, an increased (reactive) ion concentration led to an increase in particle size. Figure 8 illustrates the relation between the concentration of Cd2⫹ ([Cd2⫹]) in the film and the size of CdS particles created in the form of the band gap (Eg) of the resulting films. [Cd2⫹] was varied in this instance by the use of amphiphiles with different molecular areas and also by the intercalcation of more Cd2⫹ into the films after particle formation, by a method discussed later in Section II.A.2.c. The metal ion/amphiphile ratio can also be lowered by introducing into the subphase an inert metal ion such as Ca2⫹, which dilutes the amount of reactive Cd2⫹ in the films [113,114]. However, this change was insufficient to decrease the size of the particles produced unless dihexadecyl phosphate was mixed with the 16-8 diyonate amphiphile. The role of the phosphate is unclear, but its influence on the size of the particles may be related to amphiphile-metal interaction. To date there has been no systematic study published on the effect different surfactant headgroups exert during particle formation. Such an investigation into the phenomenon of capping

FIG. 8 The band gap energy (Eg) of CdS as a function of the concentration of Cd2⫹ per unit area ([Cd2⫹]). The concentration was altered by varying the headgroup of the amphiphile (the legend refers to the amphiphiles described in the original text) and by a series of intercalation-sulfidation cycles [94].

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would significantly enhance our understanding of particle-film synthesis. A further, final method of controlling the metal ion/ area ratio, namely that of controlling the surface pressure, was introduced earlier. In this case, an increased concentration led to smaller particles [105]. The smaller size of the particles may be caused by the increased structure of the film. This apparent anomaly to the generally observed size-concentration dependence serves to illustrate the complicated relationship between film structure and ion-amphiphile interaction during the synthesis of particles within LB films. As another contributing factor, the thickness of the film might be expected to influence the size of particles produced, but results are inconclusive with evidence both supporting [87] and opposing [60,103,113] an impact. The contrasting results may be explained by differences in conditions when the films were transferred. At the reaction stage, two factors that have been observed to affect the size of particles produced are temperature and the presence of water. Higher temperatures predictably led to the formation of larger particles when CdAr2 was exposed to H2S [82,83]. In other investigations, smaller particles were formed when care was taken to exclude water from the reacting H2S than when water-saturated H2S was used (R. S. Urquhart et al., submitted). Both these results can be explained by kinetic considerations, with water and heat facilitating the coalescence of CdS molecules within the film and assisting amphiphile rearrangement. Removal of the amphiphile after particle formation can lead to growth of the particles. For example, washing films with a solvent known to dissolve the amphiphile leads to an increase in the size of the particles remaining on the substrate. The spectra in Fig. 9 were taken before and after a CdS/ArH film was washed with chloroform. The red shift in the spectrum corresponds to an increase in particle size from 2.2 to 2.9 nm, and this accords well with other published observations [87]. Heating the film to remove some of the surfactant also led to a red shift in the absorbance spectra of CdS particles. By altering the annealing conditions, the particles could be grown in a controlled fashion [90]. The introduction of wet N2 gas to CdS/ArH films, in which CdS was formed by the exposure of CdAr2 films to dry H2S, also caused a red shift in the UV-vis absorbance spectra (R. S. Urquhart et al., submitted). This too may indicate that the size restriction of nanoparticles in these films is to some extent a kinetic phenomenon, similar to that observed for solution colloids. The processes of annealing and of dissolving


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FIG. 9 UV-vis absorbance spectra (corrected for absorbance due to the fatty acid and the substrate) of a 40-layer ArH film containing CdS before and after immersion in a stirred solution of chloroform. The inflection point of the spectra, which was used to determine the average particle size given, is indicated by the arrows [107].

surfactant would open and/or destroy the structure of the films and, like the addition of water, allow or promote coalescence of the molecules/particles. There is further discussion of the conditions affecting the particle growth in the section on mechanism. It is important to note that in spite of all the coalescence that may occur, either when the particles are being made or afterward, bulk material is not formed and the dimensions of the particles remain nanoscale. (c) Stepwise Growth of Particles. It is also possible to grow particles in support films by the addition of more reactants in a two-step process. Semiconductor particles such as CdS, PbS, and HgS have been grown in LB films by the relatively simple procedure shown schematically in Fig. 10. After particle formation more metal ions are introduced into the film by immersing it in a solution containing the metal ion at an appropriate pH. The carboxylic acid proton on the fatty acid, which has been restored during semiconductor synthesis, is again exchanged for the metal ion. Reexposure of the film to the chalcogenide gas results in growth of the particles. By repeating these intercalation and gassing steps in a cyclical fashion, the particles can be grown stepwise [77,122,126,136]. (This cycle will be referred to as intercalation-sulfidation as H2S is the most commonly used reacting gas.) Figure 11 shows the UV-vis absorption spectra for ArH films containing CdS that has been subjected to three intercalation-sulfidation cycles after the initial particle formation (four exposures to H2S in total). The spectrum is red shifted with each

FIG. 10 A schematic diagram showing the effect of exposure of a CdAr2 film to H2S. As CdS nanoparticles form, the film is disrupted, becomes thicker, and develops a greater degree of tilt. The CdS particle is drawn to show the arachidate molecules associated with surface cadmium ions in a ‘‘capping’’ effect. The growth of the particles by intercalation in Cd2⫹ solution and further sulfidation is also illustrated.

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FIG. 11 UV-vis absorbance (corrected for the absorbance of the amphiphile and the substrate) of CdS in 19-layer ArH films grown by repeating the intercalation-sulfidation cycles. (a), (b), (c), and (d) refer to films that have undergone 1, 2, 3, and 4 sulfidation steps, respectively. Inset: Particle size as determined from the absorption spectrum as a function of sulfidation steps.

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accord with the sequential red shift in the spectra. Semiconductor nanoparticles treated by this stepwise process include CdS [77–79,94,95,97,98,136], CuS [126], HgS [122], PbS [96,97,128], ZnS [96,97], and AgI [66]. Metal nanoparticles of Ag [63,64,66] have also been grown on or in LB films by analogous cycles of Ag⫹ intercalation and reduction. By taking advantage of the intercalation step to introduce a second metal to the film, mixed semiconductor (possibly core-shell) particles have been produced. The introduction of Cd2⫹ to PbS/StH and ZnS/StH films caused the displacement of Pb and Zn ions and mixed particles formed on exposure to H2S [98]. Dipping CdS/StH films into Pb2⫹ and continuing with repeated intercalation/sulfidation cycles seemed, however, to produce discrete PbS particles in the film [96,98], similar to the binary system of HgS and CdS observed in ArH from mixed subphases as discussed earlier. 3.

cycle, indicating particle growth, and the scatter in the film increases as the structure of the film is disrupted. The growth in particle size can also be seen in AFM measurements taken after one, three, and five sulfidation steps (Fig. 12). As the particles grow during the washing step prior to AFM measurements, the sizes cited are not those of the particles in the film, but the growth of the particles can be seen clearly and is in

FIG. 12 Particle size distributions of CdS formed by exposing bilayer films of ArH to H2S determined by AFM measurements. The films were prepared on mica and subjected to washing in chloroform before analysis. The particles were grown by repetitions of the intercalation and sulfidation cycle and the histograms show the distributions determined for particles formed after 1 (solid), 3 (unfilled), and 5 (shaded) exposures to H2S, respectively [79].

Characterization of Films

(a) Particle Shape. It has been claimed by many that planes rather than particles are formed within the films. This view usually results from an interpretation of XRD and Fourier transform infrared (FTIR) measurements that show maintained crystallinity and small changes in interlayer spacings within the films during the exposure of fatty acid salt films to H2S [95,99,135,136]. There is considerable evidence, however, that in almost all instances particles are formed. That spheroidal particles are produced in the films is supported by TEM images [60] such as those of Ag particles in ArH [63] shown in Fig. 7. AFM images of ArH films containing CdS showed protrusions in an otherwise smooth surface that were attributed to particle formation [102]. Further evidence for the formation of particles is the production of features of the FTIR spectrum consistent with RCOOH facing dimers when a CdAr film is exposed to H2S [86]. The formation of CdS in planes would prevent observation of such dimers. Rutherford backscattering (RBS) analysis has indicated particle formation [84], whereas x-ray diffraction/reflection studies have been interpreted to suggest the existence of disklike structures of CdS in ArH films [92]. It has been claimed that the shape of the particles formed is determined by the ability of the molecules formed to coalesce into particles [see Eqs. (3) and (4)], which is more difficult in more highly structured films. The theory has been extended to claim that in perfectly formed Y-type films with high concentrations of highly interactive surfactant, layers of semiconductor would be formed. This has been used to


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explain the very different XRD spectra for CdS/StH films of very high transfer pressure (37.5 mN m⫺1) compared with those of similar films prepared at lower pressures [99,100]. (b) Mechanism of Particle Formation. Semiconductor nanoparticles appear to be formed in a two-step process similar to that of colloids in solution. To give an example of a well-studied system, the formation of metal chalcogenide particles by reaction of a divalent metal ion with H2E requires the following steps: M2⫹ ⫹ H2E → MeE ⫹ 2H⫹

(3)

nME → (ME)n

(4)

The first equation (3) produces metal sulfide molecules that then diffuse and coalesce together to form particles according to Eq. (4). If a fatty acid is the matrix, the protons released from Eq. (3) form carboxylic acids and the overall equation becomes M2⫹{⫺OOC(CH2)nCH3}2 ⫹ H2E(g) → ME ⫹ 2HOOC(CH2)nCH3

FIG. 13 Grazing angle FTIR spectra of a 20-layer CdAr film (lower) and an identically prepared film exposed to H2S gas for 2.5 h (upper). The spectrum of the film after sulfidation has been displaced vertically for clarity. The structures responsible for the major bands are shown at the top of the plot. The circles on the lower spectrum indicate the regions that would show bands if protonated carbonyl groups were present [78].

(5)

It is difficult to differentiate the two mechanisms as they occur to some extent simultaneously. FTIR spectroscopy and quartz crystal microbalance (QCM) gravimetry have both been used to monitor the extent of the reactions taking place within LB films. Reactions of the type depicted in Eq. (5) have been shown to reach less than 100% completion according to grazing angle FTIR spectra taken before and after H2S exposure, such as that in Fig. 13. The peak due to the symmetric stretching mode of unprotonated RCOO⫺ (1400–1500 cm⫺1) is significantly reduced but does not disappear on H2S exposure, even though the stretching modes associated with the protonated RCOOH (C — O, 1700 cm⫺1; O — H, 3000–3200 cm⫺1) become apparent [78]. A similar incomplete reaction of all RCOO⫺ molecules has been observed by FTIR analysis of other fatty acid systems [91,99,100,111,131,137]. Other studies, however, have determined that the band caused by metal-associated carbonyl groups (1700 cm⫺1) does disappear entirely on H2S exposure [87,96,105,123,124,136]. If not all the carboxylate groups are reprotonated by the reaction with H2S, then it is thought that some surfactant molecules remain associated with the metal ion and it is presumed that these form a capping layer around the semiconductor particle, as represented diagrammatically in Fig. 10. The less than 100% reprotonation of the carboxylic acid salts is supported by evidence of FTIR spectra taken before and after sublimation of ArH from a CdS/ ArH film [78]. Bands due to RCOOH were observed

to disappear after heating, whereas those due to RCOO⫺ changed little, indicating that they were associated with the CdS remaining on the substrate. The association of the surfactant with the particles is supported by evidence from QCM measurements. QCM microgravimetry can be used to determine the mass changes in a film caused by a reaction and, by comparing the change in mass determined with that predicted from the stoichiometry of Eq. (2a), the extent of reaction is ascertained. Figure 14 shows an example of H2S uptake with time of a CdAr2 film exposed to H2S, with the percentage uptake calculated from the stoichiometry of Eq. (2a) and the mass of fatty acid salt film when initially transferred and left to dry. It can be seen that the uptake of H2S is about 80% of the stoichiometric amount. Similar results have been found elsewhere [87]. In other instances, more than 100% reaction has been recorded, although these did not take into account the effect of H2S on the QCM electrode [76,79]. A larger mass may also be explained by the formation of elemental chalcogenide occasionally observed by x-ray plasmon spectroscopy (XPS) [62,118,125]. The existence of a capping layer around the particles helps explain the maintenance of the quantum-sized nature of the particles when most of the amphiphile has been washed or evaporated away. It also explains the greater than expected mass remaining on a QCM electrode after thermal evaporation of the amphiphile [115].

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FIG. 14 Percentage conversion of CdAr2 to CdS on exposure of a 19-layer film to H2S as a function of time as determined by QCM measurements. The percentage is calculated according to the stoichiometry of Eq. (5) and the mass change during film transfer. The films were placed under vacuum before each measurement, and the frequency change of blank QCM electrodes on exposure to H2S has also been taken into account.

The reaction taking place during ion intercalation is the same as that taking place at a monolayer in the formation of a fatty acid salt. It can be represented by Eq. (6). M2⫹ ⫹ 2HOOC(CH2)nCH3 → M2⫹{⫺OOC(CH2)nCH3}2 ⫹ 2H⫹

(6)

This reaction has also been followed by FTIR and QCM measurements. FTIR measurements have shown that all the bands due to RCOOH virtually disappear after prolonged immersion in M2⫹ solution, indicating a complete reaction with the available surfactant molecules [78,98,128,136]. QCM measurements show [77,79] that the mass change due to Cd2⫹ adsorption into a CdAr film is consistent with the stoichiometry in Eq. (6). (c) Effects on Film Structure. The CdS/ArH particlefilm has been extensively studied. A representation of the changes in film structure that accompany the formation of CdS particles in ArH LB films can be seen in Fig. 10. Deposited films of CdAr2 are well-ordered bilayer structures with a long orientation of 8 ⫾ 5⬚ to the normal axis [148] and a bilayer thickness measured ˚ [76], 54 ⫾ 1 A ˚ [87], 55 A ˚ [93], or 55.2 A ˚ as 53.4 A [91] as measured by surface plasmon resonance (SPR), XRD, x-ray scattering (XRS), or ellipsometry, respectively. On exposure to H2S, CdS particles form in layers determined by the hydrophilic headgroups of the surfactant molecules [91]. Both the tilt and the thickness

of the film have been observed to increase, accommodating the formation of particles. The new tilt was measured by XRD to be 37⬚ to the surface normal [91], in accordance with the 25–40⬚ commonly observed for protonated fatty acid films. The tilt can also be discerned from grazing angle FTIR (GA-FTIR) spectra (Fig. 13), where the bands due to methyl groups (2800–3000 cm⫺1) increase in intensity due to increased colinearity with the incident beam. The increase in bilayer thickness has usually been measured ˚ [60,76,93], although to be slight, ranging from 1 to 6 A ˚ increases as high as 12 A have been found [87]. Evidence for the maintenance of a layered structure, although somewhat disrupted, on H2S exposure can be seen in the broadened but still discernible peaks in bilayer spacing in XRD spectra [91] and the maintenance of the progression bands in FTIR spectra (the bands at less than 1400 cm⫺1 in the spectra in Fig. 13) [78]. Moderate film disruption has been confirmed by AFM [102] and ellipsometric measurements. The observed changes can all be explained by the creation of wellstructured microdomains within the films. Further intercalation and sulfidation steps resulting in the growth of the particles lead to further disruption of the film, and this can be seen readily in the increased scatter in the UV-vis adsorption spectra such as that shown in Fig. 11 and somewhat less clearly in changes in the progression bands in GA-FTIR experiments (Fig. 13) [78]. Although the data discussed pertain to the formation of CdS in ArH films, similar increases in tilting and bilayer thickness and disorder during particle formation have been observed for most LB films, and the majority of references in Table 1 contain some information about the effects of particle formation. Although a decrease in film thickness has been observed for the formation of CdS in StH [101], this has been explained by the high pressure of H2S used [87]. Films have sometimes been observed to change spontaneously after particle formation, with coagulation seen in AFM measurements [102] and migration toward the substrate caused by sulfide reaction indicated by RBS analysis [84]. However, in general the effect of particle formation introduces a degree of film disruption while maintaining overall short-range structure throughout the whole of the film. (d) Rate of Reaction. It seems that there are both chemical and physical factors that govern the rate of reaction of M2⫹ with H2E. The formation of ME molecules [Eq. (3)] seems to be dependent on the immediate chemical environment of M2⫹. High degrees of rigidity and structure in the films, and the absence of


water, restrict the rate at which the ME molecules coalesce [Eq. (4)]. In general, it is difficult to distinguish the reactions corresponding to Eqs. (3) and (4) as they usually occur simultaneously. Structure, however, is known to play a role in the kinetics of particle formation, as it does in limiting the size of particles formed. Investigations by Peng and coworkers into the effect of film preparation on reaction rate illustrate this very well. For example, reactions in films with greater structure caused by a greater dipping speed [131], or higher transfer pressure accompanied by an increased dipping speed [99], were significantly slower as shown by FTIR spectra. The choice of metal ion, too, can influence the structure of the film and hence the rate of reaction. Long-range order, which is greater in PbSt2 than CdSt2 [149], and tight packing, greater in ZnBe2 and CuBe2 than CdBe2 [105], has been shown to slow the rate of reaction. The properties of the surfactant can also affect the structure of the film and the rate of reaction as shown by the rates of HgS formation in ArH and BeH [137]. The pressure of gas used in the reaction may also affect the rate of particle formation [99,100,125], and the diffusion of gas through the film has been shown to be governed by the film structure, illustrated by a dependence of reaction rate on the thickness (number of layers) of the film [99,100]. The low pressure of H2S used in these experiments may partially explain this result. Experiments have shown the chemical rate-determining step to be the deprotonation of the sulfide. The protons released by the sulfidation of the metal ion need a ‘‘sink,’’ usually provided by the carboxylate group of the fatty acid. By removing possible sources of sinks, the whole reaction is slowed or stopped. This is illustrated by the reaction of H2S with films formed from diallyl dimethyl ammonium bromide (DDAB) and [PdCl4]2⫺ [62]. [PdCl4]2⫺ readily undergoes hydrolysis in the subphase conditions to form [PdCln(OH)m(H2O)1]2⫺, but this can be suppressed by the addition of HCl to the subphase. Films formed in the presence of HCl, therefore, contained no base (i.e., proton sink) in the coordination sphere of the ion. In these films there was no noticeable reaction on exposure to H2S (similar to the nonreaction observed by Ichinose et al. for Cd2⫹ in already protonated amino amphiphilic films [150]), and these may possibly be compared to similar films containing [PtCl4]2⫺ and [PtCl6]2⫺ (complex ions that do not hydrolyze), which took days to react completely [62]. Spectra taken of (PdCl4)(DDA)2 films made with and without HCl before and after exposure to H2S are shown in Fig. 15. It can be seen that for the film where the [PdCl4]2⫺ is

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FIG. 15 UV-vis absorbance (corrected for the absorbance of the amphiphile and the substrate) of LB films formed from DDAB on [PdCl4]2⫺ and [PdCln(OH)m(H2O)1]2⫺. The latter film was made by the inclusion of HCl in the subphase. The spectra are taken before and after H2S exposure for the times indicated [62].

hydrolyzed, the spectrum is changed due to PdS formation after only 30 min. On the other hand, 75 min of exposure to H2S was insufficient to change the spectrum of the film containing the unhydrolyzed complex. The times required for complete particle forming reaction have varied from minutes to 368 h for H2S with (PdCl4)(DDA)2 [62] but are difficult to compare given the large range of conditions and factors that must be taken into account. In essence, nanoparticles can be readily formed in LB films. The time necessary for particles to form, the size they reach, and the degree to which the films are altered by their formation are all factors that depend on the individual constituents of the film and the conditions of its preparation and treatment. These considerations, if understood sufficiently, could provide means to tune the properties of the particle-films to some extent and optimize them for specific applications. B.

Self-Assembling Films

LB films are ideal for manufacturing particle-films with molecular-layer precision and close interaction between the film medium (amphiphile) and the particle surface. Their fastidious manufacture is, however, a disadvantage when relatively thick films are required. Self-assembled films can also be used for the in situ formation of nanoparticles. As the particle surface interacts with charged groups in the film, the possibly synergistic properties of the matrix and nanoparticles are retained, but films up to many micrometers in thickness can be prepared.

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1. Nafion An example of a self-assembling material used in the preparation of nanoparticle-films is the cation-exchange polymer Nafion. As we have first-hand experience of its use, it will be discussed in some detail, although similar particle-films can be formed using other polymers such as polyethylene–polymethacrylic acid copolymer [151, 152]. (a) Film Preparation. Nafion has the ‘‘intelligence’’ to form a regular matrix of cavities connected by narrow tunnels. The cavities and tunnels are lined by sulphonate (SO⫺ 3 ) groups, which undergo exchange with M2⫹ in a process similar to the proton exchange in Langmuir monolayers and LB films outlined earlier. Exposure of the membrane to gaseous or aqueous S2⫺ results in the formation of semiconductor nanoparticles. Countercurrent techniques where H2S and Cd2⫹ have been introduced simultaneously from opposite directions [153] have been claimed to lead to more uniform films [154] than those produced by sequential cation exchange and chalcogenide exposure. The types of particles prepared in Nafion membranes are listed in Table 2. (b) Control of Particle Size. In the first experiments of this type [153,160,161,170,171,173,174], the particles formed tended to be relatively large particles (e.g., up to 1␮m). However, particles in the tight confinement region of size quantization have been formed since and considerable control over particle size has been developed. Methods for controlling particle size include the use of dry chalcogenide gas [162,165–167,176] (wet gas was used in the initial experiments). The slow rate of particle growth in films exposed to dry H2S allows the growth to be arrested by instant degassing when the particles reach the desired size. It is then a relatively simple procedure to grow the particles to differ-

ent sizes by Ostwald ripening by exposing the films to water at various temperatures [167,178] with the possible addition of more H2S [165]. The use of Na2S instead of H2S provides another method for producing larger particles [165,167] and sonication has been used to grow the particles [165]. Controlling the concentration of M2⫹ in the films limits the size of particles that can be formed. Immersion in a dilute solution of M2⫹ [176] and dilution of the concentration of active ions by the introduction of inert ions such as Ca2⫹ [165] are two methods which have been used. The synthesis conditions can also influence the crystal structure of the particles prepared [174]. When the films are constructed to probe the physicochemical properties of nanoparticles, ammonia is often introduced to the Nafion film prior to M2⫹ exchange, and this serves to passivate the film [164,167,178]. Examples of absorbance spectra showing the effect of film treatment on particle size can be seen in Fig. 16. Platinum metal has been prepared at and under the surface of Nafion films by reacting exchanged Pt2⫹ with NaBH4 [155]. In a method corresponding to 2a in the Introduction, Fe2O3 has been made by the hydrolysis of Fe3⫹ in a Nafion solution prior to the film being cast [179]. Particle size was controlled by the metal ion/sulfonate ratio. Particles of TiO2 have also been incorporated as Nafion films were cast (method 2b in the Introduction) and grown through an aging process, but it was not clear whether the particles were on the surface or within the

TABLE 2 Nanoparticles That Have Been Formed Within Nafion Films Particle Pt TiO2 SiO2 CdS CdS.ZnS CdS/Pt CdSe PbS FeS2

References [155] [156–158] [159] [145,154,156,160–169] [170–173] [174] [165,175] [176] [177]

FIG. 16 Absorbance spectra of CdS nanoparticles in Nafion films. The diameter of the particles estimated from the inflection points (indicated) is also shown. Sample (d) was prepared by exposing a dried Cd2⫹ exchanged film to ammonia gas and then to H2S. Samples (a) and (b) underwent similar treatment to (d) but were subsequently immersed in water at room temperature (a) or boiling water (b). Sample (c) was prepared by immersing the dried Cd2⫹ exchanged film in Na2S solution [167].


cavities of the film [158,180]. When nanoparticles form within Nafion films, the molecules coalesce inside already existing cavities, so considerably less research has been conducted on structural and mechanistic effects than has been undertaken for LB films, although the structure of the particles formed was found to be dependent on the method of preparation [153,174]. 2. Cast Bilayer Films Another example of a self-assembling amphiphile that has been used to form nanoparticles is tetradecyl-N-[[4[6-(N,N⬘,N⬘-ethylenediamino)-hexyl]oxy]benxoyl]- L glutamate (DTG). The cadmium salt of this surfactant (Cd(DTG)2) was exposed to dry H2S resulting in the formation of CdS particles about 4 nm in diameter [181,182]. If the film was cast as a multibilayer structure prior to Cd2⫹ intercalation, the product of H2S exposure depended on the nature of the Cd2⫹ salt used (CdCl2 or CdBr2) [150]. CdS has also been formed in amphiphilic cast films containing cyclams as size-restricting units. The particles did not interact strongly with the amphiphile once formed, and this hindered their potential use [183]. Lead halide nanoparticles have been prepared by similar procedures in other bilayer cast films [184]. The diffusion of nanoparticles into similar multibilayer films created by thermal evaporation was discussed earlier. C.

Layer-by-Layer Assembly

The layer-by-layer (LbL) assembly technique has been known variously as the alternate or layer-by-layer (self) assembly, the ionic self-assembled monolayer, or the molecular deposition method. The films are similar to LB films in the sequential nature of their assembly, but the degree of control in LbL films is not as fine. It has also been necessary for the components, usually stabilized nanoparticles and polyelectrolytes for particlefilm formation, to be formed prior to film assembly (method 2b in the Introduction). Nanoparticle-films made by this method have been widely studied as they are very simple to prepare and a wide range of materials can be incorporated [185–187]. As the preprepared particles are usually surrounded by a stabilizer that interacts with the other material in the film, the surface of the semiconductor or metal is not in contact with the film. This makes these films different from the LB and self-assembled films discussed earlier. 1. Film Preparation This method of assembling thin films has been developed as a technique for forming polyelectrolyte films [185,188]. The method is simple and involves the im-

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mersion of a charged substrate alternately in solutions of oppositely charged polyelectrolyte. (The substrate is usually rinsed between steps.) With each immersion, polyelectrolyte is adsorbed, overcompensating the existing surface charge and thereby reversing it. In this way, a film of oppositely charged layers is built up. LbL films can be prepared on any charged surface and substrates are not restricted to flat surfaces. Colloidal silica particles are an example of an unusual substrate that has been used [189–191]. Charged particles (it is usually the stabilizer that bears the charge) can take the place of polyelectrolytes, and the assembly process for the case of a cationic polyelectrolyte and anionic particles is illustrated in Fig. 17. Charged particles that have been incorporated in polyelectrolyte films include biological entities such as proteins [192–195] and virus particles [196], dyes [197,198], latex particles [199], inorganic charged particles such as clay platelets [200–204], and oxides such as oxidized graphite [205], silica [190,191,206,207], and zirconia [208]. Ultrasmall inorganic particles have also been incorporated into films using layer-by-layer assembly. These include semiconductor nanoparticles such as CdS [200,201,209], CeO2 [210], TiO2 [200,201, 210,212], CdSe [212–214], Fe3O4 [215,216] and PbS [200,201], and large metal complexes [189,217,218]. Gold particles have also been incorporated in this way [219–221]. The films containing the nanoparticles just listed have consisted of alternate layers of polyelectrolyte and particles, often including varieties of both in the films. Polyelectrolytes commonly used have included the anion polystyrene sulfonate (PSS and cations poly(allyl hydrochloric acid) (PAH) and poly(diallyldimethyl ammonium chloride) (PDADMAC). Semiconducting polyelectrolyte precursors such as polyphenylenevinylene (PPV), which are polymerized after the films are formed, have also been used to prepare LbL light-emitting diodes (LEDs) [213,214]. Bipolar molecules have also been used to form films, such as the assemblies of bipolar pyridinium and PbI2 nanoparticles prepared by Gao and coworkers [222,223]. The interaction between the particles and the polymer may be more than simple electrostatic attraction, with displacement of existing surface molecules [217], coordination complexes [224], and specific (biochemical) interactions [225] all being used to bind the constituents. Films have also been prepared consisting purely of oppositely charged particles [226,227]. The preemptive work of Iler, in fact, concerned the buildup of oppositely charged alumina fibrils and silica [228]. A similar technique of layer-by-layer deposition using bridging molecules such as dithiols to replace existing

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stabilizers, and which form covalent rather than electrostatic bonds, has been used to construct particlefilms [212,229–234]. Also, in an innovation that increases the possible interaction of particle and film, CdS [235] and Cu2S [236] nanoparticles have been prepared in situ by exposing M2⫹ loaded PSS/poly 4-vinylpyridine (PVP) films to H2S. In situ synthesis of particles in a manner similar to that in LB films may also be possible in films such as those prepared by Decher and Hong [236] and Gao and coworkers [223] in which bipolar amphiphiles have been incorporated; however, this is an area that is yet to be investigated. Given the simple nature of the assembly process, it is straightforward to build films with multiple components for particular purposes. Films containing different semiconductor nanoparticles, deposited either in sequence [200,201,205] or premixed [210] before absorption, are examples of slightly more complicated systems. As another example, polyelectrolyte films containing ordered layers of metal particles and insulating clay have been prepared for use as small-scale capacitors [220]. Multicomponent protein films able to undergo sequential enzymatic reactions have also been manufactured [191,225].

FIG. 17 The layer-by-layer assembly process for the production of a film on a negatively charged substrate, incorporating a cationic surfactant and anionic particles. The substrate is alternately immersed in the solutions and rinsed in between until a film of the desired numer of layers is achieved.

2. Characterization of Films The underlying mechanism of alternate adsorption has been verified by a variety of techniques. For polyelectrolyte films, zeta potential [237] measurements have revealed definite reversals of charge with the successive adsorption of layers. More general techniques have been used for films containing particles. Cationic particles (TiO2) that adsorb onto anionic polyelectrolytes (PSS) were found not to adsorb onto a cationic silanated surface, verification of the significance of electrostatic attraction [211]. A similar effect was noted as a result of pH. SiO2 is negatively charged at pH 10 and would not adsorb onto an anionic poly(styrenesulfonate) surface [210]. Contact angle studies have supported the notion of alternately layered films with the contact angle dependent on the nature of the most recent component added [211,215]. (a) Film Structure. It has been observed by UV-vis spectroscopy measurements that the amount absorbed with successive layers is consistent for up to 60 layers for TiO2/PSS films [211] and hectorite/PDADMAC [238]. An example of the type of spectra that can be obtained is shown in Fig. 18. The inserted plot shows the consistent nature of film buildup. Similar linear plots can be obtained from QCM gravimetry measurements when the total mass added is plotted as a function of the number of bilayers deposited [209]; how-


FIG. 18 UV-vis absorbance spectra for the alternate absorption of CdS [mercaptoethanol stabilized; [Cd2⫹] (0.02 M)]; PDADMAC (1% w/v); all solutions pH 11. Spectra were taken after each CdS layer was absorbed. Inset: Absorbance at 380 nm as a function of the number of bilayers [1 bilayer = 1 layer (PDADMAC) ⫹ 1 layer (CdS)].

ever, the data are most frequently presented as a staircase showing the total mass as it changes with each deposition [207,210] such as the example for CdS and PDADMAC in Fig. 19. This technique has the advantage of showing changes with each step, even for nonabsorbing materials. Analyses by ellipsometry also reveal a linear relationship, in this case between film thickness and the number of immersion cycles [203,208,217,219]. Surface roughness was found to be independent of the number of layers, indicating a consistent buildup of layers [213].

FIG. 19 The total mass adsorbed on the QCM (both sides) as function of the layer number on the surface of a 9-MHz QCM electrode as alternate layers of PDADMAC (●) and CdS (䡩) are deposited by the LbL technique. Solution conditions: CdS [mercaptoethanol stabilized; [Cd2⫹] (0.02 M)]; PDADMAC (1% w/v); all solutions pH 11.

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Sometimes it has been observed that linearity is not achieved in the first (up to five) pairs of immersions, and many groups have found it necessary to pretreat a substrate surface before adsorbing the first significant layer. Examples of pretreatment include the use of polyelectrolytes such as PSS and PEI [poly(ethyleneimine)] [210] and silanization [222]. The application of an LB monolayer has also been shown to be a suitable foundation for regular polyelectrolyte film buildup [239]. Others, however, have claimed that pretreatment is unnecessary for the assembly of high-quality films [201,202]. For polyelectrolyte films of PTAA/PAH, UV-vis measurements for up to 10 layers showed very little dependence on the pretreatment of the glass substrate [240]. Films formed by the LbL technique are relatively imprecise in structure and there is thought to be considerable leakage between the layers, in particular, in films containing particles where it is impossible to form a film of 100% surface coverage. Studies have shown that if polyoxometalate particles are absorbed onto multilayers of polyelectrolytes, then the thickness of the preceding layers affects the number of particles absorbed, indicating considerable leakage into the polyelectrolyte layer [218]. There is evidence that particles can cross intervening polyelectrolyte layers. The UVvis absorbance spectra and XRD reflectivity measurements of gold nanoparticles in LbL films showed diminishing interaction as the thickness of the polyelectrolyte multilayers between the nanoparticles increased [221]. Other gold-containing films with single polyelectrolyte layers between the particles demonstrated resistivities comparable to those of bulk gold [219] (others introduced clay particles to increase resistivity and formed a capacitor [220]). The same group found that the layer spacing was less than the diameter of the gold particles [219], indicating interpenetration of particles between layers, a conclusion consistent with the three-dimensional tight packing of particles observed in scanning electron microscopy (SEM) images of SiO2-containing films [207]. Many groups have found peaks in x-ray reflection and diffraction analyses indicating a periodic, layered structure, even for films in which the particles were adsorbed with only a single deposition of polyelectrolyte between them [200,203, 209,213], whereas others have been unable to resolve layer spacings [218]. The range of contrasting observations may be caused by the large number of factors that can influence the film during its formation. (b) Particle Concentration and Film Thickness. The most significant variables in LbL particle-films are the

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thickness of the films and the concentration of the particles. These factors are very closely linked and can be controlled to a certain extent by the solutions used to form the films. Film formation is an adsorption process, so constituent solution concentration and the amount of time for which the substrate is immersed in solution both play a role. The plot in Fig. 20 illustrates the effects of exposure time and the concentration of particles in solution for films made from PDADMAC and mercaptoethanol-stabilized CdS nanoparticles (CdS/ ME). The UV-vis absorbance of the film is proportional to the concentration of particles in the film and can be seen to depend on time of exposure only when more dilute solutions of CdS are used. In this example the equilibrium number of particles in each layer was independent of particle concentration. Others have found that the saturation amount depends on the concentration of the particle solution [199,207,210]. As film formation is electrostatically driven, the charge density on the constituents and the presence of screening electrolytes will also play a role. The lower the charge density of the polyelectrolyte, the larger the loops formed when it absorbs onto the surface. This in turn allows the adsorption of greater amounts of nanoparticle into the succeeding layer and thicker films are formed [199]. Apart from the resulting dependence on the identity of the polyelectrolyte, the number of particles in the film will be affected by the pH dependence of charge on weak electrolytes and on the particle sur-

FIG. 20 The average UV-vis absorbance (at 380 nm) per bilayer for the assembly of CdS (mercaptoethanol stabilized) and PDADMAC (1% w/v) as a function of immersion time in the CdS solution. The concentration of the Cd2⫹ in the colloidal solution prior to H2S exposure ([Cd2⫹]) was 0.02 M. Films were made from this solution (●) and from the same solution diluted by a factor of 40 (䉭).

Grieve et al.

face. This is especially noticeable in bioactive particles [193]. The presence of salt further complicates matters as increased ionic strength of the colloidal solution acts to screen charges and allows tighter packing of particles and a higher concentration of particles within the film [199,206,207,210]. SEM images show closepacked particles (not layers) with a very smooth surface at NaCl concentrations of 0.1 M. The use of higher salt concentrations led to increased surface roughness, similar to that seen in films containing only polyelectrolytes. Increased ionic strength of the polyelectrolyte solution has a similar effect on charge and allows much denser layers to form. More tightly packed particle layers have also been prepared by compacting each PDADMAC layer by microwave treatment [216]. This treatment reduces surface roughness and produces more ordered nanoparticle layers on TEM analysis. The degree of packing, and therefore the amount of particles absorbed in each layer, is also influenced significantly [199,210,221] or weakly [206] by the size of the particles. Many factors have been shown to influence the nature of LbL particle-films. It has been postulated that the enormous influence of variables such as particle and salt concentration is due in part to the mismatch between the rigidity and charge density of the particle surface and the polymer [210]. A further way to increase the concentration of particles in the films and its thickness is to apply a potential to the substrate as the adsorption process is under way. The application of a positive potential to a substrate increased the amount of anionic clay adsorbed at each step [200]. It is common practice to dry the film between immersions, especially when QCM or UV-vis measurements are to be made, and this may also affect the properties of the film. Drying was shown to alter film surface structure reversibly when it allowed the adsorption of a PSS layer onto a previously deposited PSS layer, a situation that did not occur if the film remained undried [241]. Any effect drying may have on the long-term properties of a film has yet to be established. Films prepared by LbL assembly have been found to be substantially harder and more stable than those prepared by sputter coating, especially when subjected to polymer burning and annealing treatment [208]. The application of LbL films to practical devices depends to some extent on the ability to control film thickness and particle concentration. This can be done by varying the conditions of film preparation as already


outlined. Given the enormous variety of constituents that can be incorporated in prescribed orders into these films, LbL assembly has become another tool in the particle-film toolbox.

III.

PHYSICOCHEMICAL PROPERTIES OF FILMS

The possible uses for semiconductor nanoparticles in photo-optic, optoelectronic, and photochemical applications is a major driving force behind the research being carried out in this area. The electronic and optical properties of nanoparticles can be tuned over a wide range by varying the size of the particles and their immediate environment and by combining them with other photo/opto/electroactive materials including other semiconductors and metals. To utilize the properties of nanoparticles it is often necessary for a significant area of nanoparticles to be exposed to a light source and/or an electrically active environment. Amphiphilic films provide a means of creating these domains while maintaining a fine degree of control over the scale of the film in the third dimension. By building extremely thin films, one can utilize the size-quantized properties of the semiconductors in the nanoscopic dimensions necessary for modern devices. A.

Photoelectrochemistry

Examples of uses of particle-films are LEDs [213,214, 242,243] made from semiconductor nanoparticles and semiconducting polymers in LbL films. Similar films using nonconducting polyelectrolytes have been used in photocells [201] and, with the addition of clay particles, in capacitors [220]. Photoelectrochemical [154, 158,176] and photocatalytic [153,156–158,172,174] cells have been constructed using various semiconductors in Nafion films. Nanoparticulate CdS grown in situ in LB films [79,119], PbS incorporated in LB-like films [33], and TiO2 electrophoretically deposited in films [244] are examples of photoactive semiconductor particles in other types of films. Single-electron tunneling in CdS particles formed in LB films in a phenomenon of much interest to the electronics industry [245]. For optimal use of the size quantization effects of semiconductor nanoparticles, the luminescence or redox potentials reflect the increasing band gap of smaller particles. An example is the size-dependent photovoltages seen in CdS/Nafion films [158,166,176,179] and CdS/ glutaraldehyde films [33]. Following is a discussion of some investigations carried out by our group into thin-

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film photoelectrodes made from nanoparticulate CdS and certain LbL and LB films in PEC cells. 1. Langmuir-Blodgett Films Particle films can be applied to almost any substrate surface as long as the surface has been rendered sufficiently charged or hydrophilic/phobic, depending on the type of film being constructed. If the film is assembled on a conducting substrate, it can serve as an electrode of a photoelectrochemical cell. Of course, it is necessary that the film is stable under the cell conditions and that the ions of the electrolyte can permeate through the film. LB films of CdS grown in situ in ArH were prepared on indium tin oxide (ITO)-coated quartz, with the size of the CdS nanoparticles increased by the intercalationsulfidation method described earlier. Figure 21 shows typical I-V curves of a cell with this electrode in dark and light conditions. The fill factor of the light curve is 0.25, indicating significant inefficiencies, which are probably due to surface defects. When films containing differently sized particles were used as the photoelectrode, size-dependent photovoltages were observed. Figure 22 is a plot of photovoltage as a function of particle size for 19-layer CdS-ArH films. If size quantization was being observed, an increased photovoltage due to an increased band gap would be seen in smaller particles. Figure 22 shows the opposite effect, with a decrease in photovoltage accompanying a decrease in particle size. One possible explanation is the insulating effect of the surfactant in the LB film. Long-chain fatty acids are known for their insulating properties and have been used in some electronic devices to prevent elec-

FIG. 21 Typical dark and light cycle voltammograms for CdS (4 nm) in a 19-layer ArH LB film. The electrolyte is Na2SO3 (1 M, pH 7.25) and the potential was cycled from 0 to ⫺1.0 V and back at 10 mV min⫺1.

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FIG. 22 Photovoltage as a function of particle size for CdS/ ArH particle films. The electrolyte was Na2SO3 (1.0 M, pH 7.25).

tron transport. In LB particle-films, smaller particles (2–3 nm) are separated by relatively large volumes of surfactant when compared with films containing the same concentration of larger particles (4–6 nm) that are thought to be close enough to allow interparticle electron transfer. The large particles would provide electron-conducting pathways through the film, overcoming the photovoltage-diminishing retardation due to the surfactant. 2. Layer-by-Layer Films Thin-film photoelectrodes have also been constructed using the LbL technique to build alternate layers of PDADMAC and colloidal stabilized CdS on ITO plates. The preprepared nanoparticles were stabilized in solution by mercaptoethanol (CdS/ME) and hexametaphosphate (CdS/HMP). The size of the particles was controlled by adjusting the pH of the solution prior to the addition of H2S in a method similar to that used by Henglein and coworkers [142]. As the pH was increased from 7 to 11, particle sizes increased from 3.5 to 7 nm for CdS/HMP and from 2.5 to 3.5 nm for CdS/ME. In PEC cells with working electrodes of LbL particle-films on ITO-coated glass, the photocurrent was found to be dependent on the number of layers, whereas the photovoltage was found to be independent on film thickness (Fig. 23), results similar to those found for LB films. The films produced by LbL assembly were more stable than LB films and have been illuminated for over 15 h with no reduction in photovoltage magnitude. Results for photovoltage as a function of particle diameter (determined from Henglein’s calibration curve) are shown in Fig. 24. It seems that,

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FIG. 23 VOC (䡩) and ISC (●) as a function of the number of bilayers in CdS (mercaptoethanol stabilized; [Cd2⫹]: 0.02 M, 2.5 nm) and PDADMAC (1% w/v) LbL film electrodes in Na2SO4 (0.5 M) and TEA (20 mM) electrolyte at pH 9.65.

in contrast to the results for the LB film electrodes, a size quantization effect is seen, with the photovoltages of smaller particles significantly greater than that of bulk CdS. The photovoltages observed were lower than expected from the band gaps seen in the absorbance spectra. This is clearly seen for the larger particles in Fig. 24, which showed photopotentials lower than those of the bulk. The explanation may lie in either the resistance of the polyelectrolyte surrounding the particles or the presence of surface states that would lower the effective conduction band of the semiconductor particles. To understand the significance of these factors, experiments need to be undertaken to determine the

FIG. 24 Photovoltage produced by LbL particle-films of CdS [stabilized by mercaptoethanol (䡩) and HMP (●)] and PDADMAC as a function of particle size (estimated from UV-vis absorbance spectra). The electrolyte was Na2SO4 (0.5 M) and TEA (20 mM) at pH 9.65.


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effects of capping agents and particle density on the cell characteristics. 3. Electrolyte Effects The results outlined for LB films and LbL films are themselves not directly comparable as different electrolytes have been used in the cells. Electrolyte conditions are very important to quantitative analysis, as will be illustrated for the CdS/ME/PDADMAC system in Na2SO4/triethanolamine (TEA) electrolyte. When the concentration of TEA is increased, the magnitude of the photovoltage is also observed to increase (Fig. 25). A similar, although less significant, tendency is observed for an increase in pH. Electron donors or acceptors must be adsorbed onto the semiconductor surface to enable electron transfer in 2 at 430 nm) and very thick LB films (e.g., over 5000 layers) would have to be prepared. As the assembly of such thick LB films is impractical, CdS was

FIG. 26 Time-resolved transient bleaching spectra of 4.9nm CdS particles in Nafion (pump energy = 15 ␮J per pulse) after 0 ( ), 2.6 (䉭), 3.9 (▫), and 6.5 (䡩) ps. The films were excited at 400 nm with femtosecond pulses [167].

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ponent of lifetime 8 ps (45%) and a slow component were revealed. Different-sized particles gave different results but of similar orders of magnitude. It is thought that two types of electron-hole recombination are responsible for the two observed components of photobleaching recovery: direct recombination and recombination from surface states. Electrons trapped in surface states or defects have longer recombination times than those undergoing direct recombination. It is, however, possible to modify the surface of CdS to eliminate the surface traps by the formation of a Cd(OH)2 layer on the surface [141]. Transient photobleaching of aqueous colloidal CdS modified in this way has shown faster recovery times than for untreated samples [141]. IV.

OVERVIEW

The use of nanoparticles in electronic and optical devices is an area of increasing interest that has stimulated an expanding field of research. Nanoscale particle-films often display optical transparency and size quantization effects, the combination of which makes them particularly attractive for use in photo-optic, -voltaic, and -electronic applications. Amphiphilic and polyelectrolytic films are very attractive media for the formation, manipulation, and preservation of nanoparticles, and the incorporation of nanoparticles in several types of films has been discussed. Thin organic films can incorporate nanoparticles in a variety of ways. The particles can be prepared separately and then incorporated in the organic film or can be synthesized using the functionality of the organic material to ‘‘cap’’ the particles. The layer-by-layer film assembly technique is best suited for the incorporation of premade particles that have a surface charge. The charge is usually associated with the stabilizing agent on the surface and facilitates the alternate assembly with oppositely charged polyelectrolytes. Characteristics of LbL films, such as thickness and particle density, are influenced by factors that affect the charge and charge interactions of the species involved in the film structure. Solution pH, background salt, and surface charge density all play a role. As the films are constructed one layer at a time, considerable control can be exerted over the placement of the constituents of the films and their thickness can be limited to the nanometer scale. Thicker films, with much higher optical densities, are sometimes required for testing phenomena such a photobleaching. In these cases, it is often convenient to form the particles in situ, in self-assembling films.

The growth of the particles is limited by the spaces within the film structure, which may be cavities or bilayer spacings, and often there is significant interaction between the functional groups of the self-assembling polymer and the nanoparticle surface. This internal particle-matrix interaction is also present when particles are formed using self-assembling amphiphile structure to assist in growth restriction, such as when particles are synthesized under Langmuir monolayers and in vesicles. It is particularly evident when particles are grown within the confines of a Langmuir-Blodgett film. The film structure restricts the growth of the particles and evidence suggests that the particles are capped by the surrounding amphiphile, in a manner similar to that found for solution colloids. The particle size is influenced by the preparation conditions, which affect parameters such as reactant ion concentration and film structure, but once formed they can be grown within the films by a number of techniques. The film tends to be disrupted by the formation of particles but maintains an overall bilayer structure and a degree of crystallinity. Similarly to LbL films, LB films are assembled in a sequential manner, but with a greater degree of control on a molecular level. They are, however, less robust than LbL films and limited to the incorporation of a smaller range of materials. The possibilities for manipulating the properties of LB particle films lie mostly in altering the nature of the amphiphile. As an example, more durable films have been prepared by polymerizing the surfactant after particle formation [109,113]. As well as limiting the size, the amphiphile might be used to control the shape of the particles. Triangular and/or rodlike particles are often formed at Langmuir monolayers [10] and in vesicles [246]. It is conceivable that a similar variety of particle shapes could result from in situ synthesis in LB films, widening the potential applications of these films. Another way to modify properties by altering constituents is to use a functionalized surfactant with photophysical-chemical properties. This could act as a sensitizer and undergo photoexcited electron transfer with a film-incorporated semiconductor particle, in a similar manner to the dye-semiconductor system outlined by Kamat [247,248]. Such a system would fully realize the potentially powerful synergistic properties of amphiphile particle-films, which as yet remain unexplored. ACKNOWLEDGMENTS This work was supported by the Australian Research Council. KG acknowledges the receipt of an Australian


Postgraduate Award and support from the Advanced Mineral Products Research Centre. We are also grateful to our many collaborators for their contributions in studying the particle-films reported here.

REFERENCES 1. 2. 3.

4. 5. 6. 7. 8.

9. 10. 11. 12. 13.

14. 15. 16. 17. 18.

19.

20. 21. 22.

A. Pockels, Nature 43:437 (1891). I. Langmuir, J. Am. Chem. Soc. 39:1848–1906 (1917). J. Leloup, P. Maire, A. Barraud, and A. Ruaudel-Texier, J. Chim. Phys. Phys. Chim. Biol. 82:695–700 (1985). A. Ruaudel-Texier, J. Leloup, and A. Barraud, Mol. Cryst. Liq. Cryst. 134:347–354 (1986). S. Xu, X. K. Zhao, and J. H. Fendler, Adv. Mater. 2: 183–185 (1990). G. L. J. Gaines, Isoluble Monolayers at Liquid-Gas Interfaces, Interscience, New York, 1966. G. Roberts, ed., Langmuir-Blodgett Films, Plenum, New York, 1990. A. Ulman, An Introduction to Ultrathin Organic Films from Langmuir-Blodgett to Self-Assembly, Academic Press, San Diego, 1991, p. 121 and references therein. A. Henglein, Chem. Rev. 89:1861–1873 (1989). J. H. Fendler and F. C. Meldrum, Adv. Mater. 7:607– 632 (1995). Y. Tian, C. Wu, and J. H. Fendler, J. Phys. Chem. 98: 4913–4918 (1994). X. Peng, Y. Zhang, J. Y. Ang, B. Zou, L. Xiao, and T. Li, J. Phys. Chem. 96:3412–3415 (1992). X.-G. Peng, M.-L. Gao, Y.-Y. Zhao, S.-H. Kang, Y.H. Zhang, Y. Zhang, D.-J. Wang, L.-Z. Xiao, T.-J. Li, and H.-Y. Chen, Chem. Phys. Lett. 209:233–237 (1993). J. Yang, X. G. Peng, T. J. Li, and S. F. Pan, Thin Solid Films 243:643–646 (1994). Y. S. Kang, D. K. Lee, and P. Stroeve, Thin Solid Films 327–329:541–544 (1998). Y. S. Kang, S. Rishbud, J. Rabolt, and P. Stroeve, Langmuir 12:4345–4349 (1996). X. Yuan, L. Cao, H. Wan, G. Zeng, and S. Xi, Thin Solid Films 327–329:33–36 (1998). L. S. Li, J. Zhang, L. J. Wang, Y. Chen, Z. Hui, T. J. Li, L. F. Chi, and H. Fuchs, J. Vac. Sci. Technol. B 15:1618–1622 (1997). L. S. Li, Z. Hui, Y. Chen, X. T. Zhang, X. Peng, Z. Liu, and T. J. Li, J. Colloid Interface Sci. 192:275– 280 (1997). K. S. Mayya, V. Patil, P. M. Kumar, and M. Sastry, Thin Solid Films 312:300–305 (1998). K. S. Mayya, V. Patil, and M. Sastry, J. Chem. Soc. Faraday Trans. 93:3377–3381 (1997). K. S. Mayya, V. Patil, and M. Sastry, Langmuir 13: 2575–2577 (1997).

661 23. 24. 25. 26. 27. 28. 29.

30. 31. 32.

33.

34. 35. 36. 37. 38. 39. 40. 41. 42. 43. 44. 45. 46. 47. 48. 49. 50.

M. Sastry, K. S. Mayya, V. Patil, D. V. Paranjape, and S. G. Hegde, J. Phys. Chem. B 10:4954–4958 (1997). K. S. Mayya and M. Sastry, J. Phys. Chem. B 101: 9790–9793 (1997). K. S. Mayya and M. Sastry, Langmuir 14:74–78 (1998). M. Sastry, K. S. Mayya, and V. Patil, Langmuir 12: 5921–5928 (1998). K. S. Mayya and M. Sastry, Langmuir 14:6344–6346 (1998). X. K. Zhao, S. Xu, and J. H. Fendler, Langmuir 7: 520–524 (1991). J. Jin, L. S. Li, Y. Q. Tian, Y. J. Zhang, Y. Liu, Y. Y. Zhao, T. S. Shi, and T. J. Li, Thin Solid Films 327– 329:559–562 (1998). R. E. Schwerzel, Polym. Prepr. 35:116–117 (1994). R. E. Schwerzel, Naval Res. Rev. 4:24–29 (1994). R. T. Schwerzel, K. B. Spahr, J. P. Kurmer, V. E. Wood, and J. A. Jenkins, J. Phys. Chem. A 102:5622– 5626 (1998). T. Torimoto, N. Tsumura, M. Miyake, M. Nishizawa, T. Sakata, H. Mori, and H. Yoneyama, Langmuir 15: 1853–1858 (1999). F. C. Meldrum, N. A. Kotov, and J. H. Fendler, J. Phys. Chem. 98:4506–4510 (1994). F. C. Meldrum, N. A. Kotov, and J. A. Fendler, Langmuir 10:2035–2040 (1994). F. C. Meldrum, K. A. Kotov, and J. H. Fendler, Chem. Mater. 7:1112–1116 (1995). N. A. Kotov, F. C. Meldrum, C. Wu, and J. H. Fendler, J. Phys. Chem. 98:2735–2738 (1994). N. A. Kotov, F. C. Meldrum, and J. H. Fendler, J. Phys. Chem. 98:8827–8830 (1994). N. A. Kotov, G. Zavala, and J. H. Fendler, J. Phys. Chem. 99:12375–12378 (1995). J. H. Fendler, Curr. Opin. Colloid Interface Sci. 1: 202–207 (1996). B. O. Dabbousi, C. B. Murray, M. F. Rubner, and M. G. Bawendi, Chem. Mater. 6:216–219 (1994). Y. Tian and J. H. Fendler, Chem. Mater. 8:969–974 (1996). S. Yae, I. Nakanishi, Y. Nakato, N. Toishima, and H. Mori, J. Electrochem. Soc. 141:3077–3081 (1994). J. R. Heath, C. M. Knobler, and D. V. Leff, J. Phys. Chem. B 101:189–197 (1997). T. Nakaya, Y.-J. Li, and K. Shibata, J. Mater. Chem. 6:691–697 (1996). S. Doherty and D. Fitzmaurice, J. Phys. Chem. 100: 10732–10738 (1996). J. H. Fendler, Isr. J. Chem. 33:41–46 (1993). X. K. Zhao, Y. Yuan, and J. H. Fendler, J. Chem. Soc. Chem. Commun. 1248–1252 (1990). X. K. Zhao and J. H. Fendler, J. Phys. Chem. 95: 3716–3723 (1991). X. K. Zhao, L. McCormick, and J. H. Fendler, Chem. Mater. 3:922–935 (1991).

662 51. 52.

53. 54. 55. 56. 57. 58. 59. 60.

61. 62.

63.

64.

65. 66. 67.

68.

69. 70.

71. 72. 73. 74.

Grieve et al. K. C. Yi and J. H. Fendler, Synth. Met. 71:2109–2110 (1995). Z. Y. Pan, X. J. Liu, S. Y. Zhang, G. J. Shen, L. G. Zhang, Z. H. Lu, and J. Z. Liu, J. Phys. Chem. 101: 9703–9709 (1997). M. Sastry, V. Patil, and K. S. Mayya, Langmuir 13: 4490–4492 (1997). V. Patil and M. Sastry, Langmuir 13:5511–5513 (1997). V. Patil and M. Sastry, Langmuir 14:2707–2711 (1998). M. Sastry, V. Patil, and Sainkar, J. Phys. Chem. B 102: 1404–1410 (1998). V. Patil and M. Sastry, J. Chem. Soc. Faraday Trans. 93:4347–4353 (1997). J. A. Spink and J. V. Sanders, Trans. Faraday Soc. 51: 1154–1165 (1955). E. D. Goddard and J. A. Ackilli, J. Colloid Sci. 18: 585–595 (1963). E. S. Smotkin, C. Lee, A. J. Bard, A. Campion, M. A. Fox, T. E. Mallouk, S. E. Webber, and J. M. White, Chem. Phys. Lett. 152:265–268 (1988). D. J. Elliott, D. N. Furlong, and F. Grieser, Colloids Surf. A 141:9–17 (1998). D. J. Elliot, D. N. Furlong, T. R. Gegenbach, F. Grieser, R. S. Urquhart, C. L. Hoffman, and J. F. Rabolt, Colloids Surf. A 103:207–219 (1995). D. J. Elliott, D. N. Furlong, F. Grieser, P. Mulvaney, and M. Giersig, Colloids Surf. A 129–130:141–150 (1997). I. Moriguchi, N. Fujiyoshi, R. Sakamoto, Y. Teraoka, and S. Kagawa, Colloids Surf. A 126:159–166 (1997). G. Hemakanthi and A. Dhathathreyan, Langmuir 15: 3317–3320 (1999). C. Fan, T. Lu, B. Li, and L. Jiang, Thin Solid Films 286:37–39 (1996). V. Erokhin, P. Facci, L. Gobbi, S. Dante, F. Rustichelli, and C. Nicolini, Thin Solid Films 329:503–505 (1998). D. N. Furlong, R. S. Urquhart, F. Grieser, K. Matsuura, and Y. Okahata, J. Chem. Soc. Chem. Commun. 1329–1330 (1995). D. V. Paranjape, M. Sastry, and P. Ganguly, Appl. Phys. Lett. 63:18–20 (1993). M. Sastry, S. Pal, D. V. Parajape, and P. Gaguly, J. Electron Spectrusc. Relat. Phenomena 67:163–172 (1994). E. Maassen, B. Tieke, G. Jordan, and W. Rammensee, Langmuir 12:5595–5600 (1996). C. L. Mirley and J. T. Koberstein, Langmuir 11:2837– 2839 (1995). C. L. Mirley and J. T. Koberstein, Langmuir 11:1049– 1052 (1995). Y. Wang and N. Herron, J. Phys. Chem. 95:525–532 (1991).

75. 76.

77.

78.

79.

80. 81. 82. 83. 84. 85. 86. 87. 88. 89. 90. 91. 92. 93. 94. 95.

96.

97. 98.

99.

L. Brus, J. Phys. Chem. 90:2555–2560 (1986). N. J. Geddes, R. S. Urquhart, D. N. Furlong, C. R. Lawrence, K. Tanaka, and Y. Okahata, J. Phys. Chem. 97:13767–13772 (1993). R. S. Urquhart, D. N. Furlong, H. Mansur, F. Grieser, K. Tanaka, and Y. Okahata, Langmuir 10:899–904 (1994). R. S. Urquhart, C. L. Hoffman, D. N. Furlong, N. J. Geddes, J. F. Rabolt, and F. Grieser, J. Phys. Chem. 99:15987–15992, 1995. H. S. Mansur, F. Grieser, M. S. Marychurch, S. Biggs, R. S. Urquhart, and D. N. Furlong, J. Chem. Soc. Faraday Trans. 91:665–672 (1995). C.-Y. Liu and A. J. Bard, J. Phys. Chem. 93:3232– 3237 (1989). K. Asai, K. Ishigure, and H. Shibata, J. Lumin. 63: 215–222 (1995). K. Asai, T. Yamaki, K. Ishigure, and H. Shibata, Thin Solid Films 277:169–174 (1996). K. Asai, T. Yamaki, S. Seki, K. Ishigure, and H. Shibata, Thin Solid Films 284–285:541–544 (1996). T. Yamaki, K. Asai, and K. Ichigure, Chem. Phys. Lett. 273:376–380 (1997). T. Yamaki K. Asai, K. Ichigure, and H. Shibata, Radiat. Phys. Chem. 50:199–205 (1997). C. T. Ewins and B. Stewart, Thin Solid Films 284– 285:49–52 (1996). P. Facci, V. Erokhin, A. Tronin, and C. Nicolini, J. Phys. Chem. 98:13323–13327 (1994). V. Erokhin, P. Facci, S. Carrara, and C. Nicolini, J. Phys. D Appl. Phys. 28:2534–2538 (1995). P. Facci, A. Diaspro, and R. Rolandi, Thin Solid Films 327–329:532–535 (1998). P. Facci and M. P. Fontana, Solid State Commun. 108: 5–9 (1998). A. Dhanabalan, H. Kudrolli, S. S. Major, and S. S. Talwar, Solid State Commun. 99:859–862 (1996). S. Vitta, T. H. Metzger, S. S. Major, A. Dhanabalan, and S. S. Talwar, Langmuir 14:1799–1803 (1998). J. K. Basu and M. K. Sanyal, Phys. Rev. Lett. 79: 4617–4620 (1997). I. Moriguchi, F. Shibata, Y. Teraoka, and S. Kagawa, Chem. Lett. 761–762 (1995). I. Moriguchi, K. Hosoi, H. Nagaoka, I. Tanaka, Y. Teraoka, and S. Kagawa, J. Chem. Soc. Faraday Trans. 90:349–354 (1994). I. Moriguchi, H. Nii, K. Hanai, H. Nagaoka, Y. Teraoka, and S. Kagawa, Colloids Surf. A 103:173–181 (1995). I. Moriguchi, Y. Teraoka, and S. Kagawa, Kobunshi Ronbunshu 52:765–772 (1995). I. Moriguchi, K. Matsuo, M. Sakai, K. Hanai, Y. Teraoka, and S. Kagawa, J. Chem. Soc. Faraday Trans. 94:2199–2204 (1998). Z. Pan, J. Liu, X. Peng, T. Li, Z. Wu, and M. Zhu, Langmuir 12:851–853 (1996).

Nanoparticles in Organized Amphiphilic Films 100. 101.

102. 103. 104. 105. 106. 107. 108. 109. 110. 111. 112.

113. 114.

115.

116.

117.

118.

119.

120. 121. 122. 123.

Z. Pan, X. Peng, T. Li, and J. Liu, Appl. Surf. Sci. 108:439–447 (1997). V. Erokhin, L. Feigin, G. Ivakin, V. Klechkovskaya, Y. Lvov, and N. Stiopina, Makromol. Chem. Macromol. Symp. 46:359–363 (1991). X. Yang, G. Wang, and Z. Lu, Supramol. Sci. 5:549– 552 (1998). A. V. Nabok, T. Richardson, F. Davis, and C. J. M. Stirling, Langmuir 13:3198–3201 (1997). F. N. Dulstev and L. L. Sveshnikova, J. Struct. Chem. 38:673–677 (1997). F. N. Dulstev and L. L. Sveshnikova, Thin Solid Films 288:103–107 (1996). C. Zylberajch, A. Ruaudel-Texier, and A. Barraud, Synth. Met. 27:B609–B614 (1988). D. J. Elliot, D. N. Furlong, and F. Grieser, Colloids Surf. A, 15:101–110 (1999). K. C. Yi and J. H. Fendler, Langmuir 6:1519–1521 (1990). R. Zhu, Y. Wei, C. Yuan, S. Xiao, Z. Lu, and H. J. Schmitt, Solid State Commun. 84:449–451 (1992). X. Peng, R. Lu, Y. Zhao, L. Qu, H. Chen, and T. Li, J. Phys. Chem. 98:7052–7055 (1994). L. S. Li, L. Qu, R. Lu, X. Peng, Y. Zhao, and T. J. Li, Thin Solid Films 327–329:408–411. (1998). L. Wang, L. Li, L. Qu, R. Lu, X. Peng, Y. Zhao, and T. Li, Mol. Cryst. Liq. Cryst. Sci. Tech. Sec. A Mol. Cryst. Liq. Cryst. 294:473–478 (1997). D. J. Scoberg, F. Grieser, and D. N. Furlong, J. Chem. Soc. Chem. Commun. 515–517 (1991). F. Grieser, D. N. Furlong, D. J. Scoberg, I. Ichinose, N. Kimizuka, and T. Kunitake, J. Chem. Soc. Faraday Trans. 88:2207–2214 (1992). D. N. Furlong, R. Urquhart, F. Grieser, K. Tanaka, and Y. Okahata, J. Chem. Soc. Faraday Trans. 89:2031– 2035 (1993). H. Xiong, H. Li, Z. Wang, X. Zhang, J. Shen, M. Gleiche, L. Chi, and H. Fuchs, J. Colloid Interface Sci. 211:238–242 (1999). A. V. Nabok, T. Richardson, C. McCartney, N. Cowlam, F. Davis, C. J. M. Stirling, A. K. Ray, V. Gacem, and A. Gibraud, Thin Solid Films 329:510–514 (1998). R. S. Urquhart, D. N. Furlong, T. Gengenbach, N. J. Geddes, and F. Grieser, Langmuir 11:1127–1133 (1995). H. S. Mansur, F. Grieser, R. S. Urquhart, and D. N. Furlong, J. Chem. Soc. Faraday Trans. 91:3399–3404 (1995). T. Yamaki, T. Yamada, K. Asai, and K. Ishigure, Thin Solid Films 327–329:586–590 (1998). T. Yamaki, T. Yamada, K. Asai, K. Ishigure, and H. Shibata, Thin Solid Films 329:581–585 (1998). D. J. Elliot, D. N. Furlong, T. R. Gengenbach, and F. Grieser, Colloids Surf. A 102:45–46 (1995). C. Zylberajch, A. Ruadel-Texier, and A. Barraud, Thin Solid Films 179:9–14 (1989).

663 124. 125. 126. 127. 128.

129. 130. 131. 132. 133. 134. 135. 136. 137.

138. 139. 140. 141. 142. 143. 144. 145. 146. 147.

148. 149.

150.

A. C. Zylberajch, A. Barraud, H. Roulet, and G. Dufour, Appl. Surf. Sci. 52:323–327 (1991). H. Chen, X. Chai, Q. Wei, Y. Jiang, and T. Li, Thin Solid Films 178:535–540 (1989). J. Leloup, A. Ruaudel-Texier, and A. Barraud, Thin Solid Films 210/211:407–409 (1992). V. Erokhin, P. Facci, S. Carrara, and C. Nicolini, Thin Solid Films 284–285:891–893 (1996). I. Moriguchi, K. Hanai, Y. Teraoka, S. Kagawa, S. Yamada, and T. Matsu, Jpn. J. Appl. Phys. 34:L323– L325 (1995). X. Peng, Q. Wei, Y. Jiang, X. Chai, T. Li, and J. Shen, Thin Solid Films 210/211:401–403 (1992). X. Peng, S. Guan, X. Chai, Y. Jiang, and T. Li, J. Phys. Chem. 96:3170–3174 (1992). X. Peng, H. Chen, S. Kan, Y. Bai, and T. Li, Thin Solid Films 242:118–121 (1994). G. W. Min, X. M. Yang, Z. H. Lu, and W. Yu, J. Vac. Sci. Technol. B 12:1984–1987 (1994). R. Zhu, G. Min, Y. Wei, and H. J. Schmitt, J. Phys. Chem. 96:8210–8211 (1992). L. S. Li, L. Qu, L. Wang, R. Lu, X. Peng, Y. Zhao, and T. J. Li, Langmuir 13:6183–6187 (1997). X. Luo, Z. Zhang, and Y. Liang, Langmuir 10:3213– 3216 (1994). I. Moriguchi, F. Shibata, Y. Teraoka, and S. Kagawa, J. Chem. Soc. Chem. Commun. 1401–1402 (1991). D. J. Elliot, D. N. Furlong, T. R. Gengenbach, F. Grieser, R. S. Urquhart, C. L. Hoffman, and J. F. Rabolt, Langmuir 11:4773–4778 (1995). J. K. Pike, H. Byrd, A. A. Morrone, and D. R. Talham, J. Am. Chem. Soc. 115:8497–8498 (1993). J. K. Pike, H. Byrd, D. R. Talham, and A. A. Morrone, Thin Solid Films 243:510–514 (1994). J. K. Pike, H. Byrd, A. A. Morrone, and D. R. Talham, Chem. Mater. 6:1757–1765 (1994). N. Herron, Y. Wang, and H. Ecker, J. Am. Chem. Soc. 112:1322–1326 (1990). L. Spanhel, M. Haase, H. Weller, and A. Henglein, J. Am. Chem. Soc. 109:5649–5655 (1987). Y. Wang and N. Herron, J. Phys. Chem. 91:257–260 (1987). A. Ekimov, J. Lumin. 70:1–20 (1996). Y. Wang and N. Herron, Phys. Rev. B 42:7253–7255 (1990). L. Katsikas, A. Eychmu¨ller, M. Giersig, and H. Weller, Chem. Phys. Lett. 172:201–204 (1990). H. Weller, H. M. Schmidt, U. Koch, A. Fojtik, S. Baral, A. Henglein, W. Kunath, K. Weiss, and E. Dieman, Chem. Phys. Lett. 124:557–560 (1986). J. F. Rabolt, F. C. Burns, N. E. Schlotter, and J. D. Swalen, J. Chem. Phys. 78:946–952 (1983). A. Malik, M. K. Durbin, A. G. Richter, K. G. Huang, and P. Dutta, Thin Solid Films 284–285:144–146 (1996). I. Ichinose, N. Kimizuka, and T. Kunitake, J. Phys. Chem. 99:3736–3742 (1995).

664 151. 152. 153. 154. 155. 156. 157. 158.

159.

160. 161.

162. 163. 164. 165.

166. 167. 168.

169.

170.

171.

172.

173.

Grieve et al. Y. Wang, A. Suna, W. Mahler, and R. Kasowski, J. Chem. Phys. 87:7315–7322 (1987). W. Mahler, Inorg. Chem. 27:435–436 (1988). M. Krishnan, J. R. White, M. A. Fox, and A. J. Bard, J. Am. Chem. Soc. 105:7002–7003 (1983). K. Honda, A. Kuwano, K. Chiba, A. Ishikawa, and H. Miyama, Chem. Lett. 195–198 (1988). Y.-J. Hong and S. M. Oh, Sens. Actuator B Chem. 32: 7–13 (1996). J. Prekumar and R. Ramaraj, J. Mol. Catal. A Chem. 132:21–32 (1998). F.-R. F. Fan, H.-Y. Liu, and A. J. Bard, J. Phys. Chem. 89:4418–4420 (1985). H. Miyoshi, S. Nippa, H. Uchida, H. Mori, and H. Yoneyama, Bull. Chem. Soc. Jpn. 63:3380–3384 (1990). Q. Deng, K. M. Cable, R. B. Moore, and K. A. Mauritz, J. Polym. Sci. B Polym. Phys. 34:1917–1923 (1996). J. P. Kuczynski, B. H. Miloslavljevic, and J. K. Thomas, J. Phys. Chem. 88:980–984 (1984). N. Kakuta, J. M. White, A. Campion, A. J. Bard, M. A. Fox, and S. E. Webber, J. Phys. Chem. 89:48–52 (1985). Y. Wang and W. Mahler, Opt. Commun. 61:233–236 (1987). Y. Wang, W. Mahler, and A. Suna, J. Opt. Soc. Am. B 6:808–813 (1989). E. F. Hillinski, P. A. Lucas, and Y. Wang, J. Chem. Phys. 89:3435–3441 (1988). E. S. Smotkin, R. M. Brown Jr., L. K. Rasenberg, K. Salomon, A. J. Bard, A. Campion, M. A. Fox, T. E. Mallouk, S. E. Webber, and J. M. White, J. Phys. Chem. 94:7543–7549 (1990). K. R. Gopidas and P. V. Kamat, Proc. Ind. Acad. Sci. 105:505–512 (1993). H. Inoue, R. S. Urquhart, T. Nagamura, F. Grieser, and H. Sakaguchi, Colloids Surf. A 126:197–208 (1997). P. Nandakumar, C. Vijayan, Y. V. G. S. Murti, K. Dhanalakshmi, and G. Sundararajan, Bull. Mater. Sci. 20:549–582 (1997). P. Nandakumar, A. R. Dhobale, Y. Babu, M. D. Sastry, C. Vijayan, Y. V. G. S. Murti, K. Dhanalakshmi, and G. Sundararajan, Solid State Commun. 106:193–196 (1998). M. F. Finlayson, K.-H. Park, N. Kakuta, A. J. Bard, A. Campion, M. A. Fox, S. E. Webber, and J. M. White, J. Lumin. 39:205–214 (1988). N. Kakuta, K.-H. Park, M. F. Finlayson, A. J. Bard, A. Campion, M. A. Fox, S. E. Webber, and J. M. White, J. Phys. Chem. 89:5028–5031 (1985). A. Ueno, N. Kakuta, K. H. Park, M. F. Finlayson, A. J. Bard, A. Campion, M. A. Fox, S. E. Webber, and J. M. White, J. Phys. Chem. 89:3828–3833 (1985). N. Kakuta, K. H. Park, M. F. Finlayson, A. Ueno, A. J. Bard, A. Campion, M. A. Fox, S. E. Webber, and J. M. White, J. Phys. Chem. 89:732–734 (1985).

174.

175. 176.

177. 178.

179.

180. 181.

182.

183. 184. 185. 186. 187. 188. 189.

190. 191. 192. 193. 194. 195. 196.

197. 198.

A. W.-H. Mau, C.-B. Huang, N. Kakuta, A. J. Bard, A. Campion, M. A. Fox, M. White, and S. E. Webber, J. Am. Chem. Soc. 106:6537–6542 (1984). K. R. Gopidas and P. V. Kamat, Mater. Lett. 9:372– 378 (1990). H. Miyoshi, M. Yamachika, H. Yoneyama, and H. Mori, J. Chem. Soc. Faraday Trans. 86:815–818 (1990). J. M. Zen, G. Chen, F. R. Fan, and A. J. Bard, Chem. Phys. Lett. 169:23–26 (1990). Y. Wang, A. Suna, J. McHugh, E. F. Hilinski, P. A. Lucas, and R. D. Johnson, J. Chem. Phys. 92:6927– 6939 (1990). H. Miyoshi, K. Tanaka, H. Uchida, H. Yoneyama, H. Mori, and T. Sakata, J. Electroanal. Chem. 295:71–78 (1990). H. Yoneyama, Res. Chem. Intermed. 15:101–111 (1991). H. Inoue, R. S. Urquhart, T. Nagamura, F. Grieser, H. Sakaguchi, and D. N. Furlong, J. Polym. Sci. Tech. 11:73–76 (1998). T. Nagamura, H. Inoue, H. Sakaguchi, F. Grieser, R. Urquhart, D. J. Elliot, and D. N. Furlong, Proc. SPIEOrganic-Inorganic Hybrid Materials for Photonics, 3469:174–181 (1998). N. Kimizuka, T. Miyoshi, I. Ichinose, and T. Kunitake, Chem. Lett. 2039–2042 (1991). N. Kimizuka, T. Maeda, I. Ichinose, and T. Kunitake, Chem. Lett. 941–944 (1993). G. Decher, Science 277:1232–1237 (1997). G. Decher, M. Eckle, J. Schmitt, and B. Struth, Curr. Opin. Colloid Interface Sci. 3:32–39 (1998). J. H. Fendler, Chem. Mater. 8:1616–1624 (1996). G. Decher and J. Schmitt, Prog. Colloid Polym. Sci. 89:160–164 (1992). S. W. Keller, S. A. Johnson, E. Brigham, E. H. Yonemoto, and T. E. Mallouk, J. Am. Chem. Soc. 117: 12879–12880 (1995). F. Caruso, H. Lichtenfeld, M. Giersig, and H. Mo¨hwald, J. Am. Chem. Soc. 120:8523–8524 (1998). F. Caruso, R. A. Caruso, and H. Mo¨hwald, Science 282:1111–1114 (1998). Y. Lvov, K. Ariga, and T. Kunitake, Chem. Lett. 2323–2326 (1994). Y. Lvov, K. Ariga, I. Ichinose, and T. Kunitake, J. Am. Chem. Soc. 117:6117–6123 (1995). M. Onda, Y. Lvov, K. Ariga, and T. Kunitake, J. Ferment. Bioeng. 82:502–506 (1996). F. Caruso, D. N. Furlong, K. Ariga, I. Ichinose, and T. Kunitake, Langmuir 14:4559–4565 (1998). Y. Lvov, H. Haas, G. Decher, H. Mo¨hwald, A. Mikhailov, B. Mtchedlishvily, E. Morgunova, and B. Vainshtein, Langmuir 10:4232–4236 (1994). H. Fukumoto and Y. Yonezawa, Thin Solid Films 327–329:748–751 (1998). D. Yoo, A. Wu, J. Lee, and M. F. Rubner, Synth. Met. 85:1425–1426 (1997).

Nanoparticles in Organized Amphiphilic Films 199. 200.

201. 202.

203. 204. 205. 206. 207. 208. 209. 210. 211. 212. 213. 214. 215. 216. 217. 218. 219. 220. 221.

222.

223. 224.

T. Serizawa, H. Takeshita, and M. Akashi, Langmuir 14:4088–4094 (1998). J. H. Fendler, in Semiconductor Nanoclusters (P. V. Kamat and D. Meisel, eds.), Elsevier Science, Amsterdam, 1997, pp. 261–276. N. A. Kotov, I. De´kańy, and J. H. Fendler, J. Phys. Chem. 99:13065–13069 (1995). N. A. Kotov, T. Haraszti, L. Turi, G. Zavala, R. E. Geer, I. De´kańy, and J. H. Fendler, J. Am. Chem. Soc. 119:6821–6831 (1997). G. S. Ferguson and E. R. Kleinfeld, Adv. Mater. 7: 414–416 (1995). Y. Lvov, K. Ariga, I. Ichinose, and T. Kunitake, Thin Solid Films 284–285:797–801 (1996). N. A. Kotov, I. De´kańy, and J. H. Fendler, Adv. Mater. 8:637–641 (1996). A. Krozer, S.-A. Nordin, and B. Kasemo, J. Colloid Interface Sci. 176:479–484 (1995). K. Ariga, Y. Lvov, M. Onda, I. Ichinose, and T. Kunitake, Chem. Let. 125–126 (1997). A. Rosidian, Y. Liu, and R. O. Claus, Adv. Mater. 10: 1087–1091 (1998). M. Gao, X. Zhang, B. Yang, F. Li, and J. Shen, Thin Solid Films 284–285:242–245 (1996). Y. Lvov, K. Ariga, M. Onda, I. Ichinose, and T. Kunitake, Langmuir 13:6195–6203 (1997). Y. Liu, A. Wang, and R. Claus, J. Phys. Chem. B. 101: 1385–1388 (1997). T. Cassagneau, T. E. Mallouk, and J. H. Fendler, J. Am. Chem. Soc. 120:7848–7859 (1998). M. Gao, B. Richter, S. Kirstein, and H. Mo¨hwald, J. Phys. Chem. B 102:4096–4103 (1998). M. Gao, B. Richter, and S. Kirstein, Adv. Mater. 9: 802–805 (1997). Y. Liu, A. Wang, and R. O. Claus, Appl. Phys. Lett. 71:2265–2267 (1997). M. A. Correa-Duarte, M. Giersig, N. A. Kotov, and L. M. Liz-Marzan, Langmuir 14:6430–6435 (1998). S. W. Keller, H.-N. Kim, and T. E. Mallouk, J. Am. Chem. Soc. 116:8817–8818 (1994). F. Caruso, D. G. Kurth, D. Volkmer, M. J. Koop, and A. Mu¨ller, Langmuir 14:3462–3465 (1998). Y. Liu, Y. Wang, and R. O. Claus, Chem. Phys. Lett. 298:315–319 (1998). D. L. Feldheim, K. C. Grabar, M. J. Natan, and T. E. Mallouk, J. Am. Chem. Soc. 118:7640–7641 (1996). J. Schmitt, G. Decher, W. J. Dressick, S. L. Brandow, R. E. Geer, R. Shashidar, and J. M. Calvert, Adv. Mater. 9:61–65 (1997). M. Gao, M. Gao, X. Zhang, Y. Yang, B. Yang, and J. Shen, J. Chem. Soc. Chem. Commun. 2777–2778 (1994). M. Gao, X. Zhang, B. Yang, and J. Shen, J. Chem. Soc. Chem. Commun. 2229–2230 (1994). E. Hao, L. Wang, J. Zhang, B. Yang, X. Zhang, and J. Shen, Chem. Lett. 1:5–6 (1999).

665 225. 226. 227. 228. 229. 230. 231. 232.

233.

234. 235. 236. 237. 238. 239. 240. 241. 242. 243. 244.

245. 246.

247. 248.

249.

Y. Lvov, K. Ariga, I. Ichinose, and T. Kunitake, J. Chem. Soc. Chem. Commun. 2313–2314 (1995). E. Hao, B. Yang, J. Zhang, X. Zhang, J. Sun, and J. Shen, J. Mater. Chem. 8:1327–1328 (1998). F.-U. Fulda, A. Kampes, L. Krasemann, and B. Tieke, Thin Solid Films 327–329:752–757 (1998). R. K. Iler, J. Colloid Interface Sci. 21:569–594 (1966). T. Nakanishi, B. Ohtani, K. Shimazu, and K. Uosaki, Chem. Phys. Lett. 278:233–237 (1997). T. Nakanishi, B. Ohtani, and K. Uosaki, Jpn. J. Appl. Phys. 36:4053–4056 (1997). T. Nakanishi, B. Ohtani, and K. Uosaki, J. Phys. Chem. 102:1571–1577 (1998). T. Nakanishi, B. Ohtani, and K. Uosaki, Jpn. J. Appl. Phys. Part 1 Regul. Pap. Short Notes Rev. Pap. 38: 518–521 (1999). M. Brust, R. Etchenique, E. J. Calvo, and G. J. Gordillo, J. Chem. Soc. Chem. Commun. 1949–1950 (1996). M. Brust, D. Bethall, C. J. Kiely, and D. J. Schriffin, Langmuir 14:5425–5429 (1998). H. Xiong, Z. Zhou, Z. Wang, and X. Zhang, J. Chem. Supramol. Sci. 5:623–626 (1998). G. Decher and J. D. Hong, Ber. Bunsenges. Phys. Chem. 95:1430–1434 (1991). N. B. Hoogeveen, M. A. Cohen Stuart, G. J. Fleer, and M. R. Bo¨hmer, Langmuir 12:3675–3681 (1996). E. R. Kleinfeld and G. S. Ferguson, Science 265:370– 373 (1994). Y. Lvov, F. Essler, and G. Decher, J. Phys. Chem. 97: 13773–13777 (1993). M. Ferriera and M. F. Rubner, Macromolecules 28: 7107–7114 (1995). G. Decher, Y. Lvov, and J. Schmitt, Thin Solid Films 244:772–777 (1994). V. L. Colvin, M. C. Schlamp, and A. P. Alivisatos, Nature 370:354–357 (1994). B. O. Dabbousi, M. G. Bawendi, O. Onitsuka, and F. Rubner, Appl. Phys. Lett. 66:1316–1318 (1995). H. Uchida, S. Hirai, T. Torimoto, S. Kuwabata, T. Sakata, H. Mori, and H. Yoneyama, Langmuir 11:3725– 3729 (1995). V. Erokhin, S. Carrara, H. Amenitch, S. Bernstorff, and C. Nicolini, Nanotech 9:158–161 (1998). M. P. Pileni, T. Gulik-Krzywicki, J. Tanori, A. Filankembo, and J. C. Dedieu, Langmuir 14:7359–7363 (1998). P. V. Kamat, Chem. Rev. 93:267–300 (1993). P. V. Kamat, in Nanoparticles and Nanostructured Films (J. H. Fendler, ed.), Wiley-VCH, Weinheim, 1998, pp. 207–233. K. Grieve, The physicochemical properties of nanocrystalline semiconductor particles in thin organic films. Ph.D thesis, University of Melbourne, Parkville, VIC, in preparation.

33 The Role of Steric Constraints and Intermolecular Interactions in the Formation of Surfactant Phases ¨ NKE SVENSON SO

I.

The Dow Chemical Company, Midland, Michigan

INTRODUCTION

geometrical shape of the molecules and their intermolecular interactions based on isotropic forces and how this interplay influences the size and shape of surfactant mesophases and self-assembled structures. The question of whether there are general rules or models that predict the experimental observations will be addressed. The phase behavior of single-chain surfactants with mainly isotropic interactions will be reviewed, followed by the phase behavior of branched, doublechain, and multiple-chain surfactants. The review will continue with examples of the phase behavior of mixed surfactants with opposite charges. Finally, the use of the monomer solubility as a hands-on measure to tailor the aggregation behavior will be proposed. The emphasis of this review will always be on the chemical structure of the monomers. Other means to influence the aggregation and phase behavior—for example, the addition of salt, change of pH or temperature, and the presence of cosurfactants—will not be discussed in detail. The phase behavior and self-aggregation of surfactants have been described and reviewed in greater detail in numerous publications [1–23].

The self-aggregation and self-organization of surfactants and related amphiphilic compounds are of essential importance in numerous areas of industrial applications and scientific research. Industrial applications include the use of surfactants in cleaning and personal care products, as emulsifiers for paints and dyestuffs, and as formulating agents in pharmaceuticals. Surfactants are used as templates for the production of molecular sieves and related inorganic materials and the formation of metal and mineral nanocrystals of specific sizes and shapes. Surfactants find application in the development of organic-inorganic composite materials, biomaterials, and as surface coatings for medical devices. As an integral part of complex fluids, surfactants are used in the oil field industry and as drag reducers in heating fluids. In scientific research, self-organizing amphiphiles are models for biological membranes. They find use in studies of membrane processes and as carriers for drugs and other biologically relevant agents. Micellar solutions are important mediators of chemical reactions between otherwise immiscible compounds. These are just a few examples of many applications detailed in this volume that are based on the self-aggregation of surfactants. The understanding of the driving forces behind these processes and the development of reliable models that predict the size and shape of the aggregates and allow tailoring molecules for specific purposes are therefore of essential importance in all of these areas. This chapter will focus on the interplay between the

II.

SELF-AGGREGATION AND PHASE BEHAVIOR OF SINGLE-CHAIN SURFACTANTS

Surfactant aggregation in water above the critical micelle concentration (cmc) produces a wide variety of structures held together by physical interaction forces. 667

668

These structures include micelles of various shapes such as spheres, disks, and cylinders; essentially spherical vesicles and liposomes; and planar bilayers. At high enough concentrations, most surfactants eventually form mesophases or liquid crystals. In these homogeneous phases, the surfactant monomers are assembled into several possible geometries, the most common ones being lamellar (parallel stacks of surfactant bilayers), hexagonal (spherical or cylindrical aggregates are hexagonally close packed), and cubic. A schematic phase diagram for a single-chain surfactant is shown in Fig. 1a. All of these structures have two general features in common. First, the structures are

FIG. 1 (a) Schematic phase diagram of the cationic surfactant cetyltrimethylammonium bromide (CTAB) in water. (Adapted from Ref. 24.) (b) Mean (dynamic) packing shapes of surfactants and the structures they form. (Adapted from Ref. 27.)

Svenson

dynamic in nature. Surfactant monomers are constantly joining and leaving an aggregate on a time scale that can be as rapid as microseconds. This limits the lifetime of any one aggregate, which can be on the order of milliseconds for a small species such as a spherical micelle. Second, the differences in energy between these various structures are quite small. The consequence is that surfactants can often be transformed readily between the various types of aggregate simply by small changes in solution conditions such as concentration, temperature, pH, or electrolyte concentration. The unifying principle behind all the aggregation phenomena described here is the hydrophobic effect, i.e., the tendency of water molecules (or other solvent molecules connected by hydrogen bonds) to maintain their internal structure. The standard free energy of transfer of a single hydrocarbon molecule from an oil phase into water is therefore large and positive. For the same reason, water molecules are trying to ‘‘concentrate’’ randomly distributed hydrophobic tails of surfactants onto the water surface or, with increasing concentration, into micelles and other aggregates [16– 19,21,23,25,26]. The intermolecular interactions between surfactant monomers are attractive van der Waals forces between the hydrocarbon chains and repulsive forces between charged and hydrated headgroups. Both forces are isotropic. Their interplay with each other and the geometry of the monomers will determine the size and shape of the surfactant aggregates. The desire to predict size and shape of these aggregates has led to the ‘‘packing parameter’’ concept, which is mainly based on geometrical considerations. The packing properties of surfactants depend on the optimal headgroup area a0 (defined by the equilibrium between hydrocarbon tail attraction and headgroup repulsion); the volume v of the hydrocarbon chain(s), which is (are) assumed to be fluid and incompressible; and the critical chain length lc (a semiempirical parameter, because it represents a somewhat vague cutoff distance beyond which hydrocarbon chains can no longer be considered as fluid) [27–30]. A few examples of packing parameters v/a0 lc of surfactants and the structures they form are shown in Fig. 1b. This concept is apparently too simple to predict the aggregate structures of the CTAB phase diagram displayed in Fig. 1a. Even though the curvatures of cylindrical micelles and single rods and spheres of the hexagonal and cubic mesophases are quite similar, the size and shape of the whole aggregates are very different. The transformation from one structure to the next is caused solely by a change in surfactant concentration and should not

The Role of Steric Constraints

affect the shape of the monomers. Following are examples of some of the shortcomings of the packing parameter concept. The hydrocarbon chains are considered entirely fluid and not opposing any distortion until they are extended beyond lc. Any effects that may exist as a result of curvature or other distortions of the molecular packing are not considered. However, there is evidence that the chains in micelles are more fluid than in bilayers [27,31]. The charge and degree of hydration of the polar group, and the choice of counterion affect the headgroup area a0 [16,25]. Despite these shortcomings, the concept may be helpful in some areas of practical application when applied carefully.* The phase behavior of surfactants mixed with water shows both universal and particular features. Many of the same phases are formed in widely different systems, including lamellar, hexagonal cylindrical, disordered lamellar, and intermediate mesophases. Other aspects of the phase behavior are sensitive to the amphiphile type. Figure 2 illustrates some universal as well as nonuniversal aspects of the phase behavior in water of four different single-chain surfactants with nonionic, anionic, cationic, and zwitterionic headgroups. With increasing surfactant concentration, there are transitions from an isotropic micellar solution (L 1) to a hexagonal packing of cylinders (H), then to a bicontinuous cubic phase (V), and finally to a lamellar phase (L ␣) [33–37]. The order-order transitions in each case are mainly lyotropic, that is, they are driven by changes in concentration, not temperature. These similarities suggest that universal features of the surfactants, such as volume-filling constraints, entropies and energies of mixing, and entropies of surfactant chain conformation, are causing the phase transitions. However, there are some differences among the phase diagrams. For the anionic surfactant, there is a small intermediate mesophase (X) located between the hexagonal and cubic phases. This phase seems to consist

*When applied less than carefully, the concept unfortunately can result in some irritating statements, e.g., when the molecular packing of amphiphiles within fiber structures below the gel-to-liquid crystalline phase transition temperature (=the hydrocarbon chains are not fluid ) is ‘‘explained’’ by the packing parameter. Obvious mismatches between the fiber curvature and the molecular shape are then taken as evidence for the presence or absence of hydration shells around the headgroups. A list of examples given here certainly would be incomplete and therefore unfair. Readers with experience in this area will have their own examples, and newcomers will soon find some when they are keeping this comment in mind.

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of rodlike aggregates in some sort of a bicontinuous network with lower symmetry than the cubic phase [36]. For the cationic surfactant, a micellar cubic phase (I) consisting of cubic packing of spheres is wedged between the spherical micelles and hexagonal cylinders [32]. The lamellar phase (L ␣) shifts to higher surfactant concentration in the order nonionic, zwitterionic, cationic, and anionic. The hexagonal phase (H) is enlarged for the zwitterionic surfactant compared with the others. Although the different headgroup characters (EO6, COO⫺, Me3 N⫹, and PC; see Fig. 2) clearly influence the phase behavior, the enlargement of the anionic headgroup area by insertion of a methyl group in the ␣-position to it is tolerated. Sodium (R)-2-methyldecanoate and the racemic mixture show essentially the same phase behavior as sodium decanoate [36]. The packing parameter should change in favor of a more conical shape of the monomers, resulting in the preferred formation of aggregates of higher curvature. This has not been confirmed experimentally. The situation is different in cases of cationic trialkylammonium surfactants with triethyl, tripropyl, tributyl, and tripentyl headgroups instead of trimethyl. As expected, the cmc is decreasing with increasing hydrophobicity of the headgroups. But at the same time the counterion association values are decreasing as well, which results in almost identical values of the free energy of micellization for the trimethyl, triethyl, and tripropyl headgroups. Tributylammonium surfactants with C12 and C14 alkyl chains, however, spontaneously demix into dilute and concentrated conjugate phases on warming [37]. This lower consolute behavior in surfactant solutions has been found before for nonionic surfactants such as poly(oxyethylene)alkyl ethers and cationic surfactants in concentrated electrolyte solutions and has been explained by a change in the dipole moment due to a change in the headgroup conformation (nonionics) and a structural change from spherical to rodlike or wormlike micelles (cationics) [38–42]. The tributylammonium surfactants form small spherical micelles at all concentrations because of the somewhat bulky headgroup. In contrast to the spontaneous micelle formation usually observed for surfactants, there is evidence that tributylammonium monomers form premicellar aggregates that continuously grow to form spheres. This leaves a relatively high concentration of free monomers in solution, which are believed to screen the repulsive interactions between the micelles and allow micelles to form clusters and eventually separate to form the concentrated phase. The even higher tendency of the tripentylammonium surfactant to separate from water re-

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FIG. 2 Phase diagrams of four surfactants in water: (a) nonionic hexaethyleneglycol mono n-dodecylether (C12E6), (b) anionic sodium 2-methyldecanoate, (c) cationic dodecyltrimethylammonium chloride (DTAC), and (d) zwitterionic 1-oleoyl-sn-glycero3-phosphocholine (1-OPC). L1 stands for isotropic micellar solution; H, L␣, I, and V, respectively, stand for hexagonal, lamellar, micellar cubic, and bicontinuous cubic mesophases; X denotes a mesophase of rodlike aggregates in some sort of a bicontinuous network; and S stands for crystalline solid. (Adapted from Refs. 32 and 36.)

sults in the formation of metastable solutions and spontaneous crystallization [37]. The effect bulkier cationic headgroups have on the phase diagram and the alkyl chain length dependence of the phase separation are displayed in Fig. 3. The phase diagram changes again when the anionic surfactant sodium sulfopropyl octadecyl maleate (SSPOM) is studied, whose sulfopropyl headgroup is connected via a maleic acid spacer to a C18 hydrocarbon chain. SSPOM behaves like other anionic surfactants at temperatures above the Kraft boundary (TK ⬃ 37⬚C), displaying an isotropic micellar phase (L 1) followed by a hexagonal phase (H). Uncommon properties appear in the temperature range below TK where crystals and a gel-like phase (G␤) with lamellar structure exist (Fig. 4a). This gel phase is metastable but long lived. Wide-angle x-ray scattering data suggest that the molecules within the bilayers of the gel phase are densely packed and interdigitated with the hydrocarbon chains in the crystalline state [43]. The maleic

acid spacer has two effects. First, it introduces a fixed gauche-bend into the molecule that facilitates the interdigitated packing. Second, it provides attractive anisotropic intermolecular interactions in the form of hydrogen bonds between ester carbonyls and ␣-methylene hydrogens of adjacent hydrocarbon chains, which stabilize the lamellar molecular packing within the G␤ phase. Although the molecules are more cone shaped than the common single-chain surfactants because of the gauche-bend, any resulting curvature of the aggregates is compensated by the formation of linear hydrogen bridges. The introduction of a second charge within the headgroup region should strongly favor aggregates of higher curvature because of the increasing headgroup repulsion. The composition phase diagrams shown in Fig. 4b for the divalent dodecylpentamethyl-1,3-propylenebis-(ammonium chloride) (DoPPDAC) and dipotassium dodecylmalonate (K2DoM) surfactants display the same succession of phases known from monovalent


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FIG. 3 (a) Partial phase diagram of cationic tetradecyl tripentylammonium bromide (C14NPe3Br) in water. A straight line denotes a measured phase boundary, a broken line an inferred boundary, and the dotted line indicates the locus of the cmc. (b) Partial binary phase diagrams of alkyl tributylammonium bromides (CnNBu3Br) in water showing a two-phase region for dodecyl (n = 12), tetradecyl (n = 14), and hexadecyl (n = 16) alkyl chains. Horizontal hatching represents isothermal tie lines through a two-phase region. L denotes isotropic liquid phases and Saq denotes hydrated cystalline solids. (Adapted from Ref. 37.)

surfactants, but they differ in that the phase transitions are shifted toward higher surfactant concentrations. A discontinuous cubic phase, a hexagonal phase, and a mixture of liquid crystalline phases and hydrated crystals follow an isotropic micellar solution. The discontinuous cubic phase consists most likely of prolateshaped micelles and might contain two different phases in case of the surfactant K2DoM. A lamellar phase, however, has been observed for divalent surfactants only after mixing with monovalent surfactants to dilute the total charge density [44]. Another approach to increasing the headgroup area a0 and force curvature into the aggregates is realized in the ‘‘dicephalic’’ surfactant 1,3-bis(1-imidazolyl)-2propyl octadecanoate (BIPO), which has two imidazole

headgroups linked to a single C18 hydrocarbon chain. The headgroup charge (= repulsive interaction) can be controlled by the pH of the solution (pKa1 3.6 and pKa2 ⬃7). Instead of the expected spherical micelles, BIPO forms approximately 1000-nm large multilamellar vesicles at pH 5.5 (monoprotonated cationic headgroups) and extended bilayer structures at pH 9.5 (deprotonated neutral headgroups), which transform into polycrystalline platelets upon aging as revealed in freeze-fracture electron micrographys (Fig. 4c) [45]. BIPO is a second example for a situation in which linear hydrogen bridges between protonated imidazole headgroups and/ or ester carbonyls and ␣-methylene protons interfere with a higher curvature of the aggregates. Replacement of the imidazole moieties by disodium phosphate

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FIG. 4 (a) Schematic phase diagram of the anionic surfactant sodium sulfopropyloctadecyl maleate (SSPOM) in water. Note the uncommon metastable G␤ phase at temperatures below the Kraft boundary. (Adapted from Ref. 43.) (b) Composition phase diagram of dipotassium dodecylmalonate (K2DoM) and dodecylpentamethyl-1,3-propylenebis(ammonuim chloride) in D2O at 25⬚C. (Adapted from Ref. 44.) W denotes the aqueous phase below the cmc; L1, I, and H stand for the isotropic micellar, discontinuous cubic, and hexagonal phases, respectively; LC denotes unspecified liquid crystalline phases; Saq, S␣, and S␤ denote hydrated surfactant crystals and crystal modifications above and below the chain melting temperature, respectively. (c) Freeze fracture electron micrographs of dispersions of the ‘‘dicephalic’’ surfactant 1,3-bis(1-imidazolyl)-2-propyl octadecanoate (BIPO) in water prepared at (A) pH 5.5, and (B,C) pH 9.5 after aging for 16 h (B) and 1 week (C). Bars represent 250 nm. (Reprinted in part with permission from Ref. 45. Copyright 1999 American Chemical Society.)

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groups results in the formation of a dicephalic surfactant that aggregates in water to form bundles of fibers. At pH 7.0 (monoprotonated cationic headgroups), the fibers have uniform diameters of 6.5 nm (approximately twice the molecular length) and lengthens up to 15 ␮m (aspect ratio > 2000). As expected, the curvature of the aggregates is high, but again a network of linear hydrogen bridges prevents the formation of spherical micelles in favor of extended rods [46]. Both dicephalic surfactants give clear evidence that the aggregation behavior can be changed dramatically by screening the headgroup repulsion and turning it into an attractive force. A related single-chain surfactant with an imidazole headgroup is based on urocanic acid (4-imidazoleacrylic acid), a metabolite of histidine that is of biological interest. Urocanic acid can be alkylated at both nitrogen atoms of the imidazole moiety and through esterification of the carboxylic acid group. N-MethylN-alkyl-urocanic esters with a methyl group and a dodecyl (C12) hydrocarbon chain connected to the second nitrogen and the ester carbonyl or vice versa, that is, N 1,N 3-dimethyl urocanic dodecyl ester and N 1-dodecyl-N 3-methyl urocanic methyl ester, are cationic surfactants. Regardless of which position the C12 chain is connected to, both surfactants form micelles in water at a very similar critical micelle concentration (e.g., 5.4 ⫻ 10⫺4 and 6.5 ⫻ 10⫺4 with chloride as a counterion) [47]. The influence of the headgroup size on the phase behavior of nonionic oxyethylene (CiEOj ) surfactants [also called poly(oxyethylene) and poly(ethyleneoxide) surfactants, although the typical number of EO units is well below 20 and thus hardly ‘‘poly’’] is displayed in Fig. 5. The increase of the length of the linear EOj headgroup from 7 to 20 units at a constant hydrocarbon chain length results in a significant change of the phase behavior. When the headgroup contains 7 EO units, hexagonal (H) and lamellar (L ␣) phases are produced above certain surfactant concentrations (Fig. 5a). An increase of the headgroup size to 11 EO units produces a bicontinuous cubic phase (V) wedged between the hexagonal and lamellar mesophases. The lamellar phase is much smaller as before (Fig. 5b). An additional increase of the headgroup to 20 EO units eliminates the lamellar phase and a large micellar cubic phase (I) appears before the hexagonal mesophase (Fig. 5c) [48]. More detailed studies of the micellar cubic phase (I) revealed a more complicated phase behavior within this concentration range. The surfactant dodecaoxyethylene mono-n-dodecyl ether (C12 EO12), for example, forms three different cubic phases (space


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FIG. 5 Phase diagrams of nonionic tridecyl/pentadecyl poly(oxyethylene) surfactants (C13/C15EOx with x = 7, 11, 20 and C13/ C15 = 66%:34% mixture) in water. The data points were measured by rheology, differential scanning calorimetry, microscopy, and visual studies. L denotes isotropic liquid phases; H, L␣, I, and V stand for hexagonal, lamellar, micellar cubic, and bicontinuous cubic mesophases, respectively; S stands for crystalline solid; and 2␾ denotes a two-phase region (lower consolute region). The broken lines represent an equilibrium between phases. (Adapted from Ref. 48.)

groups; Pm3n, Im3m, and Fm3m) at concentrations between 30 and 60 wt% in water [49]. A large increase of the headgroup size while keeping the hydrocarbon chain at about the same length as before (C17EO84) again changes the phase behavior to some extent. The micellar cubic phase consists of only one phase over the concentration range 20–60 wt% (space group:

Im3m). This phase is composed of discrete micellar building blocks, which appear to be nonspherical, e.g., the aggregation number increases with concentration from 52 ⫾ 3 monomers at 10 wt% to 107 ⫾ 9 monomers at 40 wt% [50]. Similar results have been reported for C18:1EOj oxyethylene surfactants whose extremely pure C18:1 oleyl alcohol hydrocarbon chains are con-

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nected to EOj headgroups of varying sizes between 0 (oleyl alcohol) and 20 EO units. The increase of the oxyethylene chain, that is, the increase of the hydrophile-lipophile balance (HLB) of the monomers, corresponds to an increasing curvature of the surfactant layers toward water. Various self-aggregating structures have been found: hexagonal and lamellar liquid crystals, four kinds of isotropic liquid crystals, a sponge phase, and a reverse hexagonal liquid crystal (Fig. 6a) [51]. An interesting observation has been made on the C18:1EO50.8-water system. This binary mixture forms an aqueous micellar (L 1) and a discontinuous cubic (I1) phase. Upon addition of m-xylene, the I1 phase changes to a hexagonal phase (H1), a bicontinuous cubic phase (V1), and finally a lamellar phase (L ␣) with increasing oil content. Although the mean curvature of the surfactant aggregates changes from positive (curved toward oil) to zero, a negative (curved toward water) curvature is not achieved because of the steric hindrance caused by the long EO50.8 chains. The L ␣ phase solubilizes a large

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amount of oil, and eventually very stable reverse vesicles form in the oil-rich region [52]. These phase transformations are caused by penetration of m-xylene molecules into the palisade layer of the surfactant molecules, thus reducing the water content within the layer. A phase diagram displaying the position of the reverse vesicle phase and a micrograph of this phase are shown in Fig. 6b. It should be noted that the geometry of the molecules is not affected by the observed change of the mean curvature. The area per molecule is almost independent of the geometry of the interface [53–55]. A related example is the effect a change in temperature has on the phase behavior of ternary oxyethylene mixtures. At constant temperature, the structural sequence of normal spheres to planar bilayers via cylinders is observed as a function of decreasing water concentration in the phase diagram of the ternary C12EO5-water-decane mixture (Fig. 7) [53]. The phase diagram is strikingly similar to that observed for the binary C12EO5-water mixture despite the presence of

FIG. 6 (a) Typical birefringent textures of the liquid crystal phases found in the C18:1EOj -water system: (A) lamellar phase; (B) hexagonal phase; and (C) reverse hexagonal phase. Bars = 50 ␮m. (Reprinted with permission from Ref. 51. Copyright 1997 American Chemical Society.) (b) Phase diagram of C18:1EOj-water-m-xylene at 25⬚C as a function of the surfactant-towater ratio RSW and the number of oxyethylene groups (note the decreasing number of water molecules per EO group that leads to the formation of reverse vesicles); micrograph of reverse vesicles and myelin strands formed in the oil-rich region. (Reprinted with permission from Ref. 52. Copyright 1999 American Chemical Society.)


FIG. 7 Phase prism of temperature-dependent changes in the behavior of a ternary C12EO5-water-decane mixture showing some individual isothermal cuts. T3 corresponds to the balanced temperature where the spontaneous curvature is zero (38⬚C in the present system). At T1 and T2, the spontaneous curvature is toward oil (positive). The L3 phase is not included because it is formed at temperatures above T3. L denotes isotropic liquid phases; L␣, H1, I1, and V1 stand for lamellar, hexagonal, micellar cubic, and bicontinuous cubic phases, respectively; O denotes oil, and 2 and 2 denote oilrich and water-rich two-phase regions. (Adapted from Ref. 53.)

the oil [56]. With increasing temperature, the phase behavior can be understood in terms of a monotonic decrease of the spontaneous or preferred curvature. Oilswollen micelles are formed at low temperature, hence their curvature is toward the oil (positive). Upon heating, the micelles grow from spheres along the lower phase boundary to elongated micelles, consistent with a decrease in the mean curvature. At an intermediate temperature (38⬚C in the present system), the spontaneous curvature is zero and only structures with this mean curvature are stable, that is, either a balanced bicontinuous microemulsion containing equal volumes of water and oil or a lamellar phase. Upon further heating, the lamellar phase transforms to the liquid L 3 phase because its monolayer mean curvature is toward the water (negative). The strong temperature dependence of the spontaneous curvature originates from the fact that oxyethylene chains are increasingly less water soluble at higher temperatures; that means the equilibrium concentration of water in the palisade layer of the nonionic C12EO5 film decreases [53,57]. Because the area per surfactant molecule remains constant, as men-

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tioned before, the mean curvature of the aggregates has to decrease from sphere to cylinder to lamellae with decreasing water concentration. A more detailed discussion of the phase behavior of nonionic CiEOj surfactants and the effect of additives is given in a review [58]. Although the relationship between a change in headgroup size and the resulting change in phase behavior should be more obvious for nonionic surfactants, which lack the additional counterion interactions mentioned earlier for charged surfactants, the experimental data for oxyethylene surfactants indicate that a prediction of the phase behavior solely based on packing parameters is insufficient. Nevertheless, there are striking similarities many oxyethylene systems share and which may have some predictive power. It appears that very few empirical parameters are needed to reduce the scales of composition, temperature, length, and interfacial tension at ambient pressure. Relevant parameters are (1) the mean temperature Tm of the three-phase body (roughly the HLB temperature); (2) the temperature sensitivity of the phase behavior (equivalent to the temperature dependence of the spontaneous curvature), characterized by the extent ⌬T of the three-phase body; (3) the fraction of surfactant ␥i necessary to solubilize equal volumes of water and oil at Tm, which is inseparably linked to the maximum length scale in the system; and (4) the minimum interfacial tension at Tm [59,60]. A very detailed study of the phase behavior of the system n-butyl monoglycol ether (C4 EO1)-water-dodecane between 22 and 82⬚C and a comparison with 23 other systems of the type CiEOj -water-n-alkane are given in Ref. 59. It should be noted that the geometrical structure of the surfactant monomers is not one of the relevant parameters necessary to define a microemulsion. In fact, studies have shown that the behavior of longand short-chain CiEOj surfactants is similar [61,62]. The headgroup area at the water-oil interface was found to be independent of the number of carbon atoms (Ci) of the alkyl chain but to depend strongly, and nearly linearly, on the headgroup size (EOj) of the surfactant [63]. Most interestingly, the results reported in Ref. 59 suggest that the monomer solubility of the surfactant in water and oil might be the key to describing the main features of these microemulsion systems. This point will be discussed in more detail later in this chapter. The addition of a sulfate group to the oxyethylene head leads to the commercially very important family of alkyl ethoxy sulfate surfactants [Cn H2n⫹1 — (OCH2CH2 )m — OSO3 Na] [64–66]. These surfactants exhibit an aggregation behavior intermediate between that of nonionic and anionic surfactants, determined by

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the interplay between steric interaction of hydrated EOj groups and electrostatic repulsion of the sulfates. The relative strength of both forces depends on the number of EO groups, and the length of the hydrocarbon chain influences the hydrophile-lipophile balance. Dodecyl ethoxy sulfate surfactants with two EO groups form spherical micelles in water, which undergo a sphere-torod transition in the presence of multivalent counterions such as Ca2⫹ and Al3⫹ [65]. A more thorough study involving dodecyl ethoxy sulfates with one, two, four, and six EO groups revealed that micelles formed by surfactants with one and two EO groups undergo a onedimensional growth beyond a threshold NaCl concentration due to the salt screening of the sulfate repulsion. In contrast, micelles formed by surfactants with four and six EO groups remain spherical over the entire salt concentration and temperature range used in the study because of stronger steric hindrance between these larger headgroups. A phase separation at high temperatures analogous to the behavior of nonionic CiEOj surfactants has not been observed so far [66]. Replacement of the linear hydrocarbon chain CiEOj surfactants by a trisiloxane group leads to another family of industrial important nonionic surfactants [67– 69]. Trisiloxane or M(D⬘En)M surfactants [M denotes the trimethylsiloxy group (CH3)3 — SiO1/2 — ; D⬘ stands for — O1/2Si(CH3)(R)O1/2 — , where R is a oxyethylene group (En ) attached to the silicon atom through a propyl spacer] behave differently from conventional hydrocarbon surfactants in being surface active in nonaqueous media. Although the hydrophobicity of the MD⬘M group (which includes the propyl spacer) in water is similar to that of a linear C12 H25 hydrocarbon chain, the shape of this hydrophobic group is quite different. Its ‘‘umbrella’’ structure is shorter and wider than C12 H25 and has a larger volume (e.g., MD⬘M: 9.7 ˚ length and 530 A ˚ 3 volume; C12 H25: 15 A ˚ length and A 3 ˚ volume). Solubility and self-aggregation of tri350 A siloxane surfactants derive from the oxyethylene headgroup; that is they become less water soluble with increasing temperature, analogous to the behavior of CiEOj surfactants. Trisiloxane surfactants differ from these linear analogues in that their phase behavior resembles that of CiEOj surfactants having longer hydrophilic EOj chains because of the umbrella structure of the MD⬘M group [e.g., M(D⬘E8)M behaves more like C12 EO5 than C12 EO8] [68]. The binary phase diagram of M(D⬘E12)M is dominated by the hydrophilic character of the EO12 headgroup. An isotropic phase is formed at all concentrations in a wide temperature range between 12 and 43⬚C, the lower consolute temperature (Fig. 8a). In this one-phase region, M(D⬘E12)M

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forms spherical micelles, cylindrical micelles, random interconnected bilayers, and inverted microstructures at high surfactant concentrations. A hexagonal (H1) and a lamellar (L ␣) phase have been found below 12⬚C [67]. Reduction of the hydrophilic character of M(D⬘E12)M by reducing the length of the EO12 headgroup results in a richer phase behavior [68]. In the phase diagram of M(D⬘E 6)M, a water-rich isotropic phase (W) is formed at surfactant concentrations below 0.1 wt%, followed by a phase (W ⫹ L ␣) consisting of unilamellar vesicles in a wide size distribution (50–500 nm). Most of the phase diagram is dominated by a large lamellar phase. A 3–5⬚C wide, continuous band of a transparent and isotropic phase is present above L ␣ at all concentrations between 1 and 80 wt%. The water-rich end of this band has been labeled L 3 and the surfactant-rich end L 2. The L 3 phase exhibits strong flow birefringence, and the L 2 phase is isotropic with no birefringence. A continuous evolution between two phases with no phase boundary is not atypical but has been reported for other systems [70]. In general, trisiloxane M(D⬘En)M surfactants follow the same self-aggregation principles as linear CiEOj surfactants. They favor microstructures of higher positive curvature with increasing size of the EOj group [68,69]. The introduction of a trimethylsilyl-terminated alkyl chain [(CH3)3 — Si — (CH2)n — ] as hydrophobe instead of the bulky trisiloxane group causes another peculiarity of the phase behavior. Trimethylsilane surfactants display solution properties similar to those of the trisiloxane analogues but have the advantage of higher hydrolytic stability. Their phase behavior has been studied intensely [71–75]. Trimethylsilane surfactants behave similar to nonionic CiEOj surfactants; however, they differ in that there are two disconnected lamellar mesophases in the phase diagram, a large concentrated one and a small diluted one. As an example, the phase diagram of CH3Si(CH2)6(OCH2CH2)5OCH3 (Me3SiC6E5) in water is shown in Fig. 8b [76]. Probably the most important family of single-chain amphiphiles with zwitterionic headgroups consists of 1-acyl-sn-glycerophosphocholines or lysophosphocholines (lyso-Cn PC). Lysophosphocholines are constituents of many biological membranes. They derive from natural phosphocholines by enzymatic hydrolysis of the acyl chain in the 2-position of the glycero backbone [77–79]. The phase behavior of lyso-Cn PC molecules strongly depends on the length of the hydrocarbon chain. In general, they behave similarly to other surfactants as they show the same sequence of isotropic micellar solution (L 1), hexagonal phase (H1), and lamellar phase (L ␣) before the region of hydrated crystals


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FIG. 8 (a) Binary phase diagram of the trisiloxane surfactants M(D⬘E12)M and M(D⬘E6)M in water. For details see text. (Adapted from Ref. 67 and 68.) (b) Binary phase diagram of (A) the trimethylsilane surfactant CH3Si(CH2)6(OCH2CH2)5OCH3 (Me3SiC6E5) in water showing two separate lamellar L␣ phases and (B) an enlarged portion of the diagram. (Adapted from Ref. 76.) L and W denote isotropic liquid phases; L␣ and H, respectively, stand for lamellar and hexagonal phases; and 2␾ denotes a two-phase region.

(Fig. 9). Nevertheless, there are some peculiarities in the diagrams. Lauroyl (lyso-C12PC), myristoyl (lysoC14PC), and palmitoyl (lyso-C16PC) lysophosphocholines have a cubic phase (I1) wedged between the L 1 and H1 mesophases, which is absent in the diagram of the homologous stearoyl (lyso-C18PC) lysophosphocholine (Fig. 9a and b). Lyso-C18PC, on the other hand, has a cubic mesophase (V1) located between the H1 and L ␣ phases. The presence of two additional methylene groups (e.g., palmitoyl C16 compared with stearoyl C18) should not affect the geometry of the lysophosphocholines but clearly affects their aggregation behavior. Insertion of a cis C — —C double bond as present in the hydrocarbon chain of oleoyl (lyso-C18:1PC) lysophosphocholine does not change the sequence of mesophases but changes the phase transition temperatures compared with the saturated lyso-C18PC. The transition

from crystalline to liquid crystalline phases takes place above room temperature in case of lyso-C18PC (Fig. 9b and c) [77,78]. The micelles within the L 1 phase of saturated lysophosphocholines remain spherical over the whole concentration range of the phase, whereas the micelles of the unsaturated lyso-C18:1PC seem to be elongated and polydispersed. The cubic phase (I1) consists of disklike micelles with an axial ratio of about two, arranged in a cubic lattice as found for other surfactants [78]. In general, zwitterionic surfactants are of interest because of their insensitivity to changes of the ionic strength and their compatibility with living matter; e.g., they are used in protein solubilization without denaturation and in low-irritant shampoos. Single-chain zwitterionic surfactants form spherical micelles in water because of their usually bulky polar headgroups (>50–60

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FIG. 9 Phase diagrams of (a) palmitoyl lysophosphocholine (lyso-C16PC), (b) stearoyl lysophosphocholine (lyso-C18PC), and oleoyl lysophosphocholine (lyso-C18:1PC) in water. Note the presence of cubic I1 and V1 phases dependent on the acyl chain length, and the change in phase transition temperatures dependent on the degree of saturation of the acyl chains. L1 denotes an isotropic liquid phase; L␣, H1, I1, and V1 stand for lamellar, hexagonal, micellar cubic, and bicontinuous cubic phases, respectively; and Saq denotes hydrated crystals. (Adapted from Ref. 77.)

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˚ 2). At concentrations above 60–70 wt% they aggreA gate to form mesophases of high curvature, such as micellar cubic (I1) and hexagonal (H1) phases. The phase boundaries are often parallel to the temperature axis, resulting in weak temperature sensitivity of the phases [80–82]. The aggregation behavior of zwitterionic surfactants depends on the flexibility of the spacer between the two charges. Long hydrophobic alkyl spacers ( — CH2 — )n with n > 7, for example, fold back into the hydrophobic region of the aggregates, thus allowing the charges to get closer to each other [83,84]. Zwitterionic N-alkylpyridiniocarboxylate surfactants with the COO⫺ group in either the 3- or 4-position at the pyridinium ring (e.g., C12-Py-m-CO2 with m = 3, 4), on the contrary, have a fixed distance between the charges. They display a rather unusual phase behavior as shown in Fig. 10a. The sequence of mesophases with increasing concentration is as expected: L 1, I1, and H1. A temperature increase at a constant surfactant concentration between 60 and 68 wt%, however, also results in phase transitions form L 1 to H1 via I1. The position of the COO⫺ group does not affect the sequence of mesophases but shifts the transition temperatures. The I1 phase consists of a periodic arrangement of globular micelles, which can be slightly anisotropic (space group Pm3n), while the H1 phase contains micellar rods with the alkyl chains in the liquid state (space group p6m). The different dipole moments of the headgroups due to the 3- versus 4-position of the carboxylate COO⫺ to the ammonium N⫹ group affects the behavior in dilute solution and thus the cmc. However, this dependence vanishes with increasing concentration of the zwitterionic surfactants [85]. Another approach to changing the hydrophile-lipophile balance and to increasing attractive intermolecular interactions without major changes of the geometrical structure of the surfactants involves the use of rigid aromatic segments within the hydrocarbon chain. These molecules combine the structural element of a liquid crystal–forming compound [e.g., N-(4-methoxybenzylidene)-4-butylaniline, MBBA] with the structural element of a micelle-forming surfactant (e.g., cetyltrimethylammonium bromide, CTAB). For this purpose, azobenzene (Cn — C6H4 — N — —N — C6H4 — Cm), benzylideneaniline (Cn — C6H4 — N — CH — C6H4 — Cm), and salicylideneaniline [Cn — C6H4 — N — —CH — (2-OH) C6H3 — Cm ] containing hydrocarbon chains have been connected to cationic trialkylammonium headgroups [86–89]. The aromatic segments reduce the flexibility of the alkyl chains (thus interfering with one of the requirements of the packing parameter concept) and improve intermolecular interactions due to the stacking


of the aromatic rings. Bilayer formation with and without interdigitation of opposing half-layers has been observed [86,87]. Depending on the position of the aromatic group within the hydrocarbon chains, that is, the length of the Cn and Cm segments, the azobenzene derivative forms stable bilayer membranes for the following ratios: n:m = 12:2–12; n:m = 10:5–10; and n:m = 8:10. These results clearly indicate the higher importance of the Cn length for the bilayer formation [86]. The benzylideneaniline derivative forms unilamellar vesicles (n:m = 12:5), short fibers with diameters of ˚ (n:m = 12:10), and large unstructured aggre60–70 A gates (n:m = 8.10). The related salicylideneaniline derivative, which has a hydroxy group in the ␣-position to the CH — — group, forms not very well-defined fibrous ˚ regardless of structures with diameters around 150 A the Cn :Cm ratio (Fig. 10b) [88]. Several other rigid segments have been used, linear and bent ones with two

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and three aromatic rings. Whereas molecules containing a linear segment tend to assemble in a neat, twodimensional arrangement (membrane), molecules carrying a bent segment favor more radial structures such as rods and tubules. For more detailed information, see the reviews in Refs. 86 and 89. The concept of a rigid segment is driven even farther by the use of a three- and four-ring spiro system that has no rotational freedom as a hydrocarbon chain, connected to a trimethylammonium headgroup. Both compounds behave like surfactants and form micelles. The cmc of the three-ring spiro surfactant of 0.14 M turned out to be identical to the cmc of the related octyl trimethylammonium bromide with a similar chain length. On the other hand, the cmc is 3.3 times larger than that of the undecyl trimethylammonium bromide, a conventional surfactant with the same number of carbon atoms within the hydrocarbon chain. This observation and the

FIG. 10 (a) Binary phase diagrams of zwitterionic N-dodecylpyridinio-3-carboxylate (C12-Py-3-CO2) and N-dodecylpyridinio4-carboxylate (C12-Py-4-CO2) in water. L1 denotes an isotropic liquid phase; I1 and H1, respectively, stand for micellar cubic and hexagonal mesophases. (Adapted from Ref. 85.) (b) Transmission electron micrographs of trimethylammonium surfactants containing (A) benzylideneaniline and (B) salicylideneaniline as rigid segments in their hydrocarbon chain. (The Cn /Cm ratios are 12 : 5, and 8 : 10; for details see text). (From Ref. 88.)

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fact that micelles could not be detected by light scat˚ ) indicate tering (which had a lower size limit of 40 A the formation of very small aggregates of perhaps only 10–20 molecules by the spiro surfactant. The spiro surfactants are another example of molecules that are violating the packing concept based on the molecular geometry [90]. One final way, discussed here, to change the hydrophile-lipophile balance of a single-chain surfactant without causing major changes in the molecule’s geometry involves the use of fluorocarbon chains [91– 97]. Fluorocarbon chains are more hydrophobic and stiffer than hydrocarbon chains (note the similarity to the rigid segment discussed earlier). They possess less conformational freedom because of the larger energy difference between gauche and trans conformations. As a consequence, fluorosurfactants have a much stronger capacity to self-aggregate in water into discrete molecular assemblies: (1) their cmc corresponds to a hydrocarbon analogue with 1.5–1.7 as many carbon atoms in the tail; (2) even very short, single-chain fluorinated amphiphiles form stable vesicles without the need for supplementary attractive interactions; and (3) sturdy microtubules were obtained from nonchiral, non-hydrogen-bonding single-chain fluorosurfactants. Like hydrocarbon surfactants, fluorosurfactants form micelles and various mesophases in the same sequence as found for hydrocarbons. However, because of the chain stiffness, they often form structures with less curvature, and they have a higher tendency to form intermediate phases between the H1 and L ␣ phases. The formation of intermediate phases in surfactant-water mixtures and the self-assembly of fluorocarbon surfactants have been reviewed [91–93]. Therefore, only a few examples will be discussed here. The cationic fluorosurfactant 1,1,2,2tetrahydroperfluorodecyl-pyridinium chloride (HFDePC) aggregates in water to form micellar (L 1), hexagonal (H), centered rectangular (R), and centered trigonal (T) mesophases with increasing concentration. Evidence for a random mesh phase and a lamellar phase was found at even higher concentrations (Fig. 11a) [94]. One specific feature of fluorosurfactants is displayed in Fig. 11b. Partial screening of the headgroup repulsion by addition of a small amount of salt is sufficient to transform spherical micelles of HFDePC into threadlike micelles. The related fluorocarbon surfactant 2-hydroxy-1,1,2,3,3-pentahydroperfluoroundecyldiethylammonium chloride (I-C11) forms threadlike micelles even in the absence of salt. Spherical and threadlike micelles coexist in salt-free aqueous solution at a concentration of 50 mM [95]. Perfluoroalkylated single-chain surfactants with a neutral dimorpholino-

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phosphoramidate (CF-MPA) or a zwitterionic phosphocholine (CF-PC) headgroup aggregate in water to form rigid tubules and flexible fibers. CF-MPA tubules form readily from lipid films by hydration at 50⬚C with gentle swirling by hand within hours after preparation of the suspension. They have a length distribution of 10 to 50 ␮m and diameters between 100 and 500 nm. The tubules are fragile and transform into large vesicles when heated above 40⬚C. CF-PC fibers, on the other hand, grow within 1 to 4 months from their suspensions. They are flexible, have a length distribution of 50 to 500 ␮m with diameters between 1 and 5 ␮m, and are sometimes branched. The reversible fiber-tolarge vesicle transformation occurs at 50⬚C (Fig. 11c). The hydrocarbon analogues form only micelles, even when the hydrocarbon chain is extended to adjust the cmc to those of the fluorosurfactants [96]. The packing parameter concept is useful only in predicting the formation of vesicles versus micelles when adjusted to the specifics of the CF groups. CF2 and CF3 groups have higher volumes than the corresponding CH2 and CH3 ˚ 3 and CH2 27 A ˚ 3), and fluorogroups (e.g., CF2 41 A carbon chains are slightly longer than hydrocarbons. The contribution per CX2 group to the length of the ˚ (hydrocarfully extended fluorocarbon chain is 1.30 A ˚ ), and the cross-sectional area is 31.5 A ˚2 bon: 1.25 A 2 ˚ ) [95,97]. The surface area per (hydrocarbon: 21.4 A headgroup a 0 remains the same for the fluorinated and hydrogenated analogues. The significantly larger volume of the fluorocarbon chains results in a truncatedcone geometry of the fluorosurfactants that favors vesicles, whereas the cone geometry of the analogous hydrocarbon surfactants favors micelles [97]. Besides these adjustments, the packing parameter concept has the same shortcomings as mentioned earlier for hydrocarbon surfactants when used to explain the transformation of vesicles into either rigid tubules or flexible fibers below the gel-to-liquid crystal phase transition temperature Tc . III.

PHASE BEHAVIOR OF BRANCHED, DOUBLE-CHAIN, AND MULTIPLE-CHAIN SURFACTANTS

The phase behavior of branched, double-chain, and multiple-chain surfactants is discussed in this section. The packing parameter v /a 0 lc , (the volume v) changes because of the presence of a branch or additional hydrocarbon chains. The most thorough study of the effect the shape of the hydrophobe has on the aggregation behavior of surfactants has been carried out on asymmetrical and symmetrical nonionic oxyethylene surfac-


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FIG. 11 (a) Partial phase diagram of the cationic fluorocarbon surfactant 1,1,2,2-tetrahydroperfluorodecylpyridinium chloride (HFDePC) in D2O. L denotes isotropic liquid phases; L␣, H, R, and T stand for lamellar, hexagonal, centered rectangular, and centered trigonal (rhombohedral) mesophases, respectively; nd denotes a not safely determined portion of the diagram that might consist of a random mesh phase and a lamellar phase. (Adapted from Ref. 94.) (b) Cryo-transmission electron micrographs of (A) monodispersed spherical micelles of 50 mM HFDePC in water; (B) long, flexible, and entangled threadlike micelles of 25 mM HFDePC in 150 mM aqueous NaCl; and (C) spherical micelles in coexistence with rather stiff threadlike micelles of 50 mM 2-hydroxy-1,1,2,3,3-pentahydroperfluoroundecyldiethylammonium chloride (I-C11) in water. Bars = 100 nm. (Reprinted in part with permission from Ref. 95. Copyright 1999 American Chemical Society.) (c) Phase-contrast optical micrographs of (A) tubules obtained from CF-MPA in water; (B) a magnified single tubule, note the aqueous core visible in the upper part of the micrograph; and (C) the reversible transformation at 50⬚C of flexible fibers into large vesicles. BarsABC = 8, 4, and 8 ␮m. (From Ref. 96.)

tants of the series Ck Cn GE8M [Ck symbolizes an nbutyl (C4) or tert-butyl (C t4) chain; Cn stands for a decyl (C10) or dodecyl (C12) chain; G denotes a triglyceryl unit ( — OCH2 — CHO — CH2O — ); and E8M stands for octaoxyethylene monomethyl ether] [98–100]. The double-chain surfactants C t4C10GE8M, C4C10GE8M, and

(C 7) 2GE8M have the same hydrophile-lipophile balance and volume ratio of hydrocarbon chains to headgroup, V1 /Vh. According to the packing parameter, this should result in identical phase behavior of all three surfactants in water. This is clearly not the case, as one can see by comparison of the phase diagrams displayed in Fig.

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12a. At temperatures below the lower critical consolute temperature Tc of the miscibility gap L ⫹ L 1, the phase behavior is very similar with respect to the crystalline coexistence region and the sequence of mesophases. The isotropic micellar solution (L 1) is followed by the normal hexagonal (H1), bicontinuous cubic (V1), and lamellar (L ␣) phases with increasing surfactant concentration. At highest concentrations, an isotropic reverse solution (L 2) is formed. However, there are some differences within the phase diagrams. The L ␣ phase of C t4C10GE8M is

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smaller than those of C4C10GE8M, and (C 7) 2GE8M and surrounded by the isotropic L 1 solution, whereas L ␣ of the other surfactants has a boundary with the liquidliquid phase L 1 ⫹ L 2. In addition, the phase behavior of C t4C10GE8M at temperatures above Tc is quite different from that of C4C10GE8M and (C 7) 2GE8M (Fig. 12a) [98]. Different geometrical structures are possible with the same volume of the hydrophobic part, as shown in Fig. 12b. The packing parameter concept based on the V1 /Vh ratio therefore has to be extended by a structure parameter S that gives information about

FIG. 12 (a) Phase diagrams of the double-chain surfactants C t4 C10GE8M, C4C10GE8M, and (C7)2GE8M, which have the same HLB and ratio of the hydrophobic and hydrophilic volumes. L denotes isotropic liquid phases; L␣, H1, and V1 stand for lamellar, hexagonal, and bicontinuous cubic phases, respectively; and Saq denotes hydrated crystals. (b) Hypothetical structures of surfactants with the same parameters V1, lc, and Ah. (c) Hydrocarbon part of symmetrical and asymmetrical double-chain surfactants with their structure parameter S. (Adapted from Ref. 98.)


the degree of asymmetry of the hydrocarbon part. Examples of structure parameters S derived from the molecular geometry of the surfactants C t4C10GE8M, C4C10GE8M, and (C 7) 2GE8M are shown in Fig. 12c. Although the modified packing parameter is more suitable to describe the phase behavior of these surfactants, packing differences such as interdigitation of opposing half-layers are still not considered. For example, the symmetrical surfactant (C 7) 2GE8M forms an L ␣ phase without interdigitation, whereas the asymmetrical analogue C4C10GE8M interdigitates. This results in a different thermal stability of the L ␣ phases as observable in the respective phase diagrams. The series of Ck Cn GE8M surfactants allows some additional structural considerations. For example, elongation of the decyl chain by two methylene units (e.g., C4C10GE8M versus C4C12GE8M) does not significantly affect the phase behavior [98]. In a related study, the effect a branched headgroup [C14G(E4M) 2 = Y-shape] and a branched hydrophobe [(C 7) 2GE8M = V-shape] have on the binary phase behavior and on the behavior of ternary mixtures of both surfactants in water has been investigated. In accordance with the packing parameter, C14G(E4M)2 with its large headgroup area prefers aggregates of high curvature such as spherical micelles, micellar cubic (I1) phase, and hexagonal (H1) phase. The V-shaped (C 7) 2GE8M, on the other hand, aggregates to form structures of low curvature such as cylindrical or disklike micelles and an extended lamellar (L ␣) phase. The phase behavior of the mixture depends on the mixing ratio ␣ of the surfactants. The packing parameter concept would therefore predict the phases only in a qualitatively correct way when extended by the mixing

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parameter ␣ [99]. Systematic changes of the hydrophile-lipophile balance of (Cn) 2GEm M surfactants by varying n and m result in a phase behavior that is in accordance with the packing parameter concept. Increasing the hydrophobic volume by increasing n stabilizes phases with low curvature, and increasing the hydrophilic area by increasing m stabilizes phases of high curvature [100]. A related study investigated the aggregation behavior of diamines into bilayers with respect to the packing parameter. The compounds employed were 1,2-ethanediamine and 1,4-butanediamine connected to one or several hexadecyl (C16) hydrocarbon chains. The substitution pattern included N-alkyl, N-dialkyl, N, N⬘-dialkyl, N-alkyl-N⬘-dialkyl, and N-dialkyl-N⬘-dialkyl derivatives of both diamines [101]. Although the most compact systematic study of the phase behavior of surfactants with regard to changes in their geometrical structure has been conducted on nonionic oxyethylenes (see earlier), the most often studied double-chain compounds are cationic surfactants. The binary phase diagram of didodecyldimethylammonium bromide (DDAB or diC12NBr) in water displays an isotropic solution (L 1), a fluid phase (L 3) that is optically isotropic at rest but shows flow birefringence, and a viscous permanently birefringent L␣ phase. A twophase region (L 1 ⫹ L␣) is located between L 3 and L␣, containing L␣ aggregates dispersed in the L 1 phase. Below the melting temperature of the hydrocarbon chains are two phases, denoted as L 1 ⫹ L␤ and L␤. These two phases cannot be distinguished from L 1 ⫹ L␣ and L␣ by visual inspection, but differential scanning calorimetry (DSC) studies show the chains in the frozen state (Fig. 13a). The L 3 phase is metastable and vanishes after 90 days of equilibration and slow cooling to am-

FIG. 13 Binary phase diagram of the double-chain surfactant didodecyldimethylammonum bromide (DDAB) in water (a) at concentrations below 3 wt% and (b) in the very dilute region between 10⫺5 and 10⫺1 wt%. Note the spontaneous formation of small vesicles upon dilution of the L3 phase. L denotes isotropic liquid phases; L␣ and L␤ stand for lamellar phases above and below the melting temperature of the hydrocarbon chains; and Saq denotes hydrated crystals. (Adapted from Ref. 102 and 105.)

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bient temperature. The phase diagram of the homologous dihexadecyldimethylammonium bromide (DHAB or diC16NBr) is virtually the same as that of DDAB [102]. The structures of the L␣ and L 3 phases of DDAB have been studied by freeze-fracture electron microscopy. The micrographs clearly reveal the lamellar structure of the L␣ phase and the bicontinuous network of two aqueous subvolumes separated by a random bilayer network that builds the structure of the L 3 phase [70]. A more recent study of DDAB reports the existence of two thermodynamically stable lamellar phases. The dilute L␣ phase is stabilized mainly by electrostatic forces, whereas hydration forces stabilize the condensed L ␣⬘ phase [103]. The condensed L ␣⬘ phase seems to be stable up to very high concentrations of the surfactant. In the phase diagrams of the homologous diC10 NBr and the asymmetrical double-chain surfactant C8C16 NBr, and the L␣ phase is followed by a second liquid crystalline phase, which is believed to be hexagonal. The second mesophase vanishes in all cases when the samples are heated to temperatures above 80–90⬚C and isotropic solutions form [104]. Dilution of the L 3 phase of DDAB results in the spontaneous formation of unilamellar vesicles with a mean diameter of 33 nm. The vesicles are a part of four distinct regions that are present at low concentrations: the L 3 phase, a two-phase region consisting of small vesicles and large multilayer aggregates, the vesicular solution (L 1 phase), and the molecular solution (Fig. 13a). The phase boundaries in the diagrams of homologous dialkydimethylammonium bromides with decyl (C10) and octyl (C8) chains are shifted to higher surfactant concentrations. For example, diC10 NBr forms only three phases (molecular and vesicular solutions and twophase region), and diC8 NBr forms two phases (molecular and vesicular solutions) within the concentration range used in the study. The unilamellar vesicles of both surfactants have slightly smaller mean diameters of 28 and 30 nm. The reported phase behavior and the spontaneous formation of vesicles are considered to be in accordance with the packing parameter concept. The packing parameters of diC n NBr surfactants (P = 0.58– 0.62) are within the range of 1/2 < P < 1 where the formation of vesicles or lamellae is expected [105]. However, whereas DDAB forms small vesicles with a diameter of 33 nm upon dilution from the L 3 phase, it will form giant unilamellar vesicles with diameters of 10–200 ␮m when 0.1–0.2 mg DDAB is immersed in 450 ␮L of water without any energy input. These giant vesicles have been intensely studied as mimics of living cells, and chemically induced birthing and foraging

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as well as aggregation, budding, and fusion have been observed [106,107]. Dodecyldimethylammmonium bromide has also been one of the first synthetic compounds successfully used to form artificial bilayer membranes (BLMs). Upon ultrasonification of an aqueous DDAB dispersion, single- and multiwalled vesicles with a layer ˚ have been found [108]. It is imthickness of 30–50 A portant to make a distinction between liquid crystalline mesophases and bilayer membranes. The viscosity and stability of mesophases originate from intermicellar forces, that is, lattice forces. In contrast, a bilayer membrane should be able to maintain its structural integrity without relying on lattice forces. The presence of lamellar multilayer mesophases therefore does not warrant the formation of isolated bilayer membranes. Their formation requires a self-assembling ability greater than that of liquid crystalline dispersions. The structural elements used in a systematic survey of the aggregation behavior of surfactants or amphiphiles are displayed in Fig. 14a. These elements include the hydrophobic tail and hydrophilic headgroup as well as a spacer moiety and a connector that allows connecting two or more hydrocarbon chains to one headgroup. In Fig. 14b and c, examples of double-chain surfactants having cationic ammonium heads; anionic sulfate, phosphate, or carboxylate heads; and nonionic oxyethylene headgroups are shown together with examples of zwitterionic headgroups and some of the connectors used in the survey. Despite their different compositions, all of these surfactants have the ability to aggregate in water to bilayer membranes, either open BLMs in the form of lamellae or closed structures in the form of vesicles and liposomes, when both alkyl chains are at least 10 carbon atoms long [86]. To probe the packing parameter concept and its usefulness in predicting BLM formation, surfactants with three, four, and seven hydrocarbon chains have been prepared [109–111]. The large volume of the hydrocarbon part should force the molecules into a lamellar or even inverted bilayer structure. However, the critical micelle concentrations (cmc) of the triple-chain surfactants shown in Fig. 15a are close to those found for doublechain compounds, suggesting that the third chain has only a little effect on the aggregation behavior in water. More important is the influence of spacer and connector structures on the aggregate morphology. All triple-chain compounds form bilayer membranes except for the tridodecylmethylammonium bromide, which has no structural element that orients the three alkyl chains. The space-filling model for this surfactant


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FIG. 14 (a) Structural elements of bilayer-forming amphiphiles. (b) Examples of double-chain surfactants with cationic, anionic, and nonionic headgroups that form bilayer membranes (lamellae and/or vesicles). Note the surfactant with two acyl chains and two carboxylate heads, connected by a single C — C bond, which carries the structural element of a gemini surfactant. (c) Examples of zwitterionic headgroups and connectors used in the synthesis of double-chain surfactants. (Adapted from Ref. 86.)

clearly shows rather disordered hydrocarbon chains close to the ammonium atom because of its tetrahedral configuration (Fig. 15a). The triple chains of the other surfactants are well aligned because of the presence of ester connectors, thus allowing the ammonium head to protrude into the surrounding water layer without conformational constraints. This order requirement and the finding that these triple-chain surfactants show endo-

thermic order-disorder transitions in their DSC thermograms upon heating indicate that the hydrocarbon chains are not in the fluid state as required for the packing parameter concept [109]. The same observations hold true for the four-chain ammonium bromides used in the formation of bilayer membranes. The four hydrocarbon chains are connected via ester functions to glutamic acid and lysine residues. The presence of sev-

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FIG. 15 (a) Chemical structures and space-filling models of triple-chain surfactants used to form bilayer membranes. Note the increasing packing order of hydrocarbon chains in the models going from left to right. (Adapted from Ref. 108). (b) Chemical structures of four-chain surfactants and electron micrographs of vesicles and tubules formed by them in water. Bars = 200 nm. (From Ref. 110.)

eral amide groups allows the formation of stabilizing hydrogen bridges as mentioned earlier for single-chain surfactants containing a maleic acid moiety. The aggregation behavior of the four-chain compounds is thus based not solely on isotropic repulsive and attractive forces but to some extent also on anisotropic attractive

interactions. Both compounds aggregate in water to form vesicular and tubular structures (Fig. 15b) [110]. The seven-chain ‘‘heptopus’’ surfactant lacks any ability to form curved structures but is used to form ordered monolayer arrays at the air-water interface [111]. An interesting family of surfactants for which the


packing parameter concept is hardly suitable to describe their aggregation behavior consists of ‘‘gemini’’ surfactants. Geminis are dimeric single-chain surfactants usually connected by an alkyl spacer below the headgroup region; that is, they consist of two hydrocarbon chains and two headgroups. Most gemini surfactants aggregate in water to form micelles. For a review of geminis and related surfactant oligomers refer to the contribution by Martin In in Part 1 of this book. Only two examples of bilayer membrane–forming gemini surfactants are presented here. The first example describes the aggregation behavior of a dianionic gemini. The connection of two octadecyl (C18) chains and two phosphate headgroups via tetrol connectors derived from erythritol and tartaric acid results in the formation of optically active and meso gemini surfactants. These diphosphate surfactants aggregate in water at pH 7 to form planar bilayer membranes, which rearrange upon ultrasonication into unilamellar vesicles. The vesicles have diameters of 15–25 nm (S,S and R,R) and 50– 100 nm (R, S) and consist of intercalated bilayers with

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˚ . The addition of Ca2⫹ a wall thickness of 38 ⫾ 2 A ions triggers fusion of the (R,R) and (S,S) vesicles but fission and eventually tubule formation of the (R, S) vesicles. The wall thickness of the (R, S) aggregates in˚ , indicating a nonintercalated bicreases to 66 ⫾ 1 A layer membrane (Fig. 16a). This surprisingly different behavior of the optically active and meso surfactants is explained by intermolecular versus intramolecular interactions with the Ca2⫹ ions. Calcium-mediated intermolecular interactions between phosphate groups of adjacent molecules stabilize large surfaces of low curvature, thus favoring large vesicles. Intramolecular interaction, that is, complexation of Ca2⫹ by the two phosphates of one surfactant molecule, screens the charge and reduces the headgroup area at the interface to water, thus triggering the rearrangement of the molecules into nonintercalated bilayers and subsequently destabilizing the vesicles in favor of smaller aggregates. [112]. The second example employs a didodecyl (diC12) gemini surfactant with one cationic ammonium head

FIG. 16 (a) Chemical structure of the diphosphate gemini surfactant and electron micrographs of (A) small (S,S) vesicles immediately after addition of Ca2⫹; (B) fused large vesicles after 2 h; (C) 50–100 nm large (R,S) vesicles before addition of Ca2⫹; (D) small vesicles caused by fission after 30 min; and (E) tubules formed after 3 days. BarAB = 100 nm; BarC–E = 250 nm. (Reprinted with permission from Ref. 112. Copyright 1997 American Chemical Society.) (b) Chemical structure of the ammonium and carboxylate double-headed gemini surfactant and phase-contrast optical micrographs of giant vesicles, tubules, and filaments formed in water. Bar = 50 ␮m. (Reprinted with permission from Ref. 113. Copyright 1996 American Chemical Society.)

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and one anionic carboxylate head. Upon hydration of the dry surfactant film, the gemini monomers aggregate in water to form giant vesicles, tubules, and filaments that can be observed by phase-contrast optical microscopy (Fig. 16b). The giant vesicles are stable over weeks at room temperature but can easily be destroyed at pH 3 by hydrolysis of the C — —N double bond within the — CH2CONHN — —CCH2CH2 — spacer unit. The formation of stable bilayers can be explained by back folding of the spacer into the hydrophobic membrane region, thus bringing both headgroups close together. The molecules then assume a near-cylindrical shape wherein the cross-sectional area of the double headgroup is slightly larger than that of the alkyl chains. Such a shape is appropriate for the formation of bilayer membranes [113]. Both examples indicate the difficulties that arise from using the packing parameter concept. In the first example, the interaction with Ca2⫹ ions is more influential in the packing of molecules within the bilayer than the geometry of the single molecules. In the second example, the not so obvious (and not so predictable) back folding of the spacer unit determines the molecular shape and thus the curvature of the aggregates, which actually covers a wide range as one can see from Fig. 16b. The biologically most important and most often studied double-chain molecules with charged, neutral, or zwitterionic headgroups are phospholipids. Several reviews are available; therefore, the discussion of their phase behavior presented here will be short [114–127]. Phospholipids aggregate at temperatures below the melting temperature Tc of the hydrocarbon chains into lamellar gel phases consisting of hexagonally ordered chains with disordered headgroups. Depending on the tilt the chains have with respect to the layer normal, these phases are denoted L␤ (no tilt) or L␤⬘ (tilted). The L␤ phase is actually a sequence of three separate phases, differing in the azimuthal angle ␾ of the tilt direction with respect to the underlying hexagonal chain lattice. In the low-hydration L␤F phase, the tilt is directed toward a face of the hexagonal net (␾ = 0⬚), whereas the high-hydration L␤I phase the tilt lies toward the nearest neighbor chain (␾ = 30⬚). The L␤L phase in between both has azimuthal angles ␾ that continuously vary between 0⬚ and 30⬚. Phospholipids with a large mismatch between the cross-sectional areas of the hydrated headgroups and the hydrocarbon chains often form an interdigitated L␤I phase. The formation of a rippled lamellar phase (P␤⬘) is observed in the phase diagram of saturated phospholipids at temperatures close to the L ␤⬘-to-L ␣ phase transition. The ripples are asymmetric, have a periodicity of the order of 15–

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20 nm, and there is a phase shift in the ripple pattern from layer to layer producing a two-dimensional oblique lattice. Ripples usually form in a cooperative manner at a pretransition temperature Tp . The main reason for the rippling of lipid bilayers is the tendency of the polar headgroups to achieve a certain degree of fluidity and hydration while the hydrocarbon chains remain ordered. Phospholipids, consequently, undergo a pretransition only if the polar headgroups are sufficiently hydrophilic and hydrated and if the interchain packing is sufficiently weak. At least 12 ⫾ 2 water molecules must be associated with each headgroup for a bilayer undulation to be feasible [122,123]. Another two-dimensional modulated phase, the ‘‘hats and saddle’’ or ‘‘egg carton’’ structure, has attracted theoretical and experimental attention [128– 131]. Above the chain melting temperature Tc , the chains form the normal lamellar L␣ phase (Fig. 17a). Diacyl phospholipids tend not to form the hexagonal HI phase, whereas the reverse hexagonal HII phase is very common in phospholipids having small, weakly hydrated headgroups and attractive head-head interactions. As an example, the partial phase diagrams of dipalmitoylphosphatidylcholine (DPPC) and dipalmitoylphosphatidylethanolamine (DPPE) in water are displayed in Fig. 17b. DPPE has a less hydrophilic headgroup than DPPC, causing a smaller L␣ phase for this lipid. For a similar reason, the gel phase is metastable, the ripple phase P␤⬘ is not observed, and the reverse hexagonal HII phase is very prominent in the phase diagram of DPPE [114]. The main determinant of the phospholipid phase behavior is not so much the geometrical shape of the molecules but the type of hydrocarbon chains because of the strong chain dependence of the melting entropy. Increasing the chain length thus causes all transition temperatures at which the interfacial packing density decreases to become higher. The transition enthalpy and entropy increase with the chain length in an approximately linear manner. The more polar a given lipid, the stronger is this length dependence. Chain unsaturation and branching effectively decouple the parts of the hydrocarbon chain on either side of the double bond or the branching point, and the longest parallel segment of the chain determines the chain melting temperature Tc . These chain modifications thus reduce the length of parallel, strongly interacting chain segments and mimic the consequences of chain shortening. This effect is approximately 50% weaker in a trans than in a cis configuration. Increasing the number of double bonds per chain causes only a small further decrease of Tc . Asymmetry between the hydrocarbon chains has


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FIG. 17 (a) Chemical structure of dimyristoylphosphatidylcholine (DMPC), the temperature-humidity phase diagram of DMPC showing the gel phases and the L␣ phase above the chain melting temperature Tc, and cartoons of the L␤, L␤⬘, and P␤⬘ phases. For details see text. (Adapted from Ref. 132 and 133.) (b) Partial phase diagram of dipalmitoyophosphatidylcholine (DPPC) and -ethanolamine (DPPE). For details see text. Lc and Lc⬘ denote crystalline phases; L␤ and L␤⬘ stand for lamellar gel phases with untilted and tilted hydrocarbon chains, respectively; P␤⬘, P␦, and Q␣ denote rippled, ordered ribbon, and cubic phases, respectively; L␣ and HII stand for lamellar fluid and reverse hexagonal mesophases, respectively. (Adapted from Ref. 114.)

mainly the same consequence. Tc decreases with increasing asymmetry unless the hydrocarbon chains interdigitate in the gel phase, which results in an increase of the chain melting phase transition enthalpy by approximately a factor of 2. Finally, the chain attachment to the glycerol backbone also affects the phase behavior. The melting temperatures of dialkylphospholipids (ether bond) compared with those of diacylphospholipids (ester bond) at 1–5⬚C higher [122]. Apart from the hydrocarbon chains, the most decisive factor for the phase behavior of phospholipids is

the lipid polarity. Phospholipids at high pH, which as a rule are at their maximum polarity, respond more strongly to headgroup variations than do lipids at low pH. Other factors such as the ionic or zwitterionic character, or the size of the headgroups, play a much smaller role. In general, the thermodynamic significance of each headgroup and its interactions with neighboring headgroups and water molecules increases with the relative hydrophilicity of the polar residues and with the degree of unsaturation of the hydrocarbon chains. For example, unsaturated or short-chain phos-

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phatidylcholine and phosphatidylglycerol, which belong to the most polar phospholipids, are more sensitive to headgroup effects than saturated or long-chain analogues or the less polar phosphatidylserine, phosphatidylethanolamine, or phosphatidic acid. Deprotonation of phospholipids always increases the lipid’s polarity and thus its sensitivity to headgroup effects. The method used to achieve this is unimportant, whether it is done by increasing the pH, by replacement of lipidbound protons by other ions or chemically bound methyl groups, or by breaking interlipid hydrogen bonds. All methods cause qualitatively similar thermodynamic effects, e.g., they lower the chain melting temperature. The Tc of nearly all common phospholipids steadily decreases with increasing pH of the suspending solution and increases during acidification. The influence the headgroup size has on the stability of the bilayer membranes is less important than is often believed. This factor is of significance only when the size variations are crucial for the interlipid bonding patterns. DPPC analogues, for example, that have minimal direct interactions between the PC headgroups all melt between 40 and 44⬚C regardless of the alkyl chain lengths between phosphate and ammonium groups. On the contrary, the melting temperature of various phosphatidylethanolamines decreases considerably with increasing headgroup length. However, the decrease is highly nonlinear, indicating the significance of direct head-head interactions [122,134,135]. Although the phase behavior of phospholipids clearly follows certain rules, the observations described so far give strong evidence that geometrical considerations based on the molecular shape are insufficient to explain these observations and predict the phase behavior. The following examples describe phospholipids whose hydrocarbon chains have been modified, thus effecting the geometrical shape of the molecules and their hydrophile-lipophile balance. In general, it has been found that a small nonpolar substituent located at the beginning or the end of one or both acyl chains of a saturated phosphocholine has only a modest effect on the phase transition temperature Tc but has a substantial effect on Tc when placed in the middle of the chain. In contrast, a polar substituent (e.g., a keto group) has an only modest effect on Tc regardless of where it is positioned along the acyl chains [135]. To prove these observations further and to test the effect substituents have on the aggregation behavior of phosphocholines, distearoylphosphocholine (DSPC) has been modified by placing a dimethylketal group at the beginning, middle, and end of one octadecanoyl chain and by placing a vic-diol group in the middle of a C18 chain (Fig. 18a).

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The ketal groups of adjacent chains can participate in dipole-dipole interactions, while the diol groups can interact via stronger hydrogen bonds. Nevertheless, all four compounds form vesicles of size distributions comparable to that found for the parental DSPC (27 ⫾ 3 nm). The phase transition temperature, however, changes from 55.1⬚C for DSPC to 48.5, ⫺15.8, and 53.2⬚C for compounds with the ketal group at the beginning, middle, and end of the C18 chain. These changes are similar to those found after incorporation of a methyl group into the C18 chain, although the ketal group is larger than methyl and contains C — O bonds. The presence of the vic-diol lowers the phase transition temperature moderately to 46– 49⬚C as compared with DSPC and thus behaves similarly to a midchain keto group but enhances the transition enthalpy ⌬H considerably from 42.3 to 67 kJ/ mol. This effect has been attributed to the stabilization of the bilayer membranes by interchain hydrogen bonds, which are absent in keto groups. The results obtained with the dimethylketal and vic-diol compounds are in accord with the ‘‘statistical bend’’ model for phosphocholine bilayers that assumes the development of a critical bend near the center of the chains on going from the gel to the liquid crystalline state of the bilayer. Substituents near the center of one or both acyl chains can stabilize this bend, whereas those near the headgroup or the end of the chains have little effect. Stabilization of the bend results in lower Tc and ⌬ H values [137]. However, it depends on the individual structure of a midchain polar substituent to which extent it stabilizes the bilayer; this is how much it lowers ⌬H. In the second example, the two hexadecanoyl chains of DPPC have been exchanged by either one or two phytanyl chains or by one phytanyl and one eicosyl (C 20) chain. Phytanyl chains, having four methyl groups in the 3, 7, 11, 15-positions distributed along the C16 chain, are bulkier than their unsubstituted analogues. All chains are connected to the glycerol backbone via ether bonds instead of ester bonds to improve the molecules’ temperature stability (Fig. 18b). Despite the presence of bulky phytanyl chains and a longer C 20 chain, all three molecules aggregate in water to form stable unilamellar vesicles with diameters of 20–100 nm, which is a size distribution close to that found for DPPC vesicles in a control experiment. What has changed, however, are the phase transition temperature Tc and the stability of the bilayer membranes against leakage of 5(6)-carboxyfluorescein and sodium chloride. The chain melting temperature Tc in the case of DPPC is 41⬚C, whereas the corresponding phase transition for diPhyPC, C16 PhyPC, and C 20PhyPC occurs


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FIG. 18 Chemical structures of (a) phosphocholines carrying a dimethylketal in the beginning, middle, and end of one C18 chain and a vic-diol in the middle of one C18 chain (adapted from Ref. 136); (b) phosphocholines with one and two 3,7,11,15tetramethyl C16 (phytanyl) chains and cone C20 chain replacing linear C16 chains (adapted from Ref. 138); (c) unnatural phosphocholines with acyl and alkyl chains in 1,3-position along the glyceryl backbone (adapted from Ref. 139) and trimethylammonium bromide with acyl chains in 3,6-position at a carbozole connector and a transmission electron micrograph of the vesicular bilayers formed in water; bar = 100 nm (from Ref. 140).

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below ⫺30⬚C and around ⫺11⬚C for the two chimeric lipids. DPPC vesicles having their bilayer membranes in the gel state are stable against leakage of dyes and ions but become leaky at higher temperatures. DiPhyPC vesicles, on the other hand, are stable up to 70⬚C but have slight leakage even at room temperature. The chimeric lipids C16 PhyPC and C 20PhyPC combine the positive features of both compounds; they are stable upon heating to 70⬚C and they do not have a slight persistent leakage at room temperature [138]. Another way to change the cross-sectional area of the hydrocarbon chains involves the use of 1,3-diacylrac-glycero-2-phosphocholines and their 1,3-dialkyl analogues instead of natural 1,2-disubstituted phosphocholines (Fig. 18c). Nature’s preference for 1,2-disubstituted phospholipids could suggest a superior packing behavior of these compounds to form stable bilayer membranes compared with the unnatural 1,3derivatives. The bilayer properties of 1,3-phospholipids have been examined thoroughly using electron microscopy, differential scanning calorimetry, substrate entrapment, ion permeation across the bilayer, and phase separation. All 1,3-derivatives aggregate in water to form stable bilayer membranes in essentially the same way as natural phospholipids. The 1,3-diacyl phosphocholines form preferably multiwalled vesicles and to a small extent (ribbonlike) lamellae, whereas the 1,3dialkyl compounds form flattened vesicles and/or the ribbon structure [140]. It has also been reported that some 1,3-phospholipids tend to form a viscous solution after ultrasonication above Tc and cooling to ambient temperature. X-ray diffraction studies of 1,3-ester and 1,3-ether phosphocholines give evidence that the bilayer membranes consist of at least partly interdigited molecules (L␤I phase) [141,142]. The hydrocarbon chain length does not change the aggregate structure significantly. The phase transition temperature and enthalpy of 1,3-phospholipids are in close range with those of the 1,2-analogues. Similar observations have been made for the remaining comparisons. The somewhat surprising results of the study establish that 1,3-phospholipids form bilayers whose physicochemical characteristics are essentially the same as those of the natural 1,2-phospholipids, regardless of the hydrocarbon cross-sectional area [139]. The two acyl chains are spread even further apart using a carbazole connector in a related study of the aggregation behavior of a trimethylammonium surfactant. Nevertheless, the double-chain surfactant aggregates to closed bilayer membranes in form of singleand multiwalled vesicles with a size distribution of 20– 200 nm (Fig. 18d) [140].

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Fluorination as a way to change the hydrophile-lipophile balance has been applied to phospholipids as well. Phosphocholine and ethanolamine lipids having one or two perfluoro or partly fluorinated acyl and alkyl chains in 1,2- and 1,3-positions along the glyceryl backbone generally display a behavior similar to that of the hydrocarbon analogues. They form unilamellar vesicles with diameters between 50 and 100 nm regardless of the number of fluorinated chains or the 1,2versus 1,3-position or glycerol. The slow conversion of vesicles into ribbonlike structures at room temperature is observed only for 1,3-lipids with a fluorinated tail on both hydrocarbon chains and a chain length of at least 17 carbon atoms. No interdigitation has been found in the bilayers of fluorinated lipids. A marked contrast in the phase behavior of fluorolipids and their hydrocarbon analogues is the large half-width of the chain melting transition peak in the DSC thermograms. The longer the CF2 tail, the lower the cooperativity of the phase transition and the wider its temperature range. The impact of an ester or ether connection is insignificant in most cases. Ether phospholipids whose hydrophobic chains are ended by a CF6 or CF8 tail, however, display Tc values 6–9⬚C lower than those of their corresponding ester analogues, the opposite behavior to that found for hydrocarbon esters and ethers. In the case of the hydrocarbon lipids, the different behavior is explained by closer packing of the ether chains owing to the absence of the carbonyl groups. The higher attractive interaction between the alkyl chains thus outweighs the loss of intralayer stabilization by hydrogen bonds involving the carbonyl groups. The larger cross-sectional area of the CF6 and CF8 tails prevents such closer chain contact, and the presence or absence of carbonyl hydrogen bonds becomes decisive. The thermodynamic parameters of 1,2- and 1,3-disubstituted phospholipids are essentially the same, paralleling the trend found for the hydrocarbon analogues. A more detailed evaluation of the thermodynamic parameters reveals their dependence on the number of fluoro chains, their length, and the degree of fluorination within the chains. Replacement of one hydrocarbon chain by its perfluorinated equivalent results in a decrease of Tc , whereas Tc increases with the length of the CF2 segment for a given CH2 spacer. In addition, the degree of fluorination has a larger impact on Tc than the overall length of the chain. The phase behavior of phospholipids with fluorinated segments in both chains follows less straightforward trends [92,143]. Besides these rather minor differences, the aggregation and phase behavior of double-chain fluoro compounds seem to be much less affected by a hydrocarbon-fluo-


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FIG. 19 (a) Chemical structures, space-filling models, and electron micrograph of 1,2- and 1,3-disubstituted double-chain diester phosphate surfactants. The micrograph shows left-handed helices of the 1,3-isomer. Bar = 500 nm. (From Ref. 144.) (b) Chemical structures and electron micrographs of 1,2- and 1,3-disubstituted phosphate surfactants with ester and ether connections. Note the helices of the 1,2-isomer and the fiber bundles of the 1,3-isomer. Bars = 1000 nm and 500 nm. (From Ref. 144.) (c) Chemical structure of a double-chain histidine surfactant and electron micrographs showing long fibers of the protonated surfactant at pH 2.5 and boomerang structures formed in the presence of copper triflate (ratio 1 : 4). Bars = 250 nm, 1 ␮m, and 250 nm. (From Ref. 145.)

rocarbon replacement as observed for single-chain fluoro surfactants. This section ends with the presentation of three examples of structures generated by self-aggregation of double-chain surfactants based on directed anisotropic interactions in the form of amide hydrogen bonds and metal coordination. Contrary to the almost identical ag-

gregation behavior of 1,2- and 1,3-disubstituted hydrocarbon and fluorocarbon phospholipids, the first two examples demonstrate remarkable differences between both substitution patterns when the aggregate structure is determined by amide hydrogen bonds. The two double-chain phosphates displayed in Fig. 19a are obtained after reaction of the appropriate N-acylated aziridine

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with dibenzyl phosphate and subsequent debenzylation. Both compounds have an (R) configuration but differ in the position of the phosphate and amide groups along the backbone. The 1,2-disubstituted compound aggregates in water to form planar structures, whereas the 1,3-diacyl isomer produces left-handed helical strands coagulated to ropelike structures. The single strands of the rope appear to be tubules with a diameter of 22 nm. X-ray powder diffraction experiments re˚ for both vealed a repetitive distance of 40 and 46 A compounds, indicating interdigitated molecular packing within the bilayers. Replacement of the ester bound C4 chains by ether bound phenyl rings results in a pair of 1,2- and 1,3-isomers, which again show quite different aggregation behavior. The 1,2-derivative forms vesicles with diameters of 500–1000 nm when dispersed in water at pH 6.5. These vesicles slowly rearrange to form ribbons containing interdigited bilayer membranes. After protonation of the phosphate groups at pH 2.5, however, the ribbons start to twist and form left-handed helices, which ultimately transform into tubular structures. The 1,3-derivative, on the other hand, aggregates directly into coagulated fiber structures with interdigitated membranes that are stable for at least a week (Fig. 19b) [144]. The long-chain histidine derivative presented in the third example is insoluble in water. After protonation of the headgroup at pH 2.5, the double-chain histidine aggregates to form very long thin fibers, some showing a right-handed twist, which assemble side by side to yield bundles. In a 1:4 mixture with copper triflate, boomerang-like scrolls were generated (Fig. 19c). The boomerangs are of different thickness but all show lefthanded twists. Boomerang formation has been suggested to start by stretching and twisting at opposite sides of vesicle membranes, resulting in a thickened center and thin twisted ends of the boomerang. Eventually the boomerangs become thinner and also show the helical twist at the center region. This model was derived from the spiral growth of protoplasts induced by the action of fusicoccin. In case of the histidine derivative, the coordination of the copper ions is the driving force behind the formation of this interesting structure [145]. Packing parameter concepts based on the molecular geometry will fail to predict any of these aggregation behaviors in a reliable way. IV.

PHASE BEHAVIOR OF MIXTURES OF SURFACTANTS

The phase behavior of mixed surfactant systems has been reviewed [14,15,115,119,121,146]. Some exam-

ples will be presented that allow drawing some conclusions about the importance of the molecular geometry in describing and modeling mixed systems. Equimolar mixtures of oppositely charged single-chain surfactants aggregate in water to planar layers because of electrostatic attraction between headgroups in addition to van der Waals attraction between hydrocarbon chains. The critical aggregation concentration (cac) of mixed cationic dodecyltrimethylammonium bromide (DTAB) and anionic sodium dodecyl sulfate (SDS), for example, is about two decades in concentration lower than the cmc of the pure components for a wide range of mixing ratios [147]. It has been generally observed that for a hydrocarbon chain length longer than C8 for both cationic and anionic surfactants, the equimolar catanionic mixture is practically insoluble in water, and the phase diagram is dominated by the formation of a lamellar liquid crystalline phase in the water-poor region of the surfactant-water system. Equimolar mixtures of surfactants having C8 hydrocarbon chains form precipitates at very high water contents, which redissolve to form stable vesicle and micellar solution phases upon addition of an excess amount of one of the parent compounds. A more interesting phase behavior appears at nonequimolar mixtures of oppositely charged surfactants. The binary phase diagrams of cationic dodecyltrimethylammonium chloride (DTAC), anionic sodium nonanoate (SN), and the catanionic mixture in water at 40⬚C as well as the pseudoternary phase diagram of this system are displayed in Fig. 20. It can be seen from Fig. 20a that the DTAC surfactant forms the wellknown sequence of mesophases with increasing surfactant concentration: micellar solution (L 1), micellar cubic phase (I), hexagonal phase (H), bicontinuous cubic phase (V), and lamellar phase (L␣). On the contrary, the phase behavior of SN is rather simple. The system forms a micellar solution followed by a hexagonal phase with a limited stability range. There are two important differences between the phase behavior of the catanionic mixture and that of the parent surfactants. First, the only mesophase found is the lamellar L␣ phase; phases of higher curvature are absent. Second, the extension of the solution phase (L1) is larger for the catanionic system (total surfactant concentration 47 wt%) than for the cationic (43 wt%) and anionic (37 wt%) surfactant systems under identical conditions [148]. The isothermal pseudoternary phase diagram DTAC-SN-D2O at 40⬚C is shown in Fig. 20b. The triangle sides correspond to the different binary axes; thus the bottom side corresponds to the SN-water system,


FIG. 20 (a) Binary phase diagrams of DTAC-water, SNwater, and the catanionic mixture–water systems at 40⬚C. Blank areas correspond to two-phase regions. (b) Pseudoternary DTAB-SN-2H2O system at 40⬚C. Notations are as follows: L1 isotropic solution; H1 DTAC-rich hexagonal phase; H2 SN-rich hexagonal phase; I micellar cubic phase; V bicontinuous cubic phase; and L␣ lamellar phase. (Adapted from Ref. 148.)

and the left and right ones correspond, respectively, to the DTAC-water and DTAC-SN systems. Mixtures above the equimolar line are rich in DTAC, whereas samples below the line are rich in SN. The phase diagram contains an extended water-rich isotropic solution and five single liquid crystalline phases (two normal hexagonal phases, one lamellar phase, and two cubic phases) and one large region of hydrated surfactant crystals. It should be noted that the mixed system does not form any new phases, but the phase formed by one parent surfactant-water system can solubilize the other surfactant. For example, adding anionic SN to the micellar solution of DTAC results in micellar growth, and large asymmetric micelles (e.g., wormlike or rodlike) are found at the 1:1 molar ratio. Upon further addition

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of SN, a second aggregate species appears in addition to the asymmetrical micelles that is identical to the spherical micelles of pure SN [148]. In dilute aqueous mixtures of dodecyltrimethylammonium bromide (DTAB) and sodium dodecyl sulfate (SDS) at total surfactant concentrations below 5 wt%, the water-rich corner of the pseudoternary phase diagram displays an even more diverse phase behavior (Fig. 21a). A clear and colorless two-phase region consisting of an isotropic liquid and a crystalline precipitate (I ⫹ S) dominates the DTAB-rich side of the phase diagram. This two-phase region gives way to a micellar solution when the total surfactant concentration is greater than the cmc for the majority component (e.g., cmcDTAB = 0.46 wt%). The SDS-rich side of the phase diagram shows a narrow one-phase lobe at a mixing ratio of 35:65 CTAB to SDS, which appears bluish to the eye and contains large (>200 nm) and polydisperse vesicles. A two-phase region containing vesicles and precipitate (V ⫹ S) is located between the equimolar mixture and the vesicle phase. Samples prepared at mixing ratios between the vesicle and micellar phases are viscoelastic at lower concentrations and turbid and birefringent at higher concentrations. This might be a multiphase region or a metastable dispersion. When the total surfactant concentration is greater than the cmc for SDS (cmcSDS = 0.23 wt%), the SDS-rich micellar phase appears. Because of the formation of the 1:1 precipitate, the DTAB-SDS-water mixture yields five components: DTAB, SDS, NaBr, DTA⫹DS⫺, and water. A consistent picture of the micelle-to-vesicle transition emerges from combined time-resolved fluorescence quenching (TRFQ), video-enhanced differential interference contrast microscopy (VEM), and cryo-transmission electron microscopy (cryo-TEM). SDS-rich micelles grow to an aggregation number ratio of 20:80 DTAB to SDS with increasing DTAB concentration. Further increase of the DTAB concentration results in the formation of long rodlike micelles, which abruptly transform into large and polydisperse vesicles above a certain DTAB limit [149]. The very similar geometrical shape of both singlechain surfactants, having linear hydrocarbon chains of the same length (C12), fosters the molecular packing into lamellar aggregates. The phase behavior is therefore dominated by the formation of crystalline precipitate and polydisperse vesicles with low curvature. The tendency to form precipitates increases with the length of the hydrocarbon chains, as has been found studying the aggregation behavior of mixed alkylammonium chlorides and sodium alkyl sulfates with decyl, dodecyl, and tetradecyl chains [150]. A mismatch between

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FIG. 21 (a) Water-rich corner of the pseudoternary DTABSDS-water at 25⬚C. One-phase regions contain micelles (M) or vesicles (V), two-phase regions (shaded) consist of either clear liquid and preciptate (I and S) or vesicles and precipitate (V and S); the dark shaded region is viscoelastic and of unknown composition. (Adapted from Ref. 149.) (b) Pseudoternary phase diagram of CTAB-SOS-water at 25⬚C. The one-phase regions represent SOS-rich vesicles (V) and micelles (M), and CTAB-rich rodlike micelles (R); shaded twophase regions consist of CTAB-rich rodlike micelles and vesicles (R ⫹ V), SOS-rich vesicles and lamellar phases (V ⫹ L␣), and an isotropic liquid with precipitate along the equimolar line. Very small amounts of turbid clouds form in the SOS-rich vesicle lobe above the dashed line. (I) represents an unresolved multiphase region. (Adapted from Ref. 151.)

the hydrocarbon moieties of both surfactants should thus reduce the stability of the precipitates and improve vesicle formation. This assumption has been confirmed by replacing DTAB by cetyltrimethylammonium bromide (CTAB) and SDS by sodium octyl sulfate (SOS). Although the molecular geometry of CTAB (C16) and SOS (C8) remains the same as that of DTAB (C12) and

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SDS (C12), the interchain interactions and packing properties between CTAB and SOS have changed. As expected, vesicles form spontaneously over a wide range of compositions of the pseudoternary CTABSOS-water mixture in both CTAB-rich and SOS-rich solutions, creating a vesicle phase much larger than the one observed in the DTAB-SDS-water mixture (Fig. 21b). Moreover, the vesicles are unilamellar and less polydisperse. The bilayer properties of the vesicles depend on the ratio of CTAB and SOS, with CTAB-rich bilayers stiffer than SOS-rich ones. Whenever the hydrocarbon chain length is unequal, the extent of the vesicle lobe is largest for mixtures rich in the shorter tailed surfactant, as apparent from Fig. 21. The close packing of vesicles sets the limit of the vesicle phase. Close packing will occur at lower concentrations when the vesicles are large. Above this concentration, the surfactants form a multilamellar phase. Two modes of transition between micelles and vesicles have been identified. The first one in CTAB-rich solutions and SOS-rich solutions at higher SOS concentrations occurs between rodlike micelles and vesicles. It is first order and results in macroscopic phase separation. The second mode of transition occurs in SOS-rich mixtures at low SOS concentration and exhibits no phase separation. Instead, small micelles abruptly transform into vesicles over a narrow range of surfactant concentration. It should be noted that these vesicles represent a thermodynamic stable phase because they form under thermodynamic control [151]. Other mixtures of surfactants with mismatching hydrocarbon parts, for example, cetyltrimethylammonium tosylate (CTAT) and sodium dodecylbenzenesulfonate (SDBS), show a similar low tendency to form crystalline precipitates in favor of stable vesicles with high curvature [152,153]. Replacement of bromide by chloride in the system dodecyltrimethylammonium chloride (DTAC) and sodium dodecylbenzenesulfonate (SDBS) results in two remarkable observations. First, the transition from micelles to vesicles happens continuously in mixtures of DTAC and SDBS. This is in contrast to the abrupt firstorder transition observed in the other mixtures discussed earlier. There is no observable two-phase region separating the phases containing micelles and vesicles. Second, the vesicle phase is significantly smaller as in the presence of bromide. As mentioned earlier, the extent of the vesicle lobe appears to be set by the condition of close packing of vesicles. In the presence of strong intervesicle interactions, the limiting packing density of vesicles is reached at a comparatively low surfactant concentration, thus limiting the size of the vesicle phase. Chloride ions are more hydrated than


bromide ions and therefore less effective in shielding the charge of the vesicles. It is likely that the lower shielding leads to the observed size reduction of the vesicle lobe [154]. The prominent role electrostatic interactions play in the phase behavior of oppositely charged surfactants becomes evident when the charge distribution is changed by addition of a monovalent salt. For example, the addition of 5 wt% sodium bromide to a sample containing 2 wt% of a 3:7 weight ratio mixture of CTAB and SOS destabilizes the vesicle phase and leads to micelle formation. The addition of salt results in an increased insertion of SOS monomers into the vesicle surface, thereby increasing the surface charge and triggering the reorganization of the mixed surfactants to form smaller, more curved micelles. This assumption has been verified by contrast variation in small-angle neutron scattering (SANS) experiments [155,156]. Not only vesicle formation but also the formation and composition of mixed micelles strongly depend on composition and electrostatic condition of the surfactant mixture. For example, cationic surfactants have a greater tendency to be incorporated into mixed micelles than anionic ones. This has been attributed to either differences in micellar size or differences in the interaction between headgroups and counterions. Consequently, one can find rodlike micelles on one side of the phase diagram but spherical ones on the other side [150,151]. The formation of unusual disklike micelles in equilibrium with a lamellar L␤ phase has been observed. The crucial requirement for obtaining highly stable colloidal solutions and nanodisk self-assembly is a high osmotic pressure induced by unscreened electrostatic repulsion. This condition is met in pure catanionic surfactant solutions that contain only recombining H⫹ and OH⫺ counterions plus counterions of the component in excess. Mixing anionic myristic acid (C13H27COOH = MA) and an excess of cationic cetyltrimethylammonium hydroxide [C16H33N⫹(CH3)3 OH⫺ = CTAOH] in carbonate-free water results in the formation of a lamellar phase with the hydrocarbon chains in the frozen state (L␤) and the formation of large disklike aggregates with diameters of 2–3 ␮m. The size of the dispersed disks decreases from 3 mm to 30 nm when the positive surface charge increases by decreasing the molar ratio of MA to CTAOH from 0.45 to 0.39. The nanodisk formation requires ion pairing on planar faces coexisting with highly curved interfaces forming the edges. Therefore, part of the excess cationic surfactants form the edges of the disk. The final size is a balance between the entropy of mixing and electrostatic coupling between disks. Increasing the ex-

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cess charge favors small disks until the phase transition toward wormlike micelles occurs [157]. Contrary to the strong effects the hydrocarbon chain length and symmetry have on the phase behavior of catanionic mixtures, the chemical composition of the surfactant headgroups has been found to have little effect [148]. Furthermore, the same sequence of phases is formed in mixtures of divalent and nonionic surfactants as in mixtures of oppositely charged monovalent surfactants. The general trend is a shift of the individual phase transitions toward higher surfactant concentrations when the total headgroup charge z increases, but the succession of phases with increasing surfactant concentration is not affected to any considerable extent. However, the formation of the micellar cubic phase (I) is strongly favored by a high average surfactant charge [158]. It should be noted that the choice of solvent, H2O versus D2O, seems to have an impact on the phase behavior of (catanionic) surfactants. This observation is important because often the phase behavior is studied using different techniques. Some of them, the most obvious ones being nuclear magnetic resonance (NMR) and SANS-based studies, require the use of D2O instead of H2O. In Fig. 22, pseudoternary phase diagrams of cetyltrimethylammonium tosylate (CTAT) and sodium dodecylbenzenesulfonate (SDBS) in H2O and D2O are shown. The main features of the phase diagrams are generally the same with H2O and D2O, but there are several exceptions. First, the boundary between vesicle and lamellar phases occurs at higher water contents in D2O, resulting in smaller lobes of the vesicle phases. Second, the transition from a single lamellar phase into the multiphase region occurs at lower concentrations of added SDBS in D2O. This observation and the fact that solutions of CTAT in D2O are significantly more viscous than those in H2O suggest more elongated rodlike micelles in D2O. Finally, there is no inversion in the density of the lamellar phase L␣⫺ because D2O has a higher density than H2O [153]. One should thus keep in mind that the determination of surfactant phase diagrams based on techniques that use H2O and D2O in the same study will result in some inaccuracy of the phase boundaries. All of the preceding indicates that the phase behavior of catanionic mixtures is only indirectly related to the geometrical shape of the monomers. The main concern in developing pseudoternary systems with rich phase behavior is the prevention of crystallization. Small changes in the chain length hardly affect the individual geometrical shape but cause large changes in the phase behavior. The mismatch between hydrocar-

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FIG. 22 Pseudoternary phase diagrams for CTAT-SDBS mixtures in (a) H2O at 25⬚C and (b) D2O at 28⬚C. Differences in the phase behavior are not caused by the small temperature difference but by the solvents. Notations are as follows: Onephase regions are CTAT-rich vesicles (V⫹) and rodlike micelles (R), SDBS-rich vesicles (V⫺) and micelles (M); twophase regions are shaded and are V⫹ and CTAT-rich lamellar phase (L␣⫹), V⫺ and SDBS-rich lamellar phase (L␣⫺), R and hexagonal phase (zone I), and an isotropic liquid with precipitate along the equimolar line. There is also an unresolved multiphase region (zone II). (Adapted from Ref. 153.)

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bon tails of cationic and anionic surfactants is thus not as much triggering the formation of aggregates with high curvature as it is allowing these aggregates to form by preventing the competing formation of more stable lamellar aggregates. Chemical structure and charge of the headgroups, on the other hand, may affect the geometrical shape but have almost no input on the phase behavior. Finally, the addition of salt and the choice of solvent clearly change the phase behavior but have no direct impact on the geometrical shape of the molecules. Instead, they change the intermolecular interactions based on hydration and electrostatic forces. Consequently, it is often possible to relate an observed experimental fact to the rather fuzzy packing parameter concept, but it is not possible to predict the aggregation behavior (at best) on a more than qualitative level. The packing behavior is certainly affected by the presence of double-chain surfactants. Pseudoternary mixtures of cationic double-chain surfactant didodecyldimethylammonium bromide (DDAB) and anionic single-chain surfactant sodium dodecyl sulfate (SDS) differ from the catanionic mixtures discussed so far in the tendency to form aggregates of higher curvature because of the larger space requirement of the doublechain moiety. For example, a micellar cubic phase (I) is observed in the DDAB-SDS-water mixture at surfactant ratios at which the single-chain catanionic DTAB-SDS-water system forms a lamellar phase (Figs. 21a and 23b). The binary phase behavior of DDAB and SDS in water is displayed in Fig. 23a. Single-walled vesicles are formed at very low DDAB concentrations and begin to coexist with double-walled vesicles and tubular structures upon increasing the concentration to 0.5 wt%. This region is followed by two lamellar phases, one with high (DI) and the other with low (DII) water content, which coexist within a wide concentration range (DI and DII are also denoted L␣ and L␣⬘ by other authors). The binary phase diagram of SDS is richer, with an isotropic phase (L1) containing spherical micelles with a mean aggregation number of 60–70 at low concentration. With increasing SDS concentrations rodlike micelles appear, followed by a hexagonal phase with long rodlike micelles packed in a hexagonal array. The phase diagram continues with a lamellar phase and crystal formation at high SDS concentrations. The pseudoternary DDAB-SDS-D2O phase diagram displays several interesting features (Fig. 23b). The different regions of the lamellar phases have very different stability ranges. Phase DI, which has a large stability range in the binary DDAB-water mixture, can incorporate only small amounts of SDS before a transition to the L 1 or some other phase is induced. On the con-


FIG. 23 (a) Binary phase diagrams of DDAB-water and SDS-water at 40⬚C with blank areas corresponding to twophase regions. (b) Pseudoternary DDAB-SDS-water phase diagram at 40⬚C, where two- and three-phase regions are approximately as shown. The notations are: L1 isotropic solution; E hexagonal phase; I cubic phase; DI, DII, DIII, DIV lamellar liquid crystalline phases; and GI, GII surfactant crystals. (Adapted from Ref. 159.)

trary, the DII lamellar phase can accommodate very large amounts of SDS. The isotropic solution and hexagonal mesophase found in the binary SDS-water system are subject to phase transitions at rather low concentrations of DDAB in the ternary mixture. Furthermore, the pseudoternary mixture displays a number of phase regions that are not observed in the two binary surfactant-water systems, at least not at the same temperature. This is another difference in comparison with catanionic mixtures based on single-chain surfactants such as the DTAC-SN-water system. These new phase

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regions include two lamellar phases of limited areas of existence, the DIII phase close to the hexagonal phase and DIV phase. Furthermore, there is a wide region of a cubic phase (I) at the center of the phase diagram. Cubic phase samples are clear, optically isotropic, and extremely stiff. Finally, in the water-rich corner of the diagram are two very small separate regions of spontaneous vesicle formation, with an excess of either surfactant (not visible in Fig. 23b). Vesicles formed at the DDAB-rich side of the equimolar line have a mean diameter of 500 nm, which increases with dilution, whereas vesicles on the SDS-rich side have a mean diameter of 260 nm, which seems to be invariant with dilution. At mixtures along the equimolar line, however, precipitation occurs even at very high dilution [159]. The pseudo-triple-chain system DDAB-SDS-water forms only normal and bicontinuous-type aggregates. Replacement of SDS by the anionic double-chain surfactant sodium bis(2-ethylhexyl)sulfosuccinate (AOT) enlarges the hydrophobic volume of the mixture. AOT consists of two branched acyl chains connected via the relatively bulky C4 succinate connector to the small SO⫺ 3 headgroup. This molecular geometry should favor lamellar or even reverse-type mesophases, and, as expected, the binary AOT-water system is dominated by a wide lamellar phase (10–70 wt%) followed by a small bicontinuous cubic phase (73–80 wt%) and a reverse hexagonal phase at concentrations above 82 wt%. The tendency of AOT to favor reverse structures is even preserved in the phase behavior of the catanionic mixture. Equimolar amounts of positively charged DDAB and negatively charged AOT, forming the catanionic surfactant didocecyldimethylammonium bis(2ethylhexyl)sulfosuccinate (DDAOT), aggregate in very dilute aqueous solution of less than 1 wt% to multiwalled polydisperse vesicles. A stable precipitate follows the vesicle solution at concentrations up to 10 wt%, which redissolves upon further addition of DDAOT, giving way to a hexagonal phase in equilibrium with an isotropic solution. A single hexagonal phase exists at surfactant concentrations between 90 and 95 wt%, and above 95 wt% an equilibrium with hydrated DDAOT crystals is formed. From the position in the phase diagram it was concluded that the hexagonal phase consists of reverse-type hexagonal rods. Although the complete pseudoternary DDAB-AOT-water phase diagram is as complex as the DDAB-SDSwater system displayed in Fig. 24b, its main feature is the coexistence of two reverse hexagonal phases in the AOT-rich region. The reverse hexagonal phase of the catanionic mixture is in equilibrium with the reverse

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hexagonal phase that originates from the binary AOTwater system [160]. The main aggregate structure found for mixtures of oppositely charged single-chain surfactants such as DTAB and SDS is a lamellar phase. Bicontinuous cubic and lamellar phases dominate the mixtures of doublechain DDAB and single-chain SDS. Finally, the mixtures of double-chain surfactants DDAB and AOT preferably form reverse hexagonal phases. The increasing tendency of these surfactant mixtures to form structures of reverse curvature is caused by the geometry of the molecules involved, e.g., the increasing space requirement of the hydrophobic part. But this observation is obvious and does not require a packing parameter concept to understand. However, some kind of theoretical model is necessary to understand and eventually predict the complex phase behavior of pseudoternary surfactant mixtures as shown in Fig. 23b, but simple geometrical considerations, even when extended by electrostatic assumptions, are insufficient to serve this purpose. A very interesting study in this context is the experimental and theoretical evaluation of the phase behavior of the cationic double-chain surfactant DDAB mixed with the nonionic double-chain glycolipid N-dodecanoyl-N-nonyl lactitol (LC11C 9). The ternary phase diagram of the DDAB-LC11C 9-water systems at 25⬚C is very similar to the diagram of the binary DDABwater mixture, containing two lamellar phases (L␣ and L ␣⬘) together with two distinct critical points that close two lamellar two-phase regions (Fig. 24a) [161]. This phase behavior has been calculated using osmotic pressure measurements based on essentially three intermolecular interactions, hydration forces, electrostatic forces, and van der Waals attraction, and an adhesion energy related to the sugar headgroups. Adhesion has been designated as any lowering of the osmotic pressure from the value imposed by hydration and electrostatic interactions. The variation of the osmotic pressure was determined as a function of the sample composition. Two parameters have been used to describe the sample composition in the phase triangle, xLC11C9, the molar fraction of LC11C 9 compared with DDAB, and D, the periodicity of the lamellar phase (D = ␦ /1 ⫺ ⌽water , where ␦ is the bilayer thickness and ⌽water is the water volume fraction. The theoretical phase diagram for the DDABLC11C 9-water mixture, displayed in Fig. 24a, has been evaluated based on the force balance in the ternary system. Several hypothetical diagrams shown in Ref. 162 demonstrate how the force balance affects size and position of the lamellar two-phase regions. The diagrams

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reveal that the hydration force increasing with xLC11C9 and the induction of a steric stabilization explain the appearance of the first critical point in the DDAB-rich part of the diagram. The second critical point comes from the lowering of electrostatic repulsion due to the low cationic headgroup density and from the strong adhesion between sugar headgroups. Differences between the experimental and calculated phase diagrams may result from mixing entropies and possible cluster formation in the bilayer, which are neglected in the model, and the curvature energy that may be significant when the lamellar phase has a multilayered onion structure [163]. It should be noted that the aggregation behavior of double-chain DDAB and LC11C 9 can be described very well by a model based on variable intermolecular interactions instead of geometrical dimensions based on the molecular shape. Studies of the phase behavior of phospholipids in the presence of surfactants are strongly stimulated by their applications in biotechnology, where solubilization of cell membranes by addition of a micelle-forming surfactant into the extracellular medium is the most commonly used method of extraction and concentration of membrane proteins. Following is an example of such a phospholipid-surfactant mixture, which has been used to shed more light on the underlying theoretical model. The phase behavior of nonionic double-chain egg phosphatidylcholine (EPC) and the single-chain surfactant octylglucoside (OG) is determined by the tendency of EPC to aggregate into extended lamellar bilayers forming closed vesicles and the opposite tendency of OG to form small strongly curved micelles. The phase behavior of the mixture can be described in several steps. Addition of OG to a solution of EPC vesicles results in partitioning of the surfactant between vesicle bilayers and the bulk solution until the bilayers become saturated with OG. Further addition of surfactant results in the formation of mixed threadlike micelles, which grow in numbers at the expense of the mixed vesicles. Finally, above a certain OG concentration only elongated micelles are left in solution and continuous addition of surfactant starts to reduce the micellar length (Fig. 24b) [163]. The composition-induced transition between micelles and vesicles is generally assumed to depend solely on the surfactant-to-lipid ratio of the aggregates and to be independent of the total concentration of the compounds in water. The vesicles are regarded as one extended closed bilayer and the micelles are treated as just one threadlike micelle, which is long enough that the inhomogeneity in its structure related to the two end caps can be neglected. The experimental data


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FIG. 24 (a) Ternary phase diagram of the DDAB-LC11C9-water mixture at 25⬚C and the three-dimensional representation of the equation of state II used to describe the phase behavior. Regions with tie lines in the phase diagram represent lamellar twophase regions, and the two dots represent the two resulting critical points. The thick black lines in the 3D representation correspond to the pressure-versus-distance curves calculated for a given XLC11C9. The two white areas are the calculated lamellar two-phase regions. (Adapted from Ref. 162.) (b) Phase diagrams of egg phosphatidylcholine (EPC)-octylglucoside (OG)-water (A) based on a model that considers only the EPC/OG ratio within the aggregates and (B) experimental data points and fitting curve based on a revised model considering the finite size of threadlike micelles and the EPC and OG concentration in solution. Note the different behavior at low EPC concentration. (Adapted from Ref. 164.)

points representing the phase boundaries seems to form a straight line. Extrapolation of both phase boundaries to lipid concentration L = 0 should give identical values for the surfactant concentration in the lipid-free solution. This is not the case, as indicated by the phase diagram in Fig. 24b. The intercepts are at 15.5 and 15.9 mM, a small but reproducible difference. A revised model based on thermodynamic considerations has thus been developed, which accounts for the finite length of the the threadlike micelles, their repartitioning in the water volume, and the effects of the end caps. As a consequence, the chemical potentials in the micellar phase no longer depend only on the surfactant-to-lipid

ratio but also depend on the absolute aqueous concentrations of the lipid and surfactant in water. It should be noted that the purely thermodynamic approach does not use any model assumptions about the micellar structure (and thus the geometrical shape of the molecules generating this structure!). One result of the revised thermodynamic model is the prediction that the phase boundaries in the range of relatively low lipid concentrations have to deviate from straight lines and adopt convex shapes. This prediction has been verified by measurements of the phase boundaries in the EPCOG-water system at lower concentrations than those studied before. The theoretically derived phase bound-

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aries are in good agreement with the experimental results, as indicated by the phase diagram in Fig. 24b [164]. This is another example in which the phase behavior is not explained by individual geometrical factors. Instead, interactions between molecules and the composition of the solution are taken into account.

V.

MODELS DESCRIBING THE PHASE BEHAVIOR OF SURFACTANTS

The examples discussed so far clearly indicate the shortcomings of a packing parameter concept that treats molecules like bricks, with the geometrical shape of the single brick determining the structure to which they can assemble, but ignoring the fact that bricks held together by a glue can form a vast variety of structures not related at all to the shape of the single unit. In case of surfactant molecules as well as other amphiphiles, the glue is present in the form of intermolecular interactions. In general, any concept or model that ignores the interactions of molecules with each other and with the chemical and physical conditions of the bulk solution will fail to explain the aggregation behavior. The simplicity of the packing parameter concept has not only lured many researchers into its use but also triggered some rigorous statements against it. To clear the ground, two of them will be cited here. The most intuitively appealing characterization is to visualize the shape of the volume occupied by a molecule in the HII phase as ‘‘tapered,’’ i.e. smaller in cross-sectional area at the head group than at the tail. This may be quantitatively specified by a dimensionless shape parameter given by v/al, where v is the molecular volume, a is the area at the lipid-water interface, and l is the length of the tail. Such a ‘‘shape concept’’ characterization is often misunderstood and leaves much to be desired. Rigorously speaking, one must refer to the shape which minimizes the overall free energy of a given molecular volume under a given set of conditions. This bears only a weak resemblance to the steric shape of the molecule because lipids are highly flexible and because factors such as charge, hydrogen bonds, etc. strongly affect the free energy. If v/al is taken to be a characterization of the shape of the mean volume actually assumed in a given phase, then v/al is simply a tautological description of the phase and has no predictive value, because the shape changes sharply at the phase transition. Therefore, v, a, and l should not be taken to refer

to the actual molecular dimensions, but rather to the dimensions which the system would prefer in the absence of other constraints; this poses serious problems of definition of v, a, and l and of measuring the values for real systems [119]. The second statement is even more outspoken. Structural modeling can be a very formal affair! Take, for example, an ideal sphere with a bimolecular diameter in the shape of a micelle and divide it by the aggregation number. A cone with a surface a 0 of the circle on the top, a length lc and a volume v is obtained. So far, so good. But now, to make sense out of the cone, a 0 is called the head group area, lc a critical length ‘‘specified for a given lipid,’’ and v becomes the hydrocarbon chain volume. As a result, one now has defined nicely an ‘‘average molecule,’’ using the shape of an aggregate which is less than ill-defined. This does not sound very promising and true enough, things get worse! A ‘‘critical packing parameter’’ is defined via the cone’s measurements and conclusions such as ‘‘SDS in low salt is a cone’’ and ‘‘SDS in high salt is a truncated cone’’ are drawn. Such pseudo-structural, meandynamic-packing models do not rationalize the appearance of molecular assemblies, but mystify them. Not a single crystal structure, NMR spectrum or molecular model gives evidence of a cone-like shape of any known amphiphile and one cannot derive it from a molecular assembly, from which the models are as far apart as spherical droplets, cubic blocks and irregular reefs [165]. After all, do any models exist that allow a reliable prediction of the phase behavior of surfactants? Following are some examples of models that are more suitable for achieving this goal than the packing parameter concept. The phase transitions observed for some phospholipids, changing from lamellar phase (L␣) to inverse hexagonal phase (HII) via bicontinuous cubic phase (V) with increasing temperature, are explained by the interplay of the spontaneous radius of curvature R 0 of the bilayer membrane and the hydrocarbon chain packing energy E hc . The in-plane forces at the hydrophilic surface of a monolayer include electrical charge, hydrogen bond, and other interactions that are generally different from those of the hydrophobic surface. The resultant forces are usually functions of the molecular area at the depth of the monolayer in question. If the sum of the in-plane forces is balanced for an area


larger at the tail end than at the headgroup end, then the monolayer may have an effective moment that yields a minimum-energy configuration in which the monolayer is bent with a concave headgroup surface. In this case, the monolayer is said to have a spontaneous curvature. Spontaneous curvature is a thermodynamic property of the monolayer that has the dimensions of a curvature; it is therefore measurable and usefully describes many lipid monolayers. The hydrocarbon chain packing energy E hc results from the conformation of the hydrocarbon chains. The number of gauche rotamers is determined primarily by a competition between the energy of introducing gauche rotamers and the resultant increase in entropy of the chains. In the lamellar geometry, there is no geometrical constraint which dictates that the mean chain length for any molecule needs to be different from that for any other. In the HII phase, however, given uniformly curved (e.g., cylindrical) water cores, some of the tails have to reach further than others to fill the hydrocarbon lattice at near uniform density. Therefore, not all molecules are at the minimum of the free energy with respect to the chain extension. A lamellar phase thus has a low energy with respect to the hydrocarbon chain packing but a high energy with respect to bending of the monolayer. The situation is reversed in case of the HII phase, with low energy due to the bend but high energy due to the chain packing. The L ␣-to-HII phase transition occurs at a temperature at which the sum of the two energies in a curved geometry falls below the sum in a lamellar geometry [119]. The stability of vesicles made of mixed single-chain catanionic surfactants has been modeled based on a similar thermodynamic approach. In an earlier model, the vesicle stability has been connected to the tendency of ‘‘1-2’’ surfactant pairs to have a bond distance different from the average of ‘‘1-1’’ and ‘‘2-2’’ pairs, resulting in a release of curvature frustration upon forming vesicles [166]. There are two objections to this model. First, the molecular interactions are specific, whereas vesicle formation has been observed for a wide range of surfactants. Second, it is well known that molecules exchange (‘‘flip-flop’’) between the inner and outer layers of a vesicle membrane as well as between membrane and bulk solution, especially in the case of thermodynamically stable vesicles. This exchange eventually results in an average distribution of the surfactants in both half-layers and a spontaneous curvature equal to zero. In a more recent thermodynamic approach, neither intervesicular interactions nor specific headgroup interactions are invoked. The free energy of a geometrically

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closed bilayer is modeled with consideration of (1) the curvature dependence of the bilayer tension; (2) the gain in free energy upon bringing a hydrocarbon chain from water into an alkane bulk phase; (3) the contribution that arises when the electrical charges from headgroups, counterions, and coions are concentrated in a restricted volume near the hydrocarbon-water interface; (4) the loss of conformational flexibility of hydrocarbon chains whose headgroups are restricted at the interface compared with the freedom of the chains in bulk alkanes; (5) a number of less known effects such as shielding of the hydrocarbon-water contact by the headgroups, different hydration of headgroups, counterions, and coions near the hydrocarbon bilayer, and repulsive correlation interactions between headgroups, counterions, and coions that have not been accounted for in the Poisson-Boltzmann approximation; and finally (6) the free energy of mixing the aggregated monomers in the vesicle. Summing up the different contributions then derives the total excess energy of forming a single monolayer out of monomers in solution. The detailed model calculation for the dodecylammonium chloride–sodium dodecyl sulfate mixture reveals a steep rise of the work of bending a planar bilayer into a closed vesicle at an equimolar mixture of the surfactants. Likewise, the bending work increases as the mole fraction of either of the surfactants approaches unity, resulting in a minimum of the free bending energy on each side of the equimolar composition [167]. This model calculation is in good agreement with experimental observations of vesicle lobes in phase diagrams (e.g., see Fig. 22). It is noteworthy that the molecular geometry is only indirectly present in the calculation; most parameters reflect intermolecular interactions and the conditions of the bulk solution. The Poisson-Boltzmann cell model is an approach that has been successful in describing several features of binary monovalent surfactant–water systems and observations made for the isotropic phase of a divalent surfactant–water mixture [168]. Consequently, this model has also been applied to describe the ternary phase diagram of a mixture of divalent and monovalent surfactants having a charge of the same sign in water. The transitions from the micellar solution to the hexagonal phase and the lamellar phase are modeled on the basis of spherical micelles, circular cylinders, and flat bilayers of infinite extension in two dimensions. Micelles and cylinders are considered to be stiff and of monodisperse size distribution. The interior of the aggregates is modeled as a pure liquid hydrocarbon, and the headgroups are confined to the surface of the ag-

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gregates. The thermodynamic model includes the following important contributions to the free energy: (1) electrostatic interactions between the surfactants, (2) the entropy of mixing the surfactants in the aggregates, (3) the interfacial energy contribution that is assumed to be proportional to the area each surfactant molecule exposes to the water, and (4) the entropy of mixing the micelles. Repulsive forces (‘‘hydration forces’’) are not included in the model calculations. These forces contribute significantly to the free energy at surfactant concentrations above 50 wt%. No fitting parameters have been applied to the model. Examples of an experimentally determined and a calculated phase diagram are shown in Fig. 25. The question of whether spherical micelles form a micellar solution or a discontinuous cubic phase has not been addressed in the model. Therefore the spherical region of the model diagram would correspond to the region with both cubic and micellar solution phases of the experimental diagram. Similarly, the circular cylindrical and bilayer regions of the model diagram correspond to the hexagonal and lamellar phase regions of the experimentally determined diagram. Keeping this in mind, both diagrams are in good agreement. The inclusion of repulsive hydration forces would not change the sequence of phases but shift the phase boundaries toward higher water contents. The effect would be more pronounced the lower the water content of the system [44]. Very good agreement between experimental data and a theoretical fitting using the UNIQUAC model has been observed for binary nonionic single-chain poly(oxyethylene) surfactant–water mixtures at weight fractions of water between 0.2 and 1.0. The liquid-liquid equilibrium phase diagrams of C6EO2, C6EO3, and C 7EO3, ranging from the lower critical consolute solution temperature to 70⬚C, have been measured [169]. The techniques most often employed to model the phase behavior of surfactants are molecular dynamics (MD) and Monte Carlo (MC) simulations. The application of computer simulation to the field of self-assembly has been the subject of two reviews [170,171]. Two MD simulations describe the phase behavior of nonionic single-chain poly(oxyethylenes). In the first example, a coarse-grained model, parametrized to yield the phase behavior of the corresponding physical system, is used instead of a realistic model with its severe spatial and temporal limitations. The surfactants within the model are composed of chains of Lennard-Jones sites connected by harmonic springs. The solvent is modeled as a Lennard-Jones fluid. Different solution conditions (temperature and concentration) as well as

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FIG. 25 (a) Composition phase diagram of the dipotassium dodecylmalonate (K2DoM)-potassium tetradecanoate (KTD)D2O system at 50⬚C. L1, I1, H, R, L␣, and INT denote micellar solution, discontinuous cubic, hexagonal, ribbon, lamellar, and intermediate phases, respectively; LC ⫹ Saq stands for liquid crystalline phases plus hydrated surfactant crystals. Shaded regions are multiphase regions, and hatched lines are approximate tie lines. (b) Theoretically calculated phase diagram for a ternary divalent surfactant-monovalent surfactant-D2O system. Precipitated surfactant crystals and surfactants in spherical, circular cylindrical, and planar aggregates have been considered in the calculations. Single-phase, twophase, and three-phase regions are white, shaded, and black, respectively. (Adapted from Ref. 44.)

different model parameters (size of headgroup and tail and their ratio and strength of interaction between the different sites) have been studied with the aim of gaining insight into how far this simplified MD technique


can be used to observe self-organization of amphiphilic systems at higher concentrations. Despite the simplified approach, it has been found that the surfactants aggregate to form very different micellar phases. Lamellar and bicontinuous phases have been found as well, but no hexagonal ordering [172]. In the second example, the properties of the lamellar L␣ phase of the binary C12EO2-water mixture have been modeled using constant pressure and temperature (NPT) MD simulations. The calculated interlamellar spacing and the area per surfactant are in reasonable agreement with x-ray diffraction results. The water molecules form hydrogenbonded bridged structures linking the oxygen atoms of the same surfactant chain. This interaction stabilizes a gauche conformation of the headgroups [173]. A very thorough study of the phase behavior of nonionic, cationic, anionic, and zwitterionic single-tail surfactants based on Monte Carlo simulations has been carried out. The phase diagrams are determined by MC lattice simulations for idealized symmetric and asymmetric molecules mixed with single-site ‘‘oil’’ and ‘‘water’’ molecules. At surfactant concentrations above 20 wt%, the simulations show the formation of liquid crystalline phases, including smectic, hexagonal, and gyroid cubic mesophases, and body-centered cubic (BCC) packing of spherical micelles. The locations of the phases in the diagrams of asymmetric surfactants in ‘‘water’’ are shifted relative to those for symmetric molecules in a way that favors phases whose interfaces curve in a way that leaves bulkier groups on the convex side of the interface. Many aspects of the predicted phase behavior, including the compositions at which transitions among ordered phases occur, compare favorably with experimental observations [32]. MC simulations have also been employed to study the phase behavior of ternary surfactant-water-oil mixtures. Several short-chain surfactants with varying tail and headgroup size have been studied, and quantitative phase diagrams for both symmetric and asymmetric molecules have been determined. Two- and three-phase coexistence regions as well as the formation of microemulsions have been observed [174]. The solubility of a compound in a surfactant micelle has been successfully modeled using lattice-based MC simulations. Points of interest were the phase behavior of the surfactant-solute-solvent system and the examination of the locus and extent of the solubilization of the solute in micelles as a function of the solute hydrophobicity and chain length. A novel method based on the distribution of the solute in clusters of different sizes has been developed to study the solute phase behavior in the absence and presence of the surfactant

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[175]. Generally, the thermodynamic models of mixed micelle formation can be divided into two categories. In the first category, the process is treated as a reversible chemical reaction and the mass action approach is used. The reactants are the surfactants, the bound counterions, and solubilizates when appropriate. The standard free energy associated with this reaction is in reference to a standard state in which the reactants are dispersed at infinite dilution. This type of model is appropriate because micelle formation is reversible. Micelles have a finite lifetime, as do the individual components that form a micelle. The aggregation number is a dynamic variable and, at any instant, various individual micelles will be composed of different numbers of surfactant molecules. In the case of mixed micelles, the number of surfactant molecules of a given structure may also vary from micelle to micelle. The second approach is to consider the micelle as a separate bulk phase having an infinite lifetime. The chemical potentials of the components in the micellar phase (although not a true thermodynamically different phase) can then be equated to those of the molecules that are dispersed in the aqueous phase. Various models for the chemical potential can be used to account for the nonideal behavior in both the micellar and solution phases. One of the most popular models of this type of treatment is the regular solution theory [176]. The phase separation model defines the proportions of various components that exist within the micellar phase, and it provides equations for the cmc of mixtures. However, it does not address factors related to the size of the micelles or their aggregation number. A new model for micellization behavior of binary surfactant mixtures in solution has thus been developed. The significant features of the model are the consideration of asymmetric behavior of micellization in binary surfactant mixtures and the prediction of changes in the structure of mixed micelles with concentration that are dependent on the overall ratio of the surfactant components and their chemical characteristics. Based on the results obtained, a schematic model for the structural changes of mixed micelles has been proposed [177]. The model introduces a packing parameter P* to describe the random mixing in mixed micelles. This packing parameter, however, changes as a function of the overall mixing ratio of the surfactants, similarly to the relationship of packing density of two different particles as a function of mixing ratio, instead of being a rather static geometrical factor of the single molecules. All model calculations give reasonable to good results in modeling the phase behavior of binary and ter-

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nary surfactant-water and surfactant-water-oil mixtures. In addition, the solubility of a solute in micelles and the formation of mixed micelles can be modeled successfully. The common features of these approaches are the importance of intermolecular forces and the equilibrium between these forces; the geometry of the molecules is only indirectly involved in the calculations. Even in the one approach that uses a packing parameter term, this packing parameter is a variable that changes with the composition of the system rather than a constant number for an individual molecule. Whereas the model calculations mentioned so far depend heavily on a physical or physicochemical background, the following example is based on an organic chemical approach. The synkinetic approach treats the formation of mesophases and higher organized supramolecular structures like a synthesis. In a synthesis, appropriate precursors (‘‘synthons’’) form a desired chemical molecule in a controlled way. In exactly the same way, surfactants and other amphiphiles (‘‘synkinons’’) form a desired mesophase or supramolecular structure when equipped with the right geometry, hydrophile-lipophile balance, and, most important, the appropriate functional groups to engage in certain intermolecular interactions. Synkinesis is thus the targetoriented synthesis of noncovalent molecular aggregates. Figure 26 displays some examples of typical synkinons and their target structures [165]. VI.

MONOMER SOLUBILITY—A HANDS-ON MEASURE TO TAILOR THE AGGREGATION BEHAVIOR

Is there any measure between the trial-and-error approach (whether or not based on geometrical shapes) and rather time-consuming model simulations that would help in designing surfactants and other amphiphiles for a certain purpose, e.g., forming mesophases or supramolecular structures of a desired shape? What common macroscopic measure is affected by the molecular shape, intermolecular interactions, the concentration, the presence of cosolutes, the amount of salt, the pH, the temperature, the temperature gradient of heating or cooling, and the characteristics of the solvent? All these factors affect the solubility of the monomers. The hydrophile-lipophile balance of monomers, the character and strength of interactions between them, and the conditions of the bulk solution determine their solubility. Molecules will obviously not form aggregates in water when they are too soluble, and they will form only amorphous lamellar structures when they are too in-

soluble. For example, finding the right cooling rate that allows specific molecules to organize perfectly into single crystals is the permanent challenge in crystallography. Of course, a crystallographer is restricted in the choices to influence the aggregation behavior of a specific molecule; e.g., changing the molecular structure or adding cosolutes or even a salt is not very helpful in obtaining the structure of the true low-energy crystal of this molecule. However, if the goal is creating a certain mesophase or fiber structure or tubule with a specific inner diameter, then all of the variables mentioned can be employed to realize this goal. The monomer solubility as a measure was mentioned earlier in the context of the phase behavior of ternary CiEOj water-n-alkane mixtures and the factors influencing this behavior [59]. Some examples based on single-chain n-alkylhexonamides that will support the use of the monomeric solubility as a guide in optimizing the aggregation behavior of these compounds to form welldefined structures follow. Galactonic, mannonic, gluconic, talonic, and gulonic headgroups each connected to an n-octylamide tail aggregate on cooling from hot aqueous solution to form ribbons, rolled up planar sheets, well-defined helices, ill-defined twisted fibers, and lamellar crystals, respectively (Fig. 27) [178,179]. In addition, planar hexonamide crystals are formed by bent or linear monomers, although one linear conformation contains a geometrically unfavorable pair of 1,3-syndiaxial oxygen atoms. No close interaction between the geometrical shape of the monomers and the curvature of the aggregates has been found [180–186]. This diverse aggregation behavior can therefore not be explained by geometrical constraints but results from strong and oriented attractive forces in the form of hydrogen bonds between the molecules. Depending on the individual stereochemistry, these hydrogen bonds provide intermolecular interactions of different strengths, thus affecting the solubility of the hexonamides. The solubility is therefore an excellent measure to explain the different aggregate structures. The extremely low solubility of galactonamide in boiling water (100 wt%) hinder any fiber formation. Instead, lamellar crystals form spontaneously at room temperature from often supersaturated solutions. The observations suggest the existence of an ‘‘optimal’’ solubility (=speed of aggregate formation), which allows the formation of stable aggregates that reflect the specific interactions

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FIG. 27 Chemical structures and transmission electron micrographs of aqueous solutions of n-octyl galactonamide (D-Gal-8); mannonamide (D-Man-8); gluconamide (D-Glu-8); talonamide (D-Tal-8); and gulonamide (D-Gul-8). Bars = 500 nm. (From Ref. 187.)

between the monomers. This situation is realized in the case of gluconamide. Lower solubility (=faster aggregation) results in stable aggregates that do not reflect specific interactions between the monomers (galactonamide and mannonamide), whereas higher solubility (=slower aggregation) would allow the formation of aggregates reflecting specific monomer interactions, but the low aggregate stability limits their lifetime (talonamide). Increasing the length of the alkyl chain and thus the hydrophobic interaction while keeping the headgroup unaltered should lower the solubility and therefore change the aggregation behavior. The hydrophobic in-

teraction increases by 1.1 kT per CH2 group [26]. For example, gluconamide headgroups connected to decyl, dodecyl, and tetradecyl chains form virtually the same helices as the octyl homologue. The pentadecyl gluconamide, however, aggregates in water to twisted ribbons. The lower solubility of the pentadecyl gluconamide prevents the organization of the monomers into well-defined helices. Lowering the solubility of the more soluble octyl gulonamide by replacing the octyl chain by a hexadecyl chain, on the other hand, initiates the formation of fiber aggregates. Hexadecyl gulonamide first forms twisted ribbons, which eventually grow into flexible tubules (Fig. 28). Finally, the pres-


709

FIG. 28 Transmission electron micrographs of aqueous solutions of (A) helices of tetradecyl gluconamide; (B) twisted ribbons of pentadecyl gluconamide; (C) twisted ribbons of hexadecyl gluconamide, which (D) grow into flexible tubules; (E) helices of pentadecyl gluconamide formed in the presence of SDS micelles; and (F) helices from octadecyl mannonamide formed in the presence of SDS micelles. Bars A–E = 200 nm and Bar F = 150 nm. (From Ref. 187.)

ence of surfactant micelles as cosolute improves the solubility of the hexonamides through the formation of mixed micelles. The incorporation of the alkyl chains into the micellar core reduces the local concentration of the hexonamide molecules in the bulk solution and leads to a slower and more organized aggregation. Pentadecyl gluconamide in the presence of 15% SDS (with regard to the gluconamide) forms well-defined helices instead of the twisted ribbons observed before. The almost water-insoluble octadecyl mannonamide forms righthanded (P) and left-handed (M) helices from hot water– SDS solution instead of lamellar sheets (Fig. 28) [187]. These examples clearly indicate the close relation-

ship between solubility and aggregate formation. It would be foolish, of course, to assume this is a linear relationship in such a way that one can conclude that 0.5 wt% solubility results in ribbons and 50 wt% solubility leads to the formation of helices. This is not another packing parameter concept! However, educated guesses about factors that influence the solubility of the molecules under investigation will provide more reliable guidance on how to affect their aggregation behavior than pure trial-and-error approaches. This statement is true for studies not only of a family of homologous compounds but also (at least) of a group of similar molecules.

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CONCLUSIONS

The binary phase behavior of surfactants in water based on mainly isotropic interactions (e.g., headgroup repulsion and hydrophobic attraction) as well as the phase behavior of catanionic mixtures has been reviewed with the emphasis on whether geometrical considerations in the form of a packing parameter concept will allow prediction of the observed behavior. It has been found that intermolecular forces between surfactant monomers and the condition of the bulk solution are of more importance. Several model simulations have been presented that provide reasonable to good agreement between the calculated phase behavior and experimental results. Finally, the solubility of the surfactant monomers as a hands-on measure to tailor molecules for a certain aggregation behavior has been proposed and its feasibility has been demonstrated with several examples.

12.

13.

14.

15.

16.

17.

18.

REFERENCES 1. 2.

3.

4.

5.

6.

7.

8.

9.

10.

11.

R. G. Laughlin, The Aqueous Phase Behavior of Surfactants, Academic Press, New York, 1994. J. M. Richmond, Cationic Surfactants—Organic Chemistry, Surfactant Science Series Vol. 34, Marcel Dekker, New York, 1990. D. N. Rubingh and P. M. Holland, Cationic Surfactants—Physical Chemistry, Surfactant Science Series Vol. 37, Marcel Dekker, New York, 1990. C. Gloxhuber and K. Ku¨nstler, Anionic Surfactants— Biochemistry, Toxicology, Dermatology, 2nd ed., Surfactant Science Series Vol. 43, Marcel Dekker, New York, 1992. H. Stache, Anionic Surfactants—Organic Chemistry, Surfactant Science Series Vol. 56, Marcel Dekker, New York, 1995. M. J. Schick, Nonionic Surfactants—Physical Chemistry, Surfactant Science Series Vol. 23, Marcel Dekker, New York, 1987. N. M. Van Os, Nonionic Surfactants—Organic Chemistry, Surfactant Science Series Vol. 72, Marcel Dekker, New York, 1997. D. Balzer and H. Lu¨ders, Nonionic Surfactants—Alkylpolyglucosides, Surfactant Science Series, Marcel Dekker, New York, 2000. E. Lomax, Amphoteric Surfactants, 2nd ed., Surfactant Science Series Vol. 59, Marcel Dekker, New York, 1996. K. Holmberg, Novel Surfactants—Preparation, Applications, and Biodegradability, Surfactant Science Series Vol. 74, Marcel Dekker, New York, 1998. S. E. Friberg and B. Lindman, Organized Solutions— Surfactants in Science and Technology, Surfactant Science Series Vol. 44, Marcel Dekker, New York, 1992.

19.

20.

21.

22.

23. 24. 25. 26.

27. 28. 29. 30. 31.

32.

A. K. Chattopadhyay and K. L. Mittal, Surfactants in Solution, Surfactant Science Series, Vol. 64, Marcel Dekker, New York, 1996. N. M. Van Os, J. R. Haak, and L. A. M. Rupert, Physico-Chemical Properties of Selected Anionic, Cationic, and Nonionic Surfactants, Elsevier Science, Amsterdam, 1993. K. Ogiono and M. Abe, Mixed Surfactant Systems, Surfactant Science Series Vol. 46, Marcel Dekker, New York, 1992. P. M. Holland and D. N. Rubingh, Mixed Surfactant Systems, ACS Symposium Series, Oxford University Press, New York, 1999. D. Myers, Surfaces, Interfaces, and Colloids: Principles and Applications, 2nd ed., Wiley-VCH Publishers, New York, 1999. D. F. Evans and H. Wennerstro¨m, The Colloidal Domain: Where Physics, Chemistry, Biology, and Technology Meet, 2nd ed., Wiley-VCH Publishers, New York, 1999. D. O. Shah, Micelles, Microemulsions, and Monolayers, Marcel Dekker, New York, 1998. M. N. Jones and D. Chapman, Micelles, Monolayers, and Biomembranes, Wiley-VCH Publishers, New York, 1994. P. Kumar and K. L. Mittal, Handbook of Microemulsion Science and Technology, Marcel Dekker, New York, 1999. K. Esumi and M. Ueno, Structure-Performance Relationships in Surfactants, Surfactant Science Series Vol. 70, Marcel Dekker, New York, 1997. C. A. Herb and R. K. Prud’homme, Structure and Flow in Surfactant Solutions, ACS Symposium Series, Oxford University Press, New York, 1994. M. J. Rosen, Surfactants and Interfacial Phenomena, 2nd ed., Wiley-VCH Publishers, New York, 1989. N. K. Raman, M. T. Anderson, and C. J. Brinker, Chem. Mater. 8:1682–1701 (1996). H. H. Clint, Surfactant Aggregation, Blackie and Son, London, 1992. C. Tanford, The Hydrophobic Effect: Formation of Micelles and Biological Membranes, 2nd ed., John Wiley & Sons, New York, 1980. J. N. Israelachvili, Intermolecular and Surface Forces, 2nd ed., Academic Press, San Diego, 1991. D. J. Mitchell and B. W. Ninham, J. Chem. Soc. Faraday Trans. II 77:601–629 (1981). H. Hoffmann and G. Ebert, Angew. Chem. Int. Ed. 27:902–912 (1988). C. Hall, G. J. T. Tiddy, and B. Pfannemu¨ller, Liq. Cryst. 9:527–537 (1991). D. W. R. Gruen and E. H. B. de Lacey, in Surfactants in Solution, Vol. 1 (K. L. Mittal and B. Lindman, eds.), Plenum, New York, 1984, pp. 279–306. R. G. Larson, J. Phys. II Fr. 6:1441–1463 (1996) and references cited therein.

The Role of Steric Constraints 33. 34. 35. 36. 37. 38. 39. 40.

41. 42. 43. 44. 45.

46.

47. 48. 49. 50. 51. 52. 53.

54. 55. 56.

57. 58. 59.

P. Mariani, L. Q. Amaral, L. Saturni, and H. Delacroix, J. Phys. II Fr. 4:1393–1416 (1994). J. C. Blackburn and P. K. Kilpatrick, J. Colloid Interface Sci. 149:450–471 (1992). P. O. Eriksson, G. Lindblom, and G. Arvidson, J. Phys. Chem. 91:846–853 (1987). M. B. Sjo¨bom, H. Edlund, and B. Lindstro¨m, Langmuir 15:2654–2660 (1999). S. A. Buckingham, C. J. Garvey, and G. G. Warr, J. Phys. Chem. 97:10236–10244 (1993). T. Imae and S. Ikeda, J. Colloid Interface Sci. 113: 449–455 (1986). T. Imae, M. Sasaki, A. Abe, and S. Ikeda, Langmuir 4:414–418 (1988). B. Lindman, A. Carlsson, G. Karlstro¨m, and M. Malmsten, Adv. Colloid Interface Sci. 32:183–203 (1990). G. Porte, J. Phys. Chem. 87:3541–3550 (1983). T. Imae and S. Ikeda, J. Phys. Chem. 90:5216–5223 (1986). H. von Berlepsch, Langmuir 11:3667–3675 (1995). H. Hagsla¨tt, O. So¨derman, and B. Jo¨nsson, Langmuir 10:2177–2187 (1994). N. A. J. M. Sommerdijk, K. J. Body, A. M. A. Pistorius, M. C. Feiters, R. J. M. Nolte, and B. Zwanenburg, Langmuir 15:7008–7013 (1999). N. A. J. M. Sommerdijk, T. L. Hoeks, K. J. Booy, M. C. Feiters, R. J. M. Nolte, and B. Zwanenburg, Chem. Commun. 743–744 (1998). M. C. Monje, H. Mawlawi, A. Lattes, and M. Rivie`re, New J. Chem. 17:231–235 (1993). G. T. Dimitrova, T. F. Tadros, P. F. Luckham, and M. R. Kipps, Langmuir 12:315–318 (1996). P. Sakya, J. M. Seddon, R. H. Templer, R. J. Mirkin, and G. J. T. Tiddy, Langmuir 13:3706–3714 (1997). B. Ha˚kansson, P. Hansson, O. Regev, and O. So¨derman, Langmuir 14:5730–5739 (1998). H. Kunieda, K. Shigeta, and K. Ozawa, J. Phys. Chem. B 101:7952–7957 (1997). H. Kunieda, K. Shigeta, and M. Suzuki, Langmuir 15: 3118–3122 (1999). M. S. Leaver, U. Olsson, H. Wennerstro¨m, R. Strey, and U. Wu¨rz, J. Chem. Soc. Faraday Trans. 91:4269– 4274 (1995). U. Olsson and P. Schurtenberger, Langmuir 9:3389– 3394 (1993). K. Fukuda, U. Olsson, and U. Wu¨rz, Langmuir 10: 3222–3229 (1994). R. Strey, R. Schoma¨cker, D. Roux, F. Nallet, and U. Olsson, J. Chem. Soc. Faraday Trans. 86:2253–2261 (1990). G. Karlstro¨m, J. Phys. Chem. 89:4962–4964 (1985). R. Strey, Ber. Bunsenges. Phys. Chem. 100:182–189 (1996). S. Burauer, T. Sachert, T. Sottmann, and R. Strey, Phys. Chem. Chem. Phys. 1:4299–4306 (1999).

711 60. 61. 62.

63. 64.

65.

66. 67. 68. 69. 70. 71. 72. 73. 74. 75. 76. 77. 78. 79. 80. 81. 82. 83. 84. 85.

T. Scottmann and R. Strey, J. Chem. Phys. 106:8606– 8615 (1997). M. Kahlweit and R. Strey, Angew. Chem. Int. Ed. Engl. 24:654–668 (1985). B. M. Knickerbocker, C. V. Pesheck, L. E. Scriven, and H. T. Davis, J. Phys. Chem. 83:1984–1990 (1979). T. Scottmann, R. Strey, and S. H. Chen, J. Chem. Phys. 106:6483–6491 (1997). M. J. Schwuger, in Structure/Performance Relationships in Surfactants (M. J. Rosen, ed.), ACS Symposium Series 253, American Chemical Society, Washington, DC, 1984, chapter 1. R. G. Alargova, K. D. Danov, J. T. Petkov, P. A. Kralchevsky, G. Broze, and A. Mehreteab, Langmuir 13: 5544–5551 (1997). N. Zoeller and D. Blankschtein, Langmuir 14:7155– 7165 (1998). X. Li, R. M. Washenberger, L. E. Scriven, and H. T. Davis, Langmuir 15:2267–2277 (1999). X. Li, R. M. Washenberger, L. E. Scriven, and H. T. Davis, Langmuir 15:2278–2289 (1999). H. Kunieda, H. Taoka, T. Iwanaga, and A. Harashima, Langmuir 14:5113–5120 (1998). R. Strey, W. Jahn, G. Porte, and P. Bassereau, Langmuir 6:1635–1639 (1990). R. M. Hill, Silicone Surfactants, Surfactant Science Series Vol. 86, Marcel Dekker, New York, 1999. X. Zhu, W. G. Miller, L. E. Scriven, and H. T. Davis, Colloids Surf. A 90:63–78 (1994). T. Stoebe, R. M. Hill, M. D. Ward, and H. T. Davis, Langmuir 13:7276–7281 (1997). T. Svitova, H. Hoffmann, and R. M. Hill, Langmuir 12:1712–1721 (1996). M. He, R. M. Hill, Z. Lin, L. E. Scriven, and H. T. Davis, J. Phys. Chem. 97:8820–8834 (1993). R. Wagner and R. Strey, Langmuir 15:902–905 (1999). G. Arvidson, I. Brentel, A. Khan, G. Lindblom, and K. Fontell, Eur. J. Biochem. 152:753–759 (1985). P. O. Eriksson, G. Lindblom, and G. Arvidson, J. Phys. Chem. 91:846–853 (1987). N. Maurer, E. Prenner, F. Paltauf, and O. Glatter, Biochim. Biophys. Acta. 1192:167–176 (1994). O. So¨derman, G. Carlstro¨m, M. Monduzzi, and U. Olsson, Langmuir 4:1039–1044 (1988). P. G. Faulkner, A. J. I. Ward, and D. W. Osborne, Langmuir 5:924–926 (1989). C. LaMesa, B. Sesta, M. G. Bonicelli, and G. F. Ceccaroni, Langmuir 6:728–731 (1990). Y. Chevalier, F. Me´lis, and J. P. Dalbiez, J. Phys. Chem. 96:8614–8619 (1992). Y. Chevalier, Y. Storet, S. Pourchet, and P. Le Perchec, Langmuir 7:848–853 (1991). J. Amrhar, Y. Chevalier, B. Gallot, P. Le Perchec, X. Auvray, and C. Petipas, Langmuir 10:3435–3441 (1994).

712 86. 87. 88. 89.

90. 91. 92. 93. 94. 95. 96. 97. 98. 99. 100. 101. 102. 103. 104. 105. 106. 107. 108. 109. 110. 111.

112.

Svenson T. Kunitake, Angew. Chem. Int. Ed. Engl. 31:706–726 (1992). Y. Ishikawa, T. Nishimi, and T. Kunitake, Chem. Lett. 165–168 (1990). T. Nishimi, Y. Ishikawa, R. Ando, and T. Kunitake, Rec. Trav. Chim. Pays-Bas 113:201–208 (1994). T. Kunitake, Y. Okahata, M. Shimomura, S. Yasunami, and K. Takarabe, J. Am. Chem. Soc. 103:5401–5413 (1981). F. M. Menger and J. Ding, Angew. Chem. Int. Ed. Engl. 35:2137–2139 (1996). M. C. Holmes, Curr. Opin. Colloid Interface Sci. 3: 485–492 (1998). M. P. Krafft and J. G. Riess, Biochimie 80:489–514 (1998). M. Monduzzi, Curr. Opin. Colloid Interface Sci. 3: 467–477 (1998). K. Wang, G. Ora¨dd, M. Almgren, T. Asakawa, and B. Bergensta˚hl, Langmuir 16:1042–1049 (2000). K. Wang, G. Karlsson, M. Almgren, and T. Asakawa, J. Phys. Chem. B 103:9237–9246 (1999). F. Giulieri, M. P. Krafft, and J. G. Riess, Angew. Chem. Int. Ed. Engl. 33:1514–1515 (1994). F. Giulieri and M. P. Krafft, Colloids Surf. A 84:121– 127 (1994). K. Kratzat and H. Finkelmann, J. Colloid Interface Sci. 181:542–550 (1996). K. Kratzak, C. Stubenrauch, and H. Finkelmann, Colloid Polym. Sci. 273:257–262 (1995). K. Kratzak and H. Finkelmann, Colloid Polym. Sci. 272:400–408 (1994). E. V. Shumilina and Y. A. Shchipunov, Colloids Surf. A 121:23–26 (1997). M. Dubois and T. Zemb, Langmuir 7:1352–1360 (1991). M. Dubois, T. Zemb, N. Fuller, R. P. Rand, and V. A. Parsegian, J. Chem. Phys. 108:7855–7869 (1998). G. G. Warr, R. Sen, D. F. Evans, and J. E. Trend, J. Phys. Chem. 92:774–783 (1988). T. F. Svitova, Y. P. Smirnova, S. A. Pisarev, and N. A. Berezina, Colloids Surf. A 98:107–115 (1995). F. M. Menger and K. Gabrielson, J. Am. Chem. Soc. 116:1567–1568 (1994). F. M. Menger and N. Balachander, J. Am. Chem. Soc. 114:5862–5863 (1992). T. Kunitake and Y. Okahata, J. Am. Chem. Soc. 99: 3860–3861 (1997). T. Kunitake, N. Kimizuka, N. Higashi, and N. Nakashima, J. Am. Chem. Soc. 106:1978–1983 (1984). N. Kimizuka, H. Ohira, M. Tanaka, and T. Kunitake, Chem. Lett. 29–32 (1990). P. Bissel, M. Onda, K. Yoshihara, H. Koyano, K. Ariga, T. Kunitake, Y. Oishi, and K. Suehiro, Langmuir 15:1791–1795 (1999). N. A. J. M. Sommerdijk, T. H. L. Hoeks, M. Synak, M. C. Feiters, R. J. M. Nolte, and B. Zwanenburg, J. Am. Chem. Soc. 119:4338–4344 (1997).

113. 114. 115. 116. 117. 118.

119. 120. 121. 122. 123. 124. 125. 126. 127. 128. 129. 130. 131. 132.

133.

134. 135. 136.

137.

138. 139. 140. 141.

D. A. Jaeger, B. Li, and T. Clark Jr, Langmuir 12: 4314–4316 (1996). G. Cevc and D. Marsh, Phospholipid Bilayers: Physical Principles and Models, Wiley, New York, 1987. G. Cevc, Phospholipids Handbook, Marcel Dekker, New York, 1993. D. Marsh, Handbook of Lipid Bilayers, CRC Press, Boca Raton, FL, 1987. D. M. Small, Handbook of Lipid Research, Vol. 4, Plenum, New York, 1989. R. Lipowsky and E. Sackmann, Structure and Dynamics of Membranes, Vol. 1A, Handbook of Biological Physics, Elsevier, Amsterdam, 1995. S. M. Gruner, J. Phys. Chem. 93:7562–7570 (1989). K. Larsson, J. Phys. Chem. 93:7304–7314 (1989). J. M. Seddon, Biochim. Biophys. Acta 1031:1–69 (1990). J. M. Seddon, Ber. Bunsenges. Phys. Chem. 100:380– 393 (1996). F. C. MacKintosh, Curr. Opin. Colloid Interface Sci. 2:382–387 (1997). P. Ekwall, Adv. Liq. Cryst. 1:1–142 (1975). G. Lindblom and L. Rilfors, Biochim. Biophys. Acta 988:221–256 (1989). D. Marsh, Chem. Phys. Lipids 57:109–120 (1991). P. R. Cullis, M. J. Hope, and C. P. S. Tilcock, Chem. Phys. Lipids 40:127–144 (1986). W. Helfrich, Liq. Cryst. 5:1647–1658 (1989). R. Goetz and W. Helfrich, J. Phys. II Fr. 6:215–223 (1996). B. Klo¨sgen and W. Helfrich, Biophys. J. 73:3016– 3029 (1997). B. Klo¨sgen and W. Helfrich, Eur. Biophys. J. 22:329– 340 (1993). J. M. Seddon and G. Cevc, in Phospholipids Handbook (G. Cevc, ed.), Marcel Dekker, New York, 1993, pp. 403–454. G. S. Smith, E. B. Sirota, C. R. Safinya, R. L. Plano, and N. A. Clark, J. Chem. Phys. 92:4519–4529 (1990). D. Bach, I. Bursuker, H. Eibl, and I. R. Miller, Biochim. Biophys. Acta 514:310–319 (1978). G. Cevc, J. Phys. 50:1117–1134 (1989). D. A. Jaeger, W. Subotkowski, J. Wang, E. KubiczLoring, and H. Shinozaki, Langmuir 13:1844–1849 (1997) and references therein. F. M. Menger, M. G. Wood, Jr., Q. Z. Zhou, H. P. Hopkins, and J. Fumero, J. Am. Chem. Soc. 110: 6804–6810 (1988). K. Yamauchi, K. Doi, and M. Kinoshita, Biochim. Biophys. Acta 1283:163–169 (1996). T. Kunitake, Y. Okahata, and S.-I. Tawaki, J. Colloid Interface Sci. 103:190–201 (1985). Y. Ishikawa, T. Nishimi, and T. Kunitake, Chem. Lett. 25–28 (1990). J. Y. Kim, J. Mattai and G. G. Shipley, Biochemistry 26:6592–6598 (1987).

The Role of Steric Constraints 142. 143. 144.

145.

146. 147. 148. 149.

150. 151.

152. 153. 154. 155. 156. 157. 158. 159. 160. 161.

162.

163. 164.

E. N. Serrallach, R. Dijkman, G. H. De Haas, and G. G. Shipley, J. Mol. Biol. 170:155–174 (1983). V. Ravily, C. Santaella, P. Vierling, and A. Gulik, Biochim. Biophys. Acta 1324:1–17 (1997). N. A. J. M. Sommerdijk, P. J. J. A. Buynsters, H. Akdemir, D. G. Geurts, A. M. A. Pistorius, M. C. Feiters, R. J. M. Nolte, and B. Zwanenburg, Chem. Eur. J. 4: 127–136 (1998). N. A. J. M. Sommerdijk, M. H. L. Lambermon, M. C. Feiters, R. J. M. Nolte, and B. Zwanenburg, Chem. Commun. 455–456 (1997). B. Kronberg, Curr. Opin. Colloid Interface Sci. 2:456– 463 (1997). E. H. Lucassen-Reynders, J. Lucassen, and D. Giles, J. Colloid Interface Sci. 81:150–157 (1981). H. Edlund, A. Sadaghiani, and A. Khan, Langmuir 13: 4953–4963 (1997) and references therein. K. L. Herrington, E. W. Kaler, D. D. Miller, J. A. Zasadzinski, and S. Chiruvolu, J. Phys. Chem. 97: 13792–13802 (1993). N. Filipovic-Vincekovic, M. Bujan, D. Dragcevic, and N. Nekic, Colloid Polym. Sci. 273:182–188 (1995). M. T. Yatcilla, K. L. Herrington, L. L. Brasher, E. W. Kaler, S. Chiruvolu, and J. A. Zasadzinski, J. Phys. Chem. 100:5874–5879 (1996). E. W. Kaler, A. K. Murthy, B. Rodriguez, and J. A. Zasadzinski, Science 245:1371–1374 (1989). E. W. Kaler, K. L. Herrington, A. K. Murthy, and J. A. Zasadzinski, J. Phys. Chem. 96:6698–6707 (1992). O. So¨derman, K. L. Herrington, E. W. Kaler, and D. D. Miller, Langmuir 13:5531–5538 (1997). L. L. Brasher, K. L. Herrington, and E. W. Kaler, Langmuir 11:4267–4277 (1995). L. L. Brasher and E. W. Kaler, Langmuir 12:6270– 6276 (1996). T. Zemb, M. Dubois, B. Deme´, and T. Gulik-Krzywicki, Science 283:816–819 (1999). H. Hagsla¨tt and K. Fontell, J. Colloid Interface Sci. 165:431–444 (1994). E. Marques, A. Khan, M. da Graca Miguel, and B. Lindman, J. Phys. Chem. 97:4729–4736 (1993). A. Caria and A. Kahn, Langmuir 12:6282–6290 (1996). F. Ricoul, M. Dubois, T. Zemb, M. P. Heck, A. Vandais, D. Plusquellec, I. Rico-Lattes, and O. Diat, J. Phys. Chem. B 102:2769–2775 (1998). F. Ricoul, M. Dubois, L. Belloni, T. Zemb, C. Andre´Barre`s, and I. Rico-Lattes, Langmuir 14:2645–2655 (1998). E. Opatowski, M. M. Kozlov, and D. Lichtenberg, Biophys. J. 73:1448–1457 (1997). Y. Roth, E. Opatowski, D. Lichtenberg, and M. M. Kozlov, Langmuir 16:2052–2061 (2000).

713 165.

166. 167. 168. 169. 170. 171. 172. 173. 174. 175.

176.

177. 178. 179. 180. 181. 182. 183. 184. 185.

186.

187.

J.-H. Fuhrhop and J. Ko¨ning, Membranes and Molecular Assemblies: The Synkinetic Approach, The Royal Society of Chemistry, Cambridge, 1994. S. A. Safran, P. A. Pincus, D. Andelman, and F. C. MacKintosh, Phys. Rev. A 43:1071–1078 (1991). M. Bergstro¨m, Langmuir 12:2454–2463 (1996). B. Jo¨nsson and H. Wennerstro¨m, J. Phys. Chem. 91: 338–352 (1987). H.-H. Lai and L.-J. Chen, J. Chem. Eng. Data 44:251– 153 (1999). R. G. Larson, Curr. Opin. Colloid Interface Sci. 2: 361–364 (1997). S. Karaborni and B. Smit, Curr. Opin. Colloid Interface Sci. 1:411–415 (1996). B. Fodi and R. Hentschke, Langmuir 16:1626–1633 (2000). S. Bandyopadhyay, M. Tarek, M. L. Lynch, and M. L. Klein, Langmuir 16:942–946 (2000). A. D. Mackie, K. Onur, and A. Z. Panagiotopoulos, J. Chem. Phys. 104:3718–3725 (1996). S. K. Talsania, L. A. Rodrı´guez-Guadarrama, K. K. Mohanty, and R. Rajagopalan, Langmuir 14:2684– 2692 (1998). D. N. Rubingh, in Solution Chemistry of Surfactants, Vol. 1 (K. L. Mitall, ed.), Plenum, New York, 1979, pp. 337–348. L. Huang and P. Somasundaran, Langmuir 13:6683– 6688 (1997). J.-H. Fuhrhop, P. Schnieder, J. Rosenberg, and E. Boekema, J. Am. Chem. Soc. 109:3387–3390 (1987). J.-H. Fuhrhop, P. Schnieder, E. Boekema, and W. Helfrich, J. Am. Chem. Soc. 110:2861–2867 (1988). S. Svenson, J. Ko¨ning, and J.-H. Fuhrhop, J. Phys. Chem. 98:1022 (1994). S. Svenson, B. Kirste, and J.-H. Fuhrhop, J. Am. Chem. Soc. 116:11969 (1994). C. Andre´, P. Luger, S. Svenson, and J.-H. Fuhrhop, Carbohydr. Res. 230:31–40 (1992). C. Andre´, P. Luger, S. Svenson, and J.-H. Fuhrhop, Carbohydr. Res. 240:47–56 (1993). J.-H. Fuhrhop, S. Svenson, P. Luger, and C. Andre´, Supramol. Chem. 2:157–171 (1993). J.-H. Fuhrhop and S. Svenson, in Kinetics and Catalysis in Microheterogeneous Systems (M. Gra¨tzel and K. Kalyanasundaram, eds.), Surfactant Science Series, Vol. 38, Marcel Dekker, New York, 1991, pp. 273– 301. V. Zabel, A. Mu¨ller-Fahrnow, R. Hilgenfeld, W. Saenger, B. Pfannemu¨ller, V. Enkelmann, and W. Welte, Chem. Phys. Lipids 39:313 (1986). S. Svenson, Ph.D. thesis, Free University, Berlin, 1993.

34 Stereochemistry of Lipid Micelles and Vesicles That Survive Drying ¨ RGEN-HINRICH FUHRHOP JU

I.

Freien Universita¨t Berlin, Berlin, Germany

INTRODUCTION

observes collapse to circular structures with a flat bilayer in the center. Vesicles are also disrupted at watersolvent interfaces. When the vesicle bilayer in water is in the fluid state and is brought in contact with immiscible solvents, monomers are deposited at the interface [8] and monolayers are formed if the bulk concentration is above 10⫺5 M. The monolayer at a water-CCl4 interface is much less ordered than at the water-air interface. Long alkyl chains stand perpendicular in the organic phase, but infrared spectra show disordering. Fluid micellar rods (hexagonal phase) are obtained in concentrated aqueous solutions of amphiphiles that form spherical micelles in dilute solution. They may be isolated in dry form under favorable circumstances (cast film, liquid crystals) [9]. Fluid vesicular fibers, on the other hand, are formed upon swelling of the soft crystals of insoluble lipids in water [10] (Fig. 3). They fade away upon drying. No binding forces between the headgroups are observed in these fibrous molecular assemblies, and crystallization does not occur. Another important tubule system is made of water-soluble urea and long-chain alkanes in water. These inclusion compounds form upon crystallization and decompose again in water [11]. Here one has a case where isolation of noncovalent fibers in the solid state is easy, but the fibers do not survive in water. Stability rises drastically if the monomeric amphiphiles are replaced by amphiphilic diblock copolymers, e.g., of polystyrene (PS) or polyethylethylene (PEE), and smaller blocks of polyacrylic acid (PAA), polyethylene glycol (PEG), or polyvinyl pyridine (PVP). Such

Spherical micelles in water are dynamic species that break up and reform. On a microsecond time scale, single surfactant molecules retreat from and travel toward micelles, and within milliseconds the whole micelle, typically made of less than 100 amphiphilic molecules, disintegrates [1,2]. The reason for the short lifetime of micelles lies in the large distance and repulsive interaction between hydrated headgroups and the relatively high critical concentration of monomers that is needed to form micelles [critical micelle concentration (cmc) ⬵ 10⫺2 M]. Detergent micelles in water can only be observed by cryo-transmission electron microscopy (TEM) [3,4] (Fig. 1) because they disintegrate immediately on solid surfaces. Their diameter corresponds directly to the length of two detergent molecules, typically 4–5 nm. Micelles dissolve compounds that are not soluble in the bulk solvent. Detergent micelles usually take up just one water-insoluble dye [5] molecule or a hydrogen-bonded dimer [6]. Vesicles have a much lower critical concentration of monomers in water, namely 10⫺5 M or lower. They are made of mono- or bilayer membranes containing tens of thousands of water-insoluble amphiphilic molecules. They are stable for months in aqueous solutions and survive ultrafiltration as well as gel chromatography. On drying they collapse first to flat disks with bulgy edges and then dissipate [7] (C. Bo¨ttcher, unpublished) (Fig. 2). Aqueous phase vesicles do not survive on solid-air or liquid-liquid interfaces. If one dries vesicles on carbon grids, gold surfaces, or mica, one invariably 715

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FIG. 1 Micrographs of spherical micelles. (a) Cryo-TEM of an eicosane sulfate micelle fixated by rapid freezing (from Ref. 3). (b) AFM of a polystyrene-thiophene11-polystyrene triblock copolymer on mica from a toluene solution. (c) TEM of a closed film of the same polymer (from Ref. 14). (d) TEM of dendrimer micelles (from Ref. 18).

FIG. 2 Micrographs of spherical vesicles. (a) Typical cryo-TEM of lecithin-cholesterol vesicles. (b) TEM of (styrene)200 (acrylate)8 vesicle in water/DMF 4 : 1. The mean lamellar thickness is 30 nm (from Ref. 15). (c) Aqueous suspension of t-butyl[CH2-CH(C2H5)]37-(CH2CH2O)4-H copolymer. The mean lamellar thickness is 8 nm (from Ref. 19).

Stereochemistry of Lipid Micelles and Vesicles

717

FIG. 3 TEMs of micellar rods made of cross-linked diblock polymers. (Left) From cyclopentane solutions of polystyrenepoly(2 cinnamoyl methacrylate) (from Ref. 13). (Right) From polystyrene-polyacrylate in water (from Ref. 15).

amphiphiles with very large immiscible blocks of solvophilic and solvophobic monomers tend to form spherical or ellipsoidal micelles. Because covalent bonds do not allow separation into two bulk phases, one observes the aggregation of soluble blocks into domains within the matrix of insoluble blocks. The resulting micellar domains can then be observed by TEM. Diameters of 10–200 nm are typical. These polymeric micelles are usually formed in organic solvents, e.g., methanol/acetone or toluene (Fig. 1) and dissolve inorganic salts or colloids [12–16] in their cores. Heck reactions, for example, could be carried out in toluene instead of dimethylformamide (DMF) and similarly unpleasant polar solvents. Palladium acetate in copolymer-stabilized toluene solutions was exceptionally stable and remained active after 50,000 turnover cycles, which involve the same number of Pd2⫹/Pd0 conversions [17]. Another type of stable micelle is made of just one single spherical dendrimer molecule. They are usually based on three or four building blocks of first-generation monodendrons, which are often connected in the center. The maximal number of such monodendrons in a spherical micelle is, depending on size, between 8 and 18. Dendrimers can also easily be visualized by TEM without freezing in the solvent [18] (Fig. 1). Amphiphilic diblock copolymers of long PS and short PAA blocks give micellar spheres, cylinders, and vesicles under different conditions. Polymers consisting of cores of insoluble blocks surrounded by a thin shell of soluble blocks are called crew-cut. The morphology of their aggregates is, in addition to the usual repulsive and attractive interactions in micelles, controlled by the surface torsion at the core-corona interface at the onset of micellization. This interaction can be modified by the addition of ions and change of solvents. Hard spherical micelles are, for example, formed in DMF,

and vesicles appear in tetrahydrofuran (THF) because the central core swells. In TEM such polymer vesicles appear as three-dimensional (3D) spheres with a dent in the center. They contain so much material that flattening does not occur upon drying. Copolymers of PEG and EE (PEG40-PEE37), however, produce perfectly unilamellar vesicles, which are osmotically active (Fig. 2) [19]. In contrast to lipid vesicles in water, the polymer membranes in organic solvents have not been shown to build up osmotic pressure. The physical properties of the thick polymer walls in fluid droplets are hardly differentiated in micelles and vesicles. The strict separation of two water volumes by spherical membranes remains a unique property of lipidic vesicles. Reverse micelles made of block polymers dissolve inorganic salts (e.g., a palladium catalyst for reactions between organic substrates). Cylindrical micelles made of amphiphilic copolymers appear in a variety of morphologies in the solid state. Most of them are made of covalent block copolymers, where the solvent preferentially solvates only one of the blocks. TEM usually shows striations close to the size of the corresponding spherical micelles. The coagulation to cylinders is reversible on raising the temperature or changing the solvent. Cylinder formation is controlled by a balance between separation of the lyophobic tails and the respulsion between the solvated headgroups. The relatively large surface energy at the hemispherical ends of the molecular cylinders then provides a driving force for the formation of long cylinders. Most of the polymer micelles are, however, reverse micelles in organic solvents. The polymers are quite insoluble and growth of the individual noncovalent fibers is limited. Typically one obtains average lengths around 500 nm and diameters of 20 nm (Fig. 3, left side).

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Covalent polymeric tubules are, to the best of our knowledge, not obtained from diblock polymers. They are, however, ubiquitous in nature. Typical examples are rolled-up ␤-sheets or interwound helices of proteins [20], the helices of starch, which entrap I ⫺ 3 as a blue polymer with an inner diameter of about 1 nm [21], and cellulose tubules of 1 ␮m diameter. Only the latter are useful for entrapment in the form of hollow rayon fibers [22]. The walls of these biopolymers are rigid and do not dissolve anything, in contrast to the artificial micellar polymers described so far. Water-soluble compounds may be entrapped within the central, waterfilled cavity. In synthetic polymers a hollow center is obtained only by mechanical means (Fig. 4). The following section deals with solid noncovalent micellar and vesicular spheres, rods, and tubules. It will be shown that strong binding interactions between the headgroups do not necessarily lead to 3D crystals but that highly curved structures can be maintained without solvation spheres. II.

AN ISOLABLE, NONCOVALENT SPHERICAL MICELLE

There are, to the best of our knowledge, no reports on spherical micelles that survive isolation from water or, in the case of reverse micelles, from organic solvents. Drying leads to powders or oil droplets. The reason for this instability of nanometer spheres lies in the necessity to maintain the solvation sphere around the headgroups. If headgroup repulsion vanishes, curvature fades away and bulk materials are formed. This assumption may, however, not be true if one connects the headgroups by strong amide hydrogen bonds in three

directions on the surface of a sphere. We have, for example, played with long-chain amide derivatives, e.g., of tris-(aminoethyl)-amine but obtained vesicles only upon sonication (M. Skupin, J.-H. Fuhrhop, unpublished). Dissolution in hot water and cooling never produced the expected micelles with a hydrogen-bonded network on the surface, but ill-defined precipitates were found. The first stable micelles were formed when we precipitated amphiphile 1 with a ruthenium tris-(bipyridine) dichloride headgroup by addition of hexafluorophosphate anions. One of the bipyridine units carried a long-chain malonic diester link, which aggregated in water to form bilayer membranes. We expected formation of a planar bilayer or, after sonication, vesicles. Cryoelectron microscopy as well as TEM of negatively stained material at low-dose electron irradiation showed, however, multilayered micelles instead of ves˚ -wide bilayer of a spherical miicles (Fig. 5). A 45-A celle could be reproducibly observed in the center of the smaller micelles. The sequence of events in the formation of the onion-type micelles was then elucidated by cryo-TEM a few seconds after the addition of PF⫺6 . At first, large vesicles filled with microcrystalline debris of the ruthenium complex amphiphile appeared. After continued sonication or longer aging, the crystallites disappeared and the vesicles filled up to the center with alternating ruthenium and alkyl layers. No planar multilayers were ever observed in aqueous media. The micellar solution was then placed on solid mica or gold surfaces and atomic force microscopy (AFM) pictures were taken in the trapping mode. Perfect spheres with about equal width and height were observable for several hours. After days, some flattening occurred [23].

FIG. 4 Light micrographs of vesicular tubules. (Left) Protrusions from lecithin crystals in water. The central hole has a width of about 50 nm (Prof. I. Sakurai, personal communication). (Right) Spun fiber of acetylated cellulose. The central hole has a width of several micrometers (from Bever, 1985, Ref. 22).


719

FIG. 5 Two TEMs of spherical micelles of 1. (a) Dried samples on a carbon grid. (b) Cryo-TEM in water. (c) AFM of the micelles on mica. The black and white stripes have a thickness of 2–3 nm each. They correspond to ruthenium complex and interdigitated alkyl bilayers (see Fig. 6) (from C. Draeger et al., 1999, from Ref. 23).

˚ 2) The cross-section anion of the headgroup (100 A is so much larger than that of the two alkyl chains (40 ˚ 2) that interdigitation takes place. Furthermore, the A ruthenium hexafluorophosphate headgroups show a unique tendency to dimerize directly on the side of the cube opposite to the position of the alkyl chains. The hydrophobic alkyl chains therefore stretch to both sides of the headgroup region and interdigitate on both sides. The growth of this interdigitated and double-sided network occurs in three dimensions and produces the spherical shape of multilamellar vesicles at first and after extended sonication multilayered micelles with a CH2 bilayer in the center (Fig. 6). We think that the combination of large headgroups with two long alkyl chains will in general produce stable spheres. Currently, we are synthesizing osmium and platinum analogues, but all kinds of water-stable di-

valent metal complexes of appropriate size and solubility should also work. Such particles may then be applied as light-collecting entities (Ru, Os) or catalytic particles (Pd, Pt) as well as water-soluble dyes (multivalent Fe, W, Mo compounds). The advantage of these metal complex micelles to metal/salt-loaded polymers as described in the introduction is the well-defined environment of and the distance between metal ions. There should also be no environmental problem with these assemblies. The micelles decompose simply on heating; the components are hydrolyzable to fatty alcohols, 2,2⬘-bipyridine, and malonate. The perfect organization of the pseudocrystalline micelle also causes the main disadvantage of the material as compared with block polymers. Swelling of the latter in organic solvent–water mixtures produces loose aggregates that readily dissolve substrates and reagents. The large solid

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ducing water-soluble reagents into the gaps by hydration-dehydration cycles using aqueous solutions. III.

FIG. 6 Molecular model of the multilayered, isolable micelles made of an amphiphilic ruthenium complex (from Ref. 23).

micelles can react only on the surface. It therefore seems mandatory to produce much smaller and uniform micelles before application in catalysis becomes feasible. Application as light-collection cells, on the other hand, is also straightforward with the large micelles and is currently under investigation. The question remains: Why are the ruthenium complex micelles stable without hydration spheres? Why do they survive drying and do not rearrange to form 3D crystallites when all repulsive hydration forces disappear? A possible answer is that the micelles are only kinetically stable. We propose that at first vesicles are formed upon ultrasonication by disruption of crystallites with interdigitated multilayers. These vesicles have a very low critical concentration (cmc) and upon further sonication fill up their interior with concentric rings in water. Interdigitation of the bilayers stabilizes the densely packed alkyl bilayer. The headgroup bilayer is less rigid and highly hydrated. Upon drying, the curvature does not disappear because the interdigitated alkyl bilayers keep the headgroups in place and thus allow 30–40% of empty space in the dried ruthenium layers. This then opens the possibility of intro-

A DRY, NONCOVALENT SPHERICAL VESICLE

Vesicles survive in contrast to micelles in gel chromatography. Their cmc is usually so low (80⬚C to room temperature [28,29]. The yield of these fibers was close to quantitative when rearrangement to crystals and thicker assemblies was prevented by addition of sodium dodecyl sulfate (SDS) micelles. These micelles obviously dissolve crystallites and lead the dissolved molecules back to the fiber. These fibers can be lyophilized and stored in solid form for years. After resuspension in water at room temperature, un-

FIG. 8 (a–c) TEM, image analysis and model of the quadruple helix N-octyl-D-gluconamide (uranyl acetate negatively stained) (from Ref. 28). (d) AFM of the nonstained fiber on mica (from Ch. Messerschmidt, unpublished).


723

FIG. 9 Molecular conformation of N-octyl-D-gluconamide 3 in the fiber shown in Fig. 8. A gauche bend in the headgroup allows strong hydration of the micellar fiber without disrupting the connecting hydrogen bond chain (from Ref. 30).

changed fibers appeared. Transfer to solid surfaces was also possible, and a net of quadruple helices was detected by AFM (C. Messerschmidt and J.-H. Fuhrhop, unpublished results) (Fig. 8d). Diastereomeric glyconamides do not form tightly wound helical micelles in water. They appear as rolledup sheets (mannon) or ill-defined twisted ribbons (galacton). The beautifully uniform and well-defined structure of the gluconamide fibers allowed a detailed analysis by solid-state 13C nuclear magnetic resonance (NMR) spectroscopy combined with x-ray analysis, solution NMR, and infrared spectroscopy. As a result, the curved molecular conformation shown in Fig. 10 was established. In water, the empty room left within the bend is filled with water molecules. Upon drying, intraand intermolecular hydrogen bridges between the headgroup hydroxyls stabilize the structure and help to keep the curvature. Kinetic stability is provided by strong and well-defined hydrogen bonds between individual OH groups of the carbohydrate chains [30,31]. The hydrocarbon skeleton of micelle-forming amphiphiles and bola-amphiphiles has been replaced by porphyrins bearing the same gluconamide or amino and amino acid headgroups [32–34]. These dyes of essen˚ ) then stack to form hytially square shape (7 ⫻ 7 A drogen-bonded micelles. The thickness of these fibers corresponds essentially to the sum of the length of two ˚ of the porphyrin core. These side chains plus the 7 A dye fibers can also be isolated in solid form, stored for months, and then resuspended in water. Another example is the ultrathin fiber of a tin(IV)-porphyrin bisgluconamide (Fig. 10) [33,34], which is essentially held together by stacking and hydrogen bonding between chloride axial ligands and H3O⫹. Porphyrin fibers usually do not fluoresce, whereas the monomers do. Similar fibers are also formed between cyanine dyes in water [35] (Jelly or Scheibe aggregates). These fibers

are not of micellar character but are held together only by dipole and van der Waals forces. In this case, a reverse fluorescence behavior was observed: only the high molecular aggregate fluoresces, not the monomers. The micellar fibers described here are very easy to prepare on a large scale. The monomers can be synthesized on the kg scale. Fiber formation in water occurs spontaneously and quantitatively upon heatingcooling cycles or pH change. They can also be deposited on solid surfaces without any change of structure. So far, however, there is no obvious application for this kind of new material. V.

DRY, NONCOVALENT VESICULAR FIBERS

Several amphiphiles and bola-amphiphiles with one or two secondary amide links form vesicular tubules in water. Long-chain diamides with amino and L-lysine headgroups dissolve in water at 85⬚C and pH 4 to a maximum concentration of 2 ⫻ 10⫺4 M. Upon raising the pH to 10.5, long uniform tubules appear with an inner diameter of 50 nm and a membrane thickness of 4.4 nm. The inside of the tubules is filled with water and can be stained with heavy metal salts by imbibement [36,37] (Fig. 11). The tubules were isolated in dry form, stored for 2 years, and resuspended in water. No degradation of the tubes and length/diameter ratios of up to 103 were observed. Similar tubules have also been obtained from gluconamide/galactonamide bilayers [37,38] and from amphiphilic porphyrins [39]. These fibers look similar to asbestos fibers and can be made on a large scale. They decompose upon addition of ethanol or heating above 75⬚C in water or to 150⬚C in air. Because these fibers are made of fatty acids or amines and glucose or amino acids, they are readily biodegradable.

724

Fuhrhop

FIG. 10 33).

VI.

TEM and model of a noncovalent, micellar porphyrin fiber typical for protoporphyrin-type amphiphiles (from Ref.

CONCLUSION

Spherical and fibrous micelles and vesicles have been obtained for the first time in solid form. They survive drying, which removes the repulsive hydration forces. They are kinetically stable for different reasons: 1.

2.

The spherical micelle made of the ruthenium complex 1 cannot crystallize because the interdigitating bilayers do not allow flattening of curvature upon drying. The headgroup regions are hydrated in aqueous solution, but removal of the hydration wafer headgroup does not disturb the bilayer of the ruthenium complex. The spherical vesicle made of porphyrin-bixin 2 does not collapse upon removal of the entrapped water because the stiff amphiphiles cannot disen-

3.

4.

tangle. A mixture of porphyrin atropisomers also prevents formation of 3D crystals. The rigid gluconamide fiber keeps its shape in the dry state because the bent conformation of the headgroup is stabilized by strong intra- and intermolecular hydrogen bonds. Dehydration does not destroy the curvature. The most stable of all amphiphilic assemblies are vesicular tubules, which are stabilized by van der Waals interactions between the alkyl chains, hydrogen bond chains between the headgroups, and very low cmc values below the melting point of the amide hydrogen bond chains.

The only common structural motif in all of these solid spheres, rods, and tubules is an ultrathin (ⱕ5 nm) membrane. The rigidity of the different membrane sys-


725

FIG. 11 TEM and model of the monolayered tubules made of bola-amphiphiles with two different headgroups, e.g., amino and amino acid groups, and secondary amide links in the hydrophobic chain. The diacetylene units lead to polmeric fibers upon UV irradiation (from Ref. 36).

tems is, however, not coupled with a uniform, crystallike ordering. The polyene carboxylates lie in a chaotic crisscross ordering. The ruthenium complex bilayer forms concentric, interdigitated bilayers of extremely different curvature. The gluconamide quadruple helices produce exquisite regularity in pitch, fiber width multiplicity, and molecular conformation. The vesicular tubules, made of amino acid bola-amphiphiles, all have the same inner diameter of 50 ⫾ 10 nm and the membrane thickness is exactly 4.1 nm. The mesoscopic measures of the assemblies in the given examples are usually uniform, stable, and reproducible. They compare favorably to covalent biopolymers and the best unidisperse polymers. The dry lipid assemblies are, on the other hand, so hard that they do not dissolve anything. The selective dissolution of soft metal colloids and hard polyols, which works perfectly with fluid polymer and lipid membrane systems, is out of reach. The colloids can be used only as reactive particles in the same way as

functional proteins. They need to be loaded with fitting ‘‘coenzymes’’ and substrates will react only on the surfaces. Defined surface clefts have not been realized with the solid membraneous particles described here. The ruthenium complex micelle is currently mixed with corresponding osmium, platinum, and palladium analogues. The micellar fibers have been decorated on the surface with colloidal metal spheres, but no interparticle connection could be achieved. The vesicular tubules can be filled with all kinds of salts, e.g., silver nitrate. Attempts to produce continuous silver wires by reduction so far have failed. A new approach, which combines the motifs of rigid amide hydrogen bond chains and the self-assembly of membranes in order to form enzyme-like surface gaps, is based on successive binding of flat and upright standing amphiphiles on the surface of gold electrodes or colloids. At first, a porphyrin is bound flatly on the gold surface, and this is then embedded in a rigid monolayer

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Fuhrhop 9. 10. 11. 12. 13. 14.

15. 16. 17.

FIG. 12 Self-assembled membranes containing reactive angstrom gaps on colloidal particles of micellar size (d = 10– 20 nm). Water- or solvent-soluble particles are obtained depending on the headgroups of the amphiphiles (from J.-H. Fuhrhop, unpublished).

18. 19.

20.

containing two secondary amide group hydrogen bond chains. The resulting hydrophobic porphyrin-sized gaps take up water and bind fitting solutes in the entrapped ‘‘hydrophobic water’’ volume [40,41]. These reactive membrane systems can then be transferred to colloidal gold particles and other smooth colloids (Fig. 12). REFERENCES 1. 2.

3. 4. 5. 6. 7.

8.

J. H. Fendler, Membrane Mimetic Chemistry, Wiley, New York, 1982. J.-H. Fuhrhop and J. Ko¨ning, Molecular Assemblies and Membranes, Monographs in Supramolecular Chemistry (J. F. Stoddart, ed), Royal Society of Chemistry, London, 1994, i–xiii, 1–227. L. Bachmann, W. Dasch, and P. Kutter, Ber. Bunsenges. Phys. Chem. 85:883 (1981). J. L. Burns, Y. Cohen, and Y. Talmon, J. Phys. Chem. 94:5308 (1990). J.-H. Fuhrhop and M. Baccouche, Liebigs Ann. Chem. 2058 (1976). J. S. Nowick, J. S. Chen, and G. Noronha, J. Am. Chem. Soc. 115:7636 (1993). J.-H. Fuhrhop, H. H. David, J. Mathieu, U. Liman, H.J. Winter, and E. Boekema, J. Am. Chem. Soc. 108: 1785 (1986). R. A. Walker, J. A. Gruetzmacher, and G. L. Richmond, J. Am. Chem. Soc. 120:6991 (1998).

21. 22.

23.

24. 25. 26.

27.

28.

29. 30. 31.

N. Kimuzuka, T. Kawasaki, K. Hirata, and T. Kunitake, J. Am. Chem. Soc. 120:4094 (1998). I. Sakurai, T. Karrabura, A. Dahurai, A. Kegami, and T. Setoi, Mol. Cryst. Liq. Cryst. 130:203 (1985). K. D. M. Harris, J. Solid State Chem. 106:83 (1993). S. Fo¨rster and M. Antonietti, Adv. Mater. 10:195 (1998). J. Tao, S. Stewart, G. Liu, and M. Yang, Macromolecules 30:2738 (1997). M. A. Hempenius, B. M. W. Langeveld-Voss, J. A. E. H. van Haare, R. A. J. Janssen, S. S. Sheiko, J. P. Spatz, M. Mo¨ller, and E. W. Meijer, J. Am. Chem. Soc. 120: 2798 (1998). L. Zhang and A. Eisenberg, J. Am. Chem. Soc. 118: 3168 (1996). Y. Yu and A. Eisenberg, J. Am. Chem. Soc. 119:8383 (1997). S. Klingelho¨fer, W. Heitz, A. Greiner, S. Oestreich, S. K. Fo¨rster, and M. Antonietti, J. Am. Chem. Soc. 119: 10116 (1997). L. Balagh and D. A. Tomalia, J. Am. Chem. Soc. 120: 7355 (1998). B. M. Discher, Y. Y. Won, D. S. Ege, J. C. M. Lee, F. S. Bates, D. E. Discher, and D. A. Hammer, Science 284:1143 (1999). D. Voet, and J. G. Voet, Biochemistry, John Wiley & Sons, Inc., New York, 1990. W. Hinrichs and W. Saenger, J. Am. Chem. Soc. 112: 2789 (1990). M. B. Bever, Encyclopedia of Materials Science and Engineering, Pergamon Press, Oxford, New York, Toronto, Sydney, Frankfurt, Vol. 6, p. 4083, 1986. C. Draeger, C. Boettcher, C. Messerschmidt, L. Ruhlmann, J.-H. Fuhrhop, U. Siggel, and L. Hammarstroem, Langmuir 16:2068 (2000). H. Ohno, S. Takeoka, and E. Tsuchida, Polymer Bull. 14:487 (1985). H. Ringsdorf, B. Schlarb, and J. Venzmer, Angew. Chem. Int. Ed. Engl. 27:113 (1988). T. Komatsu, E. Tsuchida, C. Bo¨ttcher, D. Donner, C. Messerschmidt, U. Siggel, W. Stocker, J. P. Rabe, and J.-H. Fuhrhop, J. Am. Chem. Soc. 119:11660 (1997). J.-H. Fuhrhop, and S. Svenson, Stereochemistry and Separation Processes in Lipid Aggregates, in K. Kalyanasundaram and M. Gra¨tzel (eds), Kinetics and Catalysis in Microheterogeneous Systems (Surfactant Science Series), M. Dekker Inc., New York, 273–302, 1991. J. Ko¨ning, C. Bo¨ttcher, H. Winkler, E. Zeitler, Y. Talmon, and J.-H. Fuhrhop, J. Am. Chem. Soc. 115:693 (1993). J.-H. Fuhrhop and B. Rosengarten, Synlett 1015 (1997). S. Svenson, B. Kirste, and J.-H. Fuhrhop, J. Am. Chem. Soc. 116:11975 (1994). S. Svenson, J. Ko¨ning, and J.-H. Fuhrhop, J. Phys. Chem. 98:1022 (1994).

Stereochemistry of Lipid Micelles and Vesicles 32. 33. 34. 35. 36. 37.

J.-H. Fuhrhop, C. Demoulin, C. Bo¨ttcher, J. Ko¨ning, and U. Siggel, J. Am. Chem. Soc. 114:4159 (1992). J.-H. Fuhrhop, U. Bindig, and U. Siggel, Chem. Comm. 1583 (1994). J.-H. Fuhrhop, U. Bindig, and A. Schulz, New J. Chem. 19:427 (1995). A. H. Herz, Adv. Colloid Interface Sci. 8:237 (1977). J.-H. Fuhrhop, D. Spiroski, and C. Bo¨ttcher, J. Am. Chem. Soc. 115:1600 (1993). J.-H. Fuhrhop, P. Blumtritt, Lehmann, and P. Luger, J. Am. Chem. Soc. 113:7437 (1991).

727 38. 39. 40.

41.

J.-H. Fuhrhop and C. Bo¨ttcher, J. Am. Chem. Soc. 112: 1768 (1990). J.-H. Fuhrhop, U. Bindig, and U. Siggel, J. Am. Chem. Soc. 115:11036 (1993). J.-H. Fuhrhop, L. Ruhlmann, C. Messerschmidt, W. Fudickar, J. Zimmermann, and B. Roeder, Pure & Appl. Chem. 70:2385 (1998). W. Fudickar, J. Zimmermann, L. Ruhlmann, J. Schneider, B. Roeder, U. Siggel, and J.-H. Fuhrhop, J. Am. Chem. Soc. 121:9539 (1999).

35 Synthesis and Properties of Amphiphile-Based Gene Carriers NILY DAN

I.

Drexel University, Philadelphia, Pennsylvania

INTRODUCTION

linked to their performance in vivo [9–11]. Implementation of synthetic gene carriers requires, therefore, the ability to control their material properties during the synthesis stage. In this chapter we examine the synthesis of lipidbased gene carriers, concentrating on the relationship between system parameters (e.g., lipid type, solution composition) and the properties of the DNA-lipid complex. Although this system is somewhat specialized, many aspects of its phase diagram are relevant to the synthesis of other amphiphile-based, multicomponent materials that are ordered on the nanoscale. Examples include surfactant-colloid complexes [12], surfactantprotein aggregates (O. Regev, private communication), and surfactant-polymer assemblies [13–15]. DNA-lipid complexes are formed by mixing DNA with cationic liposomes. The synthesis of such materials is based, therefore, on self-assembly between oppositely charged molecules as well as the inherent selfassembly tendencies of the amphiphilic lipids. The liposomes used are typically unilamellar and contain a mixture of cationic and nonionic lipids. System parameters include, therefore, three compositional variables (DNA concentration, the ratio of DNA anionic charges to cationic lipid charges in solution, and the concentration ratio between the cationic and nonionic lipids). Other parameters include pH, salt concentration, and the valence of the solution ions. The structures formed by DNA-lipid complexation are characterized by two length scales. One scale relates to internal ordering (generally of order 1–10 nm);

Gene therapy techniques aim to eliminate disease by correcting the cell genome, which requires introducing healthy genes that can replace damaged ones into the cell environment. Techniques for the identification and synthesis of disease-related genes are now common. However, gene therapy cannot be implemented without the development of a reliable and efficient mechanism for gene delivery into affected cells. ‘‘Naked’’ genes cannot enter cells because the coil dimension of the rigid DNA is too large to allow transport through the intact cell membrane [1,2]. Moreover, cell membranes carry a net anionic charge that repels the highly charged, anionic DNA. Therefore, to transport genes into and through cells one must develop a mechanism that will both condense and invert the charge of the DNA coil [3–8]. Current techniques utilize recombinant viral vectors to deliver genes into cells. Although such carriers are highly efficient, they require extensive manipulation to eliminate toxic and immune responses. Their use in human therapy is also challenged by the need to prevent the generation of replication-competent viruses by the carrier, the limited size of genetic inserts, and their inability to target specific cell populations [3–8]. Synthetic gene carriers utilize complexes between DNA and either cationic polymers or cationic lipids. The cationic agent condenses the expanded DNA coil and reverses its anionic charge, thereby lowering the barriers for transmembrane transport. The structure and properties of synthetic gene carriers have been clearly 729

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the other describes the globular or overall aggregate dimensions (0.1–1 ␮m). Various studies suggest that whereas the internal structure is reversible and reproducible, the globular structure is nonreversible and dependent on sample history [16–19]. Moreover, there are strong indications that carrier efficiency is linked to the internal rather than globular structure [13–21]. Therefore, we will focus the discussion in this chapter on the internal composition and geometry of DNAlipid complexes. What determines the internal structure of DNA-lipid complexes? One possibility is that each component (i.e., DNA coil and lipid liposomes) keeps its preferred form. Indeed, Felgner et al. [22] suggested that the liposomes may adhere, intact, to the DNA chain in a manner similar to that of surfactant micelles adhering to an oppositely charged polyelectrolyte [23]. Another possibility is that one component may impose its geometry on the other; this will lead to tubular DNA coated by a lipid bilayer [22] or to spherical liposomes coated by an adsorbed DNA layer. However, it is well known that mixing amphiphiles can lead to the formation of new phases (e.g., equilibrium vesicles [24]). Mixing lipids with DNA may result in similarly unexpected structures. Several types of DNA-lipid complexes have been observed, as sketched in Fig. 1. The complex structures were shown to depend on the choice of the cationic and nonionic lipids as well as the different composition parameters [16,20,21,25–34]. In Section II we review the different aggregate types and their characteristics. In Section III we discuss the DNA-lipid phase diagram, and we conclude with a brief summary in Section IV. II.

DNA-LIPID AGGREGATES: GEOMETRY AND CHARACTERISTICS

The transfection properties of lipid-based gene carriers have been investigated for a couple of decades [3–8]. Lately, attention has focused on systematic investigation of their phase diagram and the relationship between structure and performance [25–27]. Several experimental methods have been used to investigate the structure of DNA-lipid complexes. These include freeze-fracture and cryoelectron microscopy, which provide direct images on scales of 10 mm to 1 ␮m; high-resolution synchrotron x-ray diffraction measurements (SAXS), which can identify order on the 1– 10 nm scale; and fluorescence and circular dichroism, which enable probing on the molecule scale. As will be shown presently, the structure of DNAlipid complexes depends not only on the system compositional parameters but also on the type of lipid mix-

FIG. 1 The different types of complexes observed for DNA-liposome aggregates. (a) Nonequilibrium structures. Coated liposomes are formed when the anionic DNA adsorbs onto the exterior of the cationic liposome [18,19]. Tubular aggregates form when the DNA is encapsulated within a lipid bilayer [9,33,34]. (b) Equilibrium structures. Multilamellar structures obtain when ordered DNA layers alternate, in a stack conformation, with cationic bilayers. The DNA layers are characterized by a finite spacing between adjacent DNA units, which is, as a rule, somewhat larger than close packing (see Fig. 2) [16,25–28]. Inverted hexagonal structures are formed when DNA molecules, encapsulated by a lipid monolayer, order in a hexagonal array [20,21,29].

ture. Systems investigated include the cationic lipids N-(1-(2,3-dioleoyloxy)propyl)-N,N,N-trimethylammonium chloride (DOTAP), N-(1-(2,3-dioleyloxy)propyl)N,N,N-trimethylammonium chloride (DOTMA), 3␤[N-(N⬘,N⬘-dimethylaminoethane)cabamoyl]- cholesterol (DC-Chol), N,N-dioctadecyl-lysineamine (lipid 43), N⬘,N⬘-dioctadecyl-1,2,6-triaminohexane (lipid 47), 1,2-dimyristoyloxypropyl-3-dimethyl-hydroxyethylammonium bromide (DMRIE), and 2⬘-(1⬙,2-dioleoyloxypropyldimethylammonium bromide)-N-ethyl-6-amidospermine tetratrifluoro-acetic acid (DOSPA), all of which are bilayer forming. The nonionic lipids used were 1,2-dioleoyl-sn-glycero-3-phosphatydylcholine (DOPC), which is bilayer forming, and 1,2-dioleoylsn-glycero-3-phosphatylethanolamine (DOPE), which forms inverted hexagonal phases. In some cases the liposomes also contained cholesterol (Chol), hexanol, monooleoyglycerol (MOG), or the zwitterionic 1,2-dimyristoyl-sn-glycero-3-phosphocholine (DMPC). A.

DNA Complexes with Unperturbed Liposomes

A common architecture of polyelectrolyte complexes with oppositely charged micelles is one where the micelles are attached, by electrostatic attraction, to the

Amphiphile-Based Gene Carriers

polyelectrolyte coil [23]. The similarities between this polyelectrolyte-micelle system and DNA-liposome systems have led to speculation that the latter may display such configurations [22]. To date, however, such arrays have not been observed. Another type of assembly between relatively unperturbed liposomes and DNA is one where the DNA adsorbs and coats the exterior of the liposome, as sketched in Fig. 1. Such structures have been inferred from zeta potentials [17] or directly observed by electron microscopy [18,19] in several different lipid systems, such as liposomes containing DMRIE, lipid 43, lipid 47 or DOSPA [17], DOTAP-DOPE and DOTAPChol mixtures [18], or DMPC–DC-Chol mixtures [19]. B.

Tubular Lipid-DNA Structures

Tubular DNA-lipid structures are structures in which the DNA is coated by a lipid bilayer, as sketched in Fig. 1. Such structures, characterized by a 7 nm diameter, were first identified in freeze-fracture electron micrographs by Sternberg et al. [33]. This diameter corresponds exactly to the DNA diameter plus the width of a bilayer. The liposomes used contained mixtures of DC-Chol and DOPE, and the DNA-to-lipid charge ratio was varied over a relatively large range. In systems that were allowed to incubate for long periods of time or in which the DNA concentration was high, globular objects of order 100 nm were found to attach to the tubular DNA complexes. The authors assumed that the globules were unperturbed cationic liposomes attached to the coated DNA strand either by electrostatic interactions or by fusion [33]. Tubular DNA aggregates were found in other systems as well. Hui et al. [9] observed, using freeze-fracture electron microscopy, tubular-fused globule arrays in liposomes containing either DOPC or DOPE. Xu et al. [34] observed tubelike aggregates whose diameter was 10 nm, partially adsorbed or extending from the surface of fused globules, in systems containing DOTAP-MOG, pure DOTAP, DOTAP-DOPC, or DOTAP-DOPE. However, the tubular aggregates were extremely short except in the case of DOTAP-DOPE complexes. C.

(Inverse) Hexagonal Arrays

Other experiments identified hexagonal (HCii) DNAlipid phases [20,21]. In this type of aggregate (see Fig. 1) DNA strands, coated by a lipid monolayer, are packed into a dense inverted hexagonal array. The hexagonal phases were observed in two types of systems: (1) liposomes containing a mixture of DOTAP and DOPE [20,21,29] and (2) liposomes containing a high ratio of hexanol to DOTAP-DOPC mixtures [20,21].

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Circular dichroism studies conducted by Zuidan et al. [29] for DNA complexes with DOTAP-DOPE liposomes showed that DNA molecules in these complexes display both secondary and tertiary structure transitions, interpreted as the formation of tightly packed phases characterized by long-range chiral order. They [29] concluded that in these aggregates most of the DNA is packed into an inverted hexagonal lipid phase, which imposes long-range order and spatial organization. D.

Lamellar Lipid-DNA Phases

One of the most common phases obtained by the synthesis of DNA-lipid aggregates is that of lamellar aggregates, where two-dimensional liquid crystalline arrays of DNA are sandwiched between cationic bilayers (see Fig. 1). This type of aggregate may seem the most obvious way of packing lamellar sheets with rodlike objects while allowing each component to keep its original geometry. However, it was not clearly identified until recently [25–28]. To date, lamellar phases have been observed in DNA mixtures with cationic liposomes containing pure DOTAP [25–28,34] or mixtures of DOTAP and DOPC at all ratios at which the two lipids mix [20,21]. Using DOTAP-DOPE liposomes led to the formation of lamellar arrays when the DOPE concentration in the liposome was low or moderate [20,21,31]. Multilamellar aggregates were also observed using cryomicroscopy in systems of DMPC–DC-Chol at low DNA-to-lipid charge ratios [19]. What is the configuration of DNA in the multilamellar aggregates? SAXS experiments [26–28] found that the spacing between adjacent bilayers was equivalent to the diameter of a DNA molecule, suggesting that the DNA is flatly adsorbed to the lamellar surfaces. This is in agreement with experiments of D. HirschLerner and Y. Barenholz (private communication) that show strong dehydration upon complex formation. DNA was found to order in a two-dimensional, liquid crystalline array between the multilamellar bilayers (see Fig. 1). The DNA array was characterized by a finite spacing limited to a relatively narrow range, between close packing (2.5 nm) and slightly larger values (6 nm), regardless of system parameters [19,25–28]. Similar configurations with similar DNA spacing were found in DNA adsorption on a single, supported cationic bilayer [35]. The DNA spacing in multilamellar aggregates was found to vary with the ratio of anionic DNA charges and cationic lipid charges in the solution, as sketched in Fig. 2 [21,26–28]. The DNA packing was found to

732

decrease rapidly with the DNA-to-lipid charge ratio in a narrow region around the isoelectric point (where the number of DNA charges in solution equals that of the cationic lipids). On either side of this transition region, the DNA spacing remained relatively constant [21,26– 28]. The width of the transition region was found to vary as a function of the salt concentration and fraction of nonionic lipid [21]. Only complexes obtained from solutions at exactly the isoelectric point were charge neutral. Complexes obtained at any other solution composition were shown to be either undercharged or overcharged [21,26–28]. In systems where the cationic lipids were in excess, fluorescence data showed the presence of many lamellar defects, indicating boundaries between DNA-rich regions and bare bilayer one [31]. The invariance of the DNA spacing as a function of DNA-to-lipid charge ratio in the limit of high DNA content can be interpreted as a saturation process, although one might have expected that the saturated structures would be charge neutral rather than overcharged. However, the constant DNA spacing in the limit of low DNA content and the coexistence between bare bilayer regions and regions containing complexed DNA indicate that, in this limit, there is a preferred DNA spacing that is set by the system parameters. The effect of (monovalent) salt concentration on the DNA was also examined [21]. In isoelectric systems

FIG. 2 The effect of the DNA-to-cationic lipid charge ratio on the spacing of DNA in multilamellar aggregates [21,25– 28]. The spacing is defined as center to center and is in most cases slightly larger than close packing (2.5 nm). At a low DNA-to-lipid charge ratio (namely, when the liposomes are in excess), the DNA spacing is usually of order 6 nm and does not decrease when more DNA is added to the solution. Around the isoelectric point, where the DNA-to-lipid charge ratio is unity, a sharp decrease is observed. The transition region ends somewhat above the isoelectric point. Beyond this region, the DNA spacing does not decrease any further. The lower value of the DNA spacing is equal to close packing only when the lipid bilayer is purely cationic. In mixed cationic-nonionic bilayers, this spacing is usually of order 4 nm.

Dan

with a high cationic-to-nonionic lipid ratio, the DNA spacing was found to increase strongly with salt concentration. This increase was associated with release of DNA from the complex into solution [21]. However, quite unexpectedly, in an isoelectric system in which the nonionic lipid content was high, the DNA spacing was found to vary nonmonotonically with salinity, slightly increasing and then decreasing with salt [21]. III.

DNA-LIPOSOME PHASE DIAGRAM

DNA-lipid complexes are multicomponent systems. Experiments show that their structure and properties depend on the type of lipids used as well as three compositional parameters: the ratio of anionic DNA to cationic lipid charges, the concentration ratio of cationic to nonionic lipid, and the salt concentration. Several theoretical models examined different aspects of the DNA-lipid phase diagram and complex properties [36– 43]. The analysis is complicated by the large number of variables and the dominant effect of the electrostatic interactions, some of which are, to date, not well understood. We therefore focus here only on the main features in qualitative terms. A.

DNA-Lipid Interactions

The details of the DNA-lipid phase diagram cannot be understood without examining the forces driving the complex formation. Generally, salts form when the Coulomb attraction between oppositely charged ions overcomes the entropy of the individual ions. In small molecules dissolved in water, entropy usually wins and complete dissociation ensues [44]. However, the electrostatic attraction between highly charged macroions (such as polyelectrolytes or colloidal particles) and their counterions can overcome, to some degree, the counterion entropy. As a result, a fraction of the counterions condenses, namely remains in the vicinity of the macroion [44,45]. Complexation between two oppositely charged macroions releases some of their condensed counterions, resulting in a gain in system entropy. This gain is especially high for DNA because approximately three fourths of its counterions are condensed [45]. This qualitative description of macroion association (or precipitation) seems to indicate that such complexes would always prefer to be charge neutral. Yet, the phenomenon of charge inversion is well known in adsorbed polyelectrolyte layers [46,47] and polyanionpolycation complexes. Similarly, DNA-lipid complexes are rarely charge neutral [20,21,25–28].


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Why are charge-neutral complexes unstable? This instability is due to the fact that the degree of entropy loss of the condensed ions increases with increasing macroion charge density. For example, the thickness of the Gouy-Chapman layer near flat surfaces, which contains the condensed ions, decreases with increasing surface charge density [44]. Similarly, the fraction of counterions condensed on a rigid rod increases with the line charge density [45]. As a result, the system prefers not to form charge-neutral complexes coexisting with highly charged macroions where the condensed counterions are closely trapped. Instead, it forms aggregates with some excess charge that can redistribute over a large area, thereby reducing the overall charge density and counterion condensation penalty [36,37]. Although this analysis is obviously oversimplified, it explains qualitatively why equilibrium charge-neutral DNAlipid complexes are unstable and may be obtained only in isoelectric solutions in which the lipid-to-DNA charge ratio is unity [21,26–28]. B.

DNA-Lipid Phases

Four types of DNA-lipid structures have been observed, as sketched in Fig. 1. The experiments suggest that two of these are nonequilibrium, namely the coated liposomes [18,19] and the tubular ones [9,33,34]. Equilibrium phases include the inverted hexagonal and multilamellar arrays. DNA-coated liposomes seem to be the precursor, or initial stage, in the formation of dense phases. Electron micrographs show that the DNA either induces invagination or leads to coalescence of liposomes. In either case, the formation of multilayer complexes ensues [18,19], as can be seen in Fig. 3. The role of tubular aggregates is somewhat less clear. It is possible that they are an equilibrium structure that is difficult to identify, given the techniques commonly used to examine these systems. However, it is more likely that the tubular aggregates are a metastable state accommodating portions of DNA strands that either ‘‘dangle’’ from multilamellar aggregates or connect two such aggregates. Indeed, tubular aggregates are always observed near dense, spherical objects of order 100 nm to 0.1 ␮m [9,33,34], as can be seen in Fig. 3. Sternberg et al. [33] speculated that these objects are intact liposomes. However, the multilamellar aggregates observed by Radler et al. [26] are also spherical objects of the same order of magnitude and are connected by strands whose diameter is much smaller than the sphere dimensions. The speculation that tubular aggregates are metastable is supported by

FIG. 3 Cryoelectron micrographs of DNA-lipid complexes (D. Danino and Y. Talmon, unpublished). The liposomes are composed of a mixture of 1:1 mole ratio DOTAP to DOPE. The bar represents 0.2 ␮m. (A) DNA-to-cationic lipid charge ratio 1:10. The DNA, which is seen here as darker, thicker lines, adsorbed on the liposome exterior, thereby inducing invagination, which may lead, with time, to the formation of intra-multilayered structures. (B) DNA-to-cationic lipid charge ratio 1.5. The DNA adsorbs onto the exterior of the liposomes, thereby leading to adhesion between neighboring liposomes. This type of aggregate may evolve, with time, to an inter-multilayer structure.

theoretical models that predict that these are unstable when compared with either lamellar [40] or hexagonal [41] arrays but should be preferred to mixtures of naked DNA and bare lipid bilayers. The two types of equilibrium DNA-lipid complexes identified to date are inverted hexagonal and lamellar

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complexes. In the hexagonal aggregates, the DNA is encapsulated within an array of lipid monolayers [20,21,29]. In the multilamellar aggregates, ordered DNA layers alternate with bilayers [16,25–28]. What determines the type of equilibrium aggregate? The experimental evidence clearly shows that the type of equilibrium DNA-lipid complex formed is mostly dominated by the lipid properties [9,16–34]. Yet, how does the lipid type affect the equilibrium structure? Comparing the packing of DNA in the hexagonal versus lamellar arrays (Fig. 1), we see that in the former the DNA can be in much closer contact with the cationic lipids than in the latter. This close contact is expected to optimize the electrostatic interactions, which are very sensitive to the distance between opposing charges [44]. However, wrapping the DNA around in the hexagonal phase may be associated with a high bending penalty that may become prohibitive in the case of lipids that form lamellae. As a result, one would expect that hexagonal phases would be favored when the lipids used tend to form hexagonal phases. Indeed, such phases were observed when the lipid mixture contained a high fraction of a nonionic lipid known to form, in its pure phase, hexagonal arrays [20,21,29]. Complexes between DNA and lipid mixtures that contain a large fraction of lamella-forming cationic lipids or in which both cationic and nonionic components form lamellae are multilamellar [25–34]. Hexagonal phases are also likely to form in systems where the (monolayer) bending energy is relatively low, so that the energetic gain associated with the close lipid-DNA contact overcomes the penalty for monolayer bending [43]. The experiments of Koltover et al. [20,21] show that, as expected, reducing the lipid monolayer bending modulus leads to the formation of hexagonal phases, even though the preferred lipid phase is lamellar. C.

DNA Packing in Lamellar Aggregates

The density or spacing of DNA in lamellar aggregates is closely related to aggregate stability and gene transfer activity [3–11,20,21,25–28]. As a result, understanding the parameters controlling the DNA packing in multilamellar aggregates is not only of scientific interest but also of technological importance. What sets the DNA spacing? In charge-neutral complexes it is obviously controlled by the fraction of cationic lipid in the complex. Indeed, Radler et al. [26,28] and Koltover et al. [21] found that the DNA spacing in charge-neutral complexes that are formed from isoelec-

tric solutions consistently increased with the fraction of nonionic lipid in the mixture. As discussed earlier, charge-neutral aggregates are unstable except in isoelectric solutions [36,37]. Indeed, the experiments show that around the isoelectric point the DNA spacing in the multilamellar complex varies sharply as a function of DNA-to-lipid charge ratio [21,26–28]. However, on both sides of this transition region the DNA spacing was found to be mostly independent of the DNA content, regardless of the type of lipid mix or salinity. This behavior seems to indicate that the system’s energy is optimized when the complexes are at a specific degree of undercharging or overcharging, regardless of the amount of excess DNA or cationic lipid in the system. Using a Poisson-Boltzmann mean field model for the system electrostatics, Bruinsma [36] and Bruinsma and Mashl [37] showed that the charge-neutral complex is unstable to the addition of either excess DNA or excess lipid. This instability is due to the complexation mechanism discussed earlier, namely that the overall energy of a system containing charge-neutral complexes and highly charged (excess) DNA or bilayers is higher than that of an overcharged or undercharged complex with a lower charge density. The Bruinsma model [36,37] predicts a spacing versus composition plot qualitatively similar to those observed experimentally. It should be noted, however, that although the model is based on the assumption that the interrod spacing is much larger than the rod diameter, the experiments [25–28] found that the interrod spacing never exceeded three times the DNA diameter. The dependence of DNA spacing on the ionic strength was also investigated experimentally [21]. In general, increasing the salt concentration should increase the screening in the system, thereby reducing the penalty associated with counterion condensation and, thus, the driving force for complex formation. On the other hand, added salt also screens the inherently repulsive DNA-DNA interactions, which should allow the rods to pack more closely [50,51]. Koltover et al. [21] found that increasing the salt concentration generally leads to a sharp decrease in the DNA spacing, indicating that the DNA spacing is affected by the repulsive DNA-DNA interactions. More surprising, though, is their observation that at low salt concentrations the DNA spacing in systems in which the DNA content is low increases with salt [21]. A qualitatively similar trend was observed by Fang and Yang [35], who found that the spacing of DNA adsorbed on a single purely cationic bilayer increased with salt.


The Bruinsma [36,37] model cannot explain the dependence of the DNA spacing on the salt concentration because it was developed for the limit where no salt is present. Using a simple mean field model that can incorporate the effects of salinity, Dan [38,39] suggested that the DNA spacing in the lamellar aggregates is set, in the limit of low DNA concentration, by a balance between an attractive and a repulsive DNA-DNA interaction. The repulsive interaction is due to the electrostatic repulsion between similarly charged rods [50,51]. The attractive interaction was assumed to arise from the DNA-induced perturbation of the equilibrium bilayer packing. This assumption has been verified, to some degree, by the experiments of HirschLerner and Barenholz [31], who found that complexation with DNA perturbs the equilibrium packing of the lipids. The Dan model predicts that there is an optimal spacing (in the limit of low DNA-to-lipid charge ratio) that is set by the balance between these two interactions [38,39]. This optimal spacing would remain constant upon increasing the DNA content until the entire lipid bilayer is occupied. Above this point, additional DNA will continue to adsorb due to the high entropy gain associated with complexation, thereby reducing the spacing and leading to an instability near the isoelectric point. Although the Dan model cannot explain overcharging above the isoelectric point, it does predict that in the limit of low DNA concentrations the DNA spacing should first increase and then sharply decrease with added salt [39], as indeed observed by Koltover et al. [21]. This counterintuitive result indicates that, although electrostatics dominate lamellar complexes in systems where the DNA charge concentration is similar to or exceeds that of the cationic lipids, membrane perturbation is important in the opposite limit where the DNA content is low.

IV.

SUMMARY

The study of DNA-lipid complexes is of interest not only because of their technological application as gene carriers but also because they provide a model system for studying complex formation in charged, multicomponent, self-assembling systems. Understanding the forces dominating such assemblies will facilitate developing methods for the synthesis of novel materials characterized by ordered domains on the nanoscale. Analysis of the DNA-lipid system shows that the driving force for complexation is the release of counterions that are condensed on the highly charged DNA

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[45] or near the bilayer surface [42,43]. As a result, charge-neutral complexes are unstable and, in fact, may be obtained only from isoelectric mixtures where the ratio of the DNA anionic charges to lipid cationic charges in solution is unity [21,26–28]. This observation has significant practical implications because to target a specific cell population the net charge of the gene carrier must be small [49]. The instability of the charge-neutral complexes means that it is unlikely that lipid-based gene complexes may be used in systems where targeting is required. The counterion release mechanism for the formation of aggregates between oppositely charged macroions is not limited to the DNA-liposome system. It has been found to lead to blisters in membrane adhesion to surfaces [52] and the formation of colloidal rafts on oppositely charged vesicles [12]. Two types of equilibrium complexes have been identified to date: inverted hexagonal and multilamellar (Fig. 1). The type of equilibrium structure is set by the lipid properties. Therefore, complexes formed with a moderate to high content of hexagonal phase forming lipids are hexagonal, and those composed of bilayerforming lipids are lamellar [21]. Hexagonal complexes may also be obtained in systems where the bilayer bending modulus has been greatly reduced, for example, by introducing a cosurfactant such as cholesterol [21]. Two other types of complexes have also been observed: tubular aggregates and coated liposomes (Fig. 1). Tubular aggregates are a metastable state in which dangling DNA ends that cannot be incorporated into lamellar complexes are coated by a lipid bilayer rather than remaining naked (tubular). Coated liposomes, with DNA adsorbed to the exterior of liposomes, are an intermediate state that leads, with time, to the formation of lamellar or hexagonal phases (coated), as shown in Fig. 3. The DNA spacing in lamellar complexes determines the net complex charge as well as the size or number of genes that a complex may carry. Experiments show that the DNA spacing is fixed for either large or low DNA content in the system except for a narrow transition region near the solution isoelectric point [26– 28]. DNA spacing increases, for any solution composition, with increasing fraction of nonionic lipids [21]. However, increasing the salinity led to nonmonotonic behavior in the low DNA concentration limit. Analysis indicates that in solutions near and above the isoelectric point, DNA spacing is set by the system electrostatics [36,37], and in the limit of low DNA content membrane perturbation energy may play a role [38,39].

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ACKNOWLEDGMENTS

23.

Thanks to D. Danino for helpful discussions and for sharing her unpublished data (with Y. Talmon). The support of NSF-BES 0096004 is acknowledged.

24.

REFERENCES

26.

1. 2. 3. 4.

5. 6. 7. 8. 9. 10.

11. 12.

13. 14. 15. 16. 17. 18.

19. 20. 21. 22.

G. Maret and G. Weill, Biopolymers 22:2727–2744 (1983). S. Smith and A. J. Bendich, Biopolymers 29:1167– 1173 (1990). V. A. Bloomfield, Curr. Opin. Struct. Biol. 96:334–340 (1996). P. L. Flegner, ed., Artificial Self-Assembly Systems for Gene Delivery, ACS Conference Proceedings Series, American Chemical Society, Washington, D.C., 1996. E. Marshall, Science 269:1050–1055 (1995). C. P. Hodgson, G. Xu, F. Solaiman, and M. A. Zink, J. Mol. Med. 75:249–258 (1997). D. D. Lasic, Liposomes in Gene Delivery, CRC Press, Boca Raton, FL, 1997. J. P. Behr, Bioconj. Chem. 5:382–389 (1994). S. W. Hui, M. Langner, Y. L. Zhao, P. Ross, E. Hurley, and K. Chan, Biophys. J. 71:590–599 (1996). B. Strenberg, K. Hong, W. Zheng, and D. Papahadjopoulos, BBA (Biochimica et Biophysica Acta) 1375: 23–35 (1998). M. I. Angelova, N. Hristova, and I. Tsoneva, Eur. Biophys. J. 28:142–150 (1999). H. Aranda-Espinoza, Y. Chen, N. Dan, T. C. Lubensky, P. Nelson, L. Ramos, and D. A. Weitz, Science 285: 394–397 (1999). M. Swanson Vethamuthu, P. L. Dubin, M. Almgren, and Y. J. Li, J. Colloid Interface Sci. 186:414–419 (1997). M. Macdonald, Colloid Surf. A Phys. Eng. 147:115– 131 (1999). E. Sokolov, F. Yeh, A. Khokhlov, V. Y. Grinberg, et al., J. Phys. Chem. B 102:7091–7098 (1998). N. J. Zuidan, D. Hirsch-Lerner, S. Margulies, and Y. Barenholz, BBA 1419:207–220 (1999). S. J. Eastman, C. Siegel, J. Tousignant, A. E. Smith, S. H. Cheng, and R. K. Sheule, BBA 1325:41–62 (1997). N. Smyth-Templeton, D. D. Lasic, P. M. Frederik, H. H. Strey, D. D. Roberts, and G. N. Pavlakis, Nat. Biotech. 15:647–652 (1997). S. Huebner, B. J. Battersby, R. Grimm, and G. Cevc, Biophys. J. 76:3158–3166 (1999). I. Koltover, T. Salditt, J. O. Radler, and C. R. Safinya, Science 281:7881 (1998). I. Koltover, T. Salditt, J. O. Radler, and C. R. Safinya, Biophys. J. 77:915–924 (1999). P. L. Felgner, Y. J. Tsai, L. Sukhu, C. J. Wheeler, M. Manthorpe, J. Marshall, and S. H. Cheng, Ann. N. Y. Acad. Sci. 126–139 (1995).

25.

27. 28. 29. 30. 31. 32. 33. 34. 35. 36. 37. 38. 39. 40. 41. 42. 43. 44.

45. 46. 47. 48. 49. 50. 51. 52.

B. Cabane and R. Duplessix, J. Phys. Fr. 48:651–657 (1987). E. W. Kaler, K. L. Herrington, A. K. Murthy, and J. A. N. Zasadzinski, J. Phys. Chem. 96:6698–6707 (1992). D. D. Lasic, H. Strey, M. C. A. Stuart, R. Podgornik, and P. M. Frederik, J. Am. Chem. Soc. 119:832–834 (1997). J. O. Radler, I. Koltover, T. Salditt, and C. R. Safinya, Science 275:810–814 (1997). C. R. Safinya, I. Koltover, and J. Raedler, Curr. Opin. Colloid Interface Sci. 3:69–77 (1998). J. O. Radler, I. Koltover, A. Jamieson, T. Salditt, and C. R. Safinya, Langmuir 14:4272–4283 (1998). N. J. Zuidan, Y. Barenholz, and A. Minsky, FEBS Lett. 457:419–422 (1999). N. J. Zuidam and Y. Barenholz, Int. J. Pharmacol. 183: 43–46 (1999). D. Hirsch-Lemer and Y. Barenholz, BBA 1370:17–30 (1998) (probing). N. J. Zuidam and Y. Barenholz, BBA 1368:115–128 (1998) (electron and structural). B. Sternberg, F. L. Sorgi, and L. Huang, FEBS Lett. 365:361–366 (1994). Y. Xu, S. W. Hui, P. Frederik, and F. C. Szoka, Biophys. J. 77:341–353 (1999). Y. Fang and J. Yang, J. Phys. Chem. 101:441–449 (1997). R. Bruinsma, Eur. Phys. J. B 4:75–88 (1998). R. Bruinsma and J. Mashl, Europhys. Lett. 41:165–170 (1998). N. Dan, Biophys. J. 71:1267–1272 (1996). N. Dan, Biophys. J. 73:1842–1846 (1997). N. Dan, BBA 1369:34–38 (1998). D. Harries, S. May, W. M. Gelbart, and A. BenShaul, Biophys. J. 75:159–173 (1998). S. May and A. BenShaul, Biophys. J. 73:2427–2440 (1997). K. Wagner, D. Harries, S. May, V. Kahl, J. O. Radler, and A. Ben-Shaul, Biophys. J., in press. S. A. Safran, Statistical Thermodynamics of Surfaces, Interfaces and Membranes, Addison-Wesley, Reading, MA, 1994. G. Manning, Q. Rev. Biophys. 11:179–246 (1978). J. F. Joanny, Eur. Phys. J. B 9:117–122 (1999). S. A. Sukhishvili and S. Granick, J. Chem. Phys. 109: 6861–6868 (1998). A. V. Kabanov, T. K. Bronich, V. A. Kabanov, K. Yu, et al. Macromolecules 29:6797–6802 (1996). D. V. Schaffer and D. A. Lauffenburger, J. Biol. Chem. 273:28004–28009 (1998). R. Podgornik, D. C. Rau, and V. A. Parsegian, Biophys. J. 66:962–997 (1994). H. H. Strey, V. A. Parsegian, and R. Podgornik, PRL 78:895–898 (1997). J. Nardi, R. Bruinsma, and E. Sackmann, Phys. Rev. E 58:6340–6347 (1998).

36 Synthesis of Microporous Materials from Reverse Micelles RAMSHARAN SINGH, MARIO CASTAGNOLA, and PRABIR K. DUTTA University, Columbus, Ohio

I.

INTRODUCTION

The Ohio State

of the zincophosphate X framework from cationic reverse micelles, in particular using the two-tailed surfactant dioctyldimethylammonium chloride (DODMAC). The use of DODMAC-based reverse micelles has opened up the range of microporous frameworks that can be synthesized. Small zincophosphate clusters (⬃15 nm) formed in DODMAC reverse micelles also provide excellent seed crystals for zincophosphate growth. Section V summarizes the current status of the field and points out potential new developments in this area.

This chapter discusses the research progress that has been made on synthesis of microporous materials from reverse micelles. Although materials synthesis, especially the synthesis of controlled-size nanoparticles from reverse micelles, has been extensively studied, the synthesis of microporous materials with controlled porosity from reverse micelles is a relatively new effort. The synthesis of microporous materials is very sensitive to the reactant composition and hence presents a departure from the commonly practiced precipitation reactions carried out in reverse micelles. As reported here, the influence of the reverse micellar environment on synthesis of microporous materials is found to be quite profound. These effects include control of crystal growth pathways, inability to crystallize open-pore frameworks in certain reverse micelles, morphology control, and seeded crystal growth. There are five sections in this chapter. In Section I, we discuss basic features of microporous materials, with particular emphasis on their synthesis. The nature of reverse micelles is briefly described and typical syntheses done in this medium are described. Section II focuses on the synthesis of zincophosphate sodalite from AOT reverse micelles. Minor variations in reactant composition lead to significant alterations of crystal growth pathways, and a description of these results forms the major thrust of this section. Section III discusses the reasons why open-pore structures such as zincophosphate X cannot be synthesized from AOT reverse micelles. Section IV discusses the synthesis

A.

Microporous Materials

Microporous materials include a large group of solids of varying chemical composition as well as porosity. These materials are characterized by channels and cavities of molecular dimensions. The framework structure is made up of interconnecting T — O — T⬘ bonds, where T and T⬘ can be Si, Al, P, Ga, Fe, Co, Zn, B, and a host of other elements [1]. Materials with Si — O — Al bonding in the framework are called zeolites and are extensively used in many applications [2]. The presence of Al in the zeolite framework leads to ionexchange capabilities. In cases in which the ionexchange sites are satisfied by hydrogen ions, the zeolites show remarkably strong superacid-type behavior [3]. Figure 1 shows the framework structures of some of the most extensively studied zeolites. The two frameworks that are of most relevance to this study are zeolite X and sodalite. Table 1 lists characteristic features of some zeolites, including their void volume and 737

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FIG. 1 Framework structures of some extensively studied zeolites (of importance to this chapter are the zeolite X framework and sodalite).

the kinetic diameter of molecules that can enter the porous structure. Table 2 shows examples of how zeolites are used commercially. As is evident from Table 2, the microporous nature and high surface area of zeolites are used in adsorption and separation applications [4]. Ion-exchange properties of these materials are ex-

ploited in the consumer and environmental industries [5]. Chemical and petroleum industries use zeolites as catalysts in hydrocarbon transformations [6]. Synthesis of new microporous frameworks has led to the development of new technologies, and thus considerable effort worldwide is expended in their discovery [2].

Microporous Materials from Reverse Micelles TABLE 1

Physical and Chemical Properties of Some Commercially Important Zeolites Unit-cell compound (typical, fully hydrated)

Pore structure

Na12[(AlO2)12(SiO2)12] ⭈ 27H2O Na86[(AlO2)86(SiO2)106] ⭈ 264H2O Na56[(AlO2)56(SiO2)136] ⭈ 250H2O K9[(AlO2)9(SiO2)27] ⭈ 22H2O Na8[(AlO2)8(SiO2)40] ⭈ 24H2O (TPA,Na)[(AlO2)(SiO2)30] ⭈ 10H2O

˚ 3D, 4.1 A ˚ 3D, 7.4 A ˚ 3D, 7.4 A ˚ 1D, 7.1 A ˚ 1D, 6.5 ⫻ 7.0 A ˚ 3D, 5.4 ⫻ 5.6 A ˚ 5.1 ⫻ 5.5 A

Type A X Y L Mordenite ZSM-5

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Because this chapter discusses the synthesis of microporous materials in reverse micelles, we will present in some detail information about the synthesis process itself. Microporous materials are typically synthesized by a hydrothermal process, which involves mixing appropriate reactants in an aqueous medium followed by heat treatment [7]. Even though the process is relatively simple, the development and control of porosity, which determines the ultimate practical use of these materials, are not easy to predict. This is primarily because the crystal growth of these materials is a very complicated chemical process [8]. For example, in zeolite formation, the silicon- and aluminum-containing reactants dissolve in the presence of base to produce many soluble species [9]. Speciation is strongly influenced by the pH, temperature, cations, and structure-directing agents [10]. Insoluble aluminosilicates (commonly referred to as gel) are rapidly formed by reaction of the solubilized species. Thus, this system is typically in a state of supersaturation for many of the aluminosilicate species. After an induction period that can extend from hours to weeks, crystals are formed. Nuclei formation that precedes crystal growth can occur by solid-state restructuring of the gel or precipitation from the su-

TABLE 2

Typical void volume Si/Al

(cm3/cm3)

Kinetic diameter (nm)

1.0 1.0–1.5 >1.5–3 2.6–3.5 4.7–5 10–100

0.47 0.50 0.48 0.32 0.28 0.34

0.39 0.81 0.81 0.81 0.63 0.60

persaturated solution. The nuclei grow using nutrients from the solution or the dissolving gel to form crystals. Figure 2 is a schematic description of the crystallization process of microporous materials [11]. The complexity of the process is evident from the numerous chemical processes that occur during crystallization. Typically, the porous structures that are formed are kinetic intermediates and transform to more condensed structures with time. Because of this kinetic stabilization, profound effects are observed on changing the synthesis conditions. The interplay between the inorganic reactants and organic additives also influences the crystal growth process. Crystal morphologies are controlled by preferential growth of crystal faces and are strongly influenced by changes in the synthesis conditions. Thus, zeolite synthesis is an exciting area of research, with major discoveries of frameworks being reported on a regular basis. However, the critical discoveries of new frameworks usually occur by trial and error. Thus, developing a comprehensive molecularlevel understanding of the synthesis process that may lead to designed synthesis is of considerable interest. Spectroscopic probes that have found considerable use in the past decade include nuclear magnetic reso-

Examples of Industrial Applications of Zeolites

Zeolite Faujasite (zeolite Y) Faujasite (zeolite Y) Mordenite Mordenite Z5M-5 Z5M-5 Zeolite A Zeolite X Clinoptilolite

Process

Products

Cracking Hydrocracking Hydroisomerization Dewaxing Xylene isomerization Benzene alkylation Ion exchange Adsorption Ion exchange

Gasoline, fuel oil Kerosene, jet fuel, benzene, toluene, xylene iC6, C7 Low-pour-point lubes p-Xylene Ethylbenzene (styrene) Detergents Separation of gases Radioactive waste cleaup

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FIG. 2 Schematic representation of the crystallization process of microporous materials (reactants A and B can be sources of silicate and aluminate, respectively, or zinc and phosphate, respectively). (Adapted from Ref. 11.)

nance (NMR) spectroscopy, which has provided information about the nucleation process [12,13]. Other techniques that have provided information on the early stages of zeolite nucleation include small-angle and wide-angle x-ray and neutron scattering [14]. Although considerable research has been done on analysis of the structural aspects of species that are present during zeolite nucleation, much less is known about how these species assemble into crystals. This issue is critical for several reasons. The competitive growth of nuclei into crystals determines the final crystalline product. Even though nuclei of a certain zeolitic framework may be formed readily, the rate of crystal growth may be limiting. Growth of large crystals and seeded crystal growth are also dependent on the type of crystal growth. Finally, the morphology of the crystals depends on the crystal growth process. We have reported several studies related to zeolite nucleation and crystal growth, primarily using Raman spectroscopy [15]. Two of these studies are relevant to how we got started in using reverse micelles for microporous material synthesis. The first study dealt with using amorphous material from a zeolite X synthesis, ion-exchanging it with a series of monovalent cations, and then continuing the synthesis by putting the solid back into a basic solution of the corresponding cation [16]. The products were analyzed by x-ray diffraction. Table 3 shows the results. Because the aluminosilicate and the hydroxide ion concentration were kept identical in all cases, the change in the framework structure must arise from the influence of the cation. Raman spectroscopy had shown that the amorphous gel is primarily

composed of four-membered aluminosilicate rings. The model shown in Fig. 3 assigns specific building blocks for each structure. These intermediate structures, derived from four-membered rings, were hypothetical and derived on the basis of their specificity for a particular zeolite as well as their ready convertibility by rearranging a few T — O — T⬘ bonds. It was proposed that the formation of these units was controlled by the presence of specific cations in the reaction medium. Why and how do the cations direct the formation of such structures? We reasoned that the different electrostatic fields around the cation were responsible for stabilizing the different structures. Because reverse micelles provide novel cation-water environments, they appeared to be attractive in examining microporous material synthesis.

TABLE 3 Zeolitic Frameworks That Are Formed from the Same Aluminosilicate Composition in the Presence of Different Monovalent Cationsa Cations Na⫹ K⫹ Cs⫹ N(CH3)⫹4 N(C2H5)⫹4 N(C3H7)⫹4 N(C4H9)⫹4 a

Zeolite Zeolite A Zeolite R (chabazite) Zeolite Cs-D (edingtonite) Zeolite ZK-4 Zeolite P (gismondine)b Zeolite Xb Zeolite P

Major constituent, other phases also present. Adapted from Ref. 16.

b

Microporous Materials from Reverse Micelles

FIG. 3 Proposed intermediate building block structure for zeolitic structures made in the presence of different monovalent cations (see also Table 3). (Adapted from Ref. 16.)

A second study along these lines dealt with the synthesis of zeolites of low Si/Al ratio in the presence of ethanol [17]. At lower levels of alcohol (60⬚C were unsuccessful because of instability of reverse micelles at high temperatures [31]. Intermicellar


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FIG. 7 Schematic representation of particle formation in reverse micelle via precipitation reaction between two reactants initially in two separate reverse micelles. (Adapted from Ref. 30.)

attractive forces increase upon raising the temperature, resulting in phase separation. Thus, in order to study the crystal growth characteristics of microporous materials in reverse micelles, we had to limit ourselves to frameworks that can be made under ambient conditions and chose to work with zincophosphates. The advantage of microporous zincophosphates over their aluminosilicate analogues relies on their low temperature and mild condition synthesis. For instance, whereas zeolite X is typically synthesized from a highly caustic gel between 70 and 100⬚C, zincophosphate X (ZnPOX) with the same topology (Fig. 1) is prepared around pH 8 at room temperature. Microporous zincophosphate materials were first synthesized in the early 1990s by Stucky and coworkers [32,33]. The first examples of these type of compounds were the analogue structures of zeolite X, sodalite and zeolite Li-A(BW).

II.

SYNTHESIS OF ZINCOPHOSPHATE SODALITE FROM AOT REVERSE MICELLES

A.

Synthesis Procedures with AOT Reverse Micelles

For synthesis of zincophosphates from AOT reverse micelles, two reverse micelle solutions have typically been used, one containing zinc ion (identified as Zn) and the other containing phosphate, sodium hydroxide, and tetramethylammonium hydroxide (TMAOH) solution (identified as P) [34,35]. Tetramethylammonium ions were necessary for the uptake of phosphate ions into the micelle. Table 4 shows the typical characteristics of each micelle system. These micelles were

made by equilibrating an AOT solution in hexane with the aqueous solutions and used for the zincophosphate synthesis experiments. Compositional changes were brought about in two ways. First, aging of the reverse micelles altered the intramicellar pH of the P micelles, making them less basic because of the reaction of the hydroxide ion with the ester functionality of the AOT headgroup. Zinc micelles, on the other hand, were acidic because of the hydrolysis of the zinc ions. Second, different volume ratios of the Zn and P micelles were mixed to vary the composition of the synthesis medium. A typical experiment begins with mixing the Zn and P micelle solutions. The solutions are clear upon mixing the micelles. Then at various times, a white product settles out. After completion of the settling process, the product is removed, washed, and analyzed by powder x-ray diffraction, the primary method for identification of the frameworks. Influence of aging of the reverse micelle preparations on the formation of zincophosphates has also TABLE 4 Composition of AOT-Based Zinc and Phosphate Micellar Solutions Zn micelle [Zn2⫹] = 0.0075 M [Na⫹] = 0.0525 M [NO⫺3 ] = 0.00507 M [AOT] = 0.065 M [AOT]/[H2O] = 13 Micelle size = 8.5 ⫾ 1 nm Source: Adapted from Ref. 35.

P micelle [P] = 0.0125 M [Na⫹] = 0.55 M [TMA⫹] = 0.346 M [AOT] = 0.065 M [AOT]/[H2O] = 21 Micelle size = 15 ⫾ 1 nm

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been examined [35]. Equal volumes of Zn and P micelles are mixed, and both solutions are aged for periods of time varying from 0 to 13 days. The products recovered with the solutions aged for 2 days of reaction are a mixture of hexagonal sodium zinc phosphate and sodalite. Pure sodalite is formed when the micelles are aged for more than 6 days. In experiments in which the volume of Zn micelle is three times that of the P micelle (both samples aged for 8 days), hopeite (zinc phosphate) is formed. This is consistent with the conventional synthesis of zincophosphates, in which hexagonal zinc phosphate is reported to form at pH 10, sodalite at neutral pH, and hopeite at acidic pH values [33]. Overall, the micellar chemistry and aqueous chemistry appear to follow similar pathways. Because among these zincophosphate frameworks, only sodalite can be considered to belong to the family of microporous materials (framework structure in Fig. 1), this system was examined in more detail. B.

Formation of Zincophosphate Sodalite from AOT Reverse Micelles

Sodalite is a member of the microporous family of frameworks and has been extensively studied in the aluminosilicate [36] as well as in silica systems [37]. Solutions of P and Zn micelles aged for 8 days were used as starting materials for sodalite synthesis. The solids formed upon mixing these two micelle solutions in different volume ratios were examined. In particular, three compositions with relative ratios of the Zn and P micelle solutions of 0.8, 1, and 1.2 were found to have interesting crystal growth dynamics [35]. These were identified as compositions A, B, and C, respectively. The overall zinc and phosphate concentrations in these compositions are shown in Table 5. Profound differences were noted in the rate of appearance of product formation in these three compositions, although they all ended up forming zincophosphate sodalite. Next, we

TABLE 5 Compositions of AOT-Based Compositions for Forming Zincophosphate Sodalite Volume (mL) Composition Zn micelle P micelle A B C

40 40 50

50 40 40

Source: Adapted from Ref. 35.

Moles Zinc

Phosphate

3 ⫻ 10⫺4 6.25 ⫻ 10⫺4 3 ⫻ 10⫺4 5 ⫻ 10⫺4 ⫺4 3.8 ⫻ 10 5 ⫻ 10⫺4

discuss in detail the reported characteristics of these three reverse micelle–led reactions and the implications for microporous material growth. 1. Composition A Upon mixing the Zn- and P-containing micelles for composition A, the solution remained clear and evidence of reaction was provided by solids appearing at the bottom of the reaction vessel for the first time after 2 days. The peaks due to sodalite were evident in the diffraction patterns obtained from this sample. With time, the crystals increased in amount and were always the sodalite framework. Light scattering studies indicated continuous growth in size as shown in Fig. 8. A scanning electron micrograph of the crystals obtained after settling (4 days) and the powder diffraction pattern are shown in Fig. 9. The sizes of these crystals were between 500 and 600 nm. The morphologies were cubic crystals or pyramids (half-cubes). Centrifugation of the reaction mixture after 18 h of reaction afforded a small quantity of solid, which was examined by transmission electron microscopy (TEM) as shown in Fig. 10. The morphology of the crystals is similar to that observed after 4 days, although the crystals appeared to be smaller (100–500 nm) and peaked between 200 and 220 nm. Selected area diffraction of the crystal showed the material to be crystalline. Thus, it appears that at all observable stages of growth, the morphology of the sodalite crystals remains similar, with size and yield increasing in time. These observations indicate that sodalite is being formed while suspended, without any detectable intermediate amorphous phase. The morphology of the crystals suggests that they grow by deposition along specific crystal planes proceeding toward a cubic structure. 2. Composition B For composition B, the visual observations were quite distinct from those for composition A. The reactor became cloudy within the first 12 h, followed by settling out of particles over the next 24 h. Light scattering data, as shown in Fig. 11, suggested that rapid growth of particles occurred after a size of 75 nm. The diffraction patterns of the solid recovered by centrifugation as soon as the solution became cloudy (12 h) as well as samples recovered after settling for 24 h were characteristic of the sodalite framework. Figure 12 shows a scanning electron microscopy (SEM) picture of the particles obtained for composition B prior to settling. The suspended particles were crystallites of sizes less than 600 nm. The crystals recovered after settling are similar in particle size and morphologies to


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FIG. 8 Change of particle size with time for composition A, as determined by light scattering (⫹ and 䊱 represent the smaller and larger sizes, respectively, obtained by fitting the data to the exponential sampling method). (Adapted from Ref. 35.)

the suspended particles, except that they appear agglomerated and 2–3 ␮m in size. Solids recovered after 6 h of reaction by centrifugation (prior to the appearance of any cloudiness) were examined by TEM and showed aggregates of small particles. Selected area diffraction showed that the material was crystalline. Thus, for composition B, crystals also appear without any apparent intermediate amorphous phase at the earliest stages examined.

FIG. 9 (a) SEM pictures of sodalite crystals grown via composition A (4 days). (b) X-ray powder diffraction pattern, typical of the sodalite structure, grown from composition A (4 days). (Adapted from Ref. 35.)

3. Composition C For composition C, the pathway was marked by the rapidity of the initial reaction to form a white solid. The reactant mixture turned turbid in 1 h, and complete settling of the solid was seen in 4 h. The growth pattern as measured by light scattering for composition C (Fig. 13) was consistent with these observations. The particles formed immediately after the appearance of turbidity and settling were found to be amorphous. These were discrete particles of approximately 5 ␮m and they agglomerated and formed a contiguous solid with time. Sodalite crystals grew out of this settled solid phase over a period of 4 days with the morphology shown in Fig. 14a. In order to keep the particles suspended during formation of sodalite from composition C, the experiment was repeated in a rotating cell. Particles in a fluid that

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FIG. 10 TEM picture of crystals obtained at the early stages (18 h) of composition A. (Adapted from Ref. 35.)

will sediment due to gravitational forces (Stokes’ law) can be kept suspended by rotation of the reaction chamber [38]. The reactor was rotated around its central axis at speeds up to 7 to 45 rpm. The orbits assumed by the particles were approximate circles around a center displaced horizontally from the axis of rotation. A minimum rotation speed was required to ensure that this center lies within the dimensions of the reactor. At very high rotation rates, particles with densities higher than the fluid (as in this case) spiraled out and hit the wall of the reactor. The choice of the rotation speed thus had to be optimized depending on the particle-fluid system. Formation of sodalite crystals by pathway C could be completed in the rotating cell at 11 rpm with min-

FIG. 11 Particle growth characteristics for composition B, as measured by light scattering (⫹ and 䊱 represent the smaller and larger sizes, respectively, obtained by fitting the data to the exponential sampling method). (Adapted from Ref. 35.)

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FIG. 12 SEM picture of crystals obtained from composition B prior to settling. (Adapted from Ref. 35.)

imal sedimentation on the walls of the reactor over a period of 10 days. From the individual amorphous particles, sodalite crystals were seen to grow, as shown in Fig. 14b. C.

Role of the Intramicellar pH in Influencing Crystal Growth Pathways

Variation of the Zn-to-P micellar volume ratios over a narrow range (0.8–1.2) has a profound influence on the rate and mechanism of sodalite crystal growth as well as the final crystal morphology. Because such a minor change in composition has no influence in the conventional synthesis of sodalite, the micellar environment

FIG. 13 Particle growth characteristics for composition C, as measured by light scattering (⫹ and 䊱 represent the smaller and larger sizes, respectively, obtained by fitting the data to the exponential sampling method). (Adapted from Ref. 35.)


FIG. 14 (a) SEM pictures of sodalite crystals obtained from the amorphous phase of composition C. (b) SEM of sodalite crystals growing from suspended amorphous particles in a rotating cell from composition C. (Adapted from Ref. 35.)

obviously plays a major role. The major differences in the compositions A–C are in the relative ratios of zinc and phosphate ions present. The phosphate ions are always in excess, with the phosphate-to-zinc molar ratio decreasing from 2.1 in composition A to 1.3 in composition C (Table 5). Increasing the content of the Zn micelle makes the overall composition more acidic. From the pH-NMR calibration data [39], the pH values in compositions A, B, and C were found to be 7.6, 7.2, and 6.8, respectively, reflecting the acidity of the Zn micelle [35]. Crystallization has been extensively studied over many decades [40,41], and we provide some instances of systems in which pH has had a major effect on the crystallization. A good example is the crystallization of calcium hydrogen phosphates [42]. The hydroxide and

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phosphate ion concentrations appeared in the ion prod6 ⫺ 2 uct [Ca2⫹]10[PO3⫺ 4 ] [OH ] as exponents, and a slight increase of pH considerably increased the supersaturation. Thus, a change in pH from 7.4 to 7.8 resulted in a considerable increase of crystal growth rates. Indeed, above a pH of 7.8, it was difficult to prepare a supersaturated solution without spontaneous precipitation of calcium phosphate. For Cr(OH)3, an amorphous precipitate was formed at pH below 10, whereas a crystalline material was formed at pH above 10 [43]. Lazic [44] has reported a reduction of the induction period in hydroxyapatite formation from amorphous calcium phosphate as a function of pH. Beyond pH 10.2, the decrease in induction period was correlated with deprotonation of HPO2⫺ 4 and the increase in concentration of CaPO⫺4. The effect of pH on crystal growth can also arise from surface charge on the particle. For example, with both CaHPO4 ⭈ 2H2O and hydroxyapatite, crystals grow more slowly at pH values less than the pH corresponding to the point of zero charge [45]. The structure of the nucleating species in sodalite growth is not known. As a matter of fact, even for simple precipitation reactions, the nature of the nucleating species is not obvious. For example, in the precipitation of Ag2WO4, it is not WO2⫺ but rather 4 2⫺ 10⫺ intermediate species such as W6O21 , W12O41 , and 5⫺ HW6O21 [46]. The same is true for formation of ferric hydroxide, in which the important reaction is between 3⫹ 4⫹ Fe9(OH)7⫹ and 20 and Fe3(OH)4 rather than between Fe ⫺ 3OH [47]. Complicated reactions involving polymeric nucleating intermediates have been proposed for formation of TiO2, Cr(OH)3, and Mg(OH)2 [41]. Hydrolysis of the Zn — O — P bond is essential in the development of nuclei of sodalite. Hydrolysis reactions have been studied in reverse micelles. Base-catalyzed hydrolysis of esters [48], as well as the formation of ferric oxyhydroxide species by hydrolysis of ferric ammonium sulfate, has been reported [49]. Hydrolyses of alkoxides in micelles have shown that the concentration of the reactants and water determine supersaturation levels [50]. Walton [51] has summarized the effects of initial supersaturation on crystal morphology. It was noted that the morphology varies from compact well-defined crystals to poorly developed crystals and finally amorphous aggregates as the initial supersaturation changes. An example is ZnC2O4 ⭈ 2H2O, whose crystals have different habits in different supersaturation ranges [52]. In the case of CaHPO4, with increasing supersaturation, rhombohedral, intergrown, and twinned crystals of CaHPO4 ⭈ 2H2O and ultimately spherical agglomerates of CaHPO4 are formed [53].

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Singh et al.

Reasons for Crystallization Pathway Control with AOT Reverse Micelles

After the micelles equilibrate, there is a distribution of zinc, phosphate, and hydroxide ion occupancies in the different micelles that exist in the medium. Depending on the intramicellar concentrations and pH, there is a fraction of these micelles in which saturation conditions are exceeded. This fraction was proposed to increase as the composition changed from A to C. For composition A, where few nuclei were formed in the micelles, the growth had to occur by acceptance of solution species present in other micelles. For composition C, on the other extreme, the particles grew rapidly by aggregation. Increased aggregation with supersaturation has been noted for silver clusters in AOT micelles [54]. Composition B represents an intermediate situation in which more particles are formed but there is enough time prior to aggregation to form sodalite nuclei. Figure 15 depicts this distribution schematically, assuming a Gaussian distribution of components (for illustration purposes), and shows that the fraction of micelles in which supersaturation has been exceeded increases from A to C. In conventional aqueous systems, in which there exists uniformity of compositions throughout the system, it is impossible to control the supersaturation levels by minor changes. Indeed, the compartmentalization of reactants in reverse micelles and the nature of the

FIG. 15 Schematic representation of the differences in the fraction of micelles in which supersaturation has been exceeded for compositions A–C.

exchange of reactants upon collision lead to the unique behavior of such micellar systems. In composition A, where the supersaturation was lowest, crystal growth proceeded slowly, controlled by surface attachment kinetics. The surfaces of the crystals were examined by atomic force microscopy (AFM), ˚ thick, typical of a sodalite which indicated layers 10 A cage [35]. Crystals of compact shapes are known to form at low supersaturation because the minimum overall energy of the crystal surface is reached under very slow growth, equilibrium-like conditions [55], which is consistent with the morphology observed for composition A. The growth process in pathway B has been analyzed as an aggregation process. The early morphology of these crystals appeared cubic, suggesting that the initial growth process may be similar to that of composition A. The crystals aggregated via diffusion and convection. Such diffusion-controlled micellar collisions have been proposed for growth of silica and carbonate particles [56,57]. In pathway C, the intramicellar conditions resulted in the highest supersaturation. This led to rapid nucleation, and because the induction time for crystal formation was longer, amorphous particles were formed. The morphology of the particles formed initially in composition C supports the high supersaturation hypothesis. If the rate of particle growth is very high, the heat of precipitation cannot be transferred efficiently into solution. This leads to convection, and the particle is surrounded by depleted regions. The particle extends its surface highly anisotropically. This leads to structures as shown in Fig. 14b. The formation of an amorphous phase in systems with high supersaturation has been noted in the crystallization of CaCO3 [58], hydroxyapatite, Mg(OH)2 [59], and Al(OH)3 [60]. In all cases, the amorphous phase finally transforms to crystals. The explanation for this phenomenon is that the nuclei formed from highly supersaturated solutions do not have an exactly defined structure and hence crystals are not formed. Crystals are formed from these amorphous materials by dissolution into the mother liquor and a solution-mediated transformation. However, in the reverse micelles, nutrients cannot dissolve in the organic medium. There are two possibilities for crystal growth. The first is direct transformation in the solid state, as reported for the transformation of vaterite to calcite. In this case, the morphology remained unchanged upon transformation [58], which is not consistent with the observations for composition C. The second possibility is based on precipitation of metal hydroxides, in which


nonstructural water that is retained in the precipitate can be liberated during the growth process [61]. Thus, after settling of the amorphous zincophosphate, with time it is surrounded by a thin water layer that can transport nutrients. Such a mechanism is supported by the rotating cell experiment, in which the suspended amorphous particles transformed directly to sodalite crystals (Fig. 14b) with the gel particles appearing to act as sites for growth. E.

Attempts at Crystal Growth of Zincophosphate X from AOT Reverse Micelles

The sodalite framework, as seen from Fig. 1, has limited porosity. Attempts were made to grow open-pore framework zincophosphate X (ZnPO-X) from AOT reverse micelles but without success [62]. In the following we outline the attempts at growth of ZnPO-X from AOT reverse micelles and the proposed reasons for failure. Several procedures for synthesis of ZnPO-X using AOT reverse micelles were attempted [62]. The most straightforward procedure was similar to that for sodalite using two reverse micelle (AOT/hexane) solutions, each made by equilibration with aqueous zinc and phosphate solutions. The compositions of the aqueous solutions were chosen such that in the absence of the micelle, they would have resulted in formation of ZnPO-X. In a relatively fast reaction (24 h), sodalite was produced. Another approach taken was to consider the intramicellar composition that was previously optimized for sodalite formation [35] and to alter it to a composition more appropriate for ZnPO-X. In the reverse micelles for sodalite formation, the aqueous Zn2⫹ solution used was 0.2 M and the Zn/P ratio was found to be 0.6. The optimal Zn/P ratio for aqueous synthesis of ZnPO-X is 0.94. To keep this ratio in the reverse micelles, the concentration of Zn2⫹ in the aqueous solution was increased to 0.32 M. For the phosphate solution, the [TMAOH] was increased by 34% to a final pH of 12.7. To keep the intramicellar pH to a maximum, the AOT/ hexane solutions were equilibrated with the aqueous zinc and phosphate solutions for 3 h and the solutions mixed without any aging. After 4 weeks of reaction, no product was recovered. Thus, the zincophosphate framework with the sodalite structure appeared to form preferentially in the AOT reverse micelle system. Under no composition conditions was it possible to form ZnPO-X.

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Typically, in the synthesis of inorganic materials from reverse micelles, the chemistry in the reverse micelle is similar to that observed in the bulk solution. Clearly, in the case of microporous material synthesis, the reverse micelle environment has an influence on the product, even though from a composition point of view, ZnPO-X should be formed with AOT reverse micelles. The possible reasons why AOT reverse micelles preferentially direct the formation of sodalite were examined. III.

EVALUATION OF WHY ZnPO-X IS NOT FORMED WITH AOT REVERSE MICELLES

In the conventional synthesis for preparing ZnPO-X, the starting Na/Zn ratio was 0.5 [32]. If NaCl was added to this reaction system, it resulted in the appearance of sodalite [62]. On the other hand, with the composition typical for sodalite, addition of Na⫹ complexing agents, such as 18-crown-6-ether or Kryptofix, in increasing amounts led to a decrease in the amount of sodalite and zincophosphate X appeared as the dominant product. The following relationship appears to exist between the two zincophosphate frameworks: Na⫹ ZnPO-X ↔ sodalite ⫺Na⫹ Each AOT detergent molecule contributes a Na⫹ to the water pool of the reverse micelle, which leads to [Na⫹] ⬃4 M inside the water pool of the reverse micelle. Up to 28% of the sodium counterions in a reverse micelle can be in the bulk water region of the micelle [63]. This high concentration of Na⫹ is proposed to be responsible for the nucleation and growth of sodalite in AOT reverse micelles under varying compositional conditions. This hypothesis would predict that complexation of the sodium ions in the reverse micelle should lead to formation of ZnPO-X. In order to convert from sodalite to ZnPO-X, the Na/Zn ratio in the reactant composition had to be lowered from 1.08 to 0.5. For comparable Na/Zn ratios in the reverse micelles, the free sodium concentration had to be lowered by 75%. The amount of crown ether necessary to bring the sodium ion to these low levels was estimated from the reported formation constants [64]. Addition of these amounts of crown ether to the phosphate reverse micelle led to phase separation. The water structure in the reverse micelles may also play a role in destabilizing ZnPO-X. Figure 16a com-

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the mixture of the Zn and P AOT reverse micelles [62]. Three types of water were also reported in reverse micelles [68,69]. These were bulklike water (3300 cm⫺1), bound water separating the interface between bulk and the micelle interface (3490 cm⫺1), and water trapped at the interface (3600 cm⫺1). In the case of the reverse micelles that were used in making zincophosphates, there was a decrease in relative intensity of the bulklike and trapped water as compared with interfacial water even though the water-swollen micelles contained a large concentration of Na⫹. This effect arose primarily from the Zn micelles. Why Zn2⫹ causes this enhanced disordering of water is not quite clear. Nevertheless, there is a parallel observation between NaCl aqueous solutions and Zn-containing AOT reverse micelles, i.e., an increase in disordered water. Because the water structure plays an important role in nucleation of openpore frameworks, the intramicellar environment is not appropriate for crystallization of ZnPO-X. This led to the study of nonionic surfactants, in particular, the polyoxyethylene surfactants [70]. Zincophosphate sodalite was readily synthesized from reverse micelle using Tween 85 in the presence of isopropanol in hexane solvent. However, attempts at preparing ZnPO-X from Tween 85 were unsuccessful.

FIG. 16 Infrared spectra in the O — H stretching region for (a) H2O (I), aqueous NaCl solution (1 M) (II) and (b) reverse micelle system with H2O (I) and both Zn and P (II) (reverse micelles made with AOT). (Adapted from Ref. 75.)

pares the infrared (IR) spectra of the O — H stretching region in pure water with aqueous saturated NaCl. Three types of water have been proposed to exist around the added ions with different peak O — H stretching frequencies [65,66]: an innermost region of weakly hydrogen bonded, ion-immobilized water (type I, 3600 cm⫺1), an intermediate structure broken region (type II, 3450 cm⫺1), and an outer region with the normal liquid water structure (type III, 3350 cm⫺1). At high NaCl concentrations, there is a decrease in intensity of the type I and III structures relative to type II structure. This would suggest a disordered, structurebroken form of water at high concentrations of salt [67]. Figure 16b compares the IR spectra of the ␯ O — H stretching in water-swollen AOT reverse micelles and

IV.

SYNTHESIS OF ZnPO-X FROM DODMAC REVERSE MICELLES

A.

Nature of Zinc and Phosphate Reverse Micelles

Cationic micelles generally solubilize less water than their anionic counterparts. However, Vera and coworkers [71–74] reported that reverse micelles of the twotailed cationic surfactant dioctyldimethylammonium chloride (DODMAC) had a high water uptake capacity. Most of the applications of DODMAC reverse micelles have been in extraction of biological molecules from aqueous media. Several reports detailing the water uptake by DODMAC reverse micelles, influence of the counterion on the reverse micelle, and the role of alcohols as cosurfactants have been published. The surfactant DODMAC, commercialized as Bardac-80, can be obtained from Lonza. Bardac-80 contains 80% DODMAC, 10% water, and 10% ethanol. The ethanol and a fraction of the water can be evaporated under vacuum. DODMAC (0.16 M) and the cosurfactant 1-decanol (0.225 M) dissolved in isooctane were used as the medium for making reverse micelles for ZnPO-X formation [75,76].


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TABLE 6 Composition of the Zinc and Phosphate Aqueous Solutions (before and after Winsor II Equilibration) and of the Aqueous Core Inside the Reverse Micelles (Surfactant, DODMAC) Solution

Original solution

Phosphate

Zinc

P Na TMA⫹ pH Zn

0.66 M 0.32 M 1.38 M 12.2 0.366 M

Remaining behind P Na TMA⫹ pH Zn

0.63 0.38 1.90 12.3 0.11

In micelle (M)

Analytical method

M M M

P Na TMA⫹

0.69 0.25 0.79

ICP–OES ICP–OES Raman

M

Zn

0.70

ICP–OES

ICP–OES: Inductively Coupled Plasma–Optical Emission Spectroscopy. Source: Adapted from Ref. 75.

Because there has been no previous report of using DODMAC-based reverse micelles for synthesis of materials, we provide some details of the nature of the zinc, phosphate, and water reverse micelles formed with this system [75]. In the preparation of the Zn and P reverse micelle solutions, it was noted that a turbid mixture was formed after the aqueous and organic phases were mixed. After a few minutes, two phases (an organic phase at the top and an aqueous phase at the bottom) were distinguishable, characteristic of a Winsor II system. The turbidity of the organic phase, due to water droplets suspended in it, disappeared during the first 2 days. In the case of the H2O reverse micelle solution, mixing the organic and a limited volume of distilled water produced a slightly cloudy mixture. After additional shaking, the mixture turned into a completely clear single-phase solution characteristic of a Winsor IV system. Table 6 details the aqueous solutions used for preparing the micelles, analysis of the aqueous solutions after equilibration with the surfactant solution, and the composition of the reverse micelle. The tetramethylammonium (TMA) ion in the phosphate reverse micelle was used as a structure-directing agent for ZnPO-X. Table 7 shows the water uptake (␾w) of the reverse micelles, the micelle size, the polydispersity, and the

conductivity. The aqueous solution uptake of the Zn and P reverse micelles was calculated from the excess volume of aqueous phase recovered from each Winsor II system. Approximately 1.4 mL of solution A (phosphate solution) and 1.3 mL of solution B (zinc solution) went into the 50 mL of reverse micellar solutions. The P micelles solubilize slightly more water than the Zn micelles. This is not surprising because the P micelles as counterions whereas contain Cl⫺, OH⫺, and PO3⫺ 4 the Zn micelles contain Cl⫺ and NO⫺3. Studies of DODMAC reverse micelles have found that, relative to chloride, polyvalent anions and hydroxide increased the water uptake in these micelles and nitrate decreased the water uptake. No significant differences in the water uptake between different cations have been reported for DODMAC micelles [77]. Note that some of these concentrations are higher in the remaining solutions because of preferential water uptake. Figure 17a and b show the change in particle size and conductivity of the different reverse micelles as water uptake (␻0) increases. In the case of the Zn and water micelles, in the initial stages of water uptake, there is an increase in size as a function of water incorporation, followed by a decrease. This could be due to change in shape of the particle from a cylindrical to a more spherical shape. The Zn and P conductivity pro-

TABLE 7 Results of Light Scattering and Conductivity Measurements Performed on Water, Phosphate, and Zinc Reverse Micelle Solutiona Reverse micelles H2O P Zn

␾w (% v/v)

Micelle size (nm)

Polydispersity index

Conductivity (␮S/cm)

3.1 3.1 2.9

23.2 ⫾ 0.1 8.9 ⫾ 0.1 20.7 ⫾ 0.2

0.077 0.005 0.081

7.8 0.65 2.0

␾w represents the aqueous volume uptake per volume unit of reverse micelle solution (surfactant, DODMAC). Source: Adapted from Ref. 75. a

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FIG. 17 (a) Size of H2O, Zn, and phosphate reverse micelles (DODMAC) as a function of water content. (b) Conductivity of H2O, Zn and phosphate reverse micelles (DODMAC) as a function of water content. (Adapted from Ref. 75.)

files appear at lower values than that of H2O. This is consistent with the literature, the conductivity values for pure water reverse micelles being generally larger than for reverse micelles containing electrolytes [78]. It is interesting to observe that, in the case of H2O reverse micelles, a percolation phenomenon is not observed at any water uptake. This behavior has also been observed in other cationic reverse micelle systems [79]. Infrared spectroscopy of the water in the AOT and DODMAC reverse micellar core also provided information on the differences between these two reverse micelles. Figure 18 compares the IR spectra of bulk water, water inside reverse micelles of AOT, and water inside reverse micelles of DODMAC. As discussed ear-

lier, the high-, medium-, and low-frequency parts of the OH stretching band region are due to nonhydrogen, stressed-hydrogen, and hydrogen-bonded O — H. These three types of O — H observed in water and AOT are also present in DODMAC reverse micelles. In the case of both surfactants, the low-frequency region that describes the hydrogen-bonded water seems substantially less intense than that found in bulk water. This is probably not surprising considering the ions that are present in both of these micelles. Differences are observed in the interfacial water. Because of strong interactions with the polar headgroup and sodium counterion, AOT reverse micelles contain larger distributions of non-hydrogen-bonded water molecules at the interface. In


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FIG. 18 Infrared spectra in the O — H stretching region for AOT and DODMAC reverse micelles (dashed line represents pure water). (Adapted from Ref. 76.)

contrast, DODMAC does not disrupt the water structure at the interface because quaternary ammonium salts have a ‘‘structure-making’’ influence. B.

Synthesis of ZnPO-X Using DODMAC Reverse Micelles

to carry it out at room temperature (25⬚C) [32]. The changes required were to make the solution dilute and more basic and increase the Zn/Na ratio [62]. The optimized procedure for making ZnPO-X involved three DODMAC reverse micelles made via the equilibration method [79]. An aqueous solution P was prepared by

The primary goal of using DODMAC reverse micelles was to synthesize porous zincophosphate frameworks, in particular ZnPO-X. Two templating agents have been studied, tetramethylammonum ion and 1,4-diazabicyclo[2,2,2]octane (DABCO), whose molecular structures are shown in Fig. 19. We discuss these results separately. 1. TMA as a Templating Agent Stucky and coworkers reported the synthesis of ZnPOX at 4⬚C, and the procedure needed to be modified

FIG. 19 Structures of the templating agents used for synthesis of ZnPO-X: (a) tetramethyl ammonium ion (TMA⫹); (b) 1,4-diaazabicyclo[2,2,2]octane (DABCO).

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combining 15.1 mL of 1.5 M H3PO4, 0.453 g of NaOH, 17 mL of 25% (w/w in water) TMAOH, and 2.15 mL of H2O. Solution Zn contained Zn(NO3)2 (0.366 M). Solution TMA contained tetramethylammonium (TMA⫹) bromide (1.0 M). Reverse micelles were made by equilibration of 3 mL each of P and Zn and 1 mL of TMA separately with 50 mL of the isooctane solution (containing the surfactant). The aqueous part that was not incorporated into the reverse micelle was removed from each solution. The three reverse micellar solutions were mixed in the Zn/P/TMA volume ratio of 6:10:5. Particle growth in the solution was monitored by dynamic light scattering and showed an initial size of 12 nm for the reverse micelles. For the first 40 min, the size remained relatively constant, followed by accelerated growth of the particle size. Visual observations indicated that the solutions turned cloudy during the first 12 h, followed by the appearance of particles at the bottom of the reactor. The amount of settled particles increased with time. Upon ultracentrifugation of the mother liquor before any cloudiness was visually evident, a small amount of solid was recovered. These suspended crystals are small, on the order of a few hundred nm. Enough sample could not be recovered for diffraction analysis, but micro-Raman spectroscopy showed bands at 765, 983, 1014, and 1119 cm⫺1, characteristic of faujasitic zincophosphate (ZnPO-X) [62]. The settled product was isolated by filtration, and Fig. 20a shows the x-ray powder diffraction pattern, which can be unambiguously assigned to ZnPO-X. Figure 20b shows the SEM picture of the sedimented crystallites, with sizes between 1 and 2 ␮m and the octahedral morphology expected of ZnPO-X. Tetramethylammonium ion is used in the synthesis of ZnPO-X because it acts to template the faujasitic structure. Whether the tetraalkylammonium unit of the headgroup of DODMAC also has a preferential influence on the nucleation of ZnPO-X is of interest. Raman spectroscopy indicated entrapment of the TMA⫹ in ZnPO-X made from DODMAC reverse micelles, but there was no indication that the surfactant was entrapped in the framework. The dynamics of the crystal growth could be controlled to some degree by changing the Zn/P ratio. For example, if the Zn/P ratio was altered from 0.6 to 0.66, the reaction was accelerated by a factor of 4. This observation is consistent with studies in conventional hydrothermal synthesis of zincophosphates [33] and in the sodalite synthesis in AOT reverse micelles [35]. By increasing the Zn2⫹ concentration, the acidity of the reaction composition is increased and the rate of crystal-

Singh et al.

FIG. 20 (a) Powder x-ray diffraction pattern and (b) SEM of crystal obtained with DODMAC reverse micelles. (Adapted from Ref. 76.)

lization increases. Sodalite, hopeite, and the hexagonal phase P61 compete with ZnPO-X in the conventional zincophosphate system [33]. By altering the composition, it was possible to crystallize these phases from DODMAC reverse micelles; e.g., hopeite was formed at Zn/P ratios >0.8. 2. DABCO as a Templating Agent With this templating agent, the DODMAC reverse micelles were made by an injection method. This method involves injecting a known volume of aqueous solution of the reactants into the surfactant solution, which completely goes into the reverse micelle formation and the system remains a single phase. The surfactant solution used was 0.2 M DODMAC and 0.33 M 1-decanol in isooctane. For the optimal synthesis of ZnPO-X, the following reactant micelle composition (abbreviated A) was developed. Two solutions were prepared: first, 0.16 M Zn(NO3)2 ⭈ 6H2O aqueous solution; and second, 0.11 M NaOH, 0.58 M DABCO, and 0.27 M H3PO4 solution as another aqueous solution. In a typical reverse micelle reactant preparation, 100 mL of surfactant solution was placed in a bottle, 2 mL of an aqueous solution of a reactant was added, and the bottle was vigorously shaken for about 1 min and then equilibrated at room temperature (25⬚C). After 24 h of equilibration, the reverse micelle reactant solutions were used for synthe-


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sis. These reactants were stable over several weeks as no phase separation occurred at any time. Light scattering experiments showed that the diameters of the Zn- and P-containing reverse micelles were 8 and 6 nm, respectively. Reaction was carried out by mixing the Zn and P micelles with volume ratio of 1:1. The reaction mixture was clear at the beginning of the reaction. Particles of the products started settling after about 8 h of reaction. This settling process became complete in about 3–4 days. The products were separated by centrifugation, washed with ethanol and water, and dried at room temperature under reduced pressure. Powder diffraction patterns as well as the octahedral morphology confirm the formation of the ZnPO-X structure. The yields of zincophosphate X from composition A were of the order of 15–20%, indicating that large fractions of the zinc and phosphate species were still present in the micellar medium. Light scattering indicated that the size of the clusters remaining in solution was of the order of 15 nm. Table 8 compares the conventional composition for ZnPO-X with that used in reverse micelles. The ratio for the reactants is the same as for the conventional synthesis. However, the aqueous solution used for the reverse micelle preparation is about four times diluted. In the reverse micelle formation, some amount of water is used up for the hydration of the headgroup of the surfactant. Therefore, the effective composition and the concentration of the reactants in the water pool are probably similar to those under the normal solution synthesis conditions. Interestingly, when diluted aqueous solutions of the reactants were used for the normal solution synthesis keeping the same reactant ratio, no ZnPO-X was crystallized. 3. Seeding Experiments Reverse micellar systems also provided a novel medium for studying seeding phenomena in the growth of microporous materials. The addition of seed crystals to

speed up the crystallization process has been practiced for microporous material synthesis for four decades. Seeding can take various forms: addition of macroscopic seed crystals obtained from a previous synthesis, aging of reactants at a lower temperature to form seeds in situ, and addition of a ‘‘seed solution’’ created by a brief hydrothermal process to a reactant composition [80–82]. The mechanism for rate enhancement is eventually related to the small seeds. Macroscopic seeds promote nucleation by providing nuclei that exist on their surfaces (secondary process), and small seeds, by virtue of their high surface area, consume reactants and grow rapidly into crystals. Two approaches to seeding have been examined in reverse micellar systems. The first dealt with taking well-washed ZnPO-X crystals prepared from composition A and added back to the reverse micelles of composition A. In order to keep the seed crystals suspended, the reaction was carried out in a rotating cell. Figure 21 shows the SEM pictures obtained from the synthesis. It appears that the seed crystals do not grow further and that a new crop of small crystals of reasonably uniform size grows on the seed crystals. The more interesting experiment dealt with taking the mother liquor from a composition A synthesis after the crystallization was completed and using this solution as a seed solution. As mentioned before, light scattering indicated that the size of the clusters present in the mother liquor was of the order of 15 nm. To use the mother liquor as an effective seed solution, a second composition B involving three micellar solutions was prepared. This composition does not produce ZnPO-X and it takes about 2 days for a solid to first appear, thus providing a good source of nutrients. The three solutions in composition B were: 0.2 M Zn(NO3)2 ⭈ 6H2O, 0.11 M NaOH and 0.27 M H3PO4, and 0.58 M DABCO solution. Reaction was carried out by mixing zinc, phosphate, and DABCO reverse micelle solution with the volume ratio of 1:1:1. Upon adding the mother liquor to composition B, a large

TABLE 8 Composition of Reactants Used in Synthesis of ZnPO-X with DABCO as Structure-Directing Agent Conventional synthesis [Zn2⫹] = 0.8 M [Na⫹] = 0.43 M [PO3⫺ 4 ] = 1.13 M [DABCO] = 2.33 M

Aqueous solution used to prepare micellar solution Composition A

Composition B

[Zn2⫹] = 0.16 M [Na⫹] = 0.11 M [PO3⫺ 4 ] = 0.27 M [DABCO] = 0.58 M

[Zn2⫹] = 0.20 M [Na⫹] = 0.11 M [PO3⫺ 4 ] = 0.27 M [DABCO] = 0.58 M

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FIG. 21 SEM pictures of products from seeding experiment. (a) Dried ZnPO-X crystals as seeds. (b) Mother liquor from a completed ZnPO-X synthesis used as seed solution.

number of very uniform ZnPO-X crystals are produced as seen in Fig. 21b. The rodlike crystals are the product from composition B and are also found in the absence of the seed solution. The seeding experiment involving addition of mother liquor to composition B was repeated in columns of different heights to examine the influence of longer suspension on crystal size. Figure 22 shows the SEM data for crystals obtained from columns of height 0.71, 1.78, and 2.62 m. With increasing column length, the crystal sizes increased and average ZnPO-X crystal sizes of 3, 6, and 15 ␮m were observed. The increase in size of crystals as a function of suspension time indicates that the crystals grow from the seed nuclei by incorporating nutrients, indicative of pathway A in sodalite growth from AOT reverse micelles.

FIG. 22 SEM pictures of ZnPO-X crystals obtained from columns of different heights: (a) 0.71, (b) 1.78, and (c) 2.62 m.


V.

CONCLUSIONS

Reverse micelles have been demonstrated over several decades to be a unique reaction medium for synthesis of nanoparticles of a wide class of materials. This chapter demonstrates that microporous materials can also be synthesized under appropriate conditions from reverse micellar reactants. The metastable nature of microporous materials requires a well-controlled compositional environment for synthesis. This is in contrast to most syntheses that are carried out in the reverse micellar medium, which involve direct precipitation chemistry. Thus, the open-pore framework ZnPO-X could not be synthesized with AOT reverse micelles because the high levels of Na⫹ in the water pool thwarted the nucleation of ZnPO-X and promoted the nucleation of sodalite. Understanding the reasons for failure of AOT reverse micelles in growing ZnPO-X led to the examination of cationic reverse micelles, especially the two-tailed surfactant DODMAC. ZnPO-X was successfully synthesized from DODMAC reverse micelles with two different structure-directing agents, tetramethylammonium ion and 1,4-diazabicyclo[2,2,2]octane. Reverse micelles could be made by equilibration with excess aqueous phase containing the zinc and phosphate reactants (Winsor II) or by injection of the correct amount of aqueous phase into the surfactant-cosurfactant-isooctane medium (Winsor IV). Several other unique aspects of the reverse micellar medium were discovered as compared with conventional synthesis. A particularly interesting feature was the control over crystallization pathways by minor changes in the reactant composition. This was well demonstrated in the crystallization of sodalite from AOT reverse micelles. Depending on the intramicellar pH, the fraction of the reverse micelles in which supersaturation conditions were achieved could be varied. For compositions in which the fraction was low, the number of nuclei formed was small and these nuclei grew slowly by incorporating nutrients from nonnucleated reverse micelles. On the other hand, for compositions where the fraction of reverse micelles in which supersaturation was exceeded was large, rapid precipitation of an amoprhous zincophosphate occurred from which sodalite crystals appeared, much like the observations in conventional synthesis. The reason that reverse micelles provide this degree of control is that they provide compartmentalized reaction centers that can exist in the same system but with different compositions. A second discovery related to the DODMAC reverse micelles was the use of this medium as a seed solution.

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Typical synthesis yields of ZnPO-X from DODMAC reverse micelles were of the order of 15–20%, indicating that at the end of the synthesis reaction, a large fraction of the reactants are still present in the organic medium. They were found to be present as clusters of size 15 nm and would grow rapidly into ZnPO-X crystals if provided with a source of zinc and phosphate nutrients. Because reverse micelles provide a novel reaction environment, it is expected that in the future new framework structures can be synthesized. Extension of reverse micellar systems for synthesis of mesoporous materials is also of interest. Reverse micelles that are more stable at higher temperatures can be used for the synthesis of zeolites (aluminosilicates). ACKNOWLEDGMENTS We acknowledge funding from NASA. REFERENCES 1. 2.

3. 4. 5. 6. 7. 8. 9. 10. 11.

12. 13. 14. 15. 16.

R. Szostak, Handbook of Molecular Sieves, Van Nostrand, New York, 1992. J. Weitkamp, H. G. Karge, H. Pfeifer, W. Holderich, eds., Zeolites and Related Microporous Materials: State of the Art 1994, Elsevier, Amsterdam, 1994. A. Corma and H. Garcia, Catal. Today 38:257–308 (1997). E. R. Geus, M. J. den Exter, and H. van Bekkum, J. Chem. Soc. Faraday Trans. 88:3101–3109 (1992). H. G. Smolka and M. Schwuger, Colloid Polym. Sci. 256:270–277 (1978). J. W. Ward, Appl. Ind. Catal. 3:271–392 (1984). D. W. Breck, Zeolite Molecular Sieves, Wiley, New York, 1974. M. E. Davis and R. F. Lobo, Chem. Mater. 4:756–768 (1992). C. T. G. Knight, Zeolites 10:140–144 (1990). R. M. Barrer, Hydrothermal Chemistry of Zeolites, Academic Press, London, 1982. E. N. Coker, J. C. Jasen, J. A. Martens, P. A. Jacobs, F. DiRenzo, F. Fajula, and A. Sacco, Jr., Microporous Mesoporous Mater. 23:119–136 (1998). E. Engelhardt and H. van Koningsveld, Zeolites 10: 650–656 (1990). S. L. Burkett and M. E. Davis, Chem. Mater. 7:920– 928 (1995). P.-P. E. A. de Moor, T. P. M. Beelen, and R. A. van Santen, J. Phys. Chem. B 103:1639–1650 (1999). P. K. Dutta, J. Inclusion Phenom. Mol. Recognit. Chem. 21:215–237 (1995). P. K. Dutta, M. Puri, and D. C. Shieh, Mater. Res. Soc. 111:101–106 (1988).

758 17. 18. 19.

20. 21. 22. 23. 24. 25. 26. 27. 28.

29. 30. 31. 32. 33.

34. 35.

36. 37. 38. 39. 40. 41.

42.

Singh et al. P. K. Dutta, M. Puri, and C. Bowers, ACS Symp. Ser. 398:98–109 (1989). H. G. Hertz, Angew. Chem. Int. Ed. Engl. 9:124–138 (1970). M. Bourrel and R. S. Schechter, Microemulsion and Related Systems: Formation, Solvency and Physical Properties, Surfactant Science Series, Vol. 30, Marcel Dekker, New York, 1988. B. H. Robinson, Nature, 320:309 (1986). M. Kotlarchyk, J. S. Huang, and S. H. Chen, J. Phys. Chem. 89:4382–4346 (1985). J. Eastoe, B. H. Robinson, D. C. Steytler, and D. ThornLeeson, Adv. Colloid Interface Sci. 36:1–31 (1991). P. D. I. Fletcher, A. M. Howe, and B. H. Robinson, J. Chem. Soc. Faraday Trans. 1 83:985–1006 (1987). C. Oldfield, J. Chem. Soc. Faraday Trans. 87:2607– 2612 (1991). F. M. Menger and K. Yamada, J. Am. Chem. Soc. 101: 6731–6734 (1979). M. P. Pileni, J. Phys. Chem. 97:6961–6973 (1993). J. H. Fendler, Chem. Rev. 87:877–899 (1987). M. L. Steigerwald, A. P. Alivisatos, J. M. Gibson, T. D. Harris, R. Kortan, A. J. Muller, A. M. Thayer, T. M. Duncan, D. C. Douglas, and L. E. Brus, J. Am. Chem. Soc. 110:3046–3050 (1988). W. F. C. Sager, Curr. Opin. Colloid Interface Sci. 3: 276–283 (1998). V. Pillai, P. Kumar, M. J. Hou, P. Ayub, and D. O. Shah, Adv. Colloid Interface Sci. 55:241–269 (1995). P. K. Dutta and D. Robins, Langmuir 7:1048–1050 (1991). T. E. Gier and G. D. Stucky, Nature 349:508–510 (1991). T. E. Gier, W. T. A. Harrison, T. M. Nenoff, and G. D. Stucky, Molecular Sieves, Van Nostrand Reinhold, New York, 1992, pp. 407–426. P. K. Dutta, K. S. N. Reddy, L. M. Salvati, and M. Jakupca, Nature 374:44–46 (1995). K. S. N. Reddy, L. M. Salvati, P. K. Dutta, P. B. Abel, K. I. Suh, and R. R. Ansari, J. Phys. Chem. 100:9870– 9880 (1996). J. Felsche, S. Luger, and C. Baerlocher, Zeolites 6:367– 372 (1986). D. M. Bibby and M. P. Dale, Nature 317:157–158 (1985). G. O. Roberts, D. M. Kornfeld, and W. W. Fowlis, J. Fluid Mech. 229:555–567 (1991). R. E. Smith and P. L. Luisi, Helv. Chim. Acta 63:2302– 2311 (1980). J. W. Mullin, Crystallization, Butterworth-Heinemann, Oxford, 1993. O. Sohnel and J. Garside, Precipitation—Basic Principles and Industrial Application, Butterworth-Heinemann, London, 1992. J. L. Meyer and G. H. Nancollas, Arch. Oral. Biol. 17: 1623–1627 (1972).

43. 44. 45. 46. 47. 48. 49. 50. 51.

52.

53.

54. 55. 56. 57. 58. 59. 60.

61.

62. 63. 64. 65. 66.

67.

M. Siddiq, T. Gilanyi, and A. C. Zettlemoyer, J. Colloid Interface Sci. 64:192–193 (1978). S. Lazic, J. Cryst. Growth 147:147–154 (1995). H. Hohl, P. G. Koutsoukos, and G. H. Nancollas, J. Cryst. Growth 57:325–335 (1982). J. B. Jensen and J. Lou, Acta Chem. Scand. A37:617– 629 (1983). J. H. A. van der Woude and P. L. deBruyn, Colloids Surf. 8:55–78 (1983). F. M. Menger, J. A. Donohue, and R. F. Williams, J. Am. Chem. Soc. 95:286–288 (1973). J. G. Darab, D. M. Pfund, J. L. Fulton, J. C. Linehan, M. Capel, and Y. Ma, Langmuir 10:135–141 (1994). T. Hirai, H. Sato, and I. Komasawa, Ind. Eng. Chem. Res. 32:3014–3019 (1993); 33:3262–3266 (1994). A. G. Walton, in Dispersion of Powder in Liquids, 2nd ed. (G. D. Parfitt, ed.), Applied Science Publishers, London, 1973, pp. 175–220. E. Kirkova and M. Djarova, Industrial Crystallization, Proc. Symp. 7th, Meeting Date 1978, 1979, pp. 81– 89. H. Furedi-Milhofer, E. Oljica-Zabcic, B. Purgaric, B. Kosar-Grasic, and N. Parkovic, J. Inorg. Nucl. Chem. 37:2047–2051 (1975). C. Petit, P. Lixon, and M.-P. Pileni, J. Phys. Chem. 97: 12974–12983 (1993). S. D. Loades, S. W. Carr, D. H. Gay, and A. L. Rohl, J. Chem. Soc. Chem. Commun. 1369–1370 (1994). K. Osseo-Asare and I. J. Arriagada, Colloid Surf. 50: 321–339 (1990). K. Kandori, K. Kon-No, and A. Kitahara, J. Dispersion Sci. Technol. 9:61–73 (1988). O. Sohnel and J. W. Mullin, J. Cryst. Growth 60:239– 250 (1982). J. L. Meyer and C. C. Weatherall, J. Colloid Interface Sci. 89:257–267 (1982). W. Kibalczyc, I. V. Melikhov, and V. F. Komarov, Industrial Crystallization, Proc. Symp. 8th, Meeting Date 1981, 1982, pp. 291–292. O. Sohnel and J. Garside, Precipitation—Basic Principles and Industrial Application, Butterworth-Heinemann, London, 1992, chapter 4. M. J. Castagnola and P. K. Dutta, Microporous Mesoporous Mater. 20:149–159 (1998). M. Wong, J. K. Thomas, and T. Nowak, J. Am. Chem. Soc. 99:4730–4736 (1977). E. T. Roach, P. R. Handy, and A. I. Popov, Inorg. Nucl. Chem. Lett. 9:359–363 (1973). H. R. Wyss and M. Falk, Can. J. Chem. 48:607–614 (1970). W. A. P. Luck, in Water, A Comprehensive Treatise, Water in Crystalline Hydrates: Aqueous Solutions of Simple Non-Electrolytes (F. Franks, ed.), Vol. 2, Plenum, New York, 1973, chapter 4. R. E. Verrall, in Water, A Comprehensive Treatise,


68. 69. 70. 71. 72. 73. 74.

Aqueous Solutions of Simple Electrolytes (F. Franks, ed.), Vol. 3, Plenum, New York, 1973, pp. 211–264. G. Onori and A. Santucci, J. Phys. Chem. 97:5430– 5434 (1993). T. K. Jain, M. Varshney, and A. Maitra, J. Phys. Chem. 93:7409–7416 (1989). C. F. Komives, D. E. Osborne, and A. J. Russel, J. Phys. Chem. 98:369–376 (1994). W. Wang, M. E. Weber, and J. H. Vera, J. Colloid Interface Sci. 168:422–427 (1994). M. S. Zabalay and J. H. Vera, J. Chem. Eng. Data 41: 1499–1504 (1996). W. Wang, M. E. Weber, and J. H. Vera, Ind. Eng. Chem. Res. 34:599–606 (1995). W. Wang, M. E. Weber, and J. H. Vera, Biotechnol. Bioeng. 46:343–350 (1995).

759 75. 76. 77. 78. 79. 80. 81. 82.

M. J. Castagnola, Thesis dissertation, Ohio State University, 1999. M. J. Castagnola and P. K. Dutta, Microporous Mesoporous Mater. 34:61–64 (2000). H. R. Rabie, M. E. Weber, and J. H. Vera, J. Colloid Interface Sci. 174:1–9 (1995). A. Derouiche and C. Tondre, J. Dispersion Sci. Technol. 12:517–530 (1991). A. Jada, J. Lang, R. Zana, R. Makhloufi, E. Hirsch, and S. J. Candau, J. Phys. Chem. 94:387–395 (1990). E. Narita, J. Cryst. Growth 78:1–8 (1986). J. Warzywoda and R. W. Thompson, Zeolites 11:577– 582 (1991). L. V. Hou and R. W. Thompson, Zeolites 9:526–530 (1989).

37 Mesoscopic Films at Interfaces SRINIVAS MANNE, R. K. WORKMAN, and J. L. WOLGEMUTH Tucson, Arizona

I.

INTRODUCTION

University of Arizona,

crystalline phase. The specific nanocomposite phase depends critically on the interactions between surfactant molecules and the solubilized inorganic ions in ways that are not yet fully understood. Controlled heating of the precipitate condenses and rigidifies the inorganic phase while pyrolyzing the surfactant phase, resulting finally in a mesoporous material with voids in the size range of micelles. By using both conventional surfactants and amphiphilic block copolymers, mesoporous oxides with void periodicities of 3–30 nm have been produced. Early work on mesoscopic materials focused primarily on bulk synthesis, which yielded fine powders with typically submicrometer particle sizes [1]. These were primarily useful for investigating the pore structure and organization, via powder diffractometry, adsorption isotherms, and so on. The arrangement of void spaces has been referred to as the material’s ‘‘primary structure’’ [3], corresponding to its mesoscopic lattice symmetry or space group. However, future applications of these materials hinge on controlling not only the primary structure but also the crystallographic coherence and spatial orientation of the pore lattice over macroscopic length scales. Thus, much of the recent literature on mesoscopic materials has focused on controlling these so-called secondary and tertiary structures. Secondary structures refers to the persistence length or coherence length (domain size) of a given lattice orientation, and tertiary structure refers to the orientation of the domains with respect to each other and with respect to the ‘‘lab frame’’ over macroscopic distances [3].

The rapid growth of mesoscopic materials in the last decade or so confirms the adage that a gradual scientific understanding usually follows rapid technological development rather than the other way around. The synthesis of surfactant-templated mesoporous silica by scientists at Mobil research laboratories [1] triggered an explosive technological development in mesoscopic materials that continues apace; the original paper of Beck et al. has, in the past 8 years, garnered well over a thousand references. The basic idea of surfactant templating has since been extended to the synthesis of a large variety of oxides, sulfides, and metals and to a variety of material geometries—powders, crystals, films, and fibers [2]. Although great strides have been made in reaction optimization and especially morphological control of the end product, we have only recently begun to understand how intermolecular and surface forces among surfactant molecules, interfaces, and soluble precursor ions actually determine the ultimate morphology. Surfactant-templated synthesis relies on inorganic polymerization (or, less often, heterogeneous nucleation) at the interfacial region between a surfactant aggregate and a solution in which the inorganic precursors are initially dispersed (Fig. 1). If the surfactant is soluble (which is most often the case), the surfactantsolution ‘‘interface’’ is dispersed in the form of micelles, and interfacial reactions yield a surfactant-inorganic nanocomposite in the form of a lyotropic liquid 761

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FIG. 1 Formation of a hypothetical mesoporous membrane (schematic). (a) Surfactant micelles initially coexist in solution with solubilized silicate species (triangles). (b) Surfactants and silicates begin to coassemble in solution to form surfactant-silicate mesophases. The silicates oligomerize and cross-link around the micelles. (c) Pyrolysis and calcination vaporize the surfactant and complete the silicate condensation, resulting in a membrane with regularly spaced holes of mesoscopic dimensions. An idealized membrane is shown with holes running perpendicular to the film plane; such a configuration has not yet been achieved.

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In one way or another, nearly all attempts to achieve control over such secondary and tertiary structures have used interfaces, and the reaction products have been in the form of mesoscopic films. Typically, these films have submicrometer thicknesses but macroscopic lengths and widths and are composed of mesoscopic subunits with unit cells in the size range of micelles. In this chapter we review both the technological development of these films and our current state of scientific understanding of their self-assembly. This is intended not to be an exhaustive literature review but rather an attempt to find order and coherence in a rapidly expanding field—an attempt to identify the overall scientific and technological goals, achievements, and challenges ahead. Technologically, the goal of surfactant-templated film synthesis can be identified as a robust membrane of finite and controllable thickness and arbitrary lateral size, whose pores are individually addressable and arranged in a lattice that is crystallographically coherent over the entire membrane surface. The simplest example is a thin film containing columnar pores normal to the film plane and arranged in a lattice (Fig. 1c). Such a membrane would find immediate use as a molecular filter, perhaps in separating polymers by molecular weight or separating branched from linear hydrocarbons. Membranes with uniformly functionalized pore walls can serve as catalytic supports, and the confined reaction space can be used to catalyze the synthesis of nanoparticles or nanowires. On the other hand, membranes with locally functionalized pores, where the chemical functionality varies in a known way across the membrane surface, can be used as chemical or biological sensors and separators. Although the ideal end product of Fig. 1c has yet to be realized by surfactant-based templating, several innovations have produced membranes of macroscopic size and with far greater control over secondary and tertiary structure than was previously available. Scientifically, the ultimate goal is to successfully explain and predict the primary, secondary, and tertiary structures given the surfactant geometry, inorganic precursor species, interface properties, and reaction conditions. The chief difficulty is the number of competing interactions. Self-assembly in pure surfactant solutions involves a competition between attractive (hydrophobic) interactions and repulsive (hydrophilic) interactions, whose interplay gives rise to the characteristic micelle curvature and lyotropic phase behavior [4]. Whereas surfactant self-assembly in pure solution is fairly well understood, the effects of interfaces and large multivalent ions have started becoming clear only

Mesoscopic Films at Interfaces

in the last few years. As a result of this work, much of the primary structure of mesoscopic films can now be understood in the context of competing surfactant-surfactant, surfactant-precursor, and surfactant-interface interactions. However, secondary and tertiary structures still remain a challenge in terms of both technological control and theoretical understanding. Because this review in part concerns our current state of understanding, it is natural to begin by considering how interfaces and solubilized precursor ions affect the self-assembly morphology of surfactant molecules in solution. II.

SELF-ASSEMBLY: EFFECTS OF INTERFACES AND PRECURSOR SPECIES

The self-assembly of soluble surfactants in free aqueous solution has been experimentally investigated and theoretically modeled for several decades, and it is worth briefly recalling the salient features [4]. At very low concentrations, surfactants dissolve completely and exist as solubilized monomers in water. But above the critical micelle concentration (cmc), surfactant molecules begin to self-assemble into finite liquid crystalline aggregates (micelles). This aggregation is driven by intertailgroup attractions (hydrophobic and van der Waals forces) but is limited by interheadgroup repulsions (electrostatic and steric/entropic forces). The balance between these intermolecular forces determines the final shape of the micelle. To first order, micelle shapes are described by the ‘‘dimensionless packing parameter’’ [5] g ⬅ v/(a0 l), where v and l are the volume and extended length, respectively, of the hydrocarbon chain, and a0 is the optimal headgroup area per molecule in the micellar environment. Values of g < 1/3 lead to spherical micelles, whereas 1/3 < g < 1/2 favors cylindrical micelles and g > 1/2 favors flat bilayers [5]. For a saturated, unbranched alkane, the chain volume v (in nm3) and chain length l (in nm) are given in terms of the number of carbon atoms n by Tanford’s formulas [6], based on known bond lengths and angles for alkanes: v ⬇ 27.4 ⫹ 26.9 ⫻ n l ⬇ 0.154 ⫹ 0.127 ⫻ n For typical surfactants, n > 10 and the second term dominates the expressions for v and l. The packing parameter therefore becomes independent of n and is approximately given by g ⬇ (0.212 nm2)/a0. Thus, the micelle shape is determined almost exclusively by the optimal headgroup area for typical single-tail surfactants. The most commonly encountered micelle shapes

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are approximately spherical and are composed of order ⬃100 molecules. Above the cmc, the monomer concentration remains roughly constant, with the newly added molecules going exclusively toward micelle formation. Some surfactants at moderate concentrations express a second cmc, which is often identified with the onset of micelle shape change, e.g., from spherical to cylindrical [7]. At higher concentrations, surfactant micelles pack into regular arrays and begin to form lyotropic liquid crystalline phases. For conventional surfactants (single head, single tail), the first lyotropic phase formed is usually one of three types. Surfactants with the largest value of a0, whose micelles remain spherical up to high concentrations, form a discontinuous cubic phase; this phase is not completely understood but is thought to consist of discrete micelles in some kind of cubic lattice [8]. On the other hand, surfactants with smaller values of a0, which undergo a sphere → cylinder micelle shape transition at the second cmc, typically form a hexagonal phase consisting of cylindrical micelles arranged in a hexagonal pattern. Finally, surfactants with the smallest headgroup areas, which form micelles in the shape of flat bilayers, form lamellar phases consisting of stacked, uniformly spaced bilayers at high concentration. The first two phases—discontinuous cubic and hexagonal—are the most relevant for mesoporous film synthesis because the pyrolytic removal of surfactants (the discrete phase) leaves a stable continuous phase of silicates. In contrast, lamellar surfactantsilicate mesophases typically collapse upon pyrolysis because the silicate phase is not continuous in this case. The presence of third components in the surfactant solution—such as foreign counterions, polymers, and interfaces—can dramatically alter the surfactant selfassembly and lyotropic phase progression. This is because foreign species modify intersurfactant interactions and introduce additional competing interactions with surfactant or solvent molecules. We now consider these effects in detail. A.

Self-Assembly at Planar Interfaces

Surfactants are, of course, generally attracted to interfaces. All hydrophobic interfaces attract surfactant tailgroups via hydrophobic and van der Waals interactions, and many hydrophilic interfaces attract surfactant headgroups via screened electrostatic and hydrogen-bonding interactions. These interactions can lead to effective interfacial concentrations that are orders of magnitude greater than bulk surfactant concentrations. In 1955 it was first proposed that this enrichment gave rise to dis-

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tinct interfacial aggregates analogous to bulk micelles [9]. In the last few years, atomic force microscopy (AFM) confirmed this view and obtained the first direct images of interfacial micellar phases [10,11]. AFM studies have since rapidly elucidated the aggregate structures of a variety of surfactants (ionic, nonionic, and zwitterionic) at a variety of solid surfaces (hydrophilic and hydrophobic) in contact with aqueous micellar solutions [10–27]. Most investigations have used atomically flat model surfaces, often the ordered cleavage planes of layered solids such as mica and graphite. These surfaces have proved ideal both for self-assembly studies and for mesoscopic film synthesis (see later). We now review the salient results for interfacial self-assembly morphologies, with special emphasis on mica and graphite; representative AFM images are shown in Fig. 2. 1. Hydrophobic Solid Surfaces On the cleavage plane of highly oriented pyrolitic graphite (HOPG), early results [10,11] showed that interfacial self-assembly was determined almost entirely by the crystalline anisotropy of the substrate. AFM images revealed aggregates in the form of parallel stripes oriented perpendicular to an underlying symmetry axis and spaced apart by roughly twice the length of a surfactant molecule (Fig. 2b). Upon comparison with adsorption isotherm data, the AFM images were interpreted as half-cylindrical micelles, where the bottom row of molecules is oriented horizontally along a symmetry axis. Similar parallel stripes were also found at the same relative orientation for the crystalline cleavage plane of MoS2 [11]. The parallel half-cylindrical morphology has since been observed on graphite for a variety of charged [11,14,18] and uncharged surfactants [16,19,22], over a surprisingly wide range of surfactant geometries. In general, surfactants capable of cylindrical curvature (i.e., those exhibiting a bulk hexagonal phase) have self-assembled into oriented half-cylinders on crystalline hydrophobic surfaces. This high degree of surface control has been attributed to the anisotropy of interaction between the horizontal alkane tail and the crystalline surface [10]. As long as the tail exceeds a certain minimum length (found to be ⬃10 carbon atoms [22,25]), the linear contact area between the tail and surface is thought to enhance the direction sensitivity of the interaction, leading to adsorption directions along the symmetry axes. When the anisotropy is removed—i.e., when the hydrophobic substrate is amorphous—interfacial aggregates appear to revert to half-spheres (Fig. 2d) for a variety of charged and uncharged surfactants [28]. This

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may be considered the ‘‘natural’’ curvature for surfactants that form spherical micelles in solution but are subjected to a hydrophobic boundary condition. (These results are, however, more equivocal than those for graphite, and observed morphologies on silanated silica are quite sensitive to surface flatness and hydrophobizing technique [22,28].) 2. Hydrophilic Solid Surfaces The most widely studied systems in this class have been ionic surfactants on oppositely charged surfaces —primarily cationic surfactants on flat, anionic surfaces of mica and silica. Here surfactant headgroups interact electrostatically with the surface, leading to ‘‘full’’ aggregates above the cmc, with headgroups facing the solution as well as the surface. Aggregate morphologies depend on both the surfactant geometry and the density of oppositely charged surface sites. On amorphous silica, AFM studies with single-tail cationic surfactants have revealed globular interfacial aggregates that resemble pinned micelles [11]; the arrangement of these globular aggregates generally resembles a glassy phase, having a well-defined nearest neighbor distance (comparable to a micelle diameter) but lacking long-range order over the surface. Single-tail cationics on the cleavage plane of mica have shown both spherical and cylindrical aggregates, depending on the surfactant geometry. Surfactants with large or unusually repulsive headgroups (e.g., triethylammonium or divalent headgroups) give rise to spherical aggregates arranged in a hexagonal lattice (Fig. 2a) [14,17]; the symmetry axes of this ‘‘micelle lattice’’ have been observed to align with the underlying mica lattice, indicating interfacial epitaxy [14]. Cationics with comparatively smaller or less repulsive headgroups have revealed parallel, meandering stripes (Fig. 2c), consistent with close-packed but flexible cylindrical aggregates lying horizontally on the mica surface [11,14,17]. Here also the cylinders can be partially aligned by the surface lattice, although to a lesser degree than on graphite. These results can be qualitatively understood by considering each oppositely charged surface site as a potential adsorption site for a surfactant molecule and therefore a potential nucleation site for an interfacial aggregate above the cmc. When the substrate charge density is smaller than that of the micelle surface, interfacial self-assembly is determined primarily by intermolecular interactions, and the natural curvature is only minimally perturbed; thus, we expect globular aggregates resembling bulk micelles at surfaces with low charge density. This is exactly what is observed on silica, whose surface potential is typically small com-


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FIG. 2 AFM images (200 ⫻ 200 nm) of interfacial surfactant micelles obtained in situ in surfactant solutions at twice the critical micelle concentration (cmc). (a) The divalent gemini surfactant C18H37N⫹(CH3)2(CH2)3N⫹(CH2)3 ⭈ 2Br⫺ (or C18-3-1 for short) self-assembles into hexagonally close-packed spherical micelles on the anionic cleavage plane of mica. (b) Sodium dodecyl sulfate (SDS) on hydrophobic graphite, showing rigid stripes consistent with parallel half-cylindrical micelles. (c) Tetradecyltrimethylammonium bromide (TTAB) on mica, showing flexible stripes consistent with full cylindrical micelles. (d) The nonionic surfactant octaethyleneglycol monododecyl ether (or C12E8 for short) on an amorphous hydrophobic surface (alkylated silica) showing hemispherical micelles.

pared with that of a micelle (⬃100 mV). On the other hand, if the effective charge density of the substrate exceeds that of micelles, adsorbed headgroups are forced closer together than would be the case in a micellar environment, and the effective packing parameter

g increases. This can cause a transition to lower aggregate curvature for surfactants that are already close to a transitional value of g but not for surfactants whose g is far from a transitional value [14]. This is exactly what is observed on mica, whose effective charge den-

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sity is very large (⬃2e⫺/nm2) due to exchangeable surface cations. Thus alkyltrimethylammonium bromides, which have g values close to 1/3 and undergo sphere → cylinder transitions at moderate bulk concentrations, self-assemble as close-packed cylinders on mica (Fig. 2c). On the other hand, divalent surfactants, which have larger headgroup areas and lower g values, favor high curvature and self-assemble as close-packed spheres on mica (Fig. 2a). These hexagonally closepacked spheres can be induced to switch to parallel flexible cylinders by the addition of strongly binding counterions such as salicylate [14], which effectively lowers the micelle surface charge and increases the packing parameter. For nonionic surfactants based on oligomeric ethylene oxide (EO) headgroups, a0 and g are determined simply by the physical headgroup size or the number n of EO units; a large n leads to spherical micelles and discontinuous cubic phases in bulk solution, whereas a small n leads to bilayers and lamellar phases [29]. Experiments with nonionic surfactants on silica show a similar trend at this interface [22]. Surfactants that form spherical micelles in bulk also reveal globular interfacial aggregtaes (with no long-range order), and surfactants that form bilayers in solution also from bilayers at the silica surface. Here the headgroup adsorption, which serves a foundation for interfacial self-assembly, is driven not by electrostatics but by hydrogen bonding between the EO oxygens and the surface SiOH units. That the interfacial self-assembly is only minimally perturbed from bulk self-assembly indicates that interfacial headgroup areas are comparable to a0 in bulk solution, which in turn implies that the density of Hbonding sites on a silica surface falls short of the density of H-bonding sites (i.e., oxygen atoms) at a micelle-solution interface. 3. Air-Liquid Interface Although the air-water interface is amorphous, hydrophobic, and relatively flat (owing to the large surface tension of water), it differs in a crucial and obvious way from, say, hydrophobized silica: Surfactant molecules can penetrate the air-water interface, giving rise to a diffuse density profile rather than a sharp boundary. Neutron reflectometry studies have indicated that carbon atoms nearest to the headgroup are oriented normal to the interface, whereas outer carbon atoms are tilted progressively further from the normal, suggesting the presence of interfacial micelles [30]. This is also in agreement with molecular dynamics simulations [31]. So far it has not been possible to determine the micelle shape directly by AFM at the air-liquid interface.

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4.

Secondary and Tertiary Structures of Interfacial Surfactant Aggregates A glance at Fig. 1 readily shows that interfaces, in addition to determining the curvature of individual aggregates, often influence how the aggregates are arranged relative to each other and relative to the surface. These can be regarded as the secondary and tertiary structures of the interfacial aggregate layer and are of key importance in the nucleation of mesoscopic films. The long-range order is most pronounced for crystalline substrates such as mica and especially graphite, where epitaxy between surfactants and surface enhances both the interaggregate order (secondary structure) and the orientation relative to the substrate symmetry axes (tertiary structure). However, it is important to note that epitaxy can also interfere with tertiary structure, because surface lattices typically have two or more symmetry directions that can serve as equivalent orientation axes for interfacial aggregates. For instance, half-cylindrical or cylindrical aggregates, instead of orienting along a single direction over the entire surface, typically show a ‘‘patchwork’’ domain structure with two or three equivalent orientations relative to the underlying lattice (see Fig. 2b). Although there has been no systematic study of domain sizes to date, they are usually in the 1–10 ␮m range and may be sensitive to local defects in the underlying substrate. These domain boundaries present a significant impediment to the nucleation of oriented, continuous mesoscopic films.

III.

SURFACTANT MICELLES: EFFECTS OF INORGANIC PRECURSORS

Solubilized inorganic species can completely alter the micelle shape and the lyotropic phase progression of surfactants. For example, highly hydrated anions (such as chloride) bind relatively weakly to alkyltrimethylammonium ions, and the consequent electrostatic repulsion between headgroups favors highly curved micelles and (often) discontinuous cubic phases. In contrast, weakly hydrated anions (such as bromide) bind more energetically to alkyltrimethylammonium headgroups, favoring sphere-to-rod transitions at moderate salt concentrations and (usually) hexagonal mesophases [32]. Similarly, during the synthesis of mesoscopic materials, inorganic precursor species do not simply ‘‘coat’’ the surface of existing surfactant micelles by polymerization; rather, inorganic species actively alter the self-assembly by binding to surfactant headgroups via electrostatic forces or hydrogen bonds.


The model of simultaneous self-organization of surfactants and polymerizable inorganics, discussed in the following, has alternatively been termed ‘‘cooperative assembly’’ or ‘‘cooperative templating.’’ Even in the first work reported by Mobil researchers [1], conditions that favored spherical micelles in pure surfactant solutions nevertheless yielded a hexagonalphase nanocomposite composed of cylindrical micelles in the presence of dissolved silicates. The mechanisms by which inorganic ions change the preferred micelle curvature and induce mesophase formation has since been a central preoccupation in the science of mesoscopic materials. The structure of the final material itself does not give definitive insight into this problem because the effects of intervening processing steps (condensation, dehydration, pyrolysis) after solutionphase self-assembly are also unknown. This problem has been addressed by probing the structure of solution mesophases before the formation of a solid phase, and this work has led to valuable insights into the effects of precursor ions on self-assembly [33–36]. These results will be discussed in detail. Inorganic-headgroup interactions depend on the state of the solubilized inorganic species, which in turn depends on the synthesis route. For the case of mesoscopic silica—by far the most common mesoscopic material synthesized—two general routes have been in common use: acidic and basic synthesis. In each case the starting material is usually an oily alkoxide precursor, typically tetraethoxysilane (TEOS) or, less frequently, tetramethoxysilane (TMOS). In aqueous solution these compounds quickly hydrolyze into monomeric and small oligomeric units that are soluble to varying degrees. In highly basic conditions, monomer units are fully deprotonated SiO4⫺ 4 ions; linear or cyclic oligomers, composed of a few (typically 13.5, where silicate ions primarily exist as monomers and are prevented from condensing, no mesophase formation is observed [33]. This behavior is exactly what would be expected of a ‘‘classical’’ surfactant solution whose concentration exceeds the second cmc but falls short of its hexagonal phase. In this regime, entropy and intermicellar electrostatic repulsions prevent further ordering among cylindrical aggregates. Thus, the original alkyltrimethylammonium halide has been transformed by ion exchange into an alkyltrimethylammonium silicate; this still behaves like a surfactant solution in its isotropic phase, albeit with a different micelle geometry. Mesophases are observed to form only at pH < 13.5, as the silicate species begin to condense and oligomerize [34]. This is also a compelling result, because silicate condensation is accompanied by charge reduction, thereby reducing interaggregate repulsion, presumably to the point where attractive van der Waals interactions start to dominate [34]. Under the influence of net attractive interactions, cylindrical aggregates orient parallel to one another in a hexagonal pattern to minimize their free energy. As the aggregates line up adjacent to one another, silicate groups that were initially associated with a single micelle become free to cross-oligomerize with those of adjacent micelles, finally creating a hexagonal mesophase with partial cross-linking. At this point the surfactant-silicate nanocomposite begins to phase-separate from the solution; however, it is still not a ‘‘solid’’ precipitate but rather a weakly cross-linked lyotropic liquid crystal. Interestingly, the

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degree of silicate oligomerization in this mesophase is found to be extremely well defined, markedly different from that of the water-rich phase, and highly specific to the headgroup type [34]. For example, when quaternary ammonium surfactants are used as templates, silicates in the mesophase are found to consist almost entirely of octamers (double-four rings) if the headgroup is trimethylammonium or hexamers (doublethree rings) if the headgroup is triethylammonium, while the water-rich phase is dominated by monomers and dimers [34]. Thus, the intermediate oligomers formed en route to condensation are evidently quite sensitive to the headgroup geometry. A change in temperature at this point can shift the oligomer distribution away from its optimal value for the headgroup, and the resulting modification of electrostatic forces can in some cases cause a global transformation to a new surfactant-silicate mesophase [34,36]. Such phase transitions are a further indication that the dense phase is not yet solid at this point in the reaction. Extensive silicate condensation and cross-linking occur gradually in the reaction vessel over a period of several days (and are completed by drying and heating the precipitate). This reaction step can be accelerated by destabilizing the solution via pH or temperature; however, this sometimes disrupts the delicate liquid crystal phase and gives poor yield qualities (G. D. Stucky, personal communication). In general, best results are obtained when the cooperative assembly of surfactants and silicates is encouraged as far as possible before the condensation step. This is corroborated by work showing that dilute micellar solutions and low silicate/surfactant ratios are important for ordered pore structures [36]. Interesting parallels exist between mesophase formation under basic conditions and interfacial surfactant aggregation on highly charged surfaces such as mica. In both cases, electrostatic attractions between headgroups and multivalent species create local regions of high surfactant concentrations that resemble lyotropic mesophases. Of course, the binding geometry is significantly different in the two systems; charge neutralization by silicates occurs symmetrically over the entire micelle surface, whereas charge neutralization by the mica plane occurs only on the bottom surface of the micelle. Nevertheless, when three-dimensional mesophases in basic surfactant-silicate synthesis are compared with two-dimensional mesophases on mica, we find that the latter morphologies are two-dimensional slices of the former for a wide variety of surfactant geometries [14]. Thus, similarities between headgroupcounterion and headgroup-‘‘countersurface’’ interac-

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tions give rise to interfacial morphologies that can serve as faithful templates for three-dimensional mesophases. This is an important factor in successful mesoscopic film synthesis on mica. B.

Acidic Synthesis Conditions

Despite the early importance and extensive studies of basic synthesis, most mesoscopic materials today are synthesized under acidic conditions (typical pH < 2.5). The chief advantage of acidic synthesis is that it has been found to promote secondary and tertiary structure [39]. Under these conditions, solution-phase silicates are neutral or weakly cationic, and the nature and strength of their interactions with cationic surfactants are expected to be very different from those under basic synthesis conditions. It is therefore surprising—even confounding—that the two synthesis routes often yield the same mesoscopic product morphology. Attempts to model the self-assembly under acidic conditions have stressed the putative role of mediating counterions. In symbolic terms, self-assembly under basic conditions has been described as involving S⫹I⫺ interactions (S = surfactant and I = inorganic), whereas under extremely acidic conditions the putative interaction has been denoted S⫹C⫺I⫹ (C = surfactant counterion) [39]. Unfortunately, no solution-phase studies of surfactant-silicate liquid crystals have yet been reported for acidic conditions to confirm this model. It is worth noting that simple coions added to surfactant solutions do not, in general, significantly affect self-assembly or cause mesophase separation. If the S⫹C⫺I⫹ model is correct, the I⫹ species may be oligomeric and multivalent (partially condensed), thereby binding several headgroups simultaneously. However, even in this case, it is worth noting that copolyelectrolytes in solution are not known to bind significantly to ionic surfactants [40]. Acidic synthesis near the isoelectric point has also been used with neutral surfactants as the structure-directing agents, the so-called S0I0 pathway [41,42]. These surfactants have included alkylamines [41], oligoethyleneoxides [42], and, more recently, polyethyleneoxide-polypropyleneoxide (PEO-PPO) block copolymers [42,43]. Here also, the addition of silicate precursor to a dilute micellar solution of amphiphile leads to mesophase formation, phase separation, and condensation to form surfactant-silicate nanocomposites. Although mesoscopic silicates produced by this pathway are similar in most respects to those produced using ionic surfactants, some differences have been noted. Mesosilicates templated by nonionic surfactants typically have thicker silicate walls (⬃2–7 nm thick)


than those templated by ionic surfactants (⬃1–2 nm thick), making them more robust and thermally stable [41–43]. Whereas early results using nonionic surfactants in moderately acidic conditions gave materials with poor secondary structure [41,42], later work using PEO-PPO copolymers in highly acidic conditions yielded products with domain sizes comparable to those of ionic surfactants [43]. The initial stages of self-assembly in the S0I0 pathway are thought to be driven by H-bond formation and/ or electrostatic interactions between headgroup sites and silicate species. For example, attractive interactions between the electronegative oxygen atoms (of oligoethyleneoxide groups) and silicate species can take the form of (1) H bonds with SiOH groups, for neutral monomers around the isoelectric point [42], and/or (2) electrostatic interactions with cationic silicate oligomers in strongly acidic solutions [43]. H-bond formation between headgroups and silicates is consistent with the observed thickness of silicate walls, as the headgroup region of PEO-based surfactants is considerably more diffuse than for ionic surfactants; wall thickness roughly scales with PEO chain length [43], further corroborating this model. Electrostatic interactions have been thought to promote secondary structure [41], and this is consistent with the greater degree of order observed in highly acidic conditions. In a recent breakthrough, the S0I0 pathway has been extended to synthesize a host of other mesoscopic metal oxides, such as TiO2, ZrO2, and Al2O3, using PEO-PPO block copolymers as the templating agents [44]. Key to this synthesis was the use of ethanol as the reaction medium, which limits the inorganic polymerization rate (while still permitting mesophase formation) so that condensation and crystallization proceed slowly while self-assembly is being established. As with aqueous S0I0 synthesis, the inorganic oxide walls are found to be relatively thick and even partially crystalline. Here, in addition to H bonds and electrostatic interactions, the complexation of metal ions by ethylene oxide groups is proposed as a possible driving mechanism for cooperative assembly [44]. While electrostatic interactions, H bonding, hydrophobic interactions, and metal ion complexation are all possible mechanisms of mesophase formation under acidic conditions, the central question is whether the interaction energy gained by these mechanisms is enough to offset the significant entropy loss associated with mesophase formation. This is difficult to address from first principles. However, headgroup-polysilicate interactions are implicated in cooperative assembly, and it is instructive to compare this system with the

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closest well-defined and well-studied analogue: polymer-surfactant complexes [45]. The analogue for the S⫹I⫺ pathway is cationic surfactants in the presence of anionic polyelectrolytes; such a combination is known to lead to micellar aggregation and mesophase formation in dilute solutions, exactly as observed in basic surfactant-silicate mesophases. However, in the remaining synthesis pathways, the analogy does not fare as well. The analogue for the S⫹C⫺I⫹ pathway is cationic polyelectrolytes in the presence of cationic surfactants —a system that is not known to significantly affect self-assembly or lead to mesophase separation. The analogue for S0I0 —nonionic (or weakly cationic) polyelectrolytes with nonionic surfactants—likewise does not lead to qualitatively different phase behavior. Thus, the mechanism for micellar shape transitions and mesophase formation in acidic conditions remains something of a mystery. C.

Liquid Crystal Templating

All of the pathways just discussed rely on spontaneous, cooperative assembly of surfactant molecules and silicate species in relatively dilute solutions, with the resulting mesophase depending critically on the nature and strength of interactions between silicate species and surfactant headgroups. A new, conceptually simpler approach uses silicate polymerization to solidify lyotropic liquid crystalline phases that are performed in highly concentrated solutions [46,47]. This approach effectively seeks to decouple the physics from the chemistry of mesoscopic materials; i.e., intermolecular forces build the templating framework, which is then solidified by hydrolysis/condensation reactions. The potential advantage of this technique is that it introduces a certain perdictability to the final structure; the surfactant phase progression reveals the range of available meoscopic morphologies. However, successful application depends on the degree to which silicate polymerization in the aqueous channels destabilizes the existing lyotropic template. Potential causes of disruption include silicate-headgroup binding, hydrolysis products such as methanol, and temperature changes due to heats of reaction, all of which can alter the optimal surfactant packing geometry. Indeed, methanol produced by the hydrolysis of TMOS has been found to destroy the liquid crystalline template [46], although the template reformed when the methanol was removed by a gentle vacuum. Hexagonal, bicontinuous cubic, and lamellar phases have been ‘‘cast’’ into mesoscopic silicate materials in this fashion.

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IV.

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MESOSCOPIC FILM NUCLEATION AT INTERFACES

Although mesoscopic single crystals of ⬃1 ␮m size have been grown from bulk solution [1], coherent domains are more typically in the ⬃100 nm size range [41] and often even smaller. Recent work has centered on ways to enhance secondary and tertiary structure to macroscopic length scales, to facilitate applications in catalysis, separation science, chemical and biosensing, and so on. In practice, structural coherence of the final product can be achieved only by controlling the size and alignment of the labile liquid crystalline domains before condensation and solidification have taken place. This necessitates a reasonable grasp of the interactions among neighboring aggregates as well as those between aggregates and any external orienting fields. One report uses strong external magnetic fields (12 tesla) to orient a surfactant-silicate hexagonal phase in bulk solution via small differences in magnetic susceptibility between the liquid crystal and the surrounding solution [48]. Because the liquid crystalline phase is highly viscoelastic, the orientational order is maintained after removal from the magnetic field. The silicate oligomer phase is then destabilized by reducing pH, thereby effecting condensation. An estimated 72% of the final calcined material is found to be oriented along the original field axis [48]. In addition to magnetic fields, another report finds evidence for enhancement of secondary structure with the use of fluoride in acidic synthesis [49]. With the exceptions noted, all other attempts to enhance higher order structure have involved interfacial confinement in some fashion. When interfaces are involved, surface forces become the dominant orienting factor, and these are often much stronger than the body forces that can be exerted by external electric, magnetic, gravitational, and flow fields. Of course, surface forces are also short ranged, which might seem to limit the degree of higher order structure that can be achieved. However, this can be largely mitigated by interaggregate interactions. A single interfacial aggregate layer, which is highly ordered by strong surface forces, can ‘‘communicate’’ its structure to subsequent overlayers by interaggregate interactions, thereby serving as a template for mesophase nucleation. The interfacial morphology, and the degree to which it can be manipulated for applications, depends on both surfactant-surface and surfactant – inorganic precursor interactions and the competition (if any) between them.

A.

Nucleation at Crystalline Surfaces

Mesoscopic films nucleated at crystalline surfaces such as graphite and mica [50–52] have revealed a significant enhancement of secondary and tertiary structure; this is not too surprising given the high orientational order observed for surfactant aggregates at these interfaces. Almost all published examples have used acidic synthesis conditions similar to those used for bulk mesosilicate synthesis, with the nucleating interface (either mica or graphite) immersed in the solution. When the reaction is complete, the nucleant surface is rinsed, dried, and calcined in the usual way. The end product is a supported mesoscopic film of order 0.1 to 1 ␮m thick with pore spacings in the size range of micelles (Fig. 3). Typical domain sizes are in the 10 to 100 ␮m range (two to three orders of magnitude greater than for bulk product), and domains are strongly aligned with respect to the substrate symmetry axes. Only two types of mesoscopic film morphologies have been synthesized to date, both of which are consistent with the interfacial morphology expected with the particular surfactant-surface combinations used. Silicate syntheses in the presence of alkyltrimethylammonium surfactants and a graphite surface have yielded hexagonal-phase films in which pore channels are oriented parallel to the film plane and perpendicular to underlying symmetry axes [51]. This is consistent with the picture of hemicylindrical interfacial aggregates serving as a template for the heterogeneous nucleation of a surfactant-silicate hexagonal phase. Two-dimensional domains are in the form of elongated strips or tapes, with the long axis parallel to the cylinder axis. A very similar morphology is also observed when mica is used as the nucleant in the presence of alkyltrimethylammonium surfactants [50,51]. Here the templating interfacial layer consists of full rather than halfcylindrical aggregates, but the end result is still a hexagonal phase with pore channels oriented in the film plane (Fig. 3). Although AFM images of the surfactantsilicate aggregates in the reaction solution do not show the kind of strong local alignment observed on graphite [51], the long-range structure (Fig. 3a) clearly reveals epitaxial alignment by the substrate, with domains highly elongated along the pore channel axes. Despite the enhanced higher order structures, these films suffer from one technological drawback: The pores are aligned strictly parallel to the film plane, making them difficult to access for applications. A very different film morphology is obtained on mica when conventional surfactants are replaced with


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FIG. 3 Images of hexagonal-phase mesoscopic silica films grown at a mica-solution interface in acidic reaction conditions. (a) Low-magnification SEM image showing oriented strips or tapes (scale bar = 10 ␮m). (b and c) TEM images of the calcined film showing the cross section and transverse views, respectively. The tubules run parallel to the film plane. (From Ref. 51.)

divalent surfactants such as C18-3-1. These have low packing parameters and therefore favor close-packed spherical micelles (analogous to a discontinuous cubic phase) on the mica surface [14] and in the bulk synthesis of mesosilicates [53]. Not surprisingly, mesosilicate films nucleated on mica are consistent with both

of these morphologies. The hexagonally ordered interfacial micelles evidently serve as a template for the nucleation of a mesophase in which silicates condense on the surface of, and in the interstices between, hexagonally close-packed discrete micelles [52]. Consistent with this primary structure, the secondary structure

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shows isotropic disklike islands (rather than elongated domains), sometimes with distinct hexagonal faceting. It might be imagined that surfactant removal by calcination would give rise to a silica framework consisting of discrete, unconnected, roughly spherical voids. However, this appears not to be the case. Gas adsorption isotherms reveal an effective surface area and a lack of hysteresis that are consistent with complete connectivity throughout the mesoscopic film [52]. This implies the presence of small ‘‘necks’’ that connect neighboring void spaces. Although not much is known about this neck distribution, a couple of details are apparent. First, each void must be connected to at least two neighboring voids for complete connectivity to be established. Second, because the film lattice symmetry is unchanged by calcination, the neck distribution must either be random (the more likely case) or limited primarily to the direction normal to the film plane [52]. The void structure and extensive connectivity make this type of mesoscopic film inherently more accessible than the horizontal cylindrical pores discussed before; however, if the connectivity is random, the pores are still not individually addressable. Film uniformity on crystalline surfaces is limited by two factors: multiple surface nucleation sites and equivalent surface symmetry directions. The former causes thickness nonuniformities and plays an important role in all surface nucleation processes. The latter is unique to crystalline surfaces and gives rise to twin boundaries in the mesoscopic film (see Fig. 3a). For films with horizontal cylindrical pores, twin boundaries manifest themselves as abrupt changes in the elongation direction of the striped domains [50]. The role of lattice defects in the substrate merits further investigation, as such defects could play a role in the establishment of a twin boundary or a new nucleation site. B.

Nucleation at Isotropic Surfaces

Whereas crystalline substrates can actively orient interfacial mesophases along specific in-plane axes, isotropic surfaces can at best sterically limit one of the mesophase symmetry axes to lie normal to the substrate plane. For example, an amorphous surface can restrict an interfacial hexagonal phase so that its cylindrical micelles lie parallel to the substrate plane, but it cannot orient the micelles along specific directions in the plane. This is consistent with observations of mesosilicate films nucleated at a silica surface [51,54,55] or at a polymer surface [56] using alkyltrimethylammonium surfactants. Experiments have revealed a primary structure consisting of hexagonally packed cylindrical pores

but a very complex higher order structure in which the cylindrical micelles bend and meander over the substrate plane and spiral outward normal to the substrate plane [51,55]. An inexact but helpful analogy is a bowl of cooked noodles upturned onto a flat surface. The noodles immediately adjacent to the surface predominantly adopt a horizontal (but otherwise isotropic) conformation, whereas those further from the surface can adopt orientations with significant normal components. The silica substrates used have been either cover glass or the native oxide on a silicon water; in the latter case, the crystalline nature of the underlying Si surface has usually been disregarded because the oxide overgrowth has been assumed to be amorphous. This may not always be a valid assumption; mesosilicates nucleated on Si(100) and Si(111) wafers show isotropic domains, whereas those grown on Si(110) wafers show elongated domains aligned along the [001] direction [55]. This effect has been attributed to a strong anistropy in the arrangement of Si atoms on the (110) surface, which is thought to be preserved by the thin surface oxide layer. Mesosilicate nucleation using alkyltrimethylammonium surfactants on silica differs from that on mica and graphite in one interesting respect. The favored surfactant-silicate morphology in bulk solution (hexagonal phase) is consistent with the interfacial micellar layer for mica and graphite (cylinders or half-cylinders), whereas it is not for silica (spheres). Thus, the silica interface does not serve a templating function as such but may simply act as a nonspecific boundary. An important special case of isotropic surfaces is the air-liquid interface, as films grown at this interface are freestanding and can be more easily shaped and manipulated for applications. Alkyltrimethylammonium surfactants have been used to template hexagonalphase mesosilicate films [57], with channels running parallel to the film plane, and the divalent surfactant C18-3-1 has been used to nucleate a film morphology consisting of spherical close-packed voids [52]. Although the c axis of both films is oriented normal to the film plane, there is little evidence of long-range order in the film plane; x-ray diffractometry of the films shows very weak secondary peaks. This is consistent with the air-water interface serving as a nonspecific boundary, in the same fashion as the silica surface already discussed. Electron microscopy of films grown at air-water interfaces shows that the air-facing side of the film is extremely flat, whereas the water-facing side is comparatively rougher [52,57]. This roughness is observed to have two distinct length scales. A smaller micellesizes roughness is thought to constitute a ‘‘snapshot’’


of silicified micelles in the process of attaching themselves to the interfacial mesophase [57]. A larger micrometer-scale roughness is also observed, consisting of dendritic bumps that have nucleated off the film and grown down into the solution [52,57]. These are similar to the hillocks observed on silica surfaces. They may likewise be caused by an ‘‘entropic strain relief’’ into the solution or alternatively by homogeneous nucleation occurring simultaneously in the solution. C.

Nucleation at Uniaxially Textured and Patterned Surfaces

A surface that is anisotropic only along one axis is potentially ideal for mesoscopic film nucleation because this axis can provide a strong interfacial orienting field while also preventing twin boundaries. Such a surface must consist of linear molecules in some kind of nematic order; polymers are therefore ideal for this purpose. Two reports show some success with this promising method [58,59]. They also serve to illustrate some of the subtle and interesting differences between nucleation mechanisms involving passive nonspecific confinement of those involving active templating. In the first case [58], uniaxial anisotropy is achieved by unidirectional rubbing of a thin polymer film (5nm-thick polyimide) spin-coated onto a glass substrate. Mesosilicate films nucleated on this rubbed surface, templated by alkyltrimethylammonium surfactants, show elongated domains of order 30 ␮m long consisting of cylindrical pores parallel to the rubbing direction. The tertiary structure is observed to be very uniform and without twin boundaries. Rubbed polymer films have long been known to align thermotropic liquid crystalline phases; similarly, in this case, they align the lyotropic surfactant-silicate mesophase before (or as) it condenses. The alignment is preserved upon calcination, which pyrolyzes both the surfactant and polymer film, leaving the aligned mesosilicate film attached to the glass substrate. In the second case [59], uniaxial anisotropy is achieved by the Langmuir-Blodgett (LB) deposition of hydrophobic polymer layers (polyimide) on a silica substrate. Controlled withdrawal of the substrate through the Langmuir monolayer aligns the macromolecules parallel to one another along the withdrawal direction. When alkyltrimethylammonium surfactants are used as templating agents, this oriented polymer film serves to nucleate a uniaxially aligned hexagonal mesophase, resulting in cylindrical pores parallel to the film plane. Again, the tertiary structure is maintained over macroscopic distances, and twin boundaries are

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absent. However, unlike the rubbed polymer film just discussed, in this case the pores are found to align perpendicular to the polymer molecules, i.e., perpendicular to the substrate withdrawal direction. This is attributed to a difference in the alignment mechanism [59]. On the polymer LB film, surfactant tails are thought to adsorb horizontally and align themselves parallel to the hydrophobic polymer; the tail-to-tail horizontal layer of surfactant molecules serves as a template for half-cylindrical micelles, whose axes are therefore oriented perpendicular to the substrate axis (as on graphite) [10]. On the other hand, in the spin-coated polymer film just discussed, polymer chains are not aligned parallel to one another, and the rubbing process does not appreciably align these chains. Rather, rubbing creates mesoscopic grooves that partially expose the substrate; the large aspect ratio of these grooves, combined with reaction conditions that favor nucleation on silica over that on polyimide, is thought to be responsible for alignment of the mesosilicate film parallel to the rubbing direction. Thus, the parallel film morphology on rubbed polymer surfaces is putatively due to steric confinement of whole cylindrical aggregates or domains in long grooves, whereas the perpendicular film morphology on LB-deposited polymer surfaces is due to active alignment or templating of the liquid crystalline phase by direct surfactant-surface interactions. D.

Order Enhancement Using External Flow and Electric Fields

In all of the preceding examples, the orienting field acting on the surfactant-silicate mesophase originates from substrate anisotropies. Others have combined heterogeneous nucleation with external orienting fields such as fluid flow and applied electric fields [60–62]. Films grown in this manner have all been on amorphous silica; this is an ideal substrate for this application because no surface anisotropies are present to compete with the orienting effects of external fields. Shear flows are known to enhance secondary and tertiary order by aligning cylindrical micelles and hexagonal phases in the direction of flow [63]. Similarly, shear flow of acidic reaction solution past a silica surface has been used to form mesosilicate domains elongated along the flow direction, with their cylindrical axes presumably oriented along this direction [60]. (Control films grown in quiescent solutions show disklike, isotropic domains.) Calcination preserves the elongation orientation, although it also induces cracks in the film. Tungsten oxide–cetyltrimethylammonium bromide (CTAB) composite films have also been ori-

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ented successfully with shear flow, resulting in a film with enhanced tertiary structure and distinct optical anisotropy [61]. However, these films did not survive calcination. Fluid flow has also been used in conjunction with confinement and electric field alignment to grow oriented mesosilicate bundles on surfaces [62]. Here an elastomeric stamp with ⬃1-␮m-square grooves is pressed down onto a silica surface, and the surfactantsilicate reaction solution is wicked in from one end of the stamp; electro-osmotic flow is maintained by applying an electric field parallel to the grooves. As the reaction proceeds, mesosilicates form from the groove surfaces inward, eventually (after a few hours) closing off the grooves completely. The stamp is then lifted off, revealing long bundles of mesosilicates on the silica surface. This textured film was observed to consist of predominantly cylindrical pores (consistent with the alkyltrimethylammonium surfactants used) oriented parallel to the groove axis. These bundles have a square cross section composed of order 105 pores, reflecting the size and shape of the elastomer grooves. At least three factors are thought to be responsible for the enhanced secondary and tertiary structure— confinement, fluid flow, and electric fields; however, the relative importance of each is not well known. It is instructive to compare these results with a similar, separate report in which confinement is the only important factor [64]. Here an elastomeric stamp is used to ‘‘ink’’ 3–10 ␮m lines of alkanethiols onto a gold surface, and this substrate is exposed to a quiescent reaction solution that favors growth only on the thiolated regions. Hexagonal-phase mesosilicate films are observed as before; however, although the pore axes are restricted to the film plane, they are more or less isotropic in this plane and not significantly oriented along the thiolated lines. Thus, fluid flow and electric fields appear to play a more dominant role than simple confinement in inducing uniaxial orientation. Mesoscopic films grown inside the channels of an elastomeric stamp can be regarded as hierarchically ordered films; self-assembly imparts order at 10 nm length scales and the stamp at 1000 nm length scales. In one report [65], colloidal latex spheres are employed to pattern surfaces also in the middle length scale of ⬃100 nm. The colloidal suspension is first wicked through the grooves of an elastomeric stamp pressed onto a silica substrate. As the solvent dries, capillary forces drive the self-assembly of colloidal particles into ordered arrangements within the confines of the grooves. The silicate reaction solution is then wicked through the grooves packed with latex spheres, and the

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solution is allowed to condense over several hours. The stamp is then removed and the film calcined, pyrolyzing the surfactant as well as the latex particles. The end result is a silicate surface macroscopically textured by the stamp, wherein the silicate contains macropores from the latex particles and micropores from the surfactant self-assembly. Because PEO-PPO block copolymers are used as the structure-directing agents, both cubic and hexagonal phase primary structures can be obtained, depending on the lengths of the blocks [65]. E.

Nucleation at the Solid-Liquid-Vapor Contact Line

In the preceding examples, mesoscopic films form by heterogeneous nucleation, with the interfacial phase near chemical equilibrium with the bulk solution. Although this near-equilibrium approach favors uniform films with high secondary and tertiary order, it limits film morphologies to those consistent with equilibrium interfacial surfactant structures, and it can require long reaction times—typically several days. An alternative and promising approach uses dip-coating, or controlled withdrawal of a substrate out of a reaction solution, to both generate and orient mesoscopic films [66,67]. The nucleation of these films occurs at the solid-liquid-vapor contact line, where solvent evaporation creates steep concentration gradients, giving rise to reaction conditions far from equilibrium. In a unique departure from other approaches, dipcoating uses predominantly ethanolic reaction solutions, with ethanol/water molar ratios of order 5:1. Because ethanol is itself somewhat amphiphilic, it tends to interfere with surfactant self-assembly in solution. Micelle formation can require far higher surfactant concentrations in ethanol-water mixtures than in purely aqueous solutions [68]. Similarly, ethanol interferes with intermicellar ordering and can delay (or suppress altogether) the onset of lyotropic liquid crystalline phases [69]. Dip-coated solutions can therefore support moderate surfactant concentrations (⬃0.1 M) without forming surfactant-silicate mesophases in solution; instead, mesophases form only at the contact line, where rapid preferential evaporation of ethanol supersaturates the remaining (mostly aqueous) reaction solution. This process can be visualized as a trajectory in the ternary water-ethanol-surfactant phase diagram, beginning near the ethanol corner and ending near the water-surfactant line [67]. Ethanol has a significantly higher vapor pressure than water and evaporates rapidly at the contact line, allowing moderate dip-coating velocities (⬃1 mm/ s) and processing times on the order of minutes. A flat,


amorphous substrate such as silica is used in order to avoid competition with surface templating effects. After dip-coating, the supported film is calcinated in the usual way. This technique has the advantage that films with a wide variety of primary structures can be produced with the same structure-directing agent; for instance, surfactant-silicate films of hexagonal, bicontinuous cubic, and lamellar phases have all been produced using alkyltrimethylammonium surfactants (although the lamellar phase, not surprisingly, did not survive calcination) [66]. The initial surfactant amount can be chosen so that the final concentration in the reaction layer, once the ethanol has evaporated, falls in the desired aqueous phase region. Stated another way, the trajectory in the ternary phase diagram need not end at the most dilute aqueous mesophase. (This would probably be the case if dip-coating were performed in aqueous solutions because solvent evaporation would slow considerably when a mesophase is established.) Despite the flexibility of this approach, the details of the ternary phase trajectories are not yet well understood, and the final morphology may be difficult to predict. In particular, it may not always be clear whether a given surfactant-silicate film represents an equilibrium or a kinetically stabilized mesophase encountered along the phase trajectory. Mesophases have been modified by thermal cycling, providing evidence for such kinetic traps [66]. The secondary and tertiary structures of dip-coated films are influenced, not surprisingly, by both the airliquid and solid-liquid boundary conditions. Hexagonal-phase films, dip-coated from reaction solutions with comparatively low surfactant concentrations, reveal three distinct zones in cross section [66]. The regions of the film closest to the air-liquid and silica-liquid interfaces both show tubules aligned in the film plane but not oriented in any specific direction in this plane; this morphology is perfectly consistent with films heterogeneously nucleated at these interfaces, as discussed earlier [51,57]. However, between these two regions of planar alignment (each ⬃50–100 nm thick) lies an interior region where the cylindrical tubules are completely disordered, denoting a disordered bulk mesophase. In contrast, when the reaction solution is prepared with a higher surfactant concentration, so that the phase trajectory ends up in the bicontinuous cubic region of the phase diagram, the resulting bicontinuous cubic film is ordered throughout its thickness [66]. Whereas the preceding results were obtained with alkyltrimethylammonium surfactants as templates, the dip-coating technique has been extended to nonionic

775

surfactants and PEO-PPO-PEO triblock copolymers [43]. Here also, ethanol evaporation destabilizes the solution during dip-coating; the resulting nanocomposite layer, after calcination, yields a mesoporous silicate film that is extremely well ordered. A variety of cubic and hexagonal primary structures have been produced, and the primary structure can be controlled by the initial amphiphile concentration (as before) as well as by the ratio of hydrophilic to hydrophobic (EO/PO) block lengths. Amphiphiles with large polar blocks typically give rise to phases with discrete close-packed micelles (leading to a mesosilicate film with a cage structure), whereas those with smaller polar blocks lead to hexagonal-phase films (Fig. 4) [43]. A high degree of secondary structure is evidenced by x-ray diffraction patterns showing reflections of several orders. Tertiary order is also greatly enhanced; unlike the dipcoated films discussed before, these are observed to be structurally uniform throughout their thickness, and hexagonal-phase films are observed to be aligned with tubules parallel to the coating direction. These enhancements may be due to the somewhat higher coating speeds used in this work or to the much larger micelles associated with block copolymers. Mesoscopic oxide films other than silicates have also been prepared by dip-coating, this time from purely ethanolic reaction media, using PEO-PPO block copolymers as templating agents [44]. As discussed in Section III.B, ethanolic solutions were necessary to slow the hydrolysis/condensation of alkoxide precursors; metal coordination complexes between the EO headgroups and condensed oligomers were proposed as a coassembly mechanism. Interestingly, the final product was observed to contain some nanocrystalline domains of the standard bulk oxide phase within the amorphous walls of the mesoscopic material [44]. In most cases the films were hexagonal phases with tubules running parallel to the film plane. V.

CONCLUSION

Interfacial confinement, often in combination with externally applied fields, has led to important advances in mesoscopic materials. These advances include primary structures that cannot be accessed in bulk solutions, enhanced secondary and tertiary structures, and hierarchically ordered morphologies. Although the idealized membrane of uniform and individually addressable pores (Fig. 1) has not yet been achieved, this has not prevented mesoscopic films from being used for some device applications, for instance, as catalytic supports [70] or as mesoscopic waveguides for mirrorless

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lasing [71]. Notwithstanding these advances, a membrane of uniform columnar pores remains a desirable goal. The major hurdle to columnar self-assembly is the energy cost associated with the end surfaces of the cylinders; whether these are flat terminations (exposing the interior hydrophobic tails) or hemispherical caps, they involve a local curvature at odds with the global cylindrical curvature of the micelle. Because unfavorable end surfaces are minimized by cylinders lying parallel to the film plane, this will in normal circumstances remain the preferred morphology. Whether interfaces can be suitably prepared to reduce the energy cost of the end surfaces, and thereby coax the surfactants into columnar self-assembly, remains to be seen.

ACKNOWLEDGMENTS We thank G. D. Stucky for useful discussions. We gratefully acknowledge support from Procter & Gamble Corp. and from the University of Arizona while writing this review.

REFERENCES 1.

2.

3. FIG. 4 Images of a hexagonal-phase mesoscopic silicate films deposited by dip-coating from a reaction solution onto an amorphous silica substrate. The structure-directing agent was the amphiphilic triblock copolymer EO20PO70EO20. (a) Low-magnification SEM image of the as-deposited film showing striations parallel to the tubule axis and parallel to the coating direction. (b and c) TEM images of the calcined film showing the transverse and cross section views, respectively. The tubules run parallel to the film plane. (From Ref. 43.)

4.

5. 6.

(a) C. T. Kresge, M. E. Leonowicz, W. J. Roth, J. C. Vartuli, and J. S. Beck, Nature 359:710–712 (1992); (b) J. S. Beck, J. C. Vartuli, W. J. Roth, M. E. Leonowicz, C. T. Kresge, K. D. Schmitt, C. T. W. Chu, D. H. Olson, E. W. Sheppard, S. B. McCullen, J. B. Higgins, and J. L. Schlenker, J. Am. Chem. Soc. 114:10834– 10843 (1992). Reviews: (a) F. Schu¨th, U. Ciesla, S. Schacht, M. Thieme, Q. Huo, and G. Stucky, Mater. Res. Bull. 34: 483–494 (1999); (b) P. T. Tanev, J. R. Butruille, and T. J. Pinnavaia, in Chemistry of Advanced Materials (L. V. Interrante and M. J. Hampden-Smith, eds.), WileyVCH, New York, 1998, pp. 329–388; (c) C. J. Brinker, Curr. Opin. Solid State Mater. Sci. 1:798–805 (1996); (d) S. Manne and I. A. Aksay, Curr. Opin. Solid State Mater. Sci. 2:358–364 (1997). J. E. Martin, M. T. Anderson, J. Odinek, and P. Newcomer, Langmuir 13:4133–4141 (1997). Reviews: (a) D. F. Evans and H. Wennerstro¨m, The Colloidal Domain, Wiley-VCH, New York, 1994, chapter 4; (b) J. N. Israelachvili, Intermolecular and Surface Forces, 2nd ed., Academic Press, London, 1992, chapters 16 and 17; (c) R. G. Laughlin, The Aqueous Phase Behavior of Surfactants, Academic Press, London, 1994. J. N. Israelachvili, D. J. Mitchell, and B. W. Ninham, J. Chem. Soc. Faraday Trans. I 72:1525–1568 (1976). C. Tanford, The Hydrophobic Effect, Wiley, New York, 1980.

Mesoscopic Films at Interfaces 7.

8.

9. 10. 11. 12.

13. 14.

15. 16. 17. 18. 19. 20. 21. 22. 23. 24. 25. 26. 27.

28. 29.

30.

(a) R. Zana, in Cationic Surfactants: Physical Chemistry (D. N. Rubingh and P. M. Holland, eds.), Marcel Dekker, New York, 1991, pp. 41–85; (b) J. G. Weers and D. R. Scheuing, ACS Symp. Ser. 447:87–122 (1991). (a) R. R. Balmbra, J. S. Clunie, and J. F. Goodman, Nature 222:1159–1160 (1969); (b) K. Fontell, Colloid Polym. Sci. 268:264–285 (1990). A. M. Gaudin and D. W. Fuerstenau, Trans. AIME 202: 958–962 (1955). S. Manne, J. P. Cleveland, H. E. Gaub, G. D. Stucky, and P. K. Hansma, Langmuir 10:4409–4413 (1994). S. Manne and H. E. Gaub, Science 270:1480–1482 (1995). Review: S. Manne and G. G. Warr, in Supramolecular Structure in Confined Geometries (S. Manne and G. G. Warr, eds.), ACS Press, Washington, DC, 1999, chapter 1. M. Jaschke, H. J. Butt, H. E. Gaub, and S. Manne, Langmuir 13:1381–1384 (1997). S. Manne, T. E. Scha¨ffer, Q. Huo, P. K. Hansma, D. E. Morse, G. D. Stucky, and I. A. Aksay, Langmuir 13: 6382–6387 (1997). S. Manne, Prog. Colloid Polym. Sci. 103:226–233 (1997). H. N. Patrick, G. G. Warr, S. Manne, and I. A. Aksay, Langmuir 13:4349–4356 (1997). H. N. Patrick, G. G. Warr, S. Manne, and I. A. Aksay, Langmuir 15:1685–1692 (1999). E. J. Wanless and W. A. Ducker, J. Phys. Chem. 100: 3207–3214 (1996). W. A. Ducker and L. M. Grant, J. Phys. Chem. 100: 11507–11511 (1996). L. M. Grant and W. A. Ducker, J. Phys. Chem. B 101: 5337–5345 (1997). R. Lamont and W. A. Ducker, J. Colloid Interface Sci. 191:303–311 (1997). L. M. Grant, F. Tiberg, and W. A. Ducker, J. Phys. Chem. B 102:4288–4294 (1998). R. E. Lamont and W. A. Ducker, J. Am. Chem. Soc. 120:7602–7607 (1998). W. A. Ducker and E. J. Wanless, Langmuir 15:160–168 (1999). N. B. Holland, M. Ruegsegger, and R. E. Marchant, Langmuir 14:2790–2795 (1998). J. F. Wall and C. F. Zukoski, Langmuir 15:7432–7437 (1999). I. Burgess, C. A. Jeffrey, X. Cai, G. Szymanski, Z. Galus, and J. Lipowski, Langmuir 15:2607–2616 (1999). J. L. Wolgemuth, R. K. Workman, and S. Manne, Langmuir 16:3077–3081 (2000). D. J. Mitchell, G. J. T. Tiddy, L. Waring, T. Bostock, and M. P. McDonald, J. Chem. Soc. Faraday Trans. 2 72:1525–1568 (1976). J. R. Lu, Z. X. Li, J. Smallwood, R. K. Thomas, and J. Penfold, J. Phys. Chem. 99:8233–8243 (1995).

777 31. 32.

33.

34. 35. 36. 37. 38.

39.

40. 41. 42. 43.

44.

45.

46. 47. 48. 49.

J. Bocker, M. Schlenkrich, P. Bopp, and J. Brickmann, J. Phys. Chem. 96:9915–9922 (1992). R. G. Laughlin, in Cationic Surfactants: Physical Chemistry (D. N. Rubingh and P. M. Holland, eds.), Marcel Dekker, New York, 1991, pp. 1–40. A. Firouzi, D. Kumar, L. M. Bull, T. Besier, P. Sieger, Q. Huo, S. A. Walker, J. A. Zasadzinski, C. Glinka, J. Nicol, D. I. Margolese, G. D. Stucky, and B. F. Chmelka, Science 267:1138–1143 (1995). A. Firouzi, F. Atef, A. G. Oertli, G. D. Stucky, and B. F. Chmelka, J. Am. Chem. Soc. 119:3596–3610 (1997). Y. S. Lee, D. Surjadi, and J. F. Rathman, Langmuir 12: 6202–6210 (1996). Y. S. Lee, D. Surjadi, and J. F. Rahtman, Langmuir 16: 195–202 (2000). R. K. Iler, The Chemistry of Silica, Wiley, New York, 1979. (a) Q. Huo, D. I. Margolese, and G. D. Stucky, Chem. Mater. 8:1147–1160 (1996); (b) Q. Huo, D. I. Margolese, U. Ciesla, D. G. Dermuth, P. Feng, T. E. Gier, P. Sieger, B. F. Chmelka, F. Schu¨th, and G. D. Stucky, Chem. Mater. 6:1176–1191 (1994); (c) A. Monnier, F. Schu¨th, Q. Huo, D. Kumar, D. Margolese, R. S. Maxwell, G. D. Stucky, M. Krishnamurty, P. Petroff, A. Firouzi, M. Janicke, and B. F. Chmelka, Science 261: 1299–1302 (1993). Q. Huo, D. I. Margolese, U. Ciesla, P. Feng, T. E. Gier, P. Sieger, R. Leon, P. M. Petroff, F. Schu¨th, and G. D. Stucky, Nature 368:317–320 (1994). V. Shubin, P. Petrov, and B. Lindman, Colloid Polym. Sci. 272:1590–1601 (1994). P. T. Tanev and T. J. Pinnavaia, Science 267:865–867 (1995). S. A. Bagshaw, E. Prouzet, and T. J. Pinnavaia, Science 269:1242–1244 (1995). (a) D. Zhao, J. Feng, Q. Huo, N. Melosh, G. H. Fredrickson, B. F. Chmelka, and G. D. Stucky, Science 279: 548–552 (1998); (b) D. Zhao, P. Yang, N. Melosh, J. Feng, B. F. Chmelka, and G. D. Stucky, Adv. Mater. 10:1380–1385 (1998). (a) P. Yang, D. Zhao, D. I. Margolese, B. F. Chmelka, and G. D. Stucky, Nature 396:152–155 (1998); (b) P. Yang, D. Zhao, D. I. Margolese, B. F. Chmelka, and G. D. Stucky, Chem. Mater. 11:2813–2826 (1999). Reviews: (a) P. Hansson and B. Lindman, Curr. Opin. Colloid Interface Sci. 1:604–613 (1996); (b) Y. J. Li and P. L. Dubin, ACS Symp. Ser. 578:320–336 (1994). G. S. Attard, J. C. Glyde, and C. G. Go¨ltner, Nature 378:366–368 (1995). C. G. Go¨ltner, S. Henke, M. C. Weissenberger, and M. Antonietti, Angew. Chem. Int. Ed. 37:613–616 (1998). S. H. Tolbet, A. Firouzi, G. D. Stucky, and B. F. Chmelka, Science 278:264–268 (1997). P. Schmidt-Winkel, P. Yang, D. I. Margolese, B. F. Chmelka, and G. D. Stucky, Adv. Mater. 11:303–307 (1999).

778 50. 51.

52. 53. 54. 55. 56. 57. 58. 59. 60. 61. 62.

Manne et al. H. Yang, A. Kuperman, N. Coombs, S. Mamiche-Afara, and G. A. Ozin, Nature 379:703–705 (1996). I. A. Aksay, M. Trau, S. Manne, I. Honma, N. Yao, L. Zhou, P. Fenter, P. M. Eisenberger, and S. M. Gruner, Science 273:892–898 (1996). S. H. Tolbert, T. E. Scha¨ffer, J. Feng, P. K. Hansma, and G. D. Stucky, Chem. Mater. 9:1962–1967 (1997). Q. Huo, R. Leon, P. M. Petroff, and G. D. Stucky, Science 268:1324–1328 (1995). M. Ogawa, Chem. Commun. 1149–1150 (1996). H. Miyata and K. Kuroda, J. Am. Chem. Soc. 121: 7618–7624 (1999). M. Ogawa and T. Kikuchi, Adv. Mater. 10:1077–1080 (1998). H. Yang, N. Coombs, I. Sokolov, and G. A. Ozin, Nature 381:589–592 (1996). H. Miyata and K. Kuroda, Chem. Mater. 11:1609–1614 (1999). H. Miyata and K. Kuroda, Adv. Mater. 11:1448–1452 (1999). H. W. Hillhouse, T. Okubo, J. W. van Egmond, and M. Tsapatsis, Chem. Mater. 9:1505–1507 (1997). H. W. Hillhouse, J. W. van Egmond, and M. Tsapatsis, Langmuir 15:4544–4550 (1999). M. Trau, N. Yao, E. Kim, Y. Xia, G. M. Whitesides, and I. A. Aksay, Nature 390:674–676 (1997).

63.

64. 65.

66.

67. 68.

69.

70. 71.

C. A. Herb and R. K. Prud’homme, Structure and Flow in Surfactant Solutions, American Chemical Society, Washington, D.C., 1994. H. Yang, N. Coombs, and G. A. Ozin, Adv. Mater. 9: 811–814 (1997). P. Yang, T. Deng, D. Zhao, P. Feng, D. Pine, B. F. Chmelka, G. M. Whitesides, and G. D. Stucky, Science 282:2244–2246 (1998). Y. Lu, R. Ganguli, C. A. Drewien, M. T. Anderson, C. J. Brinker, W. Gong, Y. Guo, H. Soyez, B. Dunn, M. H. Huang, and J. I. Zink, Nature 389:364–368 (1997). C. J. Brinker, Y. Lu, A. Sellinger, and H. Fan, Adv. Mater. 11:579–585 (1999). (a) R. Zana, in Cationic Surfactants: Physical Chemistry (D. N. Rubingh and P. M. Holland, eds.), Marcel Dekker, New York, 1991, pp. 41–85; (b) R. Zana, S. Yiv, C. Strazielle, and P. Lianos, J. Colloid Interface Sci. 80:208–223 (1981). K. Fontell, A. Khan, B. Lindstro¨m, D. Maciejewska, and S. Puang-Ngern, Colloid Polym. Sci. 269:727–742 (1991). A. Corma, Chem. Rev. 97:2373–2419 (1997). P. Yang, G. Wirnsberger, H. C. Huang, S. R. Cordero, M. D. McGehee, B. Scott, T. Deng, G. M. Whitesides, B. F. Chmelka, S. K. Buratto, and G. D. Stucky, Science 287:465–467 (2000).

38 Synthesis of Mesoscopic Silica Films at Fluid-Fluid Interfaces YOON SEOB LEE and JAMES F. RATHMAN

I.

The Ohio State University, Columbus, Ohio

BACKGROUND

tion of surfactants [2,3]. Solid surfaces are often classified as hydrophobic (Mylar, polyethylene, Teflon) or hydrophilic (borosilicate glass, silica gel). Charged sites on the surface may increase or decrease the amount of ionic surfactant adsorbed. Ionic surfactants interact with hydrophobic surfaces primarily through dispersion forces, whereas the adsorption of ionic surfactants to hydrophilic surfaces is governed predominantly by electrostatic or charge-dipole interaction. The formation of hemimicelles or admicelles induces a sharp increase in adsorption as a function of solution concentration [4,5]. Surfactant hemimicelles have been imaged by atomic force microscopy (AFM) for the adsorption of the cationic surfactant hexadecyltrimethylammonium bromide (C16TAB) on a hydrophobic graphite surface [6]. The observed hemimicelle structure is consistent with the preferential horizontal configuration of surfactant tails on the surface. The same structure has been observed for other quaternary ammonium surfactants of varying alkyl chain lengths [7] and having different geometries (e.g., gemini surfactants) [8] on hydrophobic surfaces such as graphite and MoS2. On hydrophilic surfaces such as silica and mica, adsorption of cationic surfactants from aqueous solution results in admicellar structures; the interaction is primarily between the surface and surfactant headgroups. Spherical admicelles have been observed on highly charged silica surfaces, a process that is highly dependent on pH. Aggregation of the same surfactant on a mica surface resulted in cylindrical admicelles because of ion exchange be-

This chapter provides an overview of efforts to synthesize structured mesoporous films at fluid-fluid interfaces and presents a detailed description of a novel method in which silica films are synthesized at a liquidliquid interface. Potential advantages of making films by fluid-fluid techniques over conventional dip-coating and sol-gel processes are discussed. A.

Surfactant Self-Assembly on Solid Surfaces

The adsorption of soluble surfactants from aqueous solution onto gas, liquid, and solid interfaces has been extensively studied. The configuration adopted by an adsorbed surfactant molecule at a liquid-liquid interface may be much different from that observed at gasliquid or liquid-solid interfaces. For example, at an oilwater interface the strong affinity of the surfactant tails for the oil phase results in the tails being oriented perpendicularly to the interface [1], even at very low coverage, where the surfactant tails lie down on the surface in gas-liquid or liquid-solid systems. As the amount of adsorption increases, surfactant-surface and surfactantsurfactant interactions result in the formation of selfassembled structures at surfactant concentrations well below the critical micelle concentration, the concentration at which self-assembly in solution is first observed. Adsorption to a solid is further complicated by the chemical and physical heterogeneities of the solid, which strongly influence the adsorption and aggrega779

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tween the K⫹ ions on the surface and the charged headgroups, resulting in a higher adsorption density [7,8]. B.

Synthesis of Mesoporous Silica Films

The discovery of M41S-type mesoporous materials in 1992 led to a tremendous level of research activity [9,10]. Their ordered, uniform pores and remarkably high internal surface area make these materials potential candidates for many applications where size selectivity and/or sorption capacity is important. Recent publications have reported various new synthetic schemes [11–18], development of new methods for improved characterization [19–22], and demonstrations of the application of these materials as sorbents [23,24] and catalysts [25]. A wide variety of reactions are possible. One of the most common involves the use of tetraethylorthosilicate (TEOS) as the silicate source:

Although nearly all work to date has focused on the synthesis of mesoporous materials in particulate (powder) forms, other forms such as monolithic solids [26], membranes [27], hard spheres [28], long hollow fibers [29], and thin films can be synthesized. Films have unique potential applications as membranes, membrane supports, surface coatings to improve catalyst selectivity and prevent poisoning, and size-specific coatings for sensors, electrodes, and other microelectronic devices [30]. For example, a surface acoustic wave (SAW) sensor coated with microporous zeolite films has been developed for the selective sorption of gas molecules [31,32]. Small pore sizes limit zeolite films to molecules smaller than 1.5 nm; mesoporous films will increase this selectivity to molecules up to roughly 10 nm in size [33]. As in the synthesis of bulk mesoporous materials, the cooperative organization of cationic surfactant molecules with silicate species is the key factor in the synthesis of mesoporous films. The difference is that the reaction is now performed at an interface, and confinement of the reaction to the interfacial region provides

an additional level of control over the structural evolution that occurs during the reaction. Mesoporous films have been synthesized at air-solid and liquid-solid interfaces. For the syntheses at airsolid interfaces, conventional sol-gel methods have been widely applied. Much effort has been given to the formulation of precursor silicate gels containing cationic quaternary ammonium surfactants and tetramethylorthosilicate (TMOS) or tetraethylorthosilicate (TEOS) as the silicate source, usually under acidic conditions in order to inhibit the polymerization reaction prior to depositing the gel on the solid. Dip coating and spin coating are two commonly used methods. The rapid evaporation of solvent before the formation of silica by silicate condensation is important to prevent the formation of amorphous product. Ogawa synthesized layered [34,35] and hexagonal [36] silica-surfactant nanocomposites using both single and dichain quaternary ammonium surfactant on glass surfaces. Martin et al. [37] used ammonia gas as a catalyst instead of rapid solvent evaporation to increase the rate of silicate condensation after coating. This method, referred to as gascatalyzed thin-film synthesis (GCTFS), has been used to prepare hexagonal mesoporous silica films on silicon and glass surfaces. Lu et al. [38] reported the synthesis of mesoporous films on silicon by dip coating. They monitored the evolution of lamellar, cubic, and hexagonal structures using a fluorescence depolarization method. The rapid formation of continuous nanolaminated films that mimic nacre of abalone shell on silicone surfaces by dip coating was also reported [39]. This result is one of the pioneering works in the synthesis of biomimetic nanocomposite assemblies. Their technique relies on the rapid evaporation of solvent in the early stage of reaction to ensure the formation of the desired surfactant-silicate mesophase after coating. Both the final mesophase structure and the film thickness of the ordered region are highly dependent on the process time scale (coating rate) and on the chemical properties and process used for pretreatment of the substrate. In another study, an acidic silicate gel was used in the microscopic patterning of orientated hexagonal silica film on solid surfaces [40]. The sol-gel evaporation method has also been performed in a microcapillary mold using an electric field guidance technique [41]. Patterned porous silica, nobia, and titania mesoporous films were synthesized. These techniques are potentially important in the development of low-cost lithographic techniques. Mesoporous silica films at liquid-solid interfaces are synthesized in much the same way, again using acidic silicate precursor gels. Instead of applying a thin layer

Synthesis of Mesoscopic Silica Films

of gel directly on the solid surface, the substrate is immersed into the bulk gel, allowing the formation of surfactant-silicate self-assemblies on the solid surface. The final film is obtained by removing the solid from the liquid gel and drying in air. Mica, graphite, and glass surfaces have been widely used as solid surfaces for these films. Aksay et al. [42] synthesized well-ordered mesoporous films on mica and graphite, but the product on glass transformed to a spiral-like disordered structure soon after the drying process. A hexagonal mesoporous silica film has also been synthesized on mica [43]. Attard et al. [44] coated mesoporous platinum films on a gold electrode using the same approach. The main drawback of the gas-solid and liquid-solid methods is that the film formation reaction takes place in contact with a solid substrate, so the substrate may strongly influence the resulting film structure. Syntheses under identical solution conditions but on different solid substrates often yield different film products. The influence of a solid surface on the self-assembly of surfactant molecules near the surface is well known and can be significant; indeed, it is often the most important factor. The ordering of molecules in the first layer next to a surface influences subsequent ordering in layers progressively farther away from the surface, and this effect can be propagated for thousands of layers into the liquid phase. Several researchers have suggested that this effect can be exploited to make highly sensitive sensors by taking advantage of liquid crystalline phase changes induced by minor chemical or physical properties of a surface. For film synthesis, substrate effects are a severe problem because they limit the type of film that can be produced on a given surface; for example, it turns out to be very easy to produce hexagonal-structured films on hydrophilic surfaces such as glass but much more difficult to synthesize cubic films using these methods. Liquid phase compositions that yield cubic-structured bulk (powder) material are generally observed to produce hexagonal films if the reaction is performed at a hydrophilic solid surface. These results suggest that synthesizing films at fluidfluid interfaces (gas-liquid or liquid-liquid) may offer a way to eliminate undesired substrate effects on film structure. Yang et al. [45] synthesized surfactant-silicate mesophases at air-liquid interfaces and observed the formation of thin hexagonal films. A cooperative relation between surfactant self-assembly at the interface and micelles in solution with the silicate ions (dual templating) was suggested. Another group reported the synthesis of mesoporous silica films of hexagonal and cubic structures on air–aqueous solution interfaces [46–49]. They suggested two discrete stages in the

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mechanism: induction and transition/growth. The long c axis in hexagonal films ran parallel to the surface, and the cubic film detected in the early induction period was transformed during reaction into an hexagonal structure in the final product [48]. Transitions such as this that occur in film structure during reaction are common. The remainder of this chapter describes a new method for synthesizing mesoporous silica films. A surfactant-silicate precursor gel is first spread at a liquidliquid interface and allowed to react for a prescribed period of time, after which the partially formed wet film is transferred to a solid substrate. This method eliminates structural reorganization within the film caused by the solid surface and so provides a way to synthesize selectively films of a desired mesostructure (e.g., lamellar, hexagonal, or cubic) on a wide variety of different solids.

II.

EXPERIMENTAL

A.

Materials

Cationic surfactants dodecyl-, tetradecyl-, and hexdecyltrimethylammonium chloride, denoted C12TAC, C14TAC, and C16TAC, respectively, were from Fluka Chemical Co. Also, 25 wt% aqueous solutions of C16TAC from Aldrich Chemical Co. were used. Alcohols with alkyl chains of n-octyl (C8OH, Aldrich), ndecyl (C10OH, Sigma), and n-dodecyl (C12OH, Aldrich) were used as cosurfactants. Tetraethylorthosilicate (TEOS) from Aldrich (98 wt% aqueous solution) was used as the silicate source in all reactions. Benzene and sodium hydroxide were from Fisher and Jenneile, respectively. All chemicals were used as received. Three solid surfaces were used as supporting solid substrates for films: borosilicate glass, indium-tin oxide (ITO)–coated glass, and Teflon. Precleaned microscope cover glasses were from Fisher Scientific and Surgipath Medical Industries, Inc. and were used as received. Teflon sheets (1/32 inch) from Scientific Instrument Services, Inc. were soaked in 0.1 M HCl solution for 1 day, washed with distilled water, and finally dried and stored in a desiccator at room temperature. ITO-coated glass samples were provided by the liquid crystal display (LCD) division of Hyundai Electronics, Korea. Two types of ITO glasses were used: 40 and 120 nm ITO layer thickness with 65 and 20 ohms resistance, respectively, both coated on 0.7-mm glass. They were pretreated using conventional cleaning procedures [50,51].

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Methods

1. Precursor Silicate Gel An aqueous solution containing 25.0 wt% cationic surfactant CnTAC was first prepared and the pH adjusted to 12.5 by addition of solid sodium hydroxide. An alkyl alcohol was then added to give the desired alcohol/ surfactant molar ratio. CmOH/CnTAC molar ratios from 0.01 to 1.50 were investigated; at higher alcohol content these mixtures were viscous gels. The alkaline alcohol–surfactant solution was stirred for 20 min at high speed. Benzene was then added in excess amount (6 mL benzene per mL aqueous solution) and the resulting two-phase mixture was stirred for 2 h. TEOS was then added, again with continuous stirring. Following addition of the silicate species, a white precipitate began to appear within 5–15 min and the mixture became noticeably more viscous. This solution was stirred for 2 h, during which time the reaction flask was ventilated to allow evaporation of ethanol produced during the hydrolysis of TEOS. Molar silicate/ surfactant (Si/CnTAC) ratios ranging from 0.5 to 4.5 were studied. The final reaction mixture was stored without stirring at 25⬚C for 2 days, during which time it separated into two clear liquid phases. The time required for phase separation was dependent on the length of the surfactant chain; C12TAC systems separated relatively quickly in 4–5 h, whereas C16TAC systems required 5 days. Based on chemical analysis of the two phases by Fourier transform infrared (FTIR) spectroscopy, the top phase was essentially pure benzene and all other components were contained in the bottom phase. The bottom phase was thus saturated with benzene; the benzene content was approximately 8 wt%, with benzene molecules residing predominantly in the surfactant micelles. The final molar ratio of benzene to CnTAC in this phase ranged from 1.0 to 1.5, depending on the specific surfactant system. The aqueous bottom phase was separated and stored in a sealed glass bottle; this solution is referred to hereafter as the precursor silicate gel. 2. Films The precursor silicate gel just described was used for the synthesis of all mesoporous silica films at liquidliquid and air-solid interfaces in this study. For the liquid-liquid technique, the two phases were benzene and water. The role of benzene, both as a component of the precursor gel and as the bulk organic liquid phase, is discussed in the next section. A known volume of silicate gel was carefully delivered to the interface using a micropipet positioned at the benzene-water interface,

and the gel spread spontaneously across the entire available interfacial area. The reaction begins immediately because exposure of the gel to water induces the desired condensation polymerization of the silicate monomers and oligomers. The reaction was allowed to proceed for a specific length of time and the film was then transferred to a solid substrate by simply drawing the solid slowly through the interface in a single pass. Reaction times at the liquid-liquid interface varied from 30 min to 120 h. The transferred film was placed in a ventilated container and dried at 25⬚C for 2 days. Unlike conventional sol-gel techniques in which rapid drying is required [52–55], the much slower drying process used here was important for obtaining high-quality products. Finally, films were calcined to remove all organic material. Dried films were placed in a furnace at room temperature and the temperature was increased at a rate of 2–5⬚C/min to 550⬚C. This temperature was maintained for 10 h with continuous flowing air supplied. The furnace was then shut off and the samples were slowly cooled to room temperature. For characterization purposes, samples of wet, dried, and calcined films were collected at regular intervals throughout the process. For the synthesis of films directly on a solid, two methods were used. Using the conventional dip-coating method, the solid substrate was immersed into the gel and then withdrawn. The other method was simply to deposit the gel on the solid surface using a pipette. In both cases, the film was then dried at 25⬚C for 48 h and calcined as described before. C.

Characterization

X-ray powder diffraction (XRD) patterns were obtained on a Scintag PAD-V diffractometer with Cu K␣ radi˚ wavelength at 20 mA, 45 kV at ation of 1.54060 A room temperature. Each film was analyzed in two ways. A portion of film was peeled off the solid substrate, crushed, and mounted on the silicon holder as a powder, using vacuum grease. For the second analysis, the substrate coated with the intact film was directly mounted on the sample holder. These two experiments provide information about the structure of the film and the alignment of mesostructures with respect to the substrate surface. In all experiments, samples were scanned at 1.5–30⬚ (or 10⬚) 2␪ with 0.01–0.005⬚ step size and 1.2 s per step. Both the standard (4 and 2 mm for x-ray source, 0.5 and 0.3 mm for detector) and the low-intensity (2 and 1 mm for x-ray source, 0.3 and 0.1 mm for detector) slit setups were selected depending on the intensity of the first highest peak and sample


conditions. The angles (2␪, ␻) were recalibrated for every measurement. 29 Si magic angle spinning (MAS) solid-state nuclear magnetic resonance (NMR) spectra were recorded on a Bruker AM 500 MHz spectrometer using a delrin rotor. The measurement conditions for high-quality spectra were 99.364 MHz resonance frequency, 45⬚ radiofrequency pulse width of 3 ␮s, 36.0 kHz spinning speed, and 6000 scans with 10 s interval time. External tetramethylsiliane (TMS) was used as the standard. 14N solution NMR spectra were also recorded on a Bruker AM 500 MHz spectrometer with external aqueous ammonium chloride solution as standard. All spectra were obtained at 25⬚C, and standard deconvolution techniques were used to determine chemical shifts and peak areas. SEM images were obtained on a Philips XL-30 FEG scanning electron microscope. Both dried and calcined film surfaces were coated with gold for better conductivity. For side view observations, the film was fractured and mounted vertically on the sample holder using epoxy. Freeze-fracture transmission electron microscope (FF-TEM) images were obtained on a Philips CM12 or Philips 300 TEM. The films were fixed vertically or horizontally in 2-mm round holes of a gold sample holder using glycerol or molten agar and frozen quickly in liquid ethene. The sample was then transferred and stored in liquid nitrogen for 2 h. Frozen films were fractured in a vacuum chamber using a metal knife at ⫺170⬚C and coated with platinum and carbon. Highquality film replicas were obtained by dissolving the films in KOH-NaOH solution for 1 h. This replica was then transferred on a 5-mm copper grid and observed under the TEM. A Nicolet 550 Fourier transform infrared spectrometer was used in the analysis of the silicate gel and the upper benzene phase at room temperature.

III.

RESULTS

A.

Precursor Silicate Gel

The strategy behind incorporating CmOH and benzene into the gel with a CnTAC cationic surfactant was that the concentrations of these three components could be varied in order to ‘‘tune’’ the micellar packing parameter (V/aL), where L (effective length of hydrocarbon surfactant tails) is directly related to the surfactant and alcohol chain lengths (m and n). Addition of the nonionic alkyl alcohol cosurfactant decreases a (optimal headgroup area) by reducing electrostatic repulsion be-

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tween cationic surfactant headgroups, and V (effective molar volume of the hydrocarbon tails) is increased by solubilization of benzene into the interior of the surfactant aggregates. Many organic solubilizates and nonionic cosurfactants other than benzene and n-alkanols could be used to achieve essentially the same result. The alcohol and benzene also have an important influence on two additional properties of the gel. First, the inclusion of these organic compounds in the aqueous gel results in the gel having a density (0.85 g/cm3) intermediate between those of pure water and pure benzene, so delivering the gel to a benzene-water interface is not problematic. Second, the water-gel and benzenegel interfacial tensions are such that the gel spreads spontaneously at the liquid-liquid interface, making it easy to obtain highly uniform film thickness across the entire sample. The use of gels for producing films is common in the literature. Silicate gels containing short-chain alcohols such as methanol, ethanol, and propanol as cosolvents [37] have been prepared under acidic conditions for use as precursors for film coating on solid surfaces. Despite their low pH, intended to inhibit the silicate polymerization reaction, these gels still exhibit poor chemical stability, as polymerization is observed within minutes after preparing the gel. In contrast, the precursor gel prepared here is extremely stable. FT-IR analysis showed no significant changes in composition in a gel sample stored for 1 year in a sealed container at room temperature. No phase separation was observed either, so this gel is remarkably stable both chemically and physically. Because the gel is also alkaline, simply exposing it to excess water as it spreads at the liquid-liquid interface is sufficient to initiate the reaction to form the silica film product. Both 29Si and 14N NMR spectroscopy can be used to determine the degree of silicate polymerization and also whether the surfactant micelles are homogeneous [56–60]. These spectra indicate that the gel is isotropic and contains very little silicate in the form of monomers. Nearly all of the silicate is present as oligomers, so that the reaction in fact did proceed to a limited extent but was then inhibited. B.

Effect of Surfactant Type

Films were synthesized at a benzene-water interface and then transferred to borosilicate glass surfaces. Three silicate gels were prepared having identical compositions but with different cationic surfactants C12TAC, C14TAC, and C16TAC.

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1. Lamellar Mesoporous Silica Films Syntheses using the C16TAC silicate precursor gel resulted in two different types of lamellar mesoporous ˚ . Figure silica films having d(100) spacings of 29–33 A 1 shows the XRD pattern of lamellar films prepared for various reaction times at the benzene-water interface. Six well-resolved peaks were observed in 2␪ between 2 and 10. These peaks do not match any known single structure; however, they are perfectly consistent with a lamellar structure having two distinct layer spacings. The three peaks designated as w:100, w:200, and w:300 match the lamellar h00 indexing and the d(100) ˚ ) is typical of bulk lamellar prodspacing value (29.1 A ucts synthesized in aqueous C16TAC solution [61]. The other three peaks designated as b:100, b:200, and b:300 also match the lamellar h00 indexing but with a ˚ . The lamellar film synhigher d(100) spacing of 32.3 A thesized at the liquid-liquid interface therefore exhibits two distinct distances between the sheets. Freeze-fracture TEM images confirmed this observation. Figure 2a shows the TEM image of this film fractured along the film surface; the lamellar structure is clearly evident and well developed. The surface roughness of this sample was a result of the freeze-fracture process used to prepare the sample for TEM. TEM images of the film edges (side view) are shown in Fig. 2b for the edge near the surface that was originally in contact with the benzene phase and in Fig. 2c for the edge near the water side. The average periodicities between layers ˚ , respecestimated from these images are 34 and 30 A tively, which are consistent with the d(100) spacing values from XRD. The reason for the spacing between layers being larger on the benzene-contacted side of the film than

Lee and Rathman

on the water-contacted side is most likely benzene solubilization from the bulk phase into the reacting gel phase during the initial stages of the reaction. The swelling effect of organic solubilizates such as benzene is well known not only for lamellar surfactant aggregates but also for hexagonal, cubic, and simple micellar structures and has been extensively studied [62–64]. This effect has also been observed in the synthesis of bulk mesoporous materials, where the increased micelle size due to the incorporation of organic molecules inside the micelle resulted in an increase in the unit cell sizes of various mesoporous materials [65,66]. In this case, the silicate gel was saturated with benzene before being delivered to the benzene-water interface. Because the silicate polymerization reaction is initiated by exposure to water, film formation most likely begins at the water-gel interface and then proceeds relatively slowly across the gel phase. As the reaction zone moves toward the benzene-gel interface, the advancing water phase expels excess benzene from the gel. The XRD results indicate that there is not a gradual increase in layer spacing as one moves from the water side to the benzene side; rather, the film exhibits two distinct spacings. The relative amounts of these two fractions in a film can be estimated from the XRD spectra by calculating the areas of the w:100 and b:100 peaks, A(w) and A(b), respectively. Figure 3 illustrates how the A(w)/A(b) ratio varies as a function of reaction time at the benzene-water interface for films having a thickness of 5 ␮m. For short reaction times, low values of A(w)/A(b) indicate that a considerable amount of benzene remains in the film, throughout most of the thickness. As reaction time increases, the A(w)/A(b) ratio increases and then levels off. These results are con-

FIG. 1 Typical powder x-ray diffraction (XRD) pattern of lamellar mesoporous silica film having two different sets of d spacings.


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FIG. 2 Freeze-fracture transmission electron microscopy (FF-TEM) images of platinum-carbon replicas of the lamellar mesoporous silica film shown in Fig. 1: (a) the image taken from the surface fractured along the glass surface and the images of the side views taken near (b) the benzene-contacted surface and (c) the water-contacted surface.

sistent with the expulsion of some benzene from the film as a water-rich front advances through the film during reaction. Figure 4 is a schematic representation of the lamellar layers adjacent to the two bulk liquid phases. 2. Cubic Mesoporous Silica Film Syntheses using the C14TAC silicate precursor gel gave mesoporous silica films having cubic structures. Figure

5 shows a typical XRD pattern. Fifteen peaks were resolved and indexed as a cubic mesophase with Pm3n ˚ . Unlike symmetry having a unit cell size of a = 115.4 A the case of the lamellar products obtained from C16TAC silicate gel, the liquid-liquid reaction time had no effect on the unit cell dimension—all cubic films synthesized over a range of reaction times from 30 min to 5 days ˚ . Although analogues of all three surhad a ⬇ 115 A factant bicontinuous cubic mesophases (Pm3n, Ia3d,

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FIG. 2

and Im3m) have been successfully generated in the syntheses of bulk cubic mesoporous materials [9,67,68], the Pm3n product reported here is the only cubic film observed to date. The unit cell sizes for the cubic films are significantly larger than those reported for bulk cu˚ bic materials, which are on the order of 105 to 110 A [67,68]. This is somewhat surprising because the bulk materials were synthesized using C16TAC, whereas the films were synthesized in this work using

Continued.

C14TAC. This result may be a consequence of the multiconnected water and oil channels of the Pm3n cubic structure [69–73], which may prevent expulsion of benzene molecules from the structure during film formation. 3. Hexagonal Mesoporous Silica Film The C12TAC silicate precursor gel was used to prepare mesoporous silica films with hexagonal structure. A

FIG. 3 Change of the concentration ratio of the small d spacing lamellar to the large d spacing one, A(w)/A(b), as a function of the reaction time at the benzene-water interface.


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FIG. 4 Schematic representation of the cross section of a lamellar mesoporous silica film having two different sets of d spacings.

typical XRD spectrum for relatively thick films (5–100 ␮m) is shown in Fig. 6a. The four most clearly resolved peaks match the pattern indexed for hexagonal hk0 symmetry, which is essentially identical to the pattern observed for hexagonal bulk mesoporous materials such as MCM-41. The larger d(100) spacing value ˚ ) reflects a swelling effect of benzene. The pres(31.9 A ence of relatively weak high-angle peaks at 110 and 210 indicates that although some of the pore channels

FIG. 5

are aligned otherwise, most are aligned along the c axis of the unit cell, parallel to the film surface. Figure 6b shows the XRD pattern observed here for thin films with thicknesses less than 3 ␮m. All reaction conditions were the same as before; the only difference was the amount of gel delivered to the benzene-water interface at the beginning of the reaction. In similar fashion to what was observed for the lamellar films, the XRD peaks for thin hexagonal films cannot be in-

Typical XRD pattern of cubic mesoporous silica film.

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oriented parallel to the film surface; i.e., the cylindrical pore channels run parallel to the surface and are not transverse. Synthesis at an air-solid interface of a hexagonal mesoporous silica film having similar structural features using acidic C16TAC solution has been re˚ d(100) spacing value was the ported [43]. The 29 A same as that observed here for the water side of the film and the same as those reported for the bulk hexagonal particles synthesized in aqueous C12TAC solu˚ ) determined tion. The higher d(100) spacing (31.5 A for the benzene side again is due to the swelling effect of benzene molecules solubilized into the surfactant aggregate during reaction. Unlike that of the lamellar films described earlier, the proportional distribution of small and large pores [as determined by the A(w)/A(b) ratio] in hexagonal films did not exhibit any dependence on the time allowed for reaction at the liquid-liquid interface. The reason for this is not clear, but again it seems to be related to the benzene present in the gel during synthesis. Unlike that in a lamellar structure, benzene solubilized inside hexagonal micellar aggregates is much less mobile and therefore the expulsion of benzene from a hexaganol film during formation would be expected to be much less than for a lamellar film. C.

FIG. 6 Typical XRD patterns of hexagonal mesoporous silica films: (a) film with a thickness range of 5–100 ␮m and (b) film with a smaller thickness below 3 ␮m.

dexed as any single mesophase but they do match the pattern expected for a hexagonal structure containing pore channels of two distinct sizes. The average pore diameters on the benzene and water sides were 31.5 ˚ , respectively. Absence of (110) and (210) and 29.0 A peaks indicates that the long c axis of each unit cell is

Deposition of Films on Solid Substrates

Mesoporous silica films on borosilicate glass, Teflon, and ITO glass surfaces were prepared by two different methods as described earlier. In one method, the precursor gel was spread at a benzene-water interface and allowed to react for a specified length of time, after which the film was transferred to the solid substrate, where the reaction was allowed to go to completion. The second method involved application of a conventional dip-coating technique in which the film was synthesized directly on the solid substrate. Films were then dried, calcined, and characterized by XRD to determine the mesostructure. Table 1 summarizes the results of these experiments. The most important conclusion is that the liquid-liquid method allows one to synthesize selectively lamellar, cubic, and hexagonal films on any of the three surfaces. The major disadvantage of the dip-coating method is that the solid surface is the controlling factor in determining film structure; for example, regardless of the type of precursor gel (C12-, C14-, or C16TAC), reaction on glass surfaces always resulted in hexagonal films, only lamellar films were obtained on Teflon, and none of the attempts to make cubic films by dip coating were


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TABLE 1 Comparison of the Structure Obtained for Mesoporous Silica Films on Solid Substrates Using Two Different Methodsa

Method Transfer from water-benzene interface Dip coating from solution (sol-gel)

Solid surface Glass Teflon ITO glass Glass Teflon ITO glass

Surfactant in precursor gelb C16TAC C14TAC C12TAC L L L H L H

Q Q Q H L H

H H H H L H

a

The method in which a partially formed film at a liquid-liquid interface is transferred to the solid allows the mesostructure to be selectively controlled by varying the gel composition (e.g., type of surfactant). In the conventional dip-coating method, the mesostructure is essentially determined by the solid surface. b L, lamellar; Q, cubic; H, hexagonal.

successful. In contrast, the initial reaction period at the liquid-liquid interface allows the mesostructures to become sufficiently well developed that the final film structure is determined. When this film is subsequently transferred to a solid surface, specific interactions between the film and surface occur, effectively bonding the film to the surface, but any structural changes resulting from these interactions are not propagated into

the film layer. The structure formed while at the liquidliquid interface is preserved after transfer. D.

The Control of Film Properties

1. Film Thickness Using the liquid-liquid interfacial reaction technique, the thickness of a film can be simply and very accurately controlled by adjusting the amount of silicate gel initially spread at a benzene-water interface. Figure 7 shows the variation in thickness for dried lamellar films as a function of the amount of gel delivered to the interface. Optically transparent films with thickness from 0.03 to 90 ␮m were synthesized. Much thicker films were also successfully prepared, although these were only semitransparent. XRD, SEM, and TEM results showed uniform well-developed structures even for films 300 ␮m thick. One useful quantitative measure of film quality is the surface roughness, defined as the ratio of the average distance between high and low points on the surface to the total thickness of the film. Figure 8 shows SEM images of lamellar film surfaces. Both benzenecontacted and water-contacted sides have smooth surfaces, with an approximate surface roughness of 5%. Figures 9 and 10 show SEM images of cubic and hexagonal film surfaces, respectively. In both films, surface roughness was less than 5%.

FIG. 7 Variation of the thickness of lamellar mesoporous silica films as a function of the silicate gel amount delivered at the benzene-water interface.

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FIG. 8 Scanning electron microscopy (SEM) images of the surfaces of lamellar mesoporous silica film. Benzene and water on the images represent the benzene-contacted and the water-contacted surface, respectively.

SEM images of the side edges of lamellar, cubic, and hexagonal films are shown in Fig. 11. The lamellar film exhibits perfectly developed silica sheets; this uniform structure was observed across the entire thickness of the film, even for very thick films. The SEM image of the cubic film edge clearly shows the interconnected ‘‘spongelike’’ morphology characteristic of the Pm3n structure. The SEM image of the hexagonal film is characteristic of hexagonal structures viewed along the major axis along which the rod-shaped micelles are aligned [9]. These results demonstrate that the structural properties of a product can be selectively controlled by exploiting both the self-assembly of surfac-

tant molecules in solution and the additional structure-directing effects associated with confining the reaction to an interfacial region. Combined, these strategies provide a means for obtaining not only uniform mesoscopic features (pore size and alignment) but also longer range uniformity so that the macroscopic morphology is also controlled. These results also demonstrate that the liquid-liquid technique provides a route to making improved bulk mesoporous materials because thick films (thickness 1 ␮m or greater) can easily be made. Conventional processes for synthesizing bulk M41S-type materials yield particulate powders that have well-defined mesostruc-


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FIG. 9 SEM images of the surfaces of cubic lamellar mesoporous silica film. Benzene and water on the images have the same meaning as in Fig. 8.

ture, but this structure is relatively short range. Lamellar and hexagonal mesoporous silica particles, for example, are composed of randomly oriented microdomains, as illustrated for a lamellar product in Fig. 12. In comparison, thick films synthesized at a liquid-liquid interface exhibit much longer range ordering. Thus, highly ordered particles can be prepared by synthesizing the film and then simply crushing it to a desired size. Crushing the films in Fig. 11 can produce micrometersized particles that have uniform structure throughout; i.e., the long axes of unit cells within a given particle would all be aligned.

2.

Other Strategies for Controlling Film Mesostructures

Results from a broad range of experiments have shown that the water content in the gel, the molar silicate/ surfactant ratio, and the amount of cosurfactant are the main factors in controlling the properties of films synthesized from a precursor gel. The effects of organic solvents and short-chain alcohols such as methanol and ethanol have been extensively studied in the synthesis of bulk mesoporous material [65,74,75]. Crystallinity, unit cell size, and mesophase type are greatly affected

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FIG. 10 SEM images of the surfaces of hexagonal lamellar mesoporous silica film. Benzene and water on the images have the same meaning as in Fig. 8.

by these simple additives. The elimination of the gauche defects in the surfactant chains has been observed in mixed surfactant systems of cationic surfactant and long-chain alcohol because of the strong chain-chain interaction [76,77]. Mixed micelle formation of a long-chain alcohol and cationic surfactant is thermodynamically favorable because the alcohol reduces electrostatic repulsion between the headgroups of the ionic surfactant. This reduces the effective area per headgroup and so may result in a transition in micelle structure. Long-chain alcohols can thus greatly influence both the mesophase type [68] and density of me-

soporous materials synthesized in the presence of surfactant aggregates. Mesoporous silica films have many potential applications. One currently being investigated is their use as a protective desiccant layer on ITO-coated glass. The ITO surface acts as an anode in multilayer organic electroluminescent liquid crystal display units [78–80]. The luminescent organic layer tends to absorb moisture from the air, resulting in a loss of display efficiency. A thin coating of mesoporous silica film on the ITO will retain moisture because of the mesoporous silica’s extremely large surface area (500–1000 m2/g) and thus


FIG. 11

SEM images of the side view of lamellar (L), cubic (Q), and hexagonal (H) mesoporous silica films.

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and ITO glass surfaces. The mesostructures of the films were well developed and long range, and uniform structure was observed throughout the films. Films of a wide range of thicknesses were synthesized, from 0.03 to 300 ␮m. Lamellar and hexagonal films having two different d spacings within a single film were synthesized. ACKNOWLEDGMENT The authors thank Dr. Sang-Eon Park of KRICT (Korea Research Institute of Chemical Technology) and Dr. Woo Young Kim (Hyundai Electronics, Korea) for providing ITO-coated glasses. Yani Angsani and Janine Lawrence made substantial experimental contributions to this work. FIG. 12 Comparison of particles composed of lamellar silica synthesized by (a) a conventional sol-gel process and (b) a process in which the reaction is performed at a liquid-liquid interface. Synthesis of thick films provides a route toward preparing bulk particles having extremely long-range uniform structure.

prevent water from reaching the organic layer. The silica film does not decrease the conductivity of the metal oxide coating, so a substantial extension of the useful life of the display unit can be achieved without compromising any performance characteristics. Other possible applications for mesoporous films include their use in surface acoustic wave (SAW) sensors for larger molecules, selective membrane separations, quantum optics, and other electronic devices [81]. Naturally occurring laminated nanocomposites are observed in many biological systems and are responsible for the tensile strength, hardness, and toughness of many natural materials. The production of synthetic lamellar films is similar to biomineralization processes [39,42], and so these systems are ideal for biomimetic studies.

IV.

SUMMARY

The synthesis of mesoporous silica films at a liquidliquid interface using surfactant-silicate precursor gels offers several unique advantages over conventional methods. The preorganization and initial reaction at a liquid-liquid interface before transfer to a solid substrate eliminate effects of the surface on film structure. Lamellar, cubic, and hexagonal mesoporous silica films were selectively prepared on borosilicate glass, Teflon,

REFERENCES 1. 2. 3. 4. 5. 6. 7. 8.

9. 10.

11.

12. 13. 14. 15. 16. 17. 18.

J. N. Israelachvili, Intermolecular & Surface Forces, Academic Press, New York, 1992. A. W. Adamson, Physical Chemistry of Surfaces, 5th ed., John wiley & Sons, New York, 1990. J. H. Clint, Surfactant Aggregation, Blackie, 1992. T. Gu and Z. Huang, Colloids Surf. 40:71 (1992). R. G. Laughlin, Cationic Surfactants: Physical Chemistry, Marcel Dekker, New York, 1991. S. Manne, J. P. Cleveland, H. E. Gaub, G. D. Stucky, and P. K. Hansma, Langmuir 10:4409 (1994). S. Manne and H. E. Gaub, Science 270:1480 (1995). S. Manne, T. E. Scha¨ffer, Q. Huo, P. K. Hansma, D. E. Morse, G. D. Stucky, and I. A. Aksay, Langmuir 13: 6382 (1997). C. T. Kresge, M. E. Leonowicz, W. J. Roth, J. C. Vartuli, and J. S. Beck, Nature 359:710 (1992). J. S. Beck, J. C. Vartuli, W. J. Roth, M. E. Leonowicz, C. T. Kresge, K. D. Schmitt, C. T.-W. Chu, D. H. Olson, E. W. Sheppard, S. B. McCullen, J. B. Higgins, and J. L. Schlenker, J. Am. Chem. Soc. 114:10834 (1992). M. T. Janicke, C. C. Landry, S. C. Christiansen, S. Birtalan, G. D. Stucky, and B. F. Chmelka, Chem. Mater. 11:1342 (1999). M. J. Kim and R. Ryoo, Chem. Mater. 11:487 (1999). S. S. Kim, W. Zhang, and T. J. Pinnavaia, Science 282: 1302 (1998). F. Caruso, R. A. Carsuo, and H. Mo¨hwald, Science 282: 1111 (1998). B. T. Holland, C. F. Blandord, and A. Stein, Science 281:538 (1998). A. Imhof and D. J. Pine, Nature 389:948 (1997). T. Sun and J. Y. Ying, Nature 389:704 (1997). W. Zhou, J. M. Thomas, D. S. Shephard, B. F. G. Johnson, D. Ozkaya, T. Maschmeyer, R. G. Bell, and Q. Ge, Science 280:705 (1998).

Synthesis of Mesoscopic Silica Films 19. 20. 21. 22. 23. 24. 25. 26. 27. 28. 29. 30. 31. 32. 33. 34. 35. 36. 37. 38.

39.

40. 41.

42.

43. 44.

45.

C. G. Sonwane and S. K. Bhatia, Langmuir 15:2809 (1999). M. Kruk, M. Jaroniec, and A. Sayari, Chem. Mater. 11: 492 (1999). S. K. Bhatia and C. G. Sonwane, Langmuir 14:1521 (1998). S. Inoue, Y. Hanzawa, and K. Kaneko, Langmuir 14: 3079 (1998). H. Hata, S. Saeki, T. Kimura, Y. Sugahara, and K. Kuroda, Chem. Mater. 11:1110 (1999). X. Feng, G. E. Fryxell, L.-Q. Wang, A. Y. Kim, J. Liu, and K. M. Kemner, Science 276:923 (1997). T. Maschmeyer, F. Rey, G. Sankar, and J. M. Thomas, Nature 378:159 (1995). S. H. Tolbert, A. Firouzi, G. D. Stucky, and B. F. Chmelka, Science 278:264 (1997). D. Zhao, P. Yang, B. F. Chmelka, and G. D. Stucky, Chem. Mater. 11:1174 (1999). Q. Huo, J. Feng, F. Schu¨th, and G. D. Stucky, Chem. Mater. 9:14 (1997). P. Yang, D. Zhao, B. F. Chmelka, and G. D. Stucky, Chem. Mater. 10:2033 (1998). M. M. Collinson, C. G. Rausch, and A. Voigt, Langmuir 13:7245 (1997). T. Bein and K. Brown, J. Am. Chem. Soc. 111:7640 (1989). A. J. Ricco, G. C. Frye, and S. J. Martin, Langmuir 5: 273 (1989). D. H. Olson, G. D. Stucky, and J. C. Vartuli, U.S. Patent 5,364,797 (1994). M. Ogawa, J. Am. Chem. Soc. 116:7941 (1994). M. Ogawa, Langmuir 13:1853 (1997). M. Ogawa, Chem. Commun. 1149 (1996). J. E. Martin, M. T. Anderson, J. Odinek, and P. Newcomer, Langmuir 13:4133 (1997). Y. Lu, R. Gangull, C. A. Drewlen, M. T. Anderson, C. J. Brinker, W. Gong, Y. Guo, H. Soyez, B. Dunn, M. H. Huang, and J. I. Zink, Nature 389:364 (1997). A. Sellinger, P. M. Weiss, A. Nguyen, Y. Lu, R. A. Assink, W. Gong, and C. J. Brinker, Nature 394:256 (1998). M. Trau, N. Yao, E. Kim, Y. Xia, G. M. Whitesides, and I. A. Aksay, Nature 390:674 (1997). P. Yang, T. Deng, D. Zhao, P. Feng, D. Pine, B. F. Chmelka, G. M. Whitesides, and G. D. Stucky, Science 282:2244 (1998). I. A. Aksay, M. Trau, S. Manne, I. Honma, N. Yao, L. Zhou, P. Fenter, P. M. Eisenberger, and S. M. Gruner, Science 273:892 (1996). H. Yang, A. Kuperman, N. Coombs, S. Mamiche-Afara, and G. A. Ozin, Nature 379:703 (1996). G. S. Attard, P. N. Bartlett, N. R. B. Coleman, J. M. Elliott, J. R. Owen, and J. H. Wang, Science 278:838 (1997). H. Yang, N. Coombs, I. Sokolov, and G. A. Ozin, Nature 381:589 (1996).

795 46. 47. 48.

49. 50. 51. 52. 53. 54. 55. 56. 57. 58.

59. 60. 61. 62. 63. 64. 65.

66. 67. 68. 69. 70. 71. 72.

A. S. Brown, S. A. Holt, T. Dam, M. Trau, and J. W. White, Langmuir 13:6363 (1997). A. S. Brown, S. A. Holt, P. A. Reynolds, J. Penfold, and J. W. White, Langmuir 14:5532 (1998). J. L. Ruggles, S. A. Holt, P. A. Reynolds, A. S. Brown, D. C. Creagh, and J. W. White, Phys. Chem. Chem. Phys. 1:323 (1999). S. A. Holt, G. J. Foran, and J. W. White, Langmuir 15: 2540 (1999). ˜ I. Prieto, A. J. Fernańdez, E. Munoz, M. T. Martıń, and L. Camacho, Thin Solid Films 284/285:162 (1996). ˜ A. J. Fernańdez, M. T. Martıń, J. J. Ruiz, E. Munoz, and L. Camacho, J. Phys. Chem. B 102:6799 (1998). J. Sanchez and A. V. McCormick, J. Non-Crystalline Solids 167:289 (1994). J. Kim, J. L. Plawsky, E. V. Wagenen, and G. M. Korenowski, Chem. Mater. 5:1118 (1993). A. E. McHale, Phase Diagrams and Ceramic Processes, Chapman & Hall, London, 1998. C. K. Narula, Ceramic Precursor Technology and Its Applications, Marcel Dekker, New York, 1995. S. E. Rankin, C. W. Macosko, and A. V. McCormick, J. Polym. Sci. A Polym. Chem. 35:1293 (1997). J. Sanchez, S. E. Rankin, and A. V. McCormick, Ind. Eng. Chem. Res. 35:117 (1996). L. V. Ng, P. Thompson, J. Sanchez, C. W. Macosko, and A. V. McCormick, Macromolecules 28:6471 (1995). C. T. G. Knight, J. Chem. Soc. Dalton Trans. 1457 (1988). A. Steel, S. W. Carr, and M. W. Anderson, J. Chem. Soc. Chem. Commun. 1571 (1994). Y. S. Lee and K. W. Woo, Bull. Korean Chem. Soc. 14: 599 (1993). Y. S. Lee and K. W. Woo, J. Colloid Interface Sci. 169: 34 (1995). Y. S. Lee and K. W. Woo, Bull. Korean Chem. Soc. 14: 392 (1993). Q. Huo, R. Leon, P. M. Petroff, and G. D. Stucky, Science 268:1324 (1995). Q. Huo, D. I. Margolese, U. Ciesla, D. G. Demuth, P. Feng, T. E. Gier, P. Sieger, A. Firouzi, B. F. Chmelka, F. Schu¨th, and G. D. Stucky, Chem. Mater. 6:1176 (1994). J. M. Seddon and R. H. Templer, Philos. Trans. R. Soc. Lond. A 344:377 (1993). M. E. Cates, Philos. Trans. R. Soc. Lond. A 344:339 (1993). S. T. Hyde, Pure Appl. Chem. 64:1617 (1992). U. Henriksson, E. S. Blackmore, G. J. T. Tiddy, and O. Soderman, J. Phys. Chem. 96:3894 (1992). E. S. Blackmore and G. J. T. Tiddy, J. Chem. Soc. Faraday Trans. 2 84:1115 (1988). M. T. Anderson, J. E. Martin, J. G. Odinek, and P. P. Newcomer, Chem. Mater. 10:311 (1998). M. T. Anderson, J. E. Martin, J. G. Odinek, and P. P. Newcomer, Chem. Mater. 10:1490 (1998).

796 73. 74. 75. 76.

Lee and Rathman P. B. Miranda, V. Pflumio, H. Saijo, and Y. R. Shen, J. Am. Chem. Soc. 120:12092 (1998). R. H. Yoon and S. A. Ravishankar, J. Colloid Interface Sci. 179:391 (1996). Y. Ma, H. Y. Chao, Y. Wu, S. T. Lee, W. Y. Yu, and C. M. Che, Chem. Commun. 2491 (1998). A. Kraft, A. C. Grimsdale, and A. B. Holmes, Angew. Chem. Int. Ed. Engl. 37:402 (1998).

77. 78.

H. J. Brouwer, V. V. Krasnikov, A. Hilberer, and G. Hadziioannou, Adv. Mater. 8:935 (1996). M. T. Anderson, J. E. Martin, J. G. Odinek, and P. Newcomer, Microporous and macroporous materials, in Materials Research Society Symposium Proceedings (R. F. Lobo, J. S. Beck, S. L. Suib, D. R. Corbin, M. E. Davis, L. E. Iton, and S. I. Zones, eds.), Vol. 431, Materials Research Society, 1996.

39 Inorganic Nanostructure Design with Amphiphilic Block Copolymers ¨ LTNER* CHRISTINE GO

I.


INTRODUCTION

fects increases with decreasing size of the object to be generated. A more facile and less time-consuming route toward the construction of mesostructured hybrid materials would, therefore, involve a synthetic procedure during which the desired structure forms without external manipulation. This can be achieved only through the mechanisms of spontaneous, supramolecular self-assembly [4]. Supramolecular self-assembly or ‘‘selfstructuring’’ is a principle often observed in nature and commonly takes place on exactly the length scale that is desired for the synthesis of nanochemical structures. Self-structuring is a consequence of competing interactions (e.g., Coulomb interactions, hydrogen bonding, hydrophobic interactions) and often produces structures of surprising regularity.

While searching for new materials with improved properties, scientists are increasingly focusing on the generation of composite materials instead of the synthesis of new molecular species. The main objective of these efforts is the combination of macroscopically immiscible components (e.g., metals and polymers or organic and inorganic compounds in general) on a mesoscopic length scale. Mesoscopically structured hybrid materials are fascinating because they often exhibit the typical characteristics of the components they comprise, such as the properties of a metal along with the solubility of an organic compound. Chemistry on the dimension of a few nanometers (‘‘nanochemistry’’) [1] is particularly intriguing because materials can be obtained that possess entirely new features, while their chemical composition is well known. Nanochemistry demands the application of specific nanochemical techniques and instruments [2] because the composition of a material occurs on a length scale between the dimension of a molecule and that of a macroscopic solid. Methods of classical synthetic chemistry applied to the generation of mesoscopic matter (‘‘bottom-up’’) are tedious and time consuming. The opposite approach, ‘‘top-down’’ synthesis, which utilizes microlithographic techniques (as impressively demonstrated by Whitesides et al. [3]), is broadly applicable. However, the sensitivity of this route to de-

A.

Mediation Between Incompatible Materials

The generation of a hybrid material can be achieved only by combining molecularly immiscible (incompatible) components; otherwise, some kind of alloy or homogeneous mixture (i.e., solution) would be obtained. The inherent problem of generating a mesostructured composite is that extraordinarily large interfacial areas are created, which introduce an interfacial energy of many kT into the system. In this case, macroscopic separation of the components is therefore energetically favored, and such hybrids macroscopically demix or, which is more commonly the case, do not form to begin with. However, this problem can be addressed by in-

*Current affiliation: University of Bristol, Bristol, England. 797

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troducing amphiphilic mediators into the system, which decrease the interfacial energy and therefore compatibilize the immiscible components. These amphiphiles consist of at least two covalently linked parts, of which one is miscible with one component and the other with the other component of the desired hybrid. The bestknown and most widespread amphiphiles are surfactants, which allow the mixing of oil and water, a classical application of detergents. In addressing other incompatibility problems, amphiphilic block copolymers (ABCs) have proved to be versatile [5]. These polymers, which consist of at least two immiscible polymer blocks, are produced through methods of modern polymer chemistry. ABCs are able to stabilize almost all imaginable interface areas, hence allowing the word ‘‘amphiphilicity’’ to be used in its most general sense, namely ‘‘loving both.’’ For example, this general amphiphilicity is the foundation for the creation of composite materials made from a metal and a typical polymeric species. In the absence of a mediator, both components are mutually incompatible. B.

Amphiphilic Block Copolymers Versus Surfactants

Amphiphilic block copolymers are functional polymers [5,6] whose structure can be tailored so that the interfacial energies between materials of very different chemical natures, polarities, and cohesion energies— in short, incompatible materials—can be lowered much more than would be possible with common low-molecular-weight surfactants. They are therefore technologically relevant emulsifiers, dispersants, foaming agents, thickeners, and compatibilizers. For many applications, ABCs are able to substitute low-molecularweight surfactants or extend their utilization. By analogy with low-molecular-weight surfactants, amphiphilic block copolymers form aggregation structures in so-called selective solvents that are compatible with only one of the blocks. The structurally simplest aggregate is the spherical micelle, which consists of an insoluble core and a soluble corona. When the more polar block of the polymer points outward, that is, forms the shell, the micellar structure is called regular. In the opposite case, namely where the less polar block forms the shell, the micelle is called reverse. This classification, known from classical surfactants, is also applied to more complex aggregate structures such as lyotropic liquid crystal phases. In dilute solutions of selective solvents, most amphiphilic block copolymers form spherical micelles [7– 12], although cylindrical (wormlike) micelles have also

been observed [13–15]. The synthesis of amphiphilic block copolymers is not covered here. Therefore, the interested reader may want to refer to excellent reviews [16–18]. At higher concentration, lyotropic mesomorphism is observed for many ABCs, which often comprises a wide variety of morphologies, many of which are known from lyotropic surfactant phases [19–23]. Because of their ability to stabilize interfaces between incompatible compounds, amphiphilic block copolymers are particularly suited to direct the structure of inorganic-organic composites. Their characteristic feature, namely amphiphilicity, gives rise to their spontaneous self-assembly into microphase-separated aggregation structures in the presence of solvents or even as neat polymers. This self-assembly can be utilized for a wide number of applications, of which a particularly interesting research area, namely the design of nanostructured inorganic-organic hybrid materials, is reviewed here. This chapter is dedicated to a representative selection of principles and mechanisms that demonstrate the versatile nature of amphiphilic block copolymers as structure-directing agents for nanostructure design. At first sight, the aspects covered in this section originate from rather different approaches and may appear haphazardly chosen. They range from biomimetic crystallization to the synthesis of porous ceramic oxides, from low-concentration block copolymer solutions to bulk polymers, and from precipitates to nanostructured macroscopic objects. However, all of these research areas have in common that at some stage during synthesis, amphiphilic block copolymers play a structure-directing role. II.

AMPHIPHILIC BLOCK COPOLYMER MICELLES AS NANOREACTORS

One aspect of the self-assembly or aggregation of amphiphilic block copolymers is their ability to undergo micellization in selective solvents, hence compartmentalizing one microphase in the other [7–15]. The resulting compartments can be utilized for the synthesis of nanosized inorganic particles, which are separated and protected from the ‘‘outside world’’ by the micellar corona. In contrast to the micelles formed by lowmolecular-weight surfactants in water, those formed by amphiphilic block copolymers are kinetically more stable, and molecular exchange dynamics are considerably slower. Therefore these simplest aggregate structures of amphiphilic block copolymers can be used as nanosized vessels in which chemical reactions can be conducted [24]. This procedure is called exo-templating

Inorganic Nanostructure Design

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FIG. 1 Schematic representation of the ABC nanoreactor. The amphiphilic block copolymer undergoes micellization in a selective solvent. The micelles are loaded with an inorganic precursor. The chemical reaction is confined to the cores of the micelles, hence affording colloidal particles. (From Ref. 6.)

(see Fig. 1) because the structure-directing casting mold is wrapped around the inorganic object. ABC micelles, in which chemical reactions are performed, are referred to as nanoreactors. The size [25], shape, and properties of these nanoreactors can be tailor-made by means of modern polymer chemistry [16–18]. For successful exo-templating, the polymer block, which forms the micellar core, must selectively interact with one or more of the starting materials, while the corona-forming block provides sufficient solubility of the nanoreactor in the surrounding solvent: Only then can the chemical reaction be trapped within the mesoscopic confinement of the nanoreactor. One method of loading block copolymer micelles is to form a complex of a polymerizable ligand with the inorganic precursor [26], but the number of metal-complexed monomers that are suitable for living polymerization is very limited. It is therefore more common to bind the inorganic precursor to the ready-made block copolymer from homogeneous, nonaggregated solution. For example, it is possible to bind Zn2⫹ [27] selectively to the hydrophilic blocks of poly(styrene-bmethacrylic acid) (PS-PMAc) from THF solution. Complexation of the Zn ions by PMAc causes this polymer block to become insoluble in THF; consequently, THF is turned into a selective solvent in which micellization occurs.

Most commonly, however, the confinement of an inorganic precursor within block copolymer micelles occurs via a metal-ligand interaction in which the polymer block acts as a ligand (e.g., for Pd(AcO)2 [27]) or via ‘‘ion exchange’’; i.e., the inorganic precursor species represent the counterions for an ionic polymer block [28]. Metal colloids, for example, can be made by reducing an inorganic precursor, usually a metal salt, within the micellar core. The usually hydrophilic precursor can be solubilized even in nonpolar organic solvents if these solvents contain the appropriate amphiphilic block copolymer. This nanochemical methodology even allows the dissolution of substantial amounts of sodium chloride in toluene. One representative example of the utilization of block copolymer micelles as nanosized reaction vessels is the synthesis of gold colloids in the presence of micellar poly(butadiene)-b-poly(2-vinylpyridine) (PB-P2VP, see Scheme 1). While the poly(butadiene) block is soluble in toluene (the selective solvent), the P2VP block, which shows high affinity for metal salts, is insoluble and induces micellization. Thus, a gold precursor (e.g., tetrachloroauric acid) is enriched within the micellar cores. The introduction of the inorganic species into ‘‘prefabricated’’ micelles is the most commonly applied method of loading block copolymer micelles because

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SCHEME 1 Chemical structure of poly(butadiene-b-2-vinyl pyridine).

it allows precise control of the amount of salt introduced, is simple to conduct, and is suitable for many solvent/block copolymer/precursor systems [28–31]. Within these loaded micelles, gold colloids are produced by chemical reduction, which is performed by adding a reducing agent to the micellar solution. The reducing agent reaches the micellar core via diffusion and is likewise incorporated. The stability and size of the gold nanoparticles are mainly determined by the micellar reactors (e.g., aggregation number, molecular weight, and the chemical nature of the block copolymer) in which they are generated as well as the amount of precursor introduced into the micelles. In addition, the features of the nanosized products can be influenced externally by choosing the appropriate reduction conditions: Fast reduction causes fast nucleation, so that many small particles are formed within the core of each micelle, whereas slow nucleation affords one colloidal gold particle per micelle (Fig. 2). This image of a mesoscopic ‘‘nanoreactor’’ applies well to amphiphilic-block copolymer micelles because

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a nanometer-sized object is filled with starting material, and a second starting material or even a catalyst is fed at a determined rate (or the reaction can be conducted photochemically [32]). Finally, the reaction is restricted to the dimensions of the vessel; i.e., it neither explodes nor boils over! As with a bulk reactor, reaction kinetics can be controlled externally. With the help of a nanoreactor, stable noble metal particles are obtained that are ideal candidates for catalytic processes because of their extraordinarily large surface areas [33–37]. Conducting reactions in different-sized nanoreactors or block copolymer micelles (determined by the block length) generates colloids whose size corresponds directly to that of the primary nanostructure as well as the degree of loading. This represents an additional tool to fine-tune the size of colloidal particles, which is very important whenever particular optical or magnetic [38] properties are required. The concept of the nanoreactor can also be applied to the production of colloidal metal oxides and sulfides. Quantum-size cadmium sulfide or zinc oxide can be made, safely wrapped in a stabilizing polymer shell. Most of the preparations of sulfide semiconductor nanoparticles involve the purging of solutions containing precursor-loaded ABC micelles with hydrogen sulfide [27] or causing precipitation of an oxide via external manipulation of the pH of the system. The nanoreactor need not be constructed by engineers, maintained, or cleaned. The supramolecular selfconstruction of amphiphilic block copolymers in selective solvents occurs spontaneously. The latter can be predetermined and influenced by the methodology required of a nanochemical approach, in this case polymer chemistry combined with the intuition necessary

FIG. 2 TEM images of two different gold colloids produced in ABC nanoreactor micelles. (a) Fast reaction causes the generation of many small colloids in each micelle; (b) slow reaction gives rise to a single colloid per micelle. (From Ref. 6.)


to estimate which inorganic species can be compartmentalized in which ABC micelles. III.

DESIGN OF POROUS CERAMICS

Micellar nanoreactors represent exo-templates, because the product is enveloped by the structure-directing amphiphilic block copolymer, which determines the size and shape of the resulting colloidal object. The opposite approach to nanostructure design of inorganic materials is called endo-templating, in which the structuredirecting medium is included within the inorganic material during the synthesis. The result is a solid, regularly structured inorganic-organic composite from which the organic matter can be removed. The remaining residue represents a highly porous ceramic material. This approach allows the creation of pore systems in otherwise dense inorganic materials, thereby providing them with completely new properties. These properties are again due to the increase of the interfacial area or, in this case, of the surface area. Large specific surface areas in inorganic solids usually expose a vast number of surface sites where sorption processes or even chemical reactions, such as catalytic conversion, can take place. In combination with a pore system that causes an entrapped species to follow particular diffusion pathways (i.e., defining directionality and kinetics of diffusion), these materials are expected to be unique catalyst supports or stationary phases for chromatographic separation. Why the pore systems obtained by using amphiphilic block copolymers as structure-directing agents are superior to those obtained by other methods is explained in the following. A.

Porosity Through the Displacement of Porogens

The creation of inorganic pore systems is commonly achieved by growing an inorganic polymer (ceramic oxide) within or around an organic (sometimes even an inorganic) medium, the porogen [39,40]. Once the chemical preparation of the inorganic pore system is accomplished, the porogen is removed, usually by evaporation, calcination (i.e., firing), or extraction. Depending on the nature of the porogen and its compatibility with the inorganic product, materials with different pore structures, pore size distributions, and pore sizes can be manufactured. For simplicity, the mechanisms underlying pore generation can be divided into two classes, namely the undirected displacement of a porogen and templating.

801

If the porogen shows no specific interaction with the inorganic solid or is even miscible with the inorganic material at all times during the synthesis, the pore system arises simply from physical volume exclusion or molecular displacement out of homogeneous solution. In this case, the characteristic length of the structure that arises will depend on the steric demands of the molecularly dissolved porogen. If demixing occurs at any stage during the preparation, the volume excluded by the porogen (i.e., the later pores) will depend on the degree of repulsion, the amount of possible stabilizer, as well as the time at which the macroscopic phase separation occurs. One way to tailor the pore size distribution of macroporous ceramic oxides is to generate the inorganic solid in an emulsion. The oily emulsion droplets displace the inorganic precursor from their volume, thus creating macropores [41,42]. One example of the controlled demixing of two inorganic components is the manufacturing of Vycor glass or controlled-pore glass (CPG) [43–45]. Because no driving force pushes the system into a particularly ordered state in either case, the structures of the resulting porous materials represent a snapshot of a statistical situation; therefore, broad pore size distributions are usually obtained. In the following, this strategy will be referred to as displacement of porogen. B.

Micropores Through Molecular Templating

The undoubtedly more intriguing pathway toward the design of inorganic pore systems is templating, in which a more or less specific interaction of the inorganic with the porogen causes the creation of substantially more regular pore systems because molecular recognition and supramolecular organization are the structure-directing principles. One example of very specific templating, where the template creates a precisely defined pore system in silicates, is the synthesis of crystalline zeolites (see Chapter 40 for an exhaustive review). In this case, quaternary ammonium salts are included in the cagelike voids of a crystal, thus generating a microporous inorganic material. The size and shape of the pore system in zeolites are defined by the templating species, usually one molecule or ion. As zeolites are regularly structured crystalline materials, their pore size distributions are peak shaped. Although zeolites with various structures and pore connectivities are available, their crystallinity does not permit the synthesis of pore systems with diameters larger than 1.3 nm [46,47]. The reason is that the walls that surround

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the pores in a zeolite are represented essentially by one chemical bond and are therefore too fragile to support larger pore diameters. The latter, however, are mandatory whenever a species to be catalytically converted is too bulky or too hydrophobic to enter a zeolitic pore system. To extend the limits of classical zeolites, synthetic methods have been developed that favor the production of thicker walls surrounding larger voids. The synthesis of defined mesopores [48] is a templating procedure in which the specific molecular templates known from zeolite synthesis are replaced by supramolecularly aggregated amphiphiles. Templating can therefore be divided into two subgroups, namely specific molecular and supramolecular templating. C.

Mesopores Through Supramolecular Templating

In many respects, supramolecular templating bridges the gap between specific molecular templating and the undirected displacement of a porogen. On the one hand, it allows the synthesis of materials whose pore diameter is not limited by the structure of the product as is the case for zeolites. On the other hand, the pore size distributions, albeit narrow, can never be peak shaped. This is because of one of the fundamental principles of supramolecular chemistry. In a supramolecularly assembled, dynamic system, there always exists a statistical probability of defect sites, such as domain boundaries, which are continuously repaired but also introduced simultaneously at the same rate. A defectfree supramolecular system is therefore a contradiction in terms [2,4]. In spite of this, the structures of supramolecularly templated porous ceramic oxides are astonishingly regular. The pore size distributions that are obtained from different templating mechanisms are represented in Fig. 3.

FIG. 3 Pore size distributions attainable with different methods. (From Ref. 50.)

Although this is still a field that receives great attention, it is not the aim of this chapter to dwell on the subject of low-molecular-weight surfactant templates, as review articles [49–55] and Chapter 40 in this volume provide more detailed insight for the interested reader. However, some general principles are outlined in the following to emphasize the striking similarities that can be found between low-molecular-weight surfactants and amphiphilic block copolymers and to demonstrate in what respect ABCs are often the superior choice. 1.

Low-Molecular-Weight Surfactant Templates During the past 8 years, surfactants have received increasing interest as porogens for the generation of inorganic nanostructures [49–55]. The microphase separation of a surfactant solution in water into aqueous and hydrophobic domains is the foundation of supramolecular templating. The principle is as simple as this: The inorganic precursor (hydrophilic) is expelled from the areas where the hydrophobic surfactant chains are located. The result of combining a soluble inorganic precursor with a surfactant solution is the formation of a regular hybrid material with characteristic lengths between 2 and 5 nm. Removal of the organic matter leaves behind a regularly structured, mesoporous molecular sieve. The first mesoporous siliceous nanostructure was initially ‘‘overlooked’’ as curiously discovered much later: Another property attributed to this material, namely its low density, was patented without the regular nanostructure being detected at all [56,57]. The mesoscopic structure of similarly prepared porous ceramic oxides was finally discovered and systematically investigated by researchers at Mobil Research and Development Corporation. This new class of molecular sieves subsequently became known under the general name M41S [58–63]. M41S-type materials form as a consequence of cooperative interaction between micellar aqueous solutions of ionic surfactants and charged inorganic precursor species. Ion matching, sometimes via a mediating counterion, causes a surfactant-rich gel phase to precipitate from aqueous solution. This precipitate consists of a regularly structured assembly of surfactant aggregates ‘‘filled’’ with the inorganic solid. The structures observed resemble those of lyotropic liquid crystals, for example, hexagonally packed rodlike aggregates and gyroid or lamellar phases. Nonionic surfactants used in this precipitation procedure produce less regular materials because the attraction between the ag-


gregating species, which in the absence of charges is due only to hydrogen bonding and hydrophobic interaction, is weaker. Nevertheless, the materials obtained exhibit narrow pore size distributions [64–66]. The precipitation procedures can be conducted hydrothermally or via sol-gel processing. A related approach utilizes the regular structures of performed lyotropic liquid crystal phases of nonionic surfactants as structure-directing media [67–70]. In a sol-gel process, the hydrophilic inorganic silica precursor undergoes solidification confined within the aqueous domains of the liquid crystal, hence producing a cast or replica of the lyotropic system without changing the supramolecular structure. The materials obtained are similar to M41S-type mesoporous molecular sieves. However, because they are prepared in the presence of nonionic templates, which do not demand electrostatic compensation on a specific length scale, the wall thickness can be individually adjusted via the precursor content. Furthermore, the nanostructure derived from liquid crystalline bulk phases is a result of a homogeneous mixture solidifying as opposed to a precipitation process. Therefore the dimensions of the inorganic particles are far larger. All of these mesoporous ceramic oxides are amorphous on the atomic level but show periodicities on the nanometer length scale and a narrow pore size distribution (Fig. 3). Based on the knowledge collected from utilizing surfactants as templates for mesoporous inorganics, amphiphilic block copolymers have been established as structure-directing media for porous nanostructure design [71,72]. They assist in overcoming the limitations inherent in their low-molecular-weight analogues, the classical detergents, in many aspects. The most commonly applied route toward ABC-templated inorganic nanostructures is the technologically widespread solgel process, the underlying chemistry of which is explained briefly using the synthesis of silica as a representative example. 2. Sol-Gel Processing of Silica The sol-gel process for the production of silica is an industrially widely applied procedure. As it occurs in homogeneous solution, it is possible to manufacture clear macroscopic silica objects, such as fibers or lenses. Furthermore, this process can be conducted at quiescent temperatures, and no increased pressure is necessary. Therefore, although the precursors for silica synthesis are usually more expensive than those required for other methods, such as hydrothermal processing, it has found wide application. The starting material for sol-gel processing of silica is an orthoester of

803

SCHEME 2 sis of silica.

Reaction pathways during the sol-gel synthe-

the general structure Si(OR)4, which is hydrolyzed in order to formally yield silicic acid. The latter undergoes polycondensation into a three-dimensional network of silicon dioxide whose surface is saturated by silanol (Si — OH) groups. The various reactions occurring simultaneously in a sol-gel mixture (see Scheme 2) represent equilibria that can be influenced by parameters, such as the pH of the system, temperature, or solvent content, and that all have a substantial effect on the structure of the resulting silica gel. Whereas base-catalyzed saponification of the tetraalkylorthosilicate usually produces highly condensed particulate materials, acid-catalyzed hydrolysis and polycondensation afford a weakly branched polymeric sol. The most common alkoxide precursors are tetraethylorthosilicate (TEOS) and tetramethylorthosilicate (TMOS) because of their relatively low cost, easy handling, and relatively fast hydrolysis. The reader interested in deeper insight into the physics and chemistry of sol-gel processing may want to refer to a monograph by Brinker and Scherer [73], which discusses the subject in greater detail and provides an invaluable bibliography. The sol-gel processing of silica is advantageous for the design of inorganic-ABC nanocomposites because the kinetics of the hydrolysis as well as the polycondensation of silicic acid can be fine tuned via the pH, which is of considerable importance for some of the procedures described in the following. 3.

Generating Porosity with Amphiphilic Block Copolymers The creation of ceramic nanostructures with controlled structure is a rapidly emerging field that greatly profits from the self-assembly of amphiphilic block copolymers as well as the variety of ABCs available. The ordering characteristics of amphiphilic block copoly-

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mers can be almost continuously tuned by varying the chemical nature of the blocks, solvent contents, molecular weight, block length ratios, and copolymer architecture or even by varying external parameters that influence the aggregation behavior, such as temperature or the addition of salt. Simplistically, amphiphilic block copolymers can be assumed to act as ‘‘large surfactants’’ in that they allow self-organization into larger aggregate structures than their low-molecular-weight analogues. Like the micellar systems used as nanoreactors, the more complex aggregation structures of amphiphilic block copolymers exhibit decreased exchange dynamics, which go along with higher kinetic stability. Furthermore, amphiphilic block copolymers extend the synthetic methods for mesoporous ceramic nanostructures over the inherent limits of low-molecular-weight surfactant templates. The latter are available only up to certain alkyl chain lengths (usually 22 carbon atoms at the most). Accordingly, the pore diameters available for mesoporous inorganic nanostructures are limited to a maximum of 4.5 nm unless inert organic auxiliaries are introduced into the system during synthesis. In contrast, amphiphilic block copolymers can be made (or even purchased) with considerably higher molecular weight, so that the synthesis of materials with larger pores is possible. In particular, modern polymer chemistry provides the tools to make these block copolymers in a vast variety of shapes and sizes, giving rise to the expectation that an equally rich variety of nanostructures could be produced. The objective of this section is to discuss different methods of exploiting amphiphilic block copolymer templates for the generation of sol-gel–derived inorganic-organic hybrid structures with periodicities larger than 4 nm. All approaches to such materials have in common that the growth of the inorganic matter is displaced from the hydrophobic domains of an amphiphilic block copolymer aggregate structure. The compatibilizing amphiphilic block copolymer, therefore, not only stabilizes the interfacial area of a nanoscopic structure but also acts as a porogen, leaving nanometersized voids behind after its removal. Amphiphilic block copolymer templates replace the classical low-molecular-weight surfactants that were used previously, introducing mechanical stability and access to a wider range of pore diameters. Three different approaches can be distinguished, depending on what causes the final inorganic-organic hybrid structure to form and on the amount of template present during the synthesis. The following section gives an overview of the different routes to porous ce-

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ramic nanostructures using amphiphilic block copolymers as structure-directing media. 4.

Precipitation of Inorganic-ABC Hybrid Structures By analogy with the preparation of M41S materials, the combination of an alkoxide silica precursor and a solution of amphiphilic block copolymers in a wateralcohol mixture causes the formation of a regularly structured gel phase, which precipitates from aqueous solution [74–76]. The synthetic procedure, which is conducted under acidic conditions using TEOS as the precursor utilizes mainly nonionic Pluronic-type triblock copolymers or nonionic star diblock copolymers as structure-directing agents* because of their good solubility in water, commercial availability, low cost, and biodegradability. The solidification of the silica network occurs within this polymer-rich precipitate, while the supramolecular structure is preserved. The amphiphilic block copolymer template can be completely removed from the hybrid material by solvent extraction or calcination, both of which leave behind the purely inorganic nanoporous ceramic oxide. The structure of the final product is a result of a macroscopic separation of a microphase-separated, ordered phase from water as a solvent. The solidification of the sol-gel mixture takes place in the ordered environment of this microphase-separated system. The synthesis is conducted at relatively low polymer concentrations, above the critical micelle concentration, which are far lower than those necessary to form an ordered amphiphilic block copolymer structure, i.e., a lyotropic mesophase. The system tolerates the presence of considerable amounts of inert swelling agents, usually mesitylene, so that despite the relatively low molecular weight of the hydrophobic templating block, large pores (up to 30 nm) can be created. It is also possible to fine-tune the final ceramic structures via other synthesis parameters: The hydrophilicity of poly(ethylene oxide) is temperature dependent [77]; therefore raising the temperature during the sol-gel process formally increases the hydrophobic volume of the template, which is an elegant method of finely adjusting the pore size [74]. The pore diameter of the calcined samples depends on the molecular weight of the template (Table 1), mainly that of the hydrophobic block. In contrast, the *Amphiphilic triblock copolymers of the general structure poly(ethylene oxide)-b-(propylene oxide)-b-(ethylene oxide) (PEP-PPO-PEO, Pluronics) are a trademark product of BASF, Mt. Olive, NJ.


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TABLE 1 Pore Diameters and Specific Surface Areas of Pluronic-Derived Silicas Pluronic-type template

Pore diameter (nm)

BET surface area (m2/g)

EO5PO70EO5 EO20PO70EO20 EO20PO70EO20 EO20PO70EO20 EO20PO70EO20 EO20PO70EO20 EO17PO55EO17 EO20PO30EO20 EO26PO39EO26 EO13PO70EO13 EO19PO33EO19

117 96 98 100 105 104 81 78 88 80 71

630 690 780 820 920 850 770 1000 960 950 1040

Source: Ref. 74.

specific surface areas, which are obtained from nitrogen sorption experiments, appear to be substantially affected by the size of the hydrophilic block. In fact, the specific surface areas are far larger than can be expected from simple geometrical considerations (S. Fo¨rster, unpublished results): As the interfacial area in the microphase-separated system roughly represents the specific surface area of the later purely ceramic oxide, the calculation of exactly this area should allow an estimation of the surface area contribution arising from the mesopore system. The following equation outlines the dependence of the volume fraction ␾ for a ‘‘binary’’ system consisting of hexagonally packed cylinders:

␾=

8␲ R 2cyl 3 a2

(1)

with R being the radius of the cylinders (or pores), a the distance between cylinders, and d the dimensionality of the system (in this case 2). The interfacial area A/V per unit volume between hydrophilic and hydrophobic domains is given by

␾ A =d V Rcyl

(2)

The pore radius R can be obtained from transmission electron microscopy (TEM) analysis, the distance between cylinders from small-angle x-ray scattering experiments. The density ␳ of the silica matrix can be either determined experimentally or assumed to be constant for different amorphous silicas (about 2.1 g/cm3).

For a defect-free domain the specific surface area is obtained from Eq. (3): Aspec =

d␾ (1 ⫺ ␾)Rcyl ␳SiO2

(3)

Even taking into account structural defects, domain boundaries, and external particle surface, it is evident that the specific surface areas of most mesoporous ceramic oxides obtained by different experimental approaches show a significant contribution arising from structures with smaller length scales, which are mainly due to microporosity. Suitable experiments have been devised to determine the mesopore surface area selectively by filling the micropores (B. Berton et al., unpublished results; B. Smarsly et al., unpublished results). The phenomenon of extraordinarily large specific surface areas gives rise to the assumption that the hydrophilic poly(ethylene oxide) chains of the template are ‘‘dissolved’’ or anchored in the ceramic material during and after solidification. The substructure of the resulting nanostructured hybrid material is therefore expected to be a two-phase system in which one microphase consists of an inorganic-poly(ethylene oxide) hybrid material. After removal of the organic structure-directing copolymer, the hydrophilic blocks leave behind smaller (micro)pores. Therefore, the poly(ethylene oxide) groups additionally act as porogens in their own right. By displacing the silica growth, they give rise to substantial microporosity and possibly small-scale surface roughness (B. Berton et al., unpublished results). This finding underlines the fact that in a mixture of incompatible components, each molecule of the compatibilizer contributes to the interfacial area. As the amphiphilic block copolymer templates are nonionic, the wall thickness of the resulting mesoporous silicate is substantially higher than that of MCM41–type materials, whose structure formation occurs via a complex interplay of ion matching. Therefore the mechanical and hydrolytic stabilities of the products are greatly improved. As typical polymeric species, amphiphilic block copolymers introduce considerable mechanical stability into the inorganic-organic hybrid material, which would be brittle in the absence of the template. Therefore, it is possible to cast homogeneous, smooth films by dip coating a silicon wafer into the sol-gel mixture [76] and to manufacture membranes whose structure and pore connectivity can be individually adjusted. This route toward ABC-templated mesoporous ceramic oxides also makes it possible to influence the shape of the particles via experimental parameters such as stirring. The improved mechanical

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performance of the hybrid product is a typical example of favorable effects that are observed when the hybridization of matter is conducted on the nanometer length scale. One of the most impressive and pioneering uses seems to be its combination with other methods of ‘‘shaping matter’’ [78]. The simultaneous application of ABC templating and micromolding (pathway A in Fig. 3) as well as optionally using previously established polymer latex spheres [79] as additional templates (Fig. 4, pathway B) affords patterned materials with an exceptional micrometer-scale morphology, which show additional order on the mesoscopic length scale. Hierarchical ordering over several discrete and tunable length scales (tiers) ranging from 10 nm to several micrometers is the result. Compared with the complicated multitier structure of these materials, the overall synthetic strategy is simple: In a ‘‘top-down’’ approach, the template with the largest length scale is prepared first by micromolding a poly(dimethylsiloxane) (PDMS) matrix, which is used as a stamp to imprint the micrometer-scale morphology [80–82]. This stamp is then pressed into a

FIG. 4

liquid sol-gel mixture consisting of templating Pluronic-type ABC, tetraethylorthosilicate (or other sol-gel precursors, e.g., for the synthesis of niobia), and water at a suitable pH. The sol-gel process is confined to the spaces where the micromold prevents it from wetting the substrate (usually a silicon wafer). Introducing one more step in the hierarchical order is achieved by additionally using latex templates, which were previously shown to be useful porogens in porous-silica synthesis and have been established as templates in a process called rigid-colloid templating [83]. The latex dispersion is introduced into the voids of the PDMS micromold, where it forms a colloidal-crystalline array (Fig. 4, pathway B). One example of a hierarchical ceramic oxide structure is shown in Fig. 5. The precipitation of regularly structured hybrid materials from solution is a result of cooperative supramolecular aggregation. As the phase structure forms during the synthesis, that is, upon combination of the organic structure-directing agent and inorganic precursor, the material is self-structured, but the structure on the nanometer length scale is induced. Although a given template always produces the same product un-

Schematic representation of the generation of hierarchically structured ceramic oxides. (From Ref. 78.)


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FIG. 5 Hierarchically structured (three tier) silica. (a) SEM picture of the micromolded (tier 1) structure; (b) TEM image of the latex-templated (tier 2) mesoporous substructure (tier 3). (From Ref. 78.)

der the same reaction conditions, the final structure can be determined only after the synthesis, which has the disadvantage that for a new template various experiments are necessary to map the ‘‘phase diagram’’ of the nanostructured precipitates. The structures induced resemble those of the complex aggregates formed by many amphiphilic species regardless of molecular weight: The structure of lyotropic liquid crystalline phases, which have only recently been proved to be versatile templates for inorganic nanostructure design in a process called ‘‘nanocasting.’’ 5. Lyotropic ABC Phases for ‘‘Nanocasting’’ Precipitation of inorganic ceramic oxides in the presence of amphiphilic block copolymers is only one method of preparing large-pore mesoporous materials that show a high degree of order. A more predictable route toward inorganic-organic nanostructured hybrid materials is the direct utilization of lyotropic amphiphilic block copolymer phases. This approach can be understood as the vitrification of a microphase-separated medium, during which no changes of the phase structure occur. The sol-gel synthesis of silica is conducted within the aqueous domains of the microphase-separated medium comprising amphiphilic block copolymer and water. Simplistically, the polycondensation of silicic acid is confined to exactly those aqueous domains, during which a replica of the lyotropic phase structure is formed (Fig. 6). Therefore, this procedure was termed nanocasting, and in many ways it resembles a nanoscale analogue of the lost-wax casting technique, which is still applied for manufacturing bronze statues and church bells. Nanocasting is the method that produces

an exact cast of the lyotropic block copolymer phase structure. Using the binary phase diagram of an amphiphilic block copolymer with water as a guideline, the structure of the final product can be predicted a priori: The nanocast, an ordered hybrid material consisting of silica and the templating block copolymer, is the result of adding a component to a binary lyotropic liquid crystal phase without ultimately changing the phase structure. This method is as applicable for nonionic [71,72,84,85] as for ionic [86] amphiphilic block copolymers, which is a strong indication that supramolecular templating of the lyotropic mesophase governs the mechanism of nanocasting. Lyotropic lipid crystalline phases of nonionic surfactants in water have previously proved to be versatile structure-directing media [67,68] for the synthesis of regular mesoporous ceramic oxides. This approach to controlled inorganic pore systems (the ‘‘true liquid crystal approach’’) has been extended into the field of amphiphilic block copolymers [71]. The nonionic ABC templates used for nanocasting consist of a hydrophobic soft block (Tg below or around room temperature in order to warrant sufficient solubility at room temperature), such as poly(butadiene) [87], poly(ethylene-co-butylene) (Kraton Liquid*) or relatively short poly(styrene),* and a poly(ethylene oxide) block as the hydrophilic moiety. During nanocast-

*Poly(styrene-b-ethylene oxide) (SEs) (for SE10/10 the average molecular weight is 1 kg/mol; for SE30/30, it is 3 kg/mol) of various block lengths and low-dispersity poly[(ethylene-cobutylene)-b-(ethylene oxide)]s (KLEs) are products of Th. Goldschmidt AG, Essen, Germany.

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FIG. 6 Schematic representation of nanocasting. The aqueous domains of a lyotropic mesophase (here isolated cylindrical micelles) are swollen with the silica precursor (TMOS), upon which a siliceous mesophase is formed. The system solidifies in the bulk, and after calcination an exact replica of the colloidal nanostructure is obtained.

ing, as is the case for the nanoreactor principle as well as the precipitation of regularly structured hybrids, the templating amphiphilic block copolymers are again assumed to be ‘‘big surfactants’’ in that their aggregation behavior is expected to be similar to that of low-molecular-weight surfactants, which is indeed the case. The binary phase diagrams of aqueous amphiphilic block copolymer solutions follow the general phase sequence shown by surfactants. While at low block copolymer concentration the formation of micelles is observed, high concentrations give rise to more complex aggregates, such as cylindrical micelles or lyotropic liquid crystal phases of different structures. A rich lyotropic polymorphism is observed that can be utilized directly for porous nanostructure design. The phase diagrams correspond to those of low-molecular-weight surfactants in that they are more defined the narrower the molecular weight distribution. While heterodisperse block copolymers often show a tendency to form illdefined phases, the phase diagrams of monodisperse amphiphilic block copolymers exhibit wide regions of high order. In general, the lyotropic liquid crystal phases of amphiphilic block copolymers are thermally more stable than those of classical nonionic surfactants. In most cases no clearing point is observed even at temperatures as high as 95⬚C. The temperature dependence of the phase structure, which is very pronounced for nonionic surfactants [88], is also less noticeable for the polymeric amphiphiles. Consequently, heterodisperse SE templates afford nanostructures that appear to be affected by high defect densities where the defect sites determine the overall structure [71]. In contrast, nanocasts of low-polydispersity amphiphilic block copolymers are generally more ordered. The structure elucidation of the latter by imaging or scattering methods is, therefore, considerably simplified.

To a certain extent, the lyotropic phase behavior of amphiphilic block copolymers can be predicted as a function of the ABC’s chemical nature, the overall molecular weight, and the block length ratio. These phase diagrams represent a valuable guideline for the structure design. Therefore, it is especially useful to map them for commercially available templates or for those that are likely to be used for more than one future experiment. The analytical tool for the structure elucidation of lyotropic liquid crystal phases is usually polarized-light optical microscopy or small-angle X-ray scattering. After mapping the phase diagram with respect to composition and temperature, the variation of one experimental parameter during the synthesis, namely the template concentration, allows the precise tailoring of pore systems with respect to their shape, density, and connectivity. Figure 7 shows TEM images of three samples, all obtained with the same template (KLE 3729) but at varying concentration [84]. Isolated, bent cylindrical pores result from a system at relatively low template contents, and a hexagonally packed cylindrical pore array is achieved at higher concentration. Increasing the template contents even further gives rise to an entirely different structure, which is again in accordance with the lyotropic phase diagram of the polymer. Multilamellar vesicles are found in coexistence with isolated fragments of sheetlike structures. Calcination, that is, removal of the organic scaffolding from a lamellar system drives the structure to fall apart. Nitrogen adsorption-desorption isotherms again provide valuable information about the structure of the materials and allow one to gain insight into the pore structure. They support the conclusions drawn from the TEM micrographs, but in addition they illustrate the fact that each template molecule delivers its individual contribution to the overall interface area. Within the


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FIG. 7 TEM images of three samples obtained via nanocasting of KLE 3729 after calcination. (a) At 30 wt% polymer in water, isolated cylinders are obtained; (b) 50 wt%, cylindrical pores are assembled on an hexagonal lattice; (c) 70 wt% polymer give rise to a lamellar structure, which collapses upon calcination. (From Ref. 84.)

regime of one particular pore structure, the specific surface area increases significantly with growing template concentration (see Table 2). They also demonstrate that the same double templating action can be observed for amphiphilic block copolymers used in nanocasting as well as during the precipitation of mesostructured hybrid materials discussed before: The resulting nanoporous ceramic oxides possess an undeniable microporosity, which is due to the hydrophilic poly(ethylene oxide), which is initially homogeneously distributed in the siliceous microphase, displacing silica growth from its own molecular volume (B. Berton et al., unpublished results; B. Smarsly et al., unpublished results). Some phase diagrams of low-polydispersity amphiphilic block copolymers exhibit areas of coexistence over a relatively wide range of compositions (see Fig. 8) [85]. This is probably due to kinetic inertia or to the fact that at the borderline between two thermodynamically stable phases the energetic differences between two structures are marginal. Swelling these coexisting phases with a siliceous precursor affords a microphaseseparated siliceous phase, which has the same structure

as the binary mixture consisting of water and amphiphilic block copolymer. As a result of the inorganic precursor undergoing polycondensation, the bulk phase solidifies without altering its superstructure. The fact that the structural integrity of the binary lyotropic phase does not seem to be harmed by the nanocasting procedure suggests a reversal of the principle. If the nanostructure of the silica can be predicted a priori, the a posteriori analysis of a silica cast should provide valuable information on the structural composition of an unknown binary ABC phase. Assuming the noninvasive character of nanocasting, this method can help to elucidate more complex hyotropic phase struc-

TABLE 2 Relationship Between Template Contents and Specific Surface Area for PB-PEO–Templated Silica Weight ratio template/water (%) 30 50 70 Source: Ref. 85.

BET surface area (m2/g) 770 820 1160

FIG. 8 Binary phase diagram of PB202PEO360 in water. LI = micellar, HI = regular hexagonal, L␣ = lamellar, X = crystalline.

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FIG. 9 TEM images of (a) thin-sectioned polymer gel, obtained by cross-linking a hexagonal lyotropic ABC phase, (b) silica nanocast of the lyotropic phase formed at the same polymer concentration, and (c) reference sample obtained from casting the polymer gel. (From Ref. 89.)

tures of amphiphilic block copolymers as a complementary technique to diffraction methods and may help to avoid time-consuming preparations (e.g., cryo-TEM, freeze etching). The phase structure simply has to be ‘‘frozen’’ into a solid silica cast, which is perfectly stable in a high vacuum under the electron beam. The applicability of nanocasting as an analytical tool has been demonstrated [89] by comparing the silica structures obtained from a lyotropic phase, which has been cross-linked using ␥-rays in order to provide sufficient mechanical stability to allow thin sectioning, with those of a silica nanocast obtained from a lyotropic phase of the same composition (Fig. 9). The similarity between the structures is striking. A reference sample was prepared by filling the pore system of the cross-linked polymer gel with silica and subsequent calcination. The pictures prove without doubt that the sol-gel process indeed does not have any structurally disrupting effect on the liquid crystalline phase [89]. In contrast to precipitation procedures, nanocasting allows the fabrication of objects (monoliths) that are macroscopically devoid of cracks and defects (Fig. 10) [71]. The porosity of these monoliths is as high as 85%. Moreover, diffusion pathways can be individually designed by templating a particular phase structure. Above all, the pore system of a macroscopic object is exclusively determined by the pore system, whereas particulate powders show a significant contribution to the surface area caused by the nonstructured particle surface. Nanocasting can also be used to generate hierarchical pore systems. The synthesis of silica is performed in the presence of a polymer latex dispersion as the

porogen, giving rise to spherical pores in the size and size distribution corresponding to those of the templating latex dispersion (see Fig. 11a). By adding an additional amphiphilic block copolymer as a second template, materials can be prepared with bimodal pore size distributions (see Fig. 11b) [79] that as monolithic species would be ideal candidates as stationary phases for chromatographic separation. Nanocasting of lyotropic ABC phases allows to design predictably the structure, size, connectivity, and shape of nanoscopic pore systems in sol-gel–derived silicates. The generation of defined diffusion pathways, combined with the possibility of shaping macroscopic objects, leads to the highest expectations regarding the

FIG. 10 Optically transparent silica monolith containing SE 10/10 as the template. The liquid crystalline mixture was pressed into a cylindrical mold. (From Ref. 71.)


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FIG. 11 TEM images: (a) the silica sample templated with a poly(styrene) latex dispersion is purely macroporous; (b) the material obtained in the presence of additional ABC stabilizer clearly shows a hierarchical macro-mesophorous structure. (From Ref. 79.)

application in separation processes. Increasing the concentration of amphiphilic block copolymer present during the production of inorganic-organic nanostructured hybrid systems from the structure induction in micellar solutions to the utilization of prefabricated mesoscopic casting molds (nanocasting) leads to the ultimate question of whether amphiphilic block copolymer bulk phases can be used as structure-directing media for the synthesis of mesoscopic hybrid materials. The following section is focused on this aspect of nanostructure design with ABCs. 6. Sol-Gel Processing in ABC Bulk Phases In one respect, amphiphilic block copolymers differ significantly from their low-molecular-weight analogues. Whereas a surfactant either decomposes or undergoes melting into an isotropic liquid state, the melts of amphiphilic block copolymers of sufficient molecular weights are generally microphase separated. The variety of polymorphism observed for block copolymer bulk phases is as at least as wide as that of their lyotropic phases and mainly depends on the volume fraction of each block. This bulk phase behavior is also temperature dependent. The phase behavior of amphiphilic block copolymers in the bulk is the focus of widespread research interest because it is not only the chemical composition of the block copolymer but also

the structure of the microphase-separated phase it forms that defines the macroscopic mechanical performance of such materials. Another approach to the synthesis of amphiphilic block copolymer–templated inorganic nanostructures is the solidification of a prehydrolyzed mixture of aluminum and silicon alkoxides in amphiphilic block copolymer bulk phases and subsequent formation of an ordered nanostructured alumosilicate [90]. Again, the formation of a solid, nanostructured inorganic-organic hybrid material is a consequence of the strict microphase separation between a hydrophobic (or better ‘‘silicatophobic’’) poly(isoprene) block and the ‘‘silicatophilic’’ poly(ethylene oxide) interacting with the inorganic sol-gel precursor. The novelty of this process lies in the inorganic sol acting as a swelling agent, whose volume fraction determines the overall microphase structure of the hybrid material. As the microphase-separated structure that forms depends on the volume fraction of each block (or microphase), the amount of inorganic ‘‘microphase’’ added to the amphiphilic block copolymer determines the structure of the resulting inorganic-organic hybrid material. Interestingly, the chemical nature of the inorganic phase appears to be independent of the inorganic precursor/template ratio, hence manifesting

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the main difference from the ABC templating processes discussed earlier. In ABC bulk phase templating, it is the amount of inorganic that directs the structure of the hybrid material rather than the amphiphilic block copolymer. As a consequence, the whole phase diagram of this bulk block copolymer with respect to block length ratio can be traversed without having to synthesize amphiphilic block copolymers with different block length ratios. Depending on the amount of inorganic sol present in the block copolymer, a whole variety of differently structured hybrid materials can be produced (see Fig. 12). Nuclear magnetic resonance (NMR) spectroscopic analysis finally proved the assumption made for the previous structure-directing methods, namely that the poly(ethylene oxide) blocks are firmly anchored in the inorganic phase rather than being located at the interphase adjacent to the hydrophobic domains. Solid-state NMR spectroscopy revealed that this anchoring leads to a substantial hindrance of the conformational mobility in the poly(ethylene oxide) chains compared with the relatively mobile hydrophobic poly(isoprene) [91]. Two possible scenarios can be envisaged for the structure of the hybrid material (see Fig. 13). The first is that the poly(ethylene oxide) block, albeit strongly interacting and partially penetrating, forms a pure PEO layer at the interface with the hydrophobic poly(isoprene) (Fig. 13, left-hand sketch) (‘‘three-phase’’ system). The other possibility is the complete ‘‘dissolution’’ of the PEO chains in the aluminosilicate, which

FIG. 12 Schematic representation of the phase structures created by swelling a bulk block copolymer with a prehydrolyzed sol-gel mixture. (From Ref. 91.)

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FIG. 13 Schematic representation of possible hybrid structures. Left: The poly(ethylene oxide) blocks of the template form a separate microphase at the interface to the hydrophobic block (three-phase system). Right: The poly(ethylene oxide) blocks are homogeneously distributed in the inorganic phase. (From Ref. 91.)

results in the ‘‘two-phase’’ system depicted in the righthand sketch of Fig. 12b. Spin-diffusion NMR experiments showed that there appears to be no dynamic heterogeneity in the poly(ethylene oxide) chains, as would be expected for a three-phase system, giving rise to the conclusion that the hydrophilic domains constitute one homogeneous hybrid phase consisting of poly(ethylene oxide) and the inorganic. This approach to nanostructured inorganic-organic hybrid materials is the first one to allow the synthesis of inverse-topology systems, in which the hydrophobic polymer blocks represent the outside of the microphase-separated structure. After solidification of the inorganic sol, the hydrophobic phase can be swollen with organic solvents: This procedure allows the isolation from one another of colloidal objects, such as spheres or ceramic rods (see Fig. 14), which are sterically stabilized because the hydrophilic block is firmly anchored in the ceramic material [92]. Formally, this process represents a conversion of the initial exo-templating into endo-templating. These bulk hybrid materials cannot be calcined without seriously affecting their structure. The reason is that the extremely large interface/surface area generated in such small objects makes a ceramic colloid unstable in the absence of a sterically stabilizing polymer/solvent layer. However, the steric stabilizer need not be removed in order to envisage applications of such ceramic nano-objects. The bulk preparation of their colloidal dispersions would open a variety of physicochemical aspects. For example, nanoscopic rods, when sufficiently concentrated, should give rise to colloidal nematic phase behavior in solution. Aligning such phases and incorporating the aggregated rods


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FIG. 14 TEM images of ceramic nano-objects: (a) spherical alumosilicate colloids; (b) rodlike particles obtained from a hexagonal phase. (From Ref. 90.)

into a solid polymer matrix should create unique anisotropic mechanical properties (nano-reinforced hybrid materials). IV.

BIOMIMETIC MINERALIZATION WITH ABCs

There are numerous examples of mesostructured inorganic-organic hybrid materials occurring in nature. For example, the hard outside and the iridescent inside of a shell chemically consist of the same material, namely calcium carbonate, which exists in two different crystal modifications. Mammals are able to fabricate the substance of bones and teeth, both high-performance materials, from a single mineral, hydroxyapatite. The mechanical properties of these have not yet been accomplished in any man-made ceramic. Nature completes the controlled crystallization of such minerals in the presence of certain structure-directing proteins, which are able to affect not only the crystal structure but also morphology (e.g., disks, needles, cubes) and the orientation and spatial relationship of the crystals with each other. Excellent reviews have been published, which are highly recommended to the interested reader [93–95]. Whenever a chemist attempts to precipitate calcium carbonate or hydroxyapatite in a beaker, both minerals occur in the shape of macroscopic brittle crystals of one, mostly the thermodynamically most stable, modification. Because of packing or structural defects, the resulting precipitate is mechanically useless because crystallization occurs without any directing auxiliaries. Controlled crystallization, however, as demonstrated by nature, can be mimicked [96–99]. For example, structure-directing proteins can be isolated from seashells and used to in-

fluence the crystallization of minerals. It is possible to grow calcite and aragonite, two modifications of calcium carbonate, on one substrate alternatingly by adding first one, then another protein to the supernatant calcium salt solution. This procedure, however successful it may be, is not applicable to industrial or even laboratory scale experiments because the isolation and purification of the biological structure-directing entities are tedious and time consuming. However, the chemical and physical mechanism from which the ultimate structure control arises can be mimicked with simple methods of polymer chemistry. In a biomimetic approach, amphiphilic block copolymers replace the complex protein as the structure-directing compound and have the effect of avoiding unspecific crystallization processes. These auxiliaries fulfill two tasks: On the one hand, they stabilize the primary seed and avoid agglomeration and macroscopic precipitation [100,101]. On the other hand, they selectively bind to certain crystal planes, hence directing the mineralization process, which allows control of crystal structure as well as morphology. During biomimetic crystallization, the structure-directing block copolymer acts as an amphiphile in the most general sense. One part of the molecule has strong affinity for the crystal, while the other shows only weak interaction with starting materials as well as product mineral. The task of the latter is solely stabilization of the dispersion, solubilization, and the prevention of macroscopic precipitation. As water is the most common reaction medium, both polymer blocks have to be hydrophilic. Therefore, these structure-directing block copolymers are called ‘‘double-hydrophilic’’ block copolymers. Only one block (the handle) interacts specifically with the crystal, while the second one (the

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head of the tool) adopts the role of a stabilizer, i.e., avoids macroscopic precipitation [100,101]. For example, appropriately choosing the chemical nature of double-hydrophilic block copolymers facilitates the control of particle size and morphology as well as the crystal modification of calcium carbonate. In a series of experiments presented here, the stabilizing block was poly(ethylene oxide). The specific interaction with the crystal was accomplished by either poly(ethylene imine tetraacetate) (PEDTA), poly(aspargic acid) (PAsp, well known from the biomineralization of seashells), or a synthetic poly(phosphate) (Pphos). The three polymer structures are shown in Scheme 3. Despite their apparent similarity, the three polymers have vastly different effects on the growth of calcium carbonate, hence demonstrating the sensitivity of the precipitation to the chemical nature of the ‘‘head’’ of the structure-directing tool. Control experiments in the absence of any additives afford calcium carbonate in the shape of submillimeter-sized rhombohedral crystals (see Fig. 15a). In the presence of the phosphate block, monodisperse calcium carbonate spheres are obtained (Fig. 15b), which are approximately 3 ␮m in diameter. Hollow spheres with a radius of 10 ␮m are formed in the presence of PEO-PEDTA (Fig. 15c), and the addition of PEO-b-PMMA-Asp gives rise to the formation

SCHEME 3

of twins, which apparently originate from rods or platelet-shaped seeds (Fig. 15d). One of the most important features of biomimetic crystallization is the fact that the resulting product morphology is formed as a consequence of combining the mineral solution with the structure-directing block copolymer. It therefore reflects an individual interaction between organic and inorganic components, which serves to minimize the interfacial energy. Biomimetic mineralization is therefore another aspect of induced nanostructure. Another example of the induction of structure is the controlled, nanoscopic mineralization of hydroxyapatite, the main constituent of bones and teeth. In the presence of an amphiphilic block copolymer, micrometer-sized colloids with a fibrous structure are obtained, whose individual ‘‘whiskers’’ are as thin as 3 nm (see Fig. 16) [102]. Spinning and weaving of such fibers could lay the foundation for a biocompatible bone substitute. This delicate structure can be detected neither in classical hydroxyapatite nor as an aggregate of the pure double-hydrophilic block copolymer in aqueous solution. Furthermore, this morphology appears to be specific for this particular combination of inorganic and double hydrophilic block copolymer and has not been detected for any other mineral, which confirms the as-

Double-hydrophilic block copolymers used as structure-directing agents for biomimetic mineralization.


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FIG. 15 SEM images of calcium carbonate samples: In the absence of structure-directing polymers (a) rhombohedral crystals are formed. (b) Monodisperse spherical particles; (c) hollow spheres; (d) twins. (From Ref. 101.)

sumption that an individual, specific interaction between the inorganic and the template is reflected and the process is truly biomimetic in this respect. The same extreme specificity and individuality are often observed for biomineralization, which raises the question of whether the naturally occurring processes are actually as complex as assumed or the process of biomimetic mineralization with block copolymers is as simple as it appears. V.

SUMMARY AND OUTLOOK

Five representative methodologies were chosen to demonstrate how the principles of self-structuring can be applied to the preparation of nanostructured inorganicorganic composites. The control of the resulting interface opens facile access to highly organized hybrid materials, which show typical structural elements on the length scale of a few nanometers. Amphiphilic block copolymer adopt the role of molecular ‘‘assembly teams’’ that take care of organizing and fitting of the components.

Amphiphilic block copolymers are versatile auxiliary agents for the synthesis of mesoscopically structured hybrid materials. Relatively little time and effort are necessary to tailor the chemical composition of these structure-directing media, and almost any compatibility problem can be addressed by simply choosing the right structure, size, and chemical nature of the compatibilizer, the ABC. The word ‘‘amphiphile’’ can indeed be used in its most general sense whenever there is a demand for interface stabilization on the nanometer length scale. Whether the structure of the resulting hybrid material is induced upon combining inorganic and organic components, as in biomimetic mineralization or supramolecular templating of sol-gel processes with micellar solutions, or whether the hybrid is generated in a ‘‘preassembled’’ supramolecular casting mold, whether endo-templating produces nanometer-size particles or exo-templating yields porous monolithic objects, the flexibility of ABCs as structure-directing media is in the hands of modern chemists and materials scientists. A short while ago the problem of mediating between

816

Go¨ltner

FIG. 16 TEM image of a hydroxyapatite morphology obtained from biomimetic crystallization in the presence of a structuredirecting double-hydrophilic block copolymer. (From Ref. 102.)

two incompatible materials prevented the synthesis of nanoscale hybrid materials. With the new trends and developments in amphiphilic block copolymer synthesis, access is opened to the generation of new technologies whose utilization depends on the imagination, creativity, and skills of nanochemists and, of course, on nanomarket demands.

7. 8. 9. 10. 11. 12.

ACKNOWLEDGMENTS C. G. G. would like to thank M. Antonietti for his support and helpful discussions, M. P. Hase for inspiration, and the Max-Planck-Society for financial support.

13.

14.

REFERENCES 1. 2. 3. 4. 5. 6.

G. A. Ozin, Adv. Mater. 4:612–649 (1992). M. Antonietti and C. Go¨ltner, Angew. Chem. Int. Ed. Engl. 36:910–928 (1997). Y. N. Xia, J. A. Rogers, K. E. Paul, and G. M. Whitesides, Chem. Rev. 99:1823–1848 (1999). J. M. Lehn, Supramolecular Chemistry, VCH, Weinheim, 1995. S. Fo¨rster and M. Antonietti, Adv. Mater. 10:195–217 (1998). S. Fo¨rster, Ber. Bunsen Phys. Chem. 101:1671–1678 (1997).

15. 16. 17. 18. 19. 20.

Z. Tuzar and P. Kratochvil, in Surface and Colloid Science (E. Matijevic, ed.), Plenum, New York. A. Gast, NATO ASI Ser. E 303:311, 1988. B. Chu, Langmuir 11:414 (1995). P. Alexandridis, Curr. Opin. Colloid Interface Sci. 1: 490–501 (1996). M. Moffit, K. Kougas, and A. Eisenberg, Acc. Chem. Res. 29:95 (1996). J. Selb and Y. Gallot, in Developments in Block Copolymers (I. Goodman, ed.), Vol. 2, Elsevier, Amsterdam, 1985, p. 27. P. C. Conheim, T. V. Laxly, C. Price, and R. V. Stubbersfield, J. Chem. Soc. Faraday Discuss. I 76:1857 (1980). C. Price, E. K. M. Chan, A. L. Hudd, and R. B. Stubbersfield, Polym. Commun. 27:196–198 (1986). K. Schillen, W. Brown, and R. M. Johnsen, Macromolecules 27:4825–4832 (1994). M. Moffitt, H. Vali, and A. Eisenberg, Chem. Mater. 10:1021–1028 (1998). J. P. Spatz, A. Roescher, and M. Mo¨ller, Adv. Mater. 8:337–340 (1996). R. S. Kane, R. E. Cohen, and R. Silbey, Chem. Mater. 8:1919–1924 (1996). M. Svensson, P. Alexandridis, and P. Linse, Macromolecules 32:637–645 (1999). P. Alexandridis, Macromolecules 31:6935–6942 (1998).

Inorganic Nanostructure Design 21. 22. 23. 24. 25. 26. 27.

28. 29. 30. 31. 32.

33.

34.

35.

36.

37.

38. 39.

40. 41. 42. 43.

D. L. Zhuo, P. Alexandridis, and A. Khan, J. Colloid Interface Sci. 183:339–350 (1996). P. Alexandridis, D. L. Zhou, and A. Khan, Langmuir 12:2690–2700 (1996). G. Wanka, H. Hoffmann, and W. Ulbricht, Macromolecules 27:4145–4149 (1994). M. Mo¨ller and J. P. Spatz, Curr. Opin. Colloid Interface Sci. 2:177–187 (1997). S. Fo¨rster, M. Zisenis, E. Wenz, and M. Antonietti, J. Chem. Phys. 104:9956–9970 (1996). Y. N. C. Chan, G. S. W. Craig, R. R. Schrock, and R. E. Cohen, Chem. Mater. 4:885–894 (1992). T. Schneider, M. Haase, A. Kornowski, S. Naused, H. Weller, S. Fo¨rster, and M. Antonietti, Ber. Bunsges. Phys. Chem. 101:1654–1656 (1997). S. Fo¨rster and M. Antonietti, Adv. Mater. 10:195–217 (1998). M. Antonietti, E. Wenz, L. Bronstein, and M. Seregina, Adv. Mater. 7:1000 (1995). M. Antonietti, S. Fo¨rster, J. Hartmann, and S. Oestreich, Macromolecules 29:3800–3806 (1996). M. Antonietti, S. Fo¨rster, J. Hartmann, S. Oestreich, and E. Wenz, Nachr. Chem. Tech. Lab. 44:579 (1996). L. Bronstein, D. Chernyshov, P. Valetsky, N. Tkachenko, H. Lemmetyinen, J. Hartmann, and S. Fo¨rster, Langmuir 15:83–91 (1999). S. Klingelho¨fer, W. Heitz, A. Greiner, S. Oestreich, S. Fo¨rster, and M. Antonietti, J. Am. Chem. Soc. 119: 10116–10120 (1997). E. Sulman, Y. Bodrova, V. Mateeva, N. Semagina, L. Cerveny, V. Kurtc, L. Bronstein, O. Platonova, and P. Valetsky, Appl. Catal. A Gen. 176:75–81 (1999). L. M. Bronstein, M. V. Seregina, O. A. Platonova, Y. A. Kabachii, D. M. Chernyshov, M. G. Ezernitskaya, L. V. Dubrovina, T. P. Bragina, and P. M. Valetsky, Macromol. Chem. Phys. 7:1357–1363 (1998). O. A. Platonova, L. M. Bronstein, S. P. Solodovnikov, I. M. Yanovskaya, E. S. Obolonkova, P. M. Valetsky, E. Wenz, and M. Antonietti, J. Colloid Polym. Sci. 5: 426–431 (1997). E. Sulman, V. Mateera, A. Usanov, G. Demidenko, L. Bronstein, D. Chernyshov, and P. Valetsky, J. Mol. Cat. A Chem. 146:265–269 (1999). M. Antonietti, S. Fo¨rster, and S. Oestreich, Macromol. Symp. 121:75–88 (1997). S. Wallace and L. L. Hench, in Better Ceramics Through Chemistry (C. J. Brinker, D. E. Clark, and D. R. Ulrich, eds.), Elsevier, North-Holland, New York, 1984, pp. 47–52. H. Bo¨ttcher, K. H. Kallies, H. Haufe, and J. Seidel, Adv. Mater. 11:138–140 (1999). A. Imhof and D. J. Pine, Adv. Mater. 10:697–700 (1998). A. Imhof and D. J. Pine, Nature 389:948–951 (1997). T. H. Elmer, in ASM Engineered Materials Handbook (S. J. Schneider, Jr., ed.), Materials Park, OH, 1991.

817 44. 45. 46. 47. 48.

49. 50. 51. 52. 53.

54.

55. 56. 57. 58.

59.

60.

61.

62.

63.

64.

W. Haller, Nature 206:693 (1965). W. Haller, J. Chem. Phys. 42:686 (1965). M. E. Davies, C. Saldarriaga, C. Montes, J. Garces, and C. Crowder, Nature 331:698–699 (1988). L. B. McCusker, C. Baerlocher, E. Jahn, and M. Bu¨low, Zeolites 11:308–313 (1991). K. S. W. Sing, D. H. Everett, R. A. W. Haul, L. Moscou, R. A. Pierotti, J. Rouquerol, and T. Siemieniewska, Pure Appl. Chem. 57:603–619 (1985). D. Antonelli and J. Ying, Curr. Opin. Colloid Interface Sci. 1:523–529 (1997). P. Behrens, Adv. Mater. 5:127–132 (1993). P. Behrens and G. D. Stucky, Angew. Chem. Int. Ed. Engl. 32:696–699 (1993). C. G. Go¨ltner and M. Antonietti, Adv. Mater. 9:431– 436 (1997). J. Liu, A. Y. Kim, L. Q. Wang, B. J. Palmer, Y. L. Chen, P. Bruinsma, B. C. Bunker, G. J. Exarhos, G. L. Graff, P. C. Rieke, G. E. Fryxell, J. W. Virden, B. J. Tarasevich, and L. A. Chick, Adv. Colloid Interface Sci. 69:131–180 (1996). D. Zhao, P. Yang, Q. Huo, B. F. Chmelka, and G. D. Stucky, Curr. Opin. Solid State Mater. Sci. 3:111–121 (1998). W. Meier, Curr. Opin. Colloid Interface Sci. 4:6–14 (1999). V. Chiola, J. E. Ritsko, and C. D. Vanderpool, U.S. Patent 3,556,725 (1971). F. DiRenzo, H. Cambon, and R. Dutartre, Microporous Mater. 10:283–286 (1997). C. T. Kresge, M. E. Leonowicz, W. J. Roth, J. C. Vartuli, and J. S. Beck, Nature 359:710–712 (1992); J. C. Vartuli, C. T. Kresge, M. E. Leonowicz, A. S. Chu, S. B. McCullen, I. D. Johnson, and E. W. Sheppard, Chem. Mater. 6:2070–2077 (1994). J. S. Beck, J. C. Vartuli, G. J. Kennedy, C. T. Kresge, W. J. Roth, and S. E. Schramm, Chem. Mater. 6:1816– 1821 (1994). J. S. Beck, J. C. Vartuli, W. J. Roth, M. E. Leonowicz, C. T. Kresge, K. D. Schmitt, C. T. W. Chu, D. H. Olson, E. W. Sheppard, S. B. McCullen, J. B. Higgins, and J. L. Schlenker, J. Am. Chem. Soc. 114:10834– 10843 (1992). A. Monnier, F. Schu¨th, Q. Huo, D. Kumar, D. Margolese, R. S. Maxwell, G. D. Stucky, M. Krishnamurty, P. Petroff, A. Firouzi, M. Janicke, and B. F. Chmelka, Science 261:1299–1303 (1993). Q. Huo, D. I. Margolese, U. Ciesla, D. G. Demuth, P. Feng, T. E. G. Fier, P. Sieger, A. Firouzi, B. F. Chmelka, F. Schu¨th, and G. D. Stucky, Chem. Mater. 6:1176–1191 (1994). Q. Huo, D. I. Margolese, U. Ciesla, P. Feng, T. E. Gier, P. Sieger, R. Leon, P. M. Petroff, F. Schu¨th, and G. D. Stucky, Nature 368:317–320 (1994). P. T. Tanev, M. Chibwe, and T. J. Pinnavaia, Nature 368:321–323 (1994).

818 65. 66. 67. 68. 69. 70. 71.

72. 73.

74.

75. 76. 77. 78.

79. 80. 81. 82. 83. 84.

Go¨ltner S. A. Bagshaw, E. Prouzet, and T. J. Pinnavaia, Science 267:865–867 (1995). S. A. Bagshaw and T. J. Pinnavaia, Angew. Chem. Int. Ed. Engl. 108:1102–1105 (1996). G. S. Attard, J. C. Glyde, and C. G. Go¨ltner, Nature 378:366–368 (1995). G. S. Attard, M. Edgar, and C. G. Go¨ltner, Acta Mater. 46:751–758 (1998). G. S. Attard, M. Edgar, J. W. Emsley, and C. G. Go¨ltner, MRS Conf. Proc. 425:179–184 (1996). G. S. Attard, M. Edgar, J. W. Emsley, and C. G. Go¨ltner, MRS Conf. Proc. 425:185–189 (1996). C. G. Go¨ltner, S. Henke, M. C. Weißenberger, and M. Antonietti, Angew. Chem. Int. Ed. Engl. 37:316 (1998). M. C. Weißenberger, C. G. Go¨ltner, and M. Antonietti, Ber. Bunsenges. Phys. Chem. 101:1679 (1997). C. J. Brinker and G. W. Scherer, Sol-Gel Science: The Physics and Chemistry of Sol-Gel Processing, Academic Press, San Diego, 1990. D. Zhao, J. Feng, Q. Huo, N. Melosh, G. H. Fredrickson, B. F. Chmelka, and G. D. Stucky, Science 279:548–552 (1998). D. Zhao, Q. Huo, J. Feng, B. F. Chmelka, and G. D. Stucky, J. Am. Chem. Soc. 120:6036–6042 (1998). D. Zhao, P. Yang, N. Melosh, J. Feng, B. F. Chmelka, and G. D. Stucky, Adv. Mater. 10:1380–1385 (1998). R. Zana, Colloids Surf. A Physicochem. Eng. Aspects 123:27 (1997). P. Yang, T. Deng, D. Zhao, P. Feng, D. Pine, B. F. Chmelka, G. M. Whitesides, and G. D. Stucky, Science 282:2244–2246 (1998). M. Antonietti, B. Berton, C. Go¨ltner, and H. P. Hentze, Adv. Mater. 10:154 (1998). Y. Xia and G. M. Whitesides, Angew. Chem. Int. Ed. Engl. 37:550 (1996). E. Kim, Y. Xia, and G. M. Whitesides, Adv. Mater. 8: 245 (1996). C. Marzolin, S. P. Smith, M. Pretiss, and G. M. Whitesides, Adv. Mater. 8:571 (1998). C. G. Go¨ltner, Angew. Chem., in press. C. G. Go¨ltner, B. Berton, E. Kra¨mer, and M. Antonietti, Chem. Commun. 2287–2288 (1998).

85. 86. 87. 88.

89.

90.

91.

92. 93. 94. 95.

96. 97. 98. 99. 100. 101. 102.

C. G. Go¨ltner, B. Berton, E. Kra¨mer, and M. Antonietti, Adv. Mater. 11:395–398 (1999). E. Kra¨mer, S. Fo¨rster, C. Go¨ltner, and M. Antonietti, Langmuir 14:2027 (1998). S. Fo¨rster and E. Kra¨mer, Macromolecules 32:2783– 2785 (1999). D. J. Mitchell, G. J. Tiddy, L. Waring, T. Bostock, and M. P. McDonald, J. Chem. Soc. Faraday Trans. 79: 975–1000 (1983). H. P. Hentze, E. Kra¨mer, B. Berton, S. Fo¨rster, M. Antonietti, and M. Dreja, Macromolecules 32:5803– 5809 (1999). M. Templin, A. Franck, A. Du Chesne, H. Leist, Y. Zhang, R. Ulrich, V. Scha¨dler, and U. Wiesner, Science 278:1795–1799 (1997). S. M. De Paul, J. W. Zwanziger, R. Ulrich, U. Wiesner, and H. W. Spiess, J. Am. Chem. Soc. 121:5727– 5736 (1999). R. Ulrich, A. Du Chesne, M. Templin, and U. Wiesner, Adv. Mater. 11:141–146 (1999). S. Weiner and L. Addadi, J. Mater. Chem. 7:689–702 (1997). P. Calvert and P. Rieke, Chem. Mater. 8:1715–1727 (1996). S. Mann, J. Webb, and R. J. P. Williams, eds., Biomineralizaton: Chemical and Biochemical Perspectives, VCH, Weinheim, 1989. S. Mann, ed., Biomimetic Materials Chemistry, VCH, Weinheim, 1996. R. Brace and E. Matijevic, J. Inorg. Nucl. Chem. 35: 3691 (1973). A. Chittofrati and E. Matijevic, Colloids Surf. 48:65– 78 (1990). R. S. Sapieszko and E. Matijevic, J. Colloid Interface Sci. 74:405 (1980). M. Sedlak, H. Co¨lfen, and M. Antonietti, Macromol. Chem. Phys. 199:247 (1998). H. Co¨lfen and M. Antonietti, Langmuir 14:582–589 (1998). M. Antonietti, M. Breulmann, C. G. Go¨ltner, H. Co¨lfen, K. K. W. Wong, D. Walsh, and S. Mann, Chem. Eur. J. 4:2493–4500 (1998).

40 The Role of Surfactants and Amphiphiles in the Synthesis of Porous Inorganic Solids ANDREAS STEIN and BRIAN J. MELDE

I.

University of Minnesota, Minneapolis, Minnesota

INTRODUCTION

been greatly expanded, and new structures and morphologies have been developed by tuning the synthesis procedures. This chapter focuses on the role that surfactants and other amphiphiles play in controlling and modifying the structure of porous inorganic solids.

For several decades now, organic molecules have been used to direct the structure of porous inorganic solids. For example, Barrer and Kerr (Mobil) pioneered the use of organic cations, such as tetramethylammonium ions as ingredients for zeolite synthesis [1,2]. The application of such structure directors has been extended to a large number of zeolite syntheses [3] leading to over a hundred zeolite structures [4]. The pore openings in these crystalline materials have spanned the ˚ . Because zeolites have range from about 3 to 13 A shown tremendous commercial success in applications including ion exchange, size- and shape-selective catalysis, and separation [5], much research effort has focused on tailoring material compositions and pore sizes to optimize materials properties and to accommodate larger guest molecules. In the search for larger pore materials, a breakthrough was made in the early 1990s when Mobil announced the synthesis of a new family of mesoporous molecular sieves (M41S) that were prepared in surfactant solutions [6–9]. The new class of silicates and aluminosilicates possess ordered arrays of uniform channels that are tens of angstroms in diameter. In the surfactant-templated syntheses, aggregates of surfactant molecules rather than individual molecules fill the space that eventually forms the channels in the porous solids. Since the original publications, hundreds of scientific papers as well as several review articles have appeared describing research on ordered mesoporous sieves and related mesostructured materials. The compositional range for mesoporous materials has

II.

TEMPLATING OF SILICATES AND ALUMINOSILICATES WITH CATIONIC SURFACTANTS UNDER BASIC CONDITIONS

During their studies of surfactant-clay intercalation compounds, researchers at Mobil discovered structures with unexpected hexagonal pore arrays. They soon determined that similar structures could be obtained with a variety of silica and alumina sources under alkaline hydrothermal conditions when a cationic alkylammonium surfactant was present. Depending on reaction conditions, they observed silicate or aluminosilicate structures with hexagonal arrays of uniform channels (MCM-41), cubic structures (MCM-48), or lamellar structures (MCM-50). The new class of materials was labelled M41S. Their structures are shown in Fig. 1. MCM-41 consists of amorphous silicate walls (approx˚ thick) [10] that surround cylindrical surimately 8–9 A factant micelles. On the basis of transmission electron microscopy (TEM), infrared (IR), nuclear magnetic resonance (NMR), and Raman data, Davis et al. [11] concluded that the walls of MCM-41 exhibit a broad range of T — O — T bond angles, resembling amorphous silica or aluminosilicates rather than crystalline zeolites in 819

Synthesis of Porous Inorganic Solids

821

FIG. 2 Proposed mechanisms for the formation of MCM-41 [7,22,31]. (a) Liquid crystal templating. (b) Assembly of silicacoated cylindrical micelles. (c) Cooperative nucleation and mesostructure formation. In each mechanism, condensation of the inorganic framework can continue after the surfactant-inorganic mesophase has formed.

celle concentration (cmc, the temperature and concentration at which finite organized ordered arrays can first be detected). Silicate species can then be induced to polymerize by lowering the pH or increasing the temperature [25]. Under these conditions, one observes a surfactant-poor isotropic phase and a surfactant-rich liquid crystal phase. It should be noted that the shapes of the surfactant micelles are not directly related to the shapes of the inorganic-organic composite because of the additional interaction forces introduced by the inorganic component. In spite of its limited applicability, the LCT scheme has been useful to illustrate the synthetic and structural concepts involved in the M41S system. An alternative mechanism was also proposed by the Mobil group, suggesting that the presence of the inor-

ganic species mediates the ordering of the surfactant or of silicate-encased micelles. Once an ordered array was established, subsequent processing permitted removal of the surfactant and further stabilization of the walls [7]. In support of this mechanism, Davis et al. suggested the following formation pathway, based on 14N NMR spectra of gels obtained in situ during the synthesis of MCM-41 and MCM-48. In those measurements a single isotropic line was observed and assigned to the presence of rapidly rotating rodlike micelles. These randomly ordered micelles are coated with two or three monolayers of charge-balancing silicate species (Fig. 2b). Partial condensation of the silicate oligomers leads to spontaneous organization of the cylinders into hexagonal arrangements. Unlike the formation of binary surfactant-water systems, this is a kinetically

822

controlled process. The silicate precursors cannot condense completely as charged SiO⫺ species are required to balance the charge on the surfactant molecules. However, further condensation occurs during calcination [11,22,23]. Klinowski and coworkers [26] investigated the role of surfactant micelles as templates and as catalysts in the hydrolysis and polymerization of tetraethylorthosilicate. They determined that MCM-41 can be synthesized only when the cmc is met or exceeded (cmc = 0.0013 M for CTACl in water [27]). Their results also support a model in which individual micelles are initially formed and coated with silicate anions; the silicacoated micelles then self-assemble into the solid mesophase [28]. Under certain conditions a layer mechanism was observed, involving a lamellar-to-hexagonal phase transformation [10]. In this proposed mechanism, silicate oligomers initially function as multidentate ligands with a high charge density that effects a lamellar organization of the surfactant. As polymerization of the silica progresses, the reduced charge density of the growing silica polyanions increases the average headgroup area of the surfactant assembly, inducing a lamellar-to-hexagonal phase transformation. However, a layered intermediate is not always observed [29]. It was later shown by in situ x-ray diffraction (XRD) measurements that the lamellar-hexagonal phase transition depends on the pH of the reaction mixture and that it proceeds via dissolution of the lamellar phase [30]. The lamellar phase was observed at high pH (⬃13). Upon acidification, the charge density on the silicate oligomers was reduced and the lamellar phase dissolved. At a pH close to 11.6 the hexagonal phase appeared. The hexagonal phase became most ordered at pH 10.7. The formation mechanism may be different under different synthesis conditions. Even though extensive surfactant-water phase diagrams have been developed, it was determined early on that surfactant-inorganic mesostructures could form under conditions where the surfactant alone would not form a liquid crystal phase (but above the cmc, i.e., when micelles are present) or silicate alone would not condense [10]. Stucky and coworkers pointed out that the electrostatic interaction and the matching of charge density at the surfactantinorganic interfaces should govern the cooperative assembly of the mesostructure [10,25,31,32]. Tailoring of the structure (for example, adjustment of curvature) is possible by adjusting the electrostatic interactions, other bonding interactions, and charge density matching at interfaces. The mechanism formulated by

Stein and Melde

Stucky’s group [16,31,32b] and confirmed by others [33] involves the following processes (Fig. 2c): 1.

2.

3.

Multidentate binding of oligomeric silica polyanions (three to eight Si atoms) to the cationic surfactant results in strong surfactant-silica interactions. An example of such a multiply charged anion is the double four-ring (D4R) oligomer. The polyanions replace monovalent anions (OH⫺, Cl⫺, Br⫺) by ion exchange. The new ion pairs can reorganize themselves into mesophases with liquid crystal structures, the nature of which depends on the composition of the mixture, temperature, pH, and reaction time [16]. Because different silicate oligomers can have different charges, they interact differently with the surfactant headgroups. Preferential silicate polymerization at the interface region due to the high concentration of silicate in this region, assisted by partial screening of negative charges by the cationic surfactant. Charge density matching between the surfactant and the silicate during the condensation process. Before condensation, the surfactant-silica composite has the characteristics of a salt; it can be redissolved when placed in distilled water [31]. The condensation process leads to a reduction of the framework charge and to the formation of a rigid ⫺ structure: — — → — — Si — O ⫹ HO — Si — — Si — O ⫺ — — Si — ⫹ OH . As the charge density on inorganic precursors decreases during condensation, some surfactant molecules have to leave the composite structure.

The formation of MCM-41 has been studied by several in situ methods. In a combined small-angle x-ray scattering (SAXS) and cryo-TEM study, Regev [34] observed a transition of spherical to elongated micelles as TEOS was added to a CTACl-NaOH-water mixture. He observed the formation of 50-nm-diameter ordered clusters of elongated micelles, which were ‘‘wrapped’’ with a silica film. During silica polymerization, as the formation of MCM-41 proceeded, the silica layer penetrated the cluster arrays and reduced the correlation length between micelles until eventually a hexagonal phase with ordered arrays of 5-nm pores was obtained. In an in situ ATR-FTIR study carried out with colloidal silica, sodium aluminate, and CTAOH above the critical micelle concentration and temperature, the investigators observed a gradual and irreversible loss of the colloidal silica starting material as an intermediate silicate phase was produced [35]. The silicate mesophase was formed when a temperature of 120⬚C was reached. The surfactant tails exhibited less order with increasing


823

temperature, whereas the headgroup configurations became more ordered. The increased headgroup ordering was attributed to loss of hydration water in the headgroup region, decreased average headgroup spacing upon exchange of hydrated OH⫺ ions with silicate anions, and headgroup-counterion interactions. The IR study also revealed that at room temperature the silicate starting material is largely the double four-ring octamer (Si8O8⫺ 20 ), which decomposes to low-molecular-weight oligomers upon heating. The silicate polyanions present at pH > 12 reduce repulsions between cationic headgroups by forming multidentate interactions with the headgroups. As a result, the average headgroup area becomes smaller. Klinowski and coworkers [26] pointed out the catalytic action of the surfactant. In the absence of surfactant, TEOS and water are initially immiscible. As TEOS is hydrolyzed a homogeneous solution is formed within 1 h, but precipitation of solid amorphous silica products can require days. When TEOS hydrolysis is instead carried out in a surfactant solution, hydrolysis and precipitation of a surfactant-silica mesostructure can occur in a few minutes. Klinowski et al. [26] determined that in the presence of a cetyltrimethylammonium chloride or hydroxide surfactant the rate of silicate polymerization was 2000 times faster than without the surfactant. They proposed that the cationic surfactant can concentrate hydroxide ions at the surfactant-silica interface via halide ↔ hydroxide exchange, thus promoting the hydrolysis and condensation rates. B.

Molecular Templating Versus Supramolecular Templating

Beck and coworkers [13] explored in detail the ability of Cn H(2n⫹1)(CH3)3N⫹ (Cn, n = 6, 8, 10, 12, 14, and 16)

surfactants to serve as structure-directing agents or templates for the formation of mesoporous as well as microporous molecular sieves. They carried out hydrothermal reactions with surfactant halides and sodium silicate at constant surfactant/silica mole ratios of 0.5, 11 wt% surfactant concentration, and pH 10. They investigated varying alkyl chain lengths and temperatures and, depending on these parameters, obtained either amorphous, zeolitic, or mesoporous structures. Their results are summarized in Table 1. It is interesting to note that for the C12 series, the surfactant was present and intact in both the mesoporous and the zeolitic phases; solid-state NMR evidence indicated that the surfactant molecules constituting micellar arrays within the mesoporous structures were more mobile than the isolated surfactant molecules confined in the smaller zeolite pores. Although multiple zeolite phases were sometimes present, zeolitic and mesoporous phases were never observed together, suggesting different formation pathways for these phases. Based on their experiments, Beck and coworkers proposed the mechanistic pathways for the synthesis of micro- and mesoporous materials illustrated in Fig. 3. C.

The Cubic MCM-48 Phase

The cubic MCM-48 phase consists of two independent, interwoven networks of mesoporous channels (space ¯ group Ia3d) [10,36]. The bicontinuous structure has been described as consisting of a single sheet that winds through space following a gyroid surface [37]. This phase has been studied less than MCM-41 because the synthesis appears to be less reliable [38]. Although MCM-48 can be formed over a wide range of surfactant/silicon ratios (from 0.12 to 0.8), successful product formation depends critically on the source of silica em-

TABLE 1 Products Obtained from Surfactant Templated Syntheses for Varying Surfactant Chain Lengths and Temperaturesa Cn H2n⫹1(CH3)3N⫹ n 6 8 10 12 14 16 a

Temperature 100⬚C

150⬚C

200⬚C

Amorphous Mesoporous Mesoporous MCM-41 MCM-41 MCM-41

ZSM-5 ZSM-5 Mesoporous Mesoporous MCM-41 MCM-41

ZSM-5 ZSM-5, ZSM-48, dense phase ZSM-5, ZSM-48, dense phase ZSM-5, ZSM-48, dense phase Amorphous and zeolitic Amorphous

In this table, ‘‘mesoporous’’ refers to structures that showed one or two broad diffraction peaks in the X-ray diffraction pattern, but were less ordered than true MCM-41. Source: Adapted from Ref. 13.

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thesized MCM-48 than for MCM-41, indicating a larger number of surface hydroxyl groups in the cubic phase [46]. A synthesis of micrometer-sized MCM-48 single crystals (truncated rhombic dodecahedra) was described by Ryoo and coworkers [47]. In this preparation, alcohol (MeOH, EtOH) was employed as an additive for mesophase control in the sodium silicate/ CTAB solution. The mixture was heated to 100–130⬚C in a sealed autoclave to prevent loss of alcohol. If alcohol was allowed to evaporate during the synthesis, a disordered phase was obtained, indicating that the alcohol affects the structure of the surfactant-inorganic composite during condensation. A lamellar phase was obtained with excess alcohol. D.

FIG. 3 Proposed mechanistic pathways for the formation of microporous and mesoporous materials. (Adapted from Ref. 13.)

ployed, the initial pH, temperature, and synthesis time [7,10,17,33,38–44]. Cubic phases can be favored by using surfactants with larger headgroups to increase curvature [18]. During the synthesis, several phase transitions can occur. For example, in a synthesis based on TEOS as the silicon source, with CTAB at pH 11.8 and 373 K (1 TEOS: 0.23 Na2O: 0.55 CTAB: 112 H2O), first a disordered tubular mesophase is formed, which transforms to a layered phase, then slowly to a cubic MCM-48 mesophase, and finally to another layered phase [38]. It is therefore important to time the synthesis of MCM-48 correctly to avoid production of the second layered phase. In a TEOS-based synthesis with a sufficient amount of surfactant, MCM-48 was obtained in dilute base solution, whereas a lamellar MCM-50 phase was produced at high base concentration (Na2O/H2O = 0.049) [45]. It was proposed that the cubic phase is favored by interaction of the surfactant with monomeric silicate precursors, whereas more condensed silicate oligomers produce the layered phase. 29Si MAS NMR showed a significantly higher number of Q3 species for as-syn-

Phase Transitions in Systems with Strong Interface Interactions (SⴙIⴚ)

When considering the cooperative self-organization of organic surfactant molecules and inorganic solution species, one has to take into account multiple bonding interactions (electrostatic, hydrogen bonding, covalent bonding, van der Waals forces) and multiple interfaces (inorganic-inorganic, organic-organic, organic-inorganic, precursor-solvent) [40]. The self-assembly process is dominated by surfactant behavior if condensation of the inorganic component is negligible. On the other hand, if the inorganic component has strong interactions (e.g., fast polymerization/condensation), the structure is mostly determined by this component. The interface charge matching of amphiphilic surfactants with inorganic species controls the assembly; these interactions must be balanced to control the structure. Even though the phase diagrams of surfactant-inorganic-solvent systems differ from those of pure surfactant-solvent systems, a comparison has proved valuable [40]. For classical surfactant-solvent systems the liquid crystal phases are determined by the effective surfactant ion pair packing parameter, defined as g = V/a0 l (V = total effective molecular volume of hydrophobic surfactant chains plus any cosolvent species present, a0 = effective surface area of surfactant headgroup at the hydrophilic-hydrophobic micelle aggregate interface, l = kinetic surfactant tail length) [48]. The value of g depends on a variety of factors, including the number of carbon atoms in the surfactant tail, the degree of chain saturation, the charge of the polar headgroup, the size of the headgroup, the ionic strength of the solution, pH, and temperature. The relationship is strictly valid only for dilute solutions where interactions between aggregates can be neglected. Nevertheless, an investiga-


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tion of a large number of surfactants with varying tail lengths, headgroup sizes, and charges indicated that the molecular packing parameter model can be used to a first approximation to predict inorganic-surfactant composite structures [49]. Micellar shapes for cationic surfactants in the dilute micellar concentration regime were compared by Manne et al. [50]. They are summarized in Table 2. The phase (hexagonal or lamellar) of the mesostructure is dependent on the pH and on the surfactant/silicate ratio [10,17]. Lamellar structures are favored when headgroups can pack tightly, for example, with double chain surfactants. Mixtures of charged and neutral surfactants with similar chain lengths also favor lamellar structures [41]. Curvature increases when polar headgroups occupy a larger surface area, and when g is less than 1/3, globular aggregates are preferred [24,51,52]. The headgroup area can be increased, for example, by addition of water, which decreases the charge density of the inorganic region. However, with neutral amine surfactants the phase responds differently to the water content in the reaction. At a higher water content (1 hexadecylamine: 1 TEOS: 200 H2O) a lamellar product is obtained, whereas at a lower water content (1 hexadecylamine: 1 TEOS: 60 H2O) the product is hexagonal [53]. In addition to dilution, the mesophase can be controlled by the surfactant-to-silicon ratio. Beck et al. [7] observed hexagonal MCM-41 with surfactant/Si ratios ¯ was obless than 1. The cubic form (MCM-48, Ia3d) tained with surfactant/Si ratios greater than 1. With even greater surfactant/Si ratios the lamellar phase (MCM-50) was produced, which contained slightly ˚ ) than MCM-41 (8–9 A ˚ ) [10]. thicker walls (10–11 A If the structure remains flexible enough during polymerization, the reduction in framework charge density may lead to phase transitions. Phase transitions that have been observed with different surfactants include

TABLE 2

Morphologies of Surfactants and Surfactant-Silicate Aggregates in Dilute Aqueous Solutionsa

Cationic surfactant mesophase Asymmetric gemini Conventional alkyltrimethylammonium Symmetric gemini, s ⱖ 4 Symmetric gemini, s = 2 Conventional dialkyldimethylammonium a

lamellar to MCM-41, MCM-41 to lamellar, MCM-41 to MCM-48, and MCM-48 to lamellar. These phase transitions are believed to occur in the solid phase rather than in solution [54]. A phase transformation from hexagonal to cubic was exploited in a rapid MCM-48 synthesis [42]. Using TEOS as the silicate precursor with cationic surfactants under basic conditions, the alkoxide was permitted to hydrolyze under rapid stirring for 1–3 h at 35–40⬚C, resulting in a hexagonal intermediate phase. The mixture was subsequently heated at 150⬚C for 3–5 h in a closed autoclave, producing well-ordered MCM-48 phases that were stable to calcination. It was shown that ethanol (hydrolysis product of TEOS or added cosolvent) was necessary to permit the phase transformation. The proposed role of ethanol as cosolvent was to increase the surfactant packing parameter g by increasing the effective surfactant volume. Cosolvents can be added to reaction mixtures to influence the product phase. Nonpolar cosolvents, which associate most strongly with hydrophobic surfactant tails, result in swelling of micelles. Their use in controlling the pore dimensions of MCM-41 is discussed later. Polar cosolvents (e.g., ethanol or methanol) interact more strongly with the headgroups or with tail sections closer to the headgroup, leading to increases in the total volume V. Anderson et al. [55] studied the effect of the MeOH concentration on CTAB micellization and on the formation of mesoporous silica. They observed that addition of MeOH led to an increase in cmc for CTAB from 1.3 ⫻ 10⫺3 M for 0 wt% MeOH to 5.5 ⫻ 10⫺2 M for 60 wt% MeOH in 0.22 M NaOH solution. However, the long-range order of the mesoporous silica product decreased as the MeOH concentration increased. Ordered channel arrays formed between 0 and 60% MeOH, in which range the concentration of CTAB exceeded the cmc. At higher methanol content the cmc concentration was not ex-

g

Micelle shape in aqueous solution

Micelle shape in silicate

0.7 cm3/g). The pore sizes are controlled by the length of the cationic surfactant, ˚ for Cn H2n⫹1(CH3)3N⫹ (n = 8– ranging from 18 to 37 A 16) in silicates [7]. Larger pores can be obtained by modifications of the synthesis (see later). Mesostructured materials were obtained under a wide range of conditions. Sources of silicon include sodium silicate, tetramethylammonium silicate, colloidal silica, silica gel, tetraalkylorthosilicates, and oligomeric silica clusters. Aluminum sources include alumina, sodium aluminate, and aluminum sulfate. In syntheses of M41S materials, hydrothermal reactions are carried out with cationic alkylammonium surfac-

Proposed Mechanisms for Formation of MCM-41

Before discussing possible formation mechanisms of the surfactant-inorganic composite materials, we need to define the terms ‘‘mesostructured’’ and ‘‘mesoporous.’’ ‘‘Mesostructured’’ phases possess periodicity on ˚ scale. As in pure surfactant chemistry, hexa 20–500 A agonal, lamellar, and gyroid cubic phases may be found in surfactant-inorganic composites, and transformations are possible, especially if the inorganic component is not yet highly condensed. If the surfactant template can be removed to obtain accessible pores with periodicity ˚ scale, one obtains a ‘‘mesoporous’’ on the 20–500 A material. The earliest proposed mechanism for the formation of MCM-41 was a liquid crystal templating (LCT) mechanism (Fig. 2a), in which a hexagonal array of rodlike micelles formed initially, before the anionic inorganic precursors assembled in the water region between cylindrical micelles (with positive surface charge) and condensed to form silica walls around the liquid crystal template [6]. In this mechanism the liquid crystal phase is intact before silicate species are added. Davis and coworkers [22,23] followed the synthesis of MCM-41 by in situ 14N NMR spectroscopy, a technique that can detect the presence of the hexagonal phase. They did not detect this phase, thus disproving the LCT mechanism, at least for common reaction conditions [22,23]. True liquid crystalline properties may, however, exist at pH ⱖ 12 and temperatures below 100⬚C, when anionic silicate species remain unpolymerized in aqueous solutions [24]. For silicate-surfactant mesophases to form, the surfactant concentration in the precursor organic solution must be above the critical mi-


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TABLE 4 Some Surfactant Types Used in the Synthesis of Inorganic Mesostructures Cationic

Anionic

Neutral

Nonionic

Zwitterionic

Gemini

Double-headed

Organosilane

Functionalized

Mesoporous silicates with larger mesopores and thicker walls than M41S materials have been synthesized by employing nonionic polyethylene oxide (PEO) oligomeric surfactants or poly(alkylene oxide) block copolymers in acid media [65,66]. Silica structures ¯ were obtained with cubic Im3m (SBA-16), cubic ¯ (SBA-11), 3D hexagonal (P63 /mmc) (SBA-12), Pm3m 2D hexagonal (p6mm) (SBA-15), and lamellar (L␣) symmetries. Large d100 spacings ranging from 104 to ˚ were observed in the hexagonal form synthe320 A sized in the presence of triblock copolymers (PEOPPO-PEO) [67]. Silica wall thicknesses ranged from 31

˚ . The pore size and wall thickness can be adto 64 A justed by varying the heating temperature and reaction time. With their thicker walls, these porous solids exhibited higher hydrothermal stability in boiling water than MCM-41. In syntheses employing amphiphilic block copolymers consisting of an apolar polystyrene block and a polar polyethylene oxide block, the channels in the mesoporous product were not highly ordered [68]. In block copolymer syntheses, mesoporous silica formed in acid only (HCl, HBr, HI, NHO3, H2SO4, H3PO4) but not in base. The pH must be 0.8), indicative of textural, or interparticle, mesoporosity. The textural mesoporosity was a consequence of the fine particle morphology (150 h [110]. Hydrogen bonding is believed to be the primary interaction force between the surfactant molecules and the inorganic framework walls during the assembly pathway. The stability of the bicontinuous pore structures was attributed to the high degree of cross-linking in the silicate framework (Q4/ Q3 ratios were 6.2:1) and the thickness of the walls. Salts (NaCl, KCl, sodium acetate, EDTA sodium salt) added to the synthesis mixture (base synthesis) can also improve the hydrothermal stability of MCM41 in boiling water, although the hydrothermal stability may also decrease, depending on the type and relative amount of salt added to the reaction mixture [111]. For example, with 3 mol NaCl per mol CTACl, the resulting MCM-41 product is hydrothermally stable in boiling water for 12 h, whereas MCM-41 synthesized without added salt completely loses its structure with this treatment. Increased stability was also observed during calcination in oxygen with no structural loss at 960⬚C. It is believed that the salts affect the structure of water and therefore the local structure of the surfactant-silicate composites during hydrothermal synthesis. The greater stability results in part from a higher degree of condensation (greater Q4/Q3 ratio in the product) when salt was added to the mixture. IX.

MESOPOROUS MATERIALS DERIVED FROM KANEMITE AND OTHER LAYERED PRECURSORS

A different strategy of synthesizing mesoporous silicates was first reported by Yanagisawa et al. in 1990 [112] and has been more fully developed by Inagaki and coworkers [113–120]. The precursor in this synthesis was kanemite (NaHSi2O5 ⭈ 3H2O), a layered poly˚ thick, single-layered sheets silicate composed of ⬃4 A of SiO4 tetrahedra. Yanagisawa and coworkers prepared a mesoporous structure by intercalation and subsequent condensation reactions. Surfactant-kanemite complexes were formed by cation exchange, where long-chain alkyltrimethylammonium ions replaced interlayer sodium ions, a process that had been previously demonstrated by Beneke and Lagaly [121] for a number of organic cations. During this process, the silicate components rearranged themselves around the surfactant, forming what appeared to be a wormlike channel structure. Surfactant removal by calcination between 700 and 1000⬚C resulted in the formation of mesoporous solids with surface areas of ⬃900 m2/g. As in the synthess of MCM-41, the pore sizes were controllable by altering

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the chain length of the surfactants. The calcined materials were named FSM-n, where n refers to the carbon chain length of the organic species used in the synthesis; for example, FSM-16 refers to the product obtained by calcination of a hexadecyltrimethylammonium-kanemite complex [122]. These mesoporous structures were less ordered and had significantly smaller pore volumes than MCM-41 [123]. However, by raising the pH during the initial surfactant ion exchange from 8.5 to 11.5 or 12.3, products with greater hexagonal regularity, narrow pore size distributions, and pore volumes comparable to those of MCM-41 were obtained [114–116]. Although the wall thickness of FSM-16 appeared to be the same as that ˚ after calcination or after extraction of MCM-41 (⬃8 A of the surfactant with acid) [124], FSM-16 exhibited higher thermal and hydrothermal stability than MCM41. FSM-16 was thermally stable to at least 900⬚C. It has been suggested that the improved stability arose from a higher degree of condensation in the silica walls; the Q4/Q3 ratio based on 29Si NMR was 88:12 in FSM-16 compared with 45:55 in a typical MCM41 sample. Based on water vapor adsorption isotherms, the surface of FSM-16 was hydrophobic during the first exposure to water vapor [118]. The mechanism of FSM-16 formation appears to be different from that of MCM-41 [29,116,123–125]. Since the first report of the kanemite-based synthesis, the mechanism has been studied in detail by XRD, 29Si

Stein and Melde

MAS-NMR spectroscopy, HREM, SEM, adsorption, studies and rheology measurements. It is shown schematically in Fig. 4. In the first step of the synthesis, the cationic surfactant is intercalated between kanemite single-layer sheets, displacing interlayer sodium ions. As the previously charged surfactant headgroups interact with the anionic silicate layers, the kanemite layers swell. The pH of the suspension depends on the kanemite-to-surfactant solution ratio (K:S). Initial pH values of 9.0 and 10.8 have been measured for K:S ratios of 1:150 and 1:20 (w/w), respectively [124]. These increase by about 0.5 pH units during the exchange reaction. The extent of surfactant incorporation increases with pH. At this stage of the synthesis (FSM-A), the XRD and 29Si NMR data indicate a transitional state from kanemite to a hexagonal phase. During this early period, in situ XRD also reveals an intermediate lamellar phase [29]. In the optimized FSM-16 synthesis, the kanemite-surfactant complex is then redispersed in water and the pH adjusted to a value of 8.5 (FSM-B). 29Si NMR measurements indicate that condensation between silicate units occurs during this stage. Whereas the kanemite precursor exhibits only a sharp Q3 resonance, the intercalated complex shows an additional Q4 peak, which grows in intensity with further heat treatment. The intensity ratio Q4/Q3 increases with decreasing pH, indicating that condensation between SiO4 sheets of kanemite occurs during lower pH treatment. Based on XRD and HREM

FIG. 4 Proposed mechanism for the transformation of kanemite to the hexagonal FSM-16 phase [115,116,124]. See text for explanation.


information, the layered structure is transformed into a more three-dimensional porous structure with pores that are initially wormlike and varying in length. Whereas originally a sheet-folding mechanism was proposed, more recent studies indicate that the sheets are most likely broken down into smaller units (especially at high pH) and rearrange locally around the micellelike surfactant aggregates, forming the pore structure. The morphology of the samples does not change from that of the starting kanemite in the preparations carried out at lower pH, but it does change at high pH, indicating that partial dissolution and rearrangement of silicate species occur at higher pH. To prepare pure FSM-16, it is necessary to remove the fraction of the silica precursor that dissolves completely at higher pH values [116]. Condensation of the walls progresses when the sample is heated to 70⬚C for 3 h (FSM-C) and longer (FSM-D). The extent of conversion from layered structures to more three-dimensional structures increases with exchange time. During the heating process small hexagonal domains are observed; these domains merge with further condensation [125]. After subsequent calcination to remove the surfactant, a highly ordered hexagonal structure is formed (FSM˚ 16). The wall thickness appears to increase from 4 A ˚ (a double layer) upon (a single silicate layer) to 8 A calcination. Even at the earlier stages, calcination of the kanemite-surfactant complex leads to further wall condensation (an increase in the Q4/Q3 ratio) and to the formation of a mesoporous product. The order of this product increases in the series FSM-A through FSMD. After calcination, even the layered structures or mixed layered-mesoporous phases such as FSM-A, are converted into structures with a single low-angle dif˚ [124]. The layered structures disfraction line at 47 A appear most likely from structural collapse during the calcination, while the mesopores remain intact. The role of the surfactant in the FSM-16 synthesis is notable. The intercalation reaction is carried out at a much lower surfactant concentration than that used in the original MCM-41 synthesis: 3.2 wt% compared to 26 wt%. This concentration is still higher than the cmc of CTACl in aqueous solution at 25⬚C (0.05 wt%, 1.4 mM). However, no solution structure has been detected by rheological measurements at the surfactant concentrations used in the layered silicate system [123]. The exchange most likely involves free cation chains rather than micellar aggregates. Surfactant molecules remain intact after intercalation [123]. It has been suggested that the intercalated surfactant molecules reorganize from a bilayer structure to cylindrical micellelike aggregates as they interact with silicate sheet fragments

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[124]. This hypothesis is supported by the observation that syntheses employing small molecules (e.g., tetramethylammonium chloride) that do not form micelles do not result in mesoporous products [120]. For the most ordered structures, a minimum amount of surfactant must be present in the kanemite-surfactant complex. The degree of cation exchange and thus the surfactant/silica ratios in the complex increase with increasing pH. Hence the poorer hexagonal structure of complexes prepared at pH 8.5 might be attributable to an insufficient exchange ratio of surfactant ions. Removal of the surfactant is possible not only by calcination but also by extraction with acid, where the lost positive charges are compensated by protons. Inagaki et al. [120] examined readsorption of surfactants in FSM-16. They found that FSM-16 adsorbed many types of cationic, anionic, and nonionic surfactants, especially alkyltrimethylammonium (maximum amount 60% of the original template). The amount of alkyltrimethylammonium adsorbed increased steeply at the cmc of the surfactant. It appeared that micellelike surfactants were adsorbed more readily than molecular ones. Acidic mesoporous structures were obtained by incorporating aluminum during different stages of the FSM-16 synthesis. In zeolites, surface acidity is attributable to isomorphous substitution of Al3⫹ for Si4⫹. Treatment of the hexadecyltrimethylammonium-kanemite complex with aqueous aluminum trichloride followed by calcination resulted in substitution of some tetrahedral aluminum into the framework, but extraframework octahedral aluminum was also present. As in the case of aluminosilicate MCM-41, the structural order was lower than in pure silica samples. With a surface area of 600 m2/g, the aluminum-substituted FSM-16 had an acidity comparable to that of amorphous silica-alumina but only half that of ZSM-5 with the same Al2O3 contents [113]. The acidity could be increased to ⬃0.7 times that of ZSM-5 by adding aluminum in the form of Al(NO3)3 ⭈ 9H2O or NaAlO2 during the synthesis of the kanemite precursor [119]. The resulting crystalline layered sodium silicates with Si/Al ratios between 2.5 and 100 were then transformed into mesoporous aluminosilicates by surfactant intercalation and calcination. These products contained only tetrahedral aluminum and exhibited structural regularities higher than those of MCM-41 materials with the same Si/Al ratio. With Al(NO3)3 ⭈9H2O, cristobalite was formed as a side product, but not with NaAlO2. The intercalation strategy has also been examined with other layered precursors, such as magadiite (mul˚ thick layers) tilayered silica) [124] and kenyaite (12 A

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[123]. However, mesoporous structures were not obtained in those instances. It appeared important that the precursor layers were easily deformable or easily broken up into smaller units, and hence single layers were preferred. Other clay minerals that have been studied as precursors for mesoporous silicates include sepiolite, hectorite, vermiculite, kaolinite, and chrysotile [120]. High-surface-area mesoporous products with varying degrees of pore regularity were formed from these precursors. The understanding of the synthesis mechanism, although not complete, has reached a level where product optimization for different applications has become possible. A number of applications for FSM-16 have been studied. These include oxygen adsorption by a porphyrin/FSM-16 complex [126] and the catalytic and magnetic properties of nanostructured Pt clusters in the mesopores of FSM-16 [127]. The favorable thermal stability and the possibility of forming mesoporous aluminosilicates with greater acidity and order than similar MCM-41 materials make FSM-16 a promising material for applications where these characteristics are critical, including catalytic processes. X.

COMPOSITIONS CONTAINING NONSILICON HETEROATOMS

Mobil’s original work described mesoporous sieves with silicate and aluminosilicate compositions [7]. Incorporation of aluminum atoms in the walls of aluminosilicate MCM-41 was confirmed by two-dimensional solid-state NMR spectroscopy [128]. Early patents suggested that other elements could also be incorporated in the material [8]. Over the years, many elements have been included in mesoporous materials by doping, grafting, and direct syntheses. Doping of mesoporous silica with heteroatoms other than aluminum is possible but often permits only very small loadings. Various metals, including Al [7,128– 138], Ti [139–143], V [144,145], B [143,146,147], Mn [39,148], Ga [146,149], Sn [150], Y [150], La [150,151], Ce [151], and Fe [146,150,152], have been incorporated in mesoporous silicates during the hydrothermal synthesis. Except for aluminum, the heteroatom content is typically much lower than the silicon content. This topic has been covered in a review [153]. Grafting of metals to surface hydroxyl groups of mesoporous sieves has been carried out using silane-coupling agents or reactive ligands. These methods have also been reviewed [154]. Using direct syntheses, Stucky and coworkers prepared a large number of mesostructured metal oxides,

many of which formed lamellar phases [18,31]. These include a zinc phosphate mesophase (lamellar), an alumina mesophase (lamellar), and mesophases of Pb2⫹, Fe2⫹, Fe3⫹, Mg2⫹, Mn2⫹, Co2⫹, Ni2⫹, Zn2⫹, Al3⫹, and Ga3⫹, obtained with various anionic surfactants (all lamellar, although with Pb2⫹ a hexagonal mesophase was obtained). Many of these structures are probably saltlike and conversion to condensed inorganic structures requires special treatment (see, for example, the section on cluster-surfactant mesostructures later). When anionic sulfonate or phosphate surfactants are employed, they compete with oxide/hydroxide groups for coordination. Thus their anionic polar headgroups can be incorporated into the inorganic framework [18,31]. Some other mesostructured metal oxides that have been reported include oxides of W [155–157], Mo [156,157], Sn [158,159], Zr [32b,160–164], V [156,165,166], Hf [167], Al [20,64,168,169], Mn [170], Nb [78,79], Ti [82], Ta [83], Sb [18,31], and Fe [171]. Examples of mesostructured metallophosphates include Ti [82], Zr [84,160,163,172,173], Al [174–179], Ga [174], and V [166,180,181]. In many of these compositions the surfactant could not be removed without loss of the mesostructure. Some notable exceptions are oxides of Zr, Al, and Ni and phosphates of Ti, Zr, and Al. In a mesostructured titania sample the surfactant could be removed by calcination after stabilization with phosphoric acid [32b]. The pore size distribution remained narrow; however, the pores were disordered. Syntheses employing block copolymers as templates are also amenable to a variety of mesoporous metal oxides with ˚ and relatively thick amorphous pores up to 140 A framework walls [69]. TiO2, ZrO2, Al2O3, Nb2O5, Ta2O5, WO3, HfO2, SnO2, and mixed oxides have been synthesized using amphiphilic poly(alkylene oxide) block copolymers (EO20PO70EO20) as structure-directing agents together with inorganic salt precursors in nonaqueous solution. The block copolymers are believed to complex to the inorganic metal oxide species by a chelating process. Both two-dimensional hexagonal ¯ ) mesostructures and three-dimensional cubic (Im3m were obtained by this method. Although lamellar phases are often observed for aluminophosphate-surfactant mesostructures (synthesized from pseudoboehmite alumina, phosphoric acid, and neutral amine surfactants) [177], the layers need not be planar. Chenite et al. [176] observed coaxial cylindrical bilayers of inorganic-surfactant phases. These structures resemble vesicles, such as those found in aqueous solutions of phospholipids. Ozin and coworkers [175,182,183] observed hierarchichally structured aluminophosphates in syntheses using non-


aqueous glycol-based solvents or glycol-water cosolvent systems. The lamellar aluminophosphates with alkylammonium surfactant bilayers form millimeter-sized spheroidal particles or particles with other —frequently regular [90]—shapes, often with intricate surface patterns. Bilayer and vesicle templating is believed to control the surface architecture in these materials. The glycol cosolvent is proposed to be responsible for inducing bilayer curvature. Some of the product shapes have been compared with radiolarian and diatom microskeletons. Hollow multilayer aluminophosphates were formed from phase-separated water–decylammonium dihydrogenphosphate (DDP)–tetraethylene glycol (TEG) or air-DDP-TEG liquid crystal microemulsions [90]. A modification of this synthesis has been applied to the preparation of a composite of hydroxyapatite and calcium dodecylphosphate lamellar phase as a bone mimetic system [184]. Because surfactant removal from lamellar phases normally does not result in mesoporous products, few applications of lamellar phases have been pursued. However, these phases may be useful to generate inorganic-organic composite mesostructures. These are now starting to be investigated. One example is an iron oxide–surfactant composite that is of interest for magnetic materials [171]. This phase consists of surfactant bilayers separated by iron oxide layers. The material is produced by controlled precipitation and hydrolysis of FeII or FeIII cations in aqueous solution. The iron oxide ˚ (one layer thickness can be varied between 3 and 20 A to six layers of iron–iron oxide) by adjusting the hydrolysis and solubility of iron oxide via redox chemistry and pH control. When only one or two layers are formed, the structures are surfactant salts; with three to six layers they appear to consist of cross-linked iron oxide layers separated by surfactant bilayers. XI.

CLUSTER-SURFACTANT MESOSTRUCTURES

During investigations of a variety of transition metal oxide precursors for the surfactant-based synthesis of mesostructures, Stein et al. found that tungsten, vanadium, niobium, and molybdenum oxides formed cluster-surfactant salts rather than connected open frameworks [155,185]. For example, a hydrothermal reaction of sodium metatungstate with cetyltrimethylammonium hydroxide produced a TEM image and powder x-ray diffraction patterns that were superficially similar to those of mesoporous silicates. However, closer examination revealed that in this system, the precursors formed thermodynamically stable anionic Keggin ions,

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leading to the salt (C19H42N)6(H2W12O40). These are very stable species and show little tendency to condense in the surfactant-salt structures. Hence, any attempt at removing the organic ‘‘template’’ resulted in dense WO3⫺x phases. Other salts of anionic metal oxide clusters with cationic surfactants that have been studied include [C12H25N(CH3)3]6(H2W12O40)⭈xH2O (a monoclinic structure), as well as salts composed of alternating metal oxide and surfactant layers, [C12H25N(CH3)3]0.5(MoO3.25) and [C12H25N(CH3)3]2/3V2O5.33 ⭈ H2O [156]. The surfactant templates could not be removed in any of these samples without destroying the mesostructures. A single-crystal study of a lamellar decavanadate cluster-surfactant composite (DTA4H2V10O28 ⭈8H2O) confirmed that this material consisted of discrete V10O6⫺ 28 clusters separated by long-chain cationic surfactant molecules (dodecyltrimethylammonium, DTA) [186]. The surfactants were tilted with respect to the normal of the plane and antiparallel to each other. The clusters were not directly bonded to each other but joined via hydrogen bonding from water molecules to form inorganic layers. Cationic clusters of the type MO4Al12(OH)24(H2O)7⫹ 12 (M = Al or Ga) (denoted as Al13 or GaAl12) readily precipitate as ordered salts with anionic surfactants, including sodium dodecyl sulfate (SDS), cetylphosphate, and dodecyl benzenesulfonic acid (DBSA) [174]. All of these salts are layered. The cluster-surfactant superstructure is controlled by electrostatic interactions between the clusters and the polar headgroups of the surfactant molecules and by hydrophobic interactions among the surfactant tails. The high charge density on the inorganic clusters is partially screened by the surfactant charges, resulting in a large enough ratio of chain volume to headgroup area for layering. In the case of Al13-SDS salts, the SDS molecules appear to form interpenetrating bilayers. As discussed in an earlier section, for M41S materials the long-range order of the oxide arrangement depends in part on the surfactant concentration. Low surfactant concentrations favor a hexagonal phase, and high concentrations lead to lamellar phases. The situation is different for cluster-surfactant salts. Whereas the dimensions of the Keggin salt depend on the hydrocarbon chain length [155,156], a wide range of surfactant concentrations can lead to the observed structure for a given surfactant. In the Keggin-surfactant gel, the cooperative forces between cations and anions become even more significant than in the silicate gels because of the high charge on a Keggin ion and the strong association of the surfactant molecules with a specific Keggin ion. Charge effects may also be re-

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sponsible for the difference in structures between the tungsten Keggin salt and niobotungstate salts. For example, (H2W12O40)6⫺ clusters form pseudohexagonal salts with cetyltrimethylammonium (CTA) ions, and similar Keggin ions (PW12O40)3⫺ or (H4PW11O39)3⫺ form layered phases with CTA. This structural change is not surprising because only half as many surfactant molecules are associated with the ⫺3 cluster as with the ⫺6 cluster [185]. (The size difference of these anions is relatively small; diameters range from 8 to ˚ .) 11 A In order to investigate the feasibility of converting a cluster-surfactant salt into mesoporous transitionmetal oxide networks, Stein et al. developed a ‘‘saltgel’’ reaction to connect clusters within the salt [155,185]. The principle of the salt-gel reaction is to transform a crystalline array of molecular or low-dimensional building blocks, which are not connected, into a fully connected three-dimensional array by adding a component that forms covalent links between them. The process, shown in Fig. 5, resembles the solgel method except that the precursor phase is already ordered via ionic and/or noncovalent interactions. This method was demonstrated for niobotungstate clusters linked with silicate groups. Similar to the vanadium ⫺ clusters (x = 2, 3, 4) oxide clusters, NbxW6⫺xO(2⫹x) 19 formed layered salts with cetyltrimethylammonium cations. The lamellar salt was reacted with TEOS. The TEOS molecules were absorbed, presumably into the hydrophobic portion of the structure, and could be hydrolyzed to form silica within the salt. It was shown by infrared and solid-state NMR double resonance spectra that the silica was anchored to the clusters via covalent Nb — O — Si linkages. After removal of the surfactant by extraction with HCl-ethanol, high-surface-area mesoporous materials were created, although the final network displayed only weak long-range order. Al13 or GaAl12 cluster-SDS salts could be converted into mesoporous solids by reaction with TEOS to form aluminosilicates [187] or with a buffered phosphate solution followed by acid treatment to synthesize aluminophosphates [174]. In both syntheses it did not appear that the precursor salt was dissolved during the reaction but appeared that the linking groups penetrated the salt structure. During the reaction with phosphate the surfactant/aluminum ratio was reduced from about 0.55 to 0.43. An increase in the ratio of octahedral to tetrahedral aluminum indicated that the clusters disintegrated as an extended aluminophosphate network was formed. Most of the linkages occurred between tetrahedral phosphate groups and octahedral aluminum atoms. The

Stein and Melde

FIG. 5 Principle of the salt-gel method. The diamonds (⽧) refer to charged clusters that form a salt with oppositely charged surfactant molecules (gray area). Linking molecules (⬃), such as TEOS, penetrate the surfactant-cluster salt and form a network with the clusters. Extraction of the surfactant results in a mesoporous product.

layered material was transformed into a nonlayered mesostructure with a pseudohexagonal array of channels. This transformation was related to two effects. First, upon acid addition some of the clusters broke up into smaller fragments that carried a lower positive charge per fragment than the original Al13 clusters. Second, the negative phosphate groups ‘‘neutralized’’ some of the positive charges on the polyoxocations. Thus, they decreased the charge density of the inorganic aluminophosphate region as well as the ratio of chain volume to headgroup area of the surfactant assembly. This resulted in an increased curvature of the inorganic-surfactant interface and the concomitant transformation from a lamellar to a hexagonal phase. The surfactant could be removed by extraction, resulting in open channels with a narrow pore size distribution centered ˚ and a BET surface area of 630 m2/g. This around 17 A product was demonstrated to be a good anion-exchange material with anion-exchange capacities for chromate and several monoanionic and dianionic organic dyes in the range from 1.3 to 1.6 mEq/g [174b].


In reactions of Al13/SDS salts with TEOS, the alkoxide diffused through the cluster-surfactant salt, reacted with the clusters, and transformed the layered precursor into a nonlamellar mesostructured material with a surface area of 431 m2/g [187]. Although the resulting products were less ordered than hydrothermally prepared mesoporous aluminosilicates, use of the salt-gel method permitted high aluminum content in the products with Si/Al ratios between 1.97 and 0.86. Similarly to the reaction with phosphate, an increase in the ratio of observable tetrahedral to octahedral aluminum suggested that the clusters disintegrated during the linking process, probably into octahedral units of lower nuclearity. The aluminum was then incorporated into an aluminosilicate framework, forming tetrahedral building blocks. The weakly ordered mesostructure was maintained after removal of the surfactant by calcination. More ordered mesoporous silicates and aluminosilicates were obtained by a similar two-step method based on silicate and aluminosilicate polyanions as building blocks [41,188]. Fyfe and coworkers investigated double four-ring (D4R) silicate polyanions, 8⫺ Si8O20 (Si8) or the D4R aluminosilicate anion Al4Si4(OH)8O4⫺ 12 (Al4Si4) as precursors, and suggested AlSi7, Al2Si6, and Al3Si5 as additional feasible cluster precursors. These polyanions possess cubelike structures. Through electrostatic interactions with cationic surfactants they precipitate as mesoscopic salts. The salts were treated with acidic vapors, leading to the condensation of clusters. The Si/Al ratio in the condensed product was controllable by the choice of the precursor, although calcination resulted in partial dealumination and conversion of tetrahedrally coordinated Al into octahedral Al. By increasing the duration of the acidification treatment it was possible to effect structural transformations from lamellar to cubic and hexagonal mesostructures. Based on evidence from FTIR spectra, it was concluded that intact D4R clusters were present in the condensed products (before calcination). Fyfe and Fu rationalized that the structural transformations occurred as the charge densities on the clusters were partially reduced by protonation during the acid vapor treatment. This resulted in larger headto-chain volume ratios of the surfactant assembly and in an increase in curvature of the interface between the surfactant and the inorganic wall. The charge density balance at the cluster-surfactant interface could be varied by adjusting the charge of the cluster or that of the surfactant [188]. Although Si8 and Al4Si4 were both cubic molecules, the difference in cluster charge resulted in different initial structure or-

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ganizations. Notably, the charge-structure relationship was opposite to that observed for the acid Keggin or phosphorus Keggin structures mentioned earlier. The Al4Si4 cube with the lower charge formed a rod-based phase with curved interfaces as a surfactant composite under pH conditions where a layered phase predominated for the more highly charged Si8 precursor. Another reason for the product differences may have been the different terminal groups (O⫺ vs. OH) present in Si8 and Al4Si4 clusters. The latter condensed much more readily even in the absence of acid during the vaporphase treatment. The effect of the surfactant charge on the product structure was studied by substituting quaternary ammonium surfactants with primary ammonium ions. CTA/Al4Si4 systems were hexagonal, cetylammonium (CAM)/Al4Si4 structures remained lamellar. This was interpreted by considering the partial deprotonation of CAM in the basic (pH 11) reaction mixture. As a result, both charged ammonium ions and neutral amine groups could act as structure-directing agents. With reduced headgroup repulsions, the headto-chain volume decreased, lowering the curvature and leading to layered mesostructures. In addition, the headgroup of each individual CAM ion was smaller than that of a CTA ion. XII.

SURFACTANT-ASSISTED GALLERY FORMATION IN CLAYS

Hybrid materials consisting of layered silicates intercalated with alkylammonium surfactants have been employed in a wide variety of industrial and scientific applications [189]. Using a method related to the salt-gel synthesis, Pinnavaia and coworkers [190] synthesized mesoporous solids, so-called porous clay heterostructures (PCHs), by intercalating cosurfactant mixtures into layered clays and forming silicate structures within the interlayer species of clays. A variety of clays (rectorite, fluorohectorite, magadiite, vermiculite) were intercalated with quaternary ammonium surfactants by an ion-exchange reaction. The expanded products were then stirred in mixtures of TEOS and a long-chain neutral amine. The neutral amine acted as a cosurfactant, leading to further swelling of the clay, and providing accessible space for TEOS molecules. In addition, the amine directed the hydrolysis and condensation of the silicate precursor, which then formed columns between the layers. It is worth noting that both surfactant components were necessary for the formation of a gallery structure. An open pore system was obtained by calcination, and the product was active as a solid acid catalyst, for example, in the selective dehydration of 2-

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methylbut-3-yn-2-ol to 2-methylbut-3-yn-1-ene [191]. TEOS/amine ratios ⱖ7.5 were required to form a uniform phase. With less TEOS two phases were observed: a surfactant-templated PCH and a silica-inter˚ . Pore calated derivative with a basal spacing of 12.6 A ˚ widths in the range 14–22 A were obtained. The gallery heights depended on the chain lengths of the neutral amine as well as those of the cationic amine but were independent of the type of clay used. Figure 6 shows the proposed mechanism for this synthesis. Additional selectivity can be imparted on a swelled porous material by employing a layered zeolitic precursor, such as the precursor to the lamellar molecular sieve, MCM-22 [192]. This material consists of aluminosilicate layers connected together by a layer of organic material, such as hexamethyleneimine. The ˚ inorganic layers are believed to consist of hex⬃25 A agonal arrays of pockets (rings of 12 — Si — O — Si — ˚ window openings and units) on each face, with ⬃7 A ˚ depths of ⬃7 A [193]. Within the layers, rings of 10 — Si — O — Si — units provide additional pores. When the MCM-22 precursor is reacted with a hexadecyltrimethylammonium surfactant and base and subsequently pillared with TEOS, a significantly more open structure is created [194]. The product, called MCM˚ range 36 [195], contains mesopores in the 30–35 A ˚ mibetween inorganic layers in addition to the 6–7 A cropores within the layers. The larger pores provide increased accessibility to the micropores in catalytic reactions. Similar results can be obtained by calcining the surfactant-intercalated MCM-22 precursor directly without any additional TEOS [193]. The more open product exhibited improved performance in the catalytic cracking of heavy gasoil fractions compared with the nondelaminated precursor. XIII.

SURFACE-MODIFIED MESOPOROUS SIEVES

Inclusion chemistry in mesoporous host materials, such as MCM-41 or MCM-48, has been reviewed by Moller and Bein [154] and by Ozin et al. [196]. Modifications of mesoporous solids include ion exchange, complexation, inclusion of molecules, clusters, polymers and enzymes, surface attachment of ligands and functional groups, and cocondensation reactions for the synthesis of hybrid materials. Here we will emphasize examples of functionalized mesoporous sieves where the surfactant molecules play an important role in the surface modification or where the additional surface groups influence the overall structure of the material through interactions with the surfactants.

FIG. 6 Proposed mechanism for the formation of a porous clay heterostructure by gallery-templated synthesis. The Q⫹clay is prepared by ion-exchanging Li⫹-fluorohectorite (clay layers indicated in gray) with a quaternary ammonium surfactant (chains with filled headgroups). The layers are further swollen with neutral amine molecules (open headgroups). TEOS displaces some of the amine molecules. Rodlike micellar arrays form between the layers and are surrounded by hydrated silica structures. A porous clay heterostructure forms after calcination. (Adapted from Ref. 190.)

A.

Surfactants as Space Fillers

Instead of acting as templates or structure-directing agents, surfactant arrays can play the role of space fillers during the synthesis of surface-modified mesoporous sieves. Isolated metal centers have been grafted to mesoporous silica using, for example, the organometallic precursors titanocene dichloride [197,198], manganese decarcarbonyl [199], and vanadium tetrakis-


isopropoxide [200]. For each of these systems, the organometallic precursor was introduced into the open channels of calcined MCM-41. With certain reactive precursors, such as TiCl4, it has been found that the tendency of TiCl4 to polymerize uncontrollably led to the formation of large titania agglomerates and clogging of channels. The space-filling properties of the surfactant were exploited in the solution-phase grafting of titania onto the pore surface of MCM-41, a method that avoids pore clogging (Fig. 7) [201]. As-synthesized MCM-41, which still contained the surfactant, was dried under vacuum at a temperature low enough to avoid decomposition of the surfactant. The sample was then stirred for up to 24 h in a hexane solution of TiCl4 under nitrogen. During this room temperature reaction, TiCl4 entered the channels, probably by diffusing through the hydrophobic region of the micelles, which should be considered as dynamic rather than static entities. When TiCl4 moved to the polar head of the surfactant, it formed a bright yellow chloride-amine complex. It was hydrolyzed and condensed as it encountered surface hydroxyl groups or trapped water molecules. The physical constraint of the pore walls and the chemical constraint of the surfactant acted as barriers to the formation of large titania agglomerates. After the reaction, the samples were washed with excess hexane under nitrogen. Further condensation occurred during subsequent exposure to air and calcination to remove the surfactant. Extensive characterization indicated that the mesoporous product contained a significant amount of titania (⬃15 wt%), which in careful preparations was present as isolated (TiO2)n

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clusters (n ⬃ 30–70) that were attached to the silica walls and were uniformly distributed throughout the channels. The products were active catalysts in photooxidation and thermal oxidation reactions. This technique of constraining precursors for surface groups and minimizing uncontrolled polymerization may be amendable to other compositions as long as the precursor molecules can migrate through the micellar array. B.

Hybrid Organic-Inorganic Mesoporous Materials

Organic functionalization by grafting trimethylsilyl derivatives onto mesoporous silicates was first demonstrated in 1990 for materials derived from kanemite [202] and in 1992 for MCM-41 [7,203]. Addition of chlorotrimethylsilane to surface silanol groups allowed reduction of the pore sizes. Other surface attachment methods using silane-coupling agents or reactive ligands have been reviewed [154]. Mann and coworkers [204,205] prepared phenyland alkyl-functionalized mesoporous silicas by the cocondensation of the corresponding organosiloxanes with tetraethoxysilane in the presence of the C16TMABr surfactant. Subsequently, mesoporous sieves with reactive functional groups were prepared, including aminopropyl [206,207] and cyanoethyl [207], vinyl [208,209], mercaptopropyl [207,210,211], as well as allyl-, imidazole- and epoxy-functional [207] groups. The ordered mesostructure was significantly disrupted for the last three compositions and was also lower than

FIG. 7 Schematic of the titania grafting procedure in surfactant-containing MCM-41 [201]. A single pore is shown. The white region represents the silica framework, the gray gradient represents the surfactant, and the flattened hemispheres the grafted titania agglomerates. The TEM image shows the ordered channel structure of the grafted product.

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typically observed for MCM-41 for aminopropyl materials. The difference in order may be attributed to different hydrolysis/condensation rates of tetraalkoxysilanes (TAOSs) and organotrialkoxysilanes (OTOSs) as well as to the effect of organic groups on the interaction with the surfactant. Stein and coworkers synthesized mesoporous silicates with reactive organic functional groups, such as vinyl-MCM-41 [208,208b,212] and thiol-MCM-41 [210], and carried out further functionalizations within the mesoporous channels. Vinyl groups, for example, could be brominated in solution or gas-phase reactions. The intrachannel reactions provided proof for the location of the organic functional groups mainly within the mesopores. Further confirmation of the location of these groups was obtained from nitrogen adsorption measurements and small-angle neutron scanning experiments, using contrast matching techniques [212]. Moller and Bein [213] carried out a similar cocondensation of TMOS and 3-(trimethoxysilyl)propyl methacrylate in the presence of CTACl and also showed that methacrylate groups could be brominated. ThiolMCM-41 was oxidized to produce a high-surface-area mesoporous support with sulfonic acid groups. This material was active as an acid catalyst for the dehydration and protection of alcohols [210]. Jacobs et al. [211] showed that sulfonic acid–MCM-41 is an effi-

Stein and Melde

cient catalyst for the formation of polyol esters and bisfurylalkanes. The cocondensation reactions can be carried out at room temperature. However, elevated temperatures up to about 95⬚C have led to more ordered products with more highly condensed walls. The surfactant templates were typically removed by acid extraction without breaking the Si — C bond through hydrolysis. In all these cases the organic functional groups were incorporated in the wall structure via covalent linkage to framework silicon atoms. The organic groups appeared to be uniformly distributed [208,208b,212]. Figure 8 is a plot of d100 spacings, pore diameters and wall thicknesses for hybrid MCM-41 samples obtained by cocondensation of PTES/TEOS [204] or VTAS/TAOS [208b] with varying concentrations of organosiloxane in the synthesis mixture. As the concentration of organosiloxane increases, both the d100 spacings and the pore sizes of the channels are significantly reduced, even when the same surfactant is used (acetyltrimethylammonium surfactant). At the same time, the apparent wall thickness increases, partly because organic groups extend into the channels. One possible reason for the shrinkage in cell dimensions may be a stronger interaction between the phenyl or vinyl groups and the less polar tails of the surfactant molecules, which draw the organic precursors further into the mi-

FIG. 8 Effect of organosilane concentration on pore dimensions of organically functionalized MCM-41 prepared by cocondensation of PTES with TEOS, VTMS with TMOS, or VTES with TEOS. PTES/TEOS system: (䡲) unit cell dimension, ao; (䊱) HK pore size; (●) wall thickness. VTMS/TMOS or VTES/TEOS system: (▫) unit cell dimension, ao; (䉭) HK pore size; (䡩) wall thickness.


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celles. Similar pore shrinkage was observed when other organosiloxanes, such as mercaptopropylsiloxane, were included in a direct cocondensation reaction. At too high an organosiloxane concentration the products no longer exhibit hexagonal order.

products were obtained whose unit cell dimensions ˚ larger than in products synthesized were up to 20 A without DNA. The presence of DNA in the product was confirmed by ultraviolet (UV)-visible spectroscopy (absorption at 255 nm). Subsequent template removal was possible by extraction with methanolic HCl solution.

XIV.

XV.

TEMPLATING WITH INTERCALATED MICELLES

Functional organic molecules of various degrees of complexity can be encapsulated in inorganic glasses by sol-gel methods [214]. Normally, dense packed, amorphous structures are obtained by these methods. If, on the other hand, the organic molecules are intercalated in surfactant micelles during a typical synthesis of mesoporous silicates, they can be embedded in accessible channels. For example, phthalocyanine complexes [215,216] and porphyrins [217] can be incorporated in mesostructured hosts directly during the hydrothermal synthesis. In these cases the organic complexes are included in the surfactant micelles as the molecular sieve is formed. More ordered mesostructures are typically obtained at high ratios of surfactant to additional guest, where the additional guest provides only a minor perturbation in the structure. In case of an MCM-41 material containing encapsulated cationic porphyrin guests the surfactant molecules could be extracted without removing the porphyrin molecules [217]. The subsequently metallated porphyrin rings were accessible to other guest molecules and were active catalysts in the oxidation of an azo dye. The porphyrin molecules were stabilized to autoxidation by entrapment in the mesoporous sieve. Enzymes (cytochrome c, papain, trypsin) have also been immobilized in MCM-41 to stabilize the enzymes and exploit their catalytic activity [218]. The encapsulated enzymes were catalytically active in the hydrolysis of N-␣-benzoyl-DL-arginine-4-nitroanilide but to a lesser extent than with other immobilization techniques. Stein, Lim and Schroden (unpublished work) incorporated herring sperm DNA in surfactant-containing synthesis mixtures for mesoporous silicates.* Surfactants are known to form aggregates with DNA and stabilize the DNA over a wider pH and temperature range than in the absence of the surfactants. In room temperature reactions at an initial pH 9, mesostructured ⫹

*The synthesis mixture contained 1 DNA, 10 CnTMA , 75 TEOS, 12.5 NaOH, 10,300 H2O; n = 12, 14, 16; DNA was in its acid form, (C39H51O25N15P)n, and was not highly polymerized.

CONCLUSIONS

During this decade much progress has been made in controlling the architecture of porous inorganic solids by using organic molecules or molecular aggregates as structure directors, space fillers, or templates. Functional porous nanostructures can now be designed with a high degree of complexity by combining processes from a number of fields, including sol-gel chemistry, zeolite chemistry, surfactant chemistry, colloid chemistry, and polymer chemistry. Beautiful hierarchical structures that were synthesized in the laboratory but resemble skeletons of natural organisms have already been described [175,182,183]. Surface patterning of mesoporous structures is also possible. For example, Ozin and coworkers deposited mesostructured surfactant-silicate assemblies on a gold substrate patterned with self-assembled monolayers (SAMs) of alkanethiolates, using a surfactant-alkanethiolate heterobilayer as a ‘‘buffer layer’’ [90,219]. Other recent methods of creating solids with pores on multiple length scales have involved combining surfactant templating with latex sphere [220–226] or emulsion templating of inorganic oxides [227,228]. The resulting structures contain organized arrays of pores in the submicrometer range, surrounded by walls that are themselves mesoporous [220,222] or even microporous [229]. Combination with stamping techniques permits patterning on an additional length scale [71]. The flexibility in choosing organic, inorganic, or hybrid building blocks and combinations of templates allows one to control the materials properties and to optimize them for each desired application. In the next few years one can expect new developments, not only in the nanometer architecture of porous materials but also in the design of macroscopic shape, morphology, and interfaces with other materials. ACKNOWLEDGMENTS Portions of some of the work described here were funded by 3M, Dupont, the David & Lucile Packard Foundation, the McKnight Foundation, the Petroleum Research Fund, the NSF (DMR-9701507 and the MRSEC Program of the NSF under award number

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DMR-9809364), and the Office of the Vice President for Research and Dean of the Graduate School of the University of Minnesota. ABBREVIATIONS 2D: two dimensional 3D: three-dimensional ATR: attenuated total reflectance CAM: cetyl ammonium cmc: critical micelle concentration CnTMA . . .: alkyl ammonium group with three methyl functionalities and one linear alkyl chain containing n carbon atoms CTA, CTA⫹: cetyltrimethylammonium (ion) CTACl: cetyltrimethylammonium chloride CTAB or CTABr: cetyltrimethylammonium bromide CTAOH: cetyltrimethylammonium hydroxide CTEABr: cetyltriethylammonium bromide D4R: double four-ring EO: ethylene oxide HMS: hexagonal mesoporous silica HREM: high-resolution electron microscopy FTIR: Fourier transform infrared spectroscopy LAT: ligand-assisted templating LCT: liquid crystal templating MAS-NMR spectroscopy: magic angle spinning–nuclear magnetic resonance spectroscopy M41S: designation by Mobil for the class of materials including MCM-41, MCM-48, MCM-50 MCM-41: hexagonal mesoporous structure MCM-48: cubic mesoporous structure MCM-50: lamellar mesoporous structure PCH: porous clay heterostructure PEO: polyethylene oxide PPO: polypropylene oxide PTES: phenyltriethyoxy silane Q3: a Q3 resonance corresponds to SiO4 tetrahedra with one terminal hydroxyl group [HO — Si( — OSi — )3] Q4: a Q4 resonance corresponds to fully connected SiO4 tetrahedra [Si( — OSi — )4] SAM: self-assembled monolayer SAXS: small-angle x-ray scattering SDS: sodium dodecyl sulfate SEM: scanning electron microscopy T: tetrahedral framework atom such as Si, Al, or P TAOS: tetraalkoxy silane TEA⫹: tetraethylammonium ion TEM: transmission electron microscopy TEOS: tetraethyl orthosilicate, tetraethoxy silane TMA⫹: tetramethylammonium ion TMAOH: tetramethylammonium hydroxide

Stein and Melde

TMOS: tetramethyl orthosilicate, tetramethoxy silane VTAS: vinyl trialkoxy silane VTES: vinyl triethoxy silane VTMS: vinyl trimethoxy silane XANES: X-ray absorption near edge structure XRD: X-ray diffraction (in this chapter refers to powder x-ray diffraction) REFERENCES 1. 2. 3. 4. 5.

6. 7.

8.

9. 10.

11. 12.

13.

14. 15. 16.

17.

B. M. Lok, T. R. Cannan, and C. A. Messina. Zeolites 3:282–291 (1983). R. Szostak, Molecular Sieves, Van Nostrand Reinhold, New York, 1989. H. Robson and K. P. Lillerud, Microporous Mesoporous Mater. 22:511–663 (1998). W. M. Meier, D. H. Olson, and C. Baerlocher, Zeolites 17:1–230 (1996). J. M. Newsam, in Solid State Chemistry, Compounds (A. K. Cheetham and P. Day, eds.), Clarendon Press, Oxford, 1992, pp. 234–280. C. T. Kresge, M. E. Leonowicz, W. J. Roth, J. C. Vartuli, and J. S. Beck, Nature 359:710–712 (1992). J. S. Beck, J. C. Vartuli, W. J. Roth, M. E. Leonowicz, C. T. Kresge, K. D. Schmitt, C. T.-W. Chu, D. H. Olson, E. W. Sheppard, S. B. McCullen, J. B. Higgins, and J. L. Schlenker, J. Am. Chem. Soc. 114:10834– 10843 (1992). C. T. Kresge, M. E. Leonowicz, W. J. Roth, and J. C. Vartuli, U.S. Patent 5,098,684, Mobil Oil Corp. (1992). J. S. Beck, U.S. Patent 5,057,296, Mobil Oil Corp. (1991). A. Monnier, F. Schu¨th, Q. Huo, D. Kumar, D. Margolese, R. S. Maxwell, G. D. Stucky, M. Krishnamurty, P. Petroff, A. Firouzi, M. Janicke, and B. F. Chmelka, Science 261:1299–1303 (1993). C.-Y. Chen, H.-X. Li, and M. E. Davis, Microporous Mater. 2:17–26 (1993). M. Fro¨ba, P. Behrens, J. Wong, G. Engelhardt, C. Haggenmu¨ller, G. van de Goor, M. Rowen, T. Tanaka, and W. Schwieger, Mater. Res. Soc. Symp. Proc. 371:99– 104 (1995). J. S. Beck, J. C. Vartuli, G. J. Kennedy, C. T. Kresge, W. J. Roth, and S. E. Schramm, Chem. Mater. 6:1816– 1821 (1994). X. Chen, L. Huang, and Q. Li, J. Phys. Chem. B 101: 8460–8467 (1997). G. S. Attard, J. C. Glyde, and C. G. Goltner, Nature 378:366 (1995). A. Firouzi, D. Kumar, L. M. Bull, T. Besier, P. Sieger, Q. Huo, S. A. Walker, J. A. Zasadzinski, C. Glinka, J. Nicol, D. Margolese, G. D. Stucky, and B. F. Chmelka, Science 267:1138–1143 (1995). J. C. Vartuli, K. D. Schmitt, C. T. Kresge, W. J. Roth, M. E. Leonowicz, S. B. McCullen, S. D. Hellring, J.


18.

19. 20. 21. 22.

23. 24.

25.

26. 27. 28. 29.

30. 31.

32.

33. 34. 35. 36. 37. 38. 39. 40.

S. Beck, J. L. Schlenker, D. H. Olson, and E. W. Sheppard, Chem. Mater. 6:2317–2326 (1994). Q. Huo, D. I. Margolese, U. Ciesla, P. Feng, T. E. Gier, P. Sieger, R. Leon, P. M. Petroff, F. Schu¨th, and G. D. Stucky, Nature 368:317–321 (1994). N. Coustel, F. Di Renzo, and F. Fajula, J. Chem. Soc. Chem. Commun. 967–968 (1994). S. A. Bagshaw, E. Prouzet, and T. J. Pinnavaia, Science 269:1242–1244 (1995). C. T. W. Chu and C. T. Kresge, U.S. Patent 5,104,515, Mobil Oil Corp. (1992). M. E. Davis, C. Y. Chen, S. L. Burkett, and R. F. Lobo, Mater. Res. Soc. Symp. Proc. 346:831–842 (1994). C.-Y. Chen, S. L. Burkett, H.-X. Li, and M. E. Davis, Microporous Mater. 2:27–34 (1993). A. Firouzi, D. J. Schaefer, S. H. Tolbert, G. D. Stucky, and B. F. Chmelka, J. Am. Chem. Soc. 119:9466–9477 (1997). A. Firouzi, F. Atef, A. G. Oertli, G. D. Stucky, and B. F. Chmelka, J. Am. Chem. Soc. 119:3596–3610 (1997). C.-F. Cheng, Z. Luan, and J. Klinowski, Langmuir 11: 2815–2819 (1995). A. W. Ralston, D. N. Eggengerger, H. J. Harwood, and P. L. DuBrow, J. Am. Chem. Soc. 69:883 (1947). C. F. Cheng, H. He, W. Zhou, and J. Klinowski, Chem. Phys. Lett. 244:117–120 (1995). S. O’Brien, R. J. Francis, S. J. Price, D. O’Hare, S. M. Clark, N. Okazaki, and K. Kuroda, J. Chem. Soc. Chem. Commun. 2423–2424 (1995). A. Matijasic, A. C. Voegtlin, J. Patarin, J. L. Guth, and L. Huve, Chem. Commun. 1123–1124 (1996). Q. Huo, D. I. Margolese, U. Ciesla, D. G. Demuth, P. Feng, T. E. Gier, P. Sieger, A. Firouzi, B. F. Chmelka, F. Schu¨th, and G. D. Stucky, Chem. Mater. 6:1176– 1191 (1994). (a) G. D. Stucky, A. Monnier, F. Schu¨th, Q. Huo, D. Margolese, D. Kumar, M. Krishnamurty, P. Petroff, A. Firouzi, M. Janicke, and B. F. Chmelka, Mol. Cryst. Liq. Cryst. 1994:187–200 (1994). (b) F. Schu¨th, U. Ciesla, S. Schacht, M. Thieme, Q. Huo, G. D. Stucky, Materials Research Bulletin 34:483–494 (1999). A. A. Romero, M. D. Alba, W. Zhou, and J. Klinowski, J. Phys. Chem. B 101:5294–5300 (1997). O. Regev, Langmuir 12:4940–4944 (1996). D. C. Calabro, E. W. Valyocsik, and F. X. Ryan, Microporous Mater. 7:243–259 (1996). R. Schmidt, M. Sto¨cker, D. Akporiaye, E. H. Tørstad, and A. Olsen, Microporous Mater. 5:1–7 (1995). M. W. Anderson, Zeolites 19:220–227 (1997). J. Xu, Z. Luan, H. He, W. Zhou, and L. Kevan, Chem. Mater. 10:3690–3698 (1998). D. Zhao and D. Goldfarb, J. Chem. Soc. Chem. Commun. 875–876 (1995). Q. Huo, D. I. Margolese, and G. D. Stucky, Chem. Mater. 8:1147–1160 (1996).

847 41. 42. 43. 44. 45.

46.

47. 48. 49.

50.

51. 52. 53. 54. 55. 56. 57.

58. 59. 60.

61. 62. 63. 64.

C. A. Fyfe and G. Fu, J. Am. Chem. Soc. 117:9709– 9714 (1995). K. W. Gallis and C. C. Landry, Chem. Mater. 9:2035– 2038 (1997). W. Z. Zhang and T. J. Pinnavaia, Catal. Lett. 38:261 (1996). R. Schmidt, H. Junggreen, and M. Sto¨cker, Chem. Commun. 875 (1996). J. Lujano, Y. Romero, and J. Carrazza, in Zeolites: A Refined Tool for Designing Catalytic Sites (L. Bonneviot and S. Kaliaguine, eds.), Elsevier Science, Amsterdam, 1995, pp. 489–494. R. Schmidt, M. Sto¨cker, and O. H. Ellestad, in Zeolites: A Refined Tool for Designing Catalytic Sites (L. Bonneviot and S. Kaliaguine, eds.), Elsevier Science, Amsterdam, 1995, pp. 149–156. J. M. Kim, S. K. Kim, and R. Ryoo, Chem. Commun. 259–260 (1998). J. N. Israelachvili, D. J. Mitchell, and B. W. Ninham, J. Chem. Soc. Faraday Trans. 2 72:1525–1568 (1976). G. D. Stucky, Q. Huo, A. Firouzi, B. F. Chmelka, S. Schacht, I. G. Voigt-Martin, and F. Schu¨th. Proceedings, 11th International Zeolite Association Conference, Seoul, Korea, 1996. S. Manne, T. E. Scha¨ffer, Q. Huo, P. K. Hansma, D. E. Morse, G. D. Stucky, and I. A. Aksay. Langmuir 13:6382–6387 (1997). P. Yang, D. Zhao, B. F. Chmelka, and G. D. Stucky, Chem. Mater. 10:2033–2036 (1998). U. Henriksson, E. S. Blackmore, G. J. T. Tiddy, and O. Soderman, J. Phys. Chem. 96:3894 (1992). N. Ulagappan, Neeraj, B. V. N. Raju, and C. N. R. Rao, Chem. Commun. 2243–2244 (1996). Q. Huo, R. Leon, P. M. Petroff, and G. D. Stucky, Science 268:1324–1327 (1995). M. T. Anderson, J. E. Martin, J. G. Odinek, and P. P. Newcomer, Chem. Mater. 1998:1490–1500 (1998). A. Navrotsky, I. Petrovic, Y. Hu, C. Y. Chen, and M. E. Davis, Microporous Mater. 4:95–98 (1995). C. J. Brinker and G. W. Scherer, Sol-Gel Science: The Physics and Chemistry of Sol-Gel Processing, Academic Press, San Diego, 1990. S. H. Tolbert, A. Firouzi, G. D. Stucky, and B. F. Chmelka, Science 278:264–268 (1997). D. Khushalani, A. Kuperman, N. Coombs, and G. A. Ozin, Chem. Mater. 8:2188–2193 (1996). D. Khushalani, A. Kuperman, G. A. Ozin, K. Tanaka, J. Garce´s, M. M. Olken, and N. Coombs, Adv. Mater. 7:842–846 (1995). A. Corma, Q. Kan, M. Navarro, J. Pe´rez-Pariente, and F. Rey, Chem. Mater. 9:2123–2126 (1997). C. F. Cheng, W. Zhou, and J. Klinowski, Chem. Phys. Lett. 263:247–252 (1996). E. Prouzet and T. J. Pinnavaia, Angew. Chem. Int. Ed. Engl. 36:516–518 (1997). S. A. Bagshaw and T. J. Pinnavaia, Angew. Chem. Int. Ed. Engl. 35:1102–1105 (1996).

848 65.

66. 67.

68. 69. 70.

71.

72. 73. 74. 75. 76. 77. 78. 79. 80. 81. 82. 83. 84. 85. 86. 87. 88. 89. 90.

Stein and Melde D. Zhao, J. Feng, Q. Huo, N. Melosh, G. H. Fredrickson, B. F. Chmelka, and G. D. Stucky, Science 279:548–552 (1998). D. Zhao, Q. Huo, J. Feng, B. F. Chmelka, and G. D. Stucky, J. Am. Chem. Soc. 120:6024–6036 (1998). D. Zhao, P. Yang, Q. Huo, B. F. Chmelka, and G. D. Stucky, Curr. Opin. Solid State Mater. Sci. 3:111–121 (1998). C. G. Go¨ltner, S. Henke, M. C. Weissberger, and M. Antonietti, Angew. Chem. 110:633–636 (1998). P. Yang, D. Zhao, D. I. Margolese, B. F. Chmelka, and G. D. Stucky, Nature 396:152–155 (1998). P. Schmidt-Winkel, W. W. Lukens, D. Zhao, P. Yang, B. F. Chmelka, and G. D. Stucky, J. Am. Chem. Soc. 121:254–255 (1999). P. Yang, T. Deng, D. Zhao, P. Feng, D. Pine, B. F. Chmelka, G. M. Whitesides, and G. D. Stucky, Science 282:2244–2246 (1998). P. T. Tanev and T. J. Pinnavaia, Science 267:865–867 (1995). P. T. Tanev and T. J. Pinnavaia, Chem. Mater. 8:2068– 2079 (1996). W. Zhang, T. R. Pauly, and T. J. Pinnavaia, Chem. Mater. 9:2491–2498 (1997). P. T. Tanev and T. J. Pinnavaia, Science 271:1267– 1269 (1996). P. T. Tanev, Y. Liang, and T. J. Pinnavaia, J. Am. Chem. Soc. 119:8616–8624 (1997). R. Ryoo, J. M. Kim, C. H. Ko, and C. H. Shin, J. Phys. Chem. 100:17718–17721 (1996). D. M. Antonelli, A. Nakahira, and J. Y. Ying, Inorg. Chem. 35:3126–3136 (1996). D. M. Antonelli and J. Y. Ying, Angew. Chem. Int. Ed. Engl. 35:426–430 (1996). T. Sun and J. Y. Ying, Nature 389:704–706 (1997). T. Sun and J. Y. Ying, Angew. Chem. Int. Ed. 37:664– 667 (1998). D. M. Antonelli and J. Y. Ying, Angew. Chem. Int. Ed. Engl. 34:2014–2017 (1995). D. M. Antonelli and J. Y. Ying, Chem. Mater. 8:874– 881 (1996). M. S. Wong and J. Y. Ying, Chem. Mater. 10:2067– 2077 (1998). M. Grun, I. Lauer, and K. K. Unger, Adv. Mater. 9: 254 (1997). L. Qi, J. Ma, H. Cheng, and Z. Zhao, Chem. Mater. 10:1623–1626 (1998). H. Yang, G. Vovk, N. Coombs, I. Sokolov, and G. A. Ozin, J. Mater. Chem. 8:743–750 (1998). S. Schacht, Q. Huo, I. G. Voigt-Martin, G. D. Stucky, and F. Schu¨th, Science 273:768–771 (1996). Q. Huo, J. Feng, F. Schu¨th, and G. D. Stucky, Chem. Mater. 9:14–17 (1997). N. Coombs, D. Khushalani, S. Oliver, G. A. Ozin, G. C. Shen, I. Sokolov, and H. Yang, J. Chem. Soc. Dalton Trans. 3941–3952 (1997).

91. 92. 93. 94.

95. 96. 97. 98. 99. 100.

101. 102. 103. 104. 105.

106. 107. 108. 109. 110. 111. 112. 113.

114. 115. 116.

S. Mann and G. A. Ozin, Nature 382:313–318 (1996). H. Yang, G. A. Ozin, and C. T. Kresge, Adv. Mater. 10:883–887 (1998). P. J. Bruinsma, A. Y. Kim, J. Liu, and S. Baskaran, Chem. Mater. 9:2507–2512 (1997). Q. Huo, D. Zhao, J. Feng, K. Weston, S. K. Buratto, G. D. Stucky, S. Schacht, and F. Schuüth, Adv. Mater. 9:974–978 (1997). R. Ryoo, C. H. Ko, S. J. Cho, and J. M. Kim, J. Phys. Chem. B 101:10610–10613 (1997). H. Yang, N. Coombs, and G. A. Ozin, J. Mater. Chem. 8:1205–1211 (1998). ¨ . Dag, I. Sokolov, and G. A. H. Yang, N. Coombs, O Ozin, J. Mater. Chem. 7:1755–1761 (1997). H. Yang, N. Coombs, I. Sokolov, and G. A. Ozin, Nature 381:589–592 (1996). S. H. Tolbert, T. E. Scha¨ffer, J. Feng, P. K. Hansma, and G. D. Stucky, Chem. Mater. 9:1962–1967 (1997). Y. Lu, R. Ganguli, C. A. Drewien, M. T. Anderson, C. J. Brinker, W. Gong, Y. Guo, H. Soyez, B. Dunn, M. H. Huang, and J. I. Zink, Nature 389:364–368 (1997). M. Ogawa, J. Am. Chem. Soc. 116:7941 (1994). M. Ogawa, Chem. Commun. 1149–1150 (1996). H. Yang, A. Kuperman, N. Coombs, S. MamicheAfara, and G. A. Ozin, Nature 379:703–705 (1996). H. Yang, N. Coombs, I. Sokolov, and G. A. Ozin, J. Mater. Chem. 7:1285–1290 (1997). I. A. Aksay, M. Trau, S. Manne, I. Honma, N. Yao, L. Zhou, P. Fenter, P. M. Eisenberger, and S. M. Gruner, Science 273:892–898 (1996). D. Zhao, P. Yang, N. Melosh, J. Feng, B. F. Chmelka, and G. D. Stucky, Adv. Mater. 10:1380 (1998). J. E. Martin, M. T. Anderson, J. Odinek, and P. Newcomer, Langmuir 13:4133–4141 (1997). S. B. McCullen and J. C. Vartuli, U.S. Patent 5,156,829, Mobil Oil Corp. (1992). T. Tatsumi, K. A. Koyano, Y. Tanaka, and S. Nakata, Stud. Surf. Sci. Catal. 117:143–150 (1998). S. S. Kim, W. Zhang, and T. J. Pinnavaia, Science 282: 1302–1305 (1998). R. Ryoo and S. Jun, J. Phys. Chem. B 101:317–320 (1997). T. Yanagisawa, T. Shimizu, K. Kuroda, and C. Kato, Bull. Chem. Soc. Jpn. 63:988–992 (1990). S. Inagaki, Y. Fukushima, A. Okada, T. Kurauchi, K. Kuroda, and C. Kato, in Proceedings of the 9th International Zeolite Conference (R. von Ballmoos, ed.), Butterworth-Heinemann, Montreal, 1992, pp. 305– 311. S. Inagaki, Y. Fukushima, and K. Kuroda, J. Chem. Soc. Chem. Commun. 680–682 (1993). S. Inagaki, Y. Fukushima, and K. Kuroda, Stud. Surf. Sci. Catal. 84:125–132 (1994). S. Inagaki, A. Koiwai, N. Suzuki, Y. Fukushima, and K. Kuroda, Bull. Chem. Soc. Jpn. 69:1449–1457 (1996).

Synthesis of Porous Inorganic Solids 117. 118. 119. 120. 121. 122.

123.

124. 125.

126. 127.

128.

129. 130. 131. 132.

133. 134. 135. 136.

137.

138.

139.

S. Inagaki, Y. Sakamoto, Y. Fukushima, and O. Terasaki, Chem. Mater. 2089–2095 (1996). S. Inagaki, Y. Fukushima, K. Kuroda, and K. Kuroda, J. Colloid Interface Sci. 180:623–624 (1996). S. Inagaki, Y. Yamada, and Y. Fukushima, Stud. Surf. Sci. Catal. 105:109–116 (1997). S. Inagaki, S. Ogata, Y. Goto, and Y. Fukushima, Stud. Surf. Sci. Catal. 117:65–76 (1998). K. Beneke and G. Lagaly, Am. Mineral. 62:763–771 (1977). P. J. Branton, K. Kaneko, N. Setoyama, K. S. W. Sing, S. Inagaki, and Y. Fukushima, Langmuir 12:599–600 (1996). J. C. Vartuli, C. T. Kresge, M. E. Leonowicz, A. S. Chu, S. B. McCullen, I. D. Johnson, and E. W. Sheppard, Chem. Mater. 6:2070–2077 (1994). C.-Y. Chen, S.-Q. Xiao, and M. E. Davis, Microporous Mater. 4:1–20 (1995). Y. Sakamoto, S. Inagaki, T. Ohsuna, N. Ohnishi, Y. Fukushima, Y. Nozue, and O. Terasaki, Microporous Mesoporous Mater. 21:589–596 (1998). K. Moller, T. Bein, and R. X. Fischer, Chem. Mater. 11:665–673 (1999). M. Sasaki, M. Osada, N. Sugimoto, S. Inagaki, Y. Fukushima, A. Fukuoka, and M. Ichikawa, Microporous Mesoporous Mater. 21:597–606 (1998). M. T. Janicke, C. C. Landry, S. C. Christiansen, D. Kumar, G. D. Stucky, and B. F. Chmelka, J. Am. Chem. Soc. 120:6940–6951 (1998). K. R. Kloetstra, H. W. Zandbergen, and H. van Bekkum, Catal. Lett. 33:157–163 (1995). R. B. Borade and A. Clearfield, Catal. Lett. 31:267– 272 (1995). Z. Luan, C.-F. Cheng, W. Zhou, and J. Klinowski, J. Phys. Chem. 99:1018–1024 (1995). Z. H. Luan, H. Y. He, W. Z. Zhou, C. F. Cheng, and J. Klinowski, J. Chem. Soc. Faraday Trans. 91:2955– 2959 (1995). Z. Luan, C.-F. Cheng, H. He, and J. Klinowski, J. Phys. Chem. 99:10590–10593 (1995). A. Corma, V. Fornes, M. T. Navarro, and J. Pe´rezPariente, J. Catal. 148:569–574 (1994). A. Stein and B. Holland, J. Porous Mater. 3:83–92 (1996). M. Janicke, D. Kumar, G. D. Stucky, and B. F. Chmelka, in Zeolites and Related Microporous Materials: State of the Art 1994 (J. Weitkamp et al., eds.), Elsevier Science, Amsterdam, 1994, pp. 243–250. R. Schmidt, D. Akporiaye, M. Sto¨cker, and O. H. Ellestad, J. Chem. Soc. Chem. Commun. 1493–1494 (1994). R. Schmidt, D. Akporiaye, M. Sto¨cker, and O. H. Ellestad, in Zeolites and Related Microporous Materials: State of the Art 1994 (J. Weitkamp et al., eds.), Elsevier Science, Amsterdam, 1994, pp. 61–68. A. Corma, M. T. Navarro, and J. P. Pariente, J. Chem. Soc. Chem. Commun. 147–148 (1994).

849 140. 141.

142. 143. 144. 145. 146. 147.

148. 149.

150. 151. 152. 153. 154. 155.

156. 157.

158. 159. 160.

161. 162. 163. 164. 165.

T. Blasco, A. Corma, M. T. Navarro, and J. P. Pariente, J. Catal. 156:65–74 (1995). W. Zhang, M. Fro¨ba, J. Wang, P. T. Tanev, J. Wong, and T. J. Pinnavaia, J. Am. Chem. Soc. 118:9164– 9171 (1996). M. Morey, A. Davidson, and G. Stucky, Microporous Mater. 6:99–104 (1996). P. T. Tanev, M. Chibwe, and T. J. Pinnavaia, Nature 368:321–323 (1994). K. M. Reddy, I. Moudrakovski, and A. Sayari, J. Chem. Soc. Chem. Commun. 1059–1060 (1994). J. S. Reddy and A. Sayari, J. Chem. Soc. Chem. Commun. 2231–2232 (1995). A. Tuel and S. Gontier, Chem. Mater. 8:114–122 (1996). A. Sayari, I. Moudrakovski, C. Danumah, C. I. Ratcliffe, J. A. Ripmeester, and K. F. Preston, J. Phys. Chem. 99:16373–16379 (1995). M. Yonemitsu, Y. Tanaka, and M. Iwamoto, Chem. Mater. 9:2679–2681 (1997). Z. Gabelica, J. M. Clacens, R. Sobry, and G. Van den Bossche, in Zeolites: A Refined Tool for Designing Catalytic Sites (L. Bonneviot and S. Kaliaguine, eds.), Elsevier Science, Amsterdam, 1995, pp. 143–147. T. M. Abdel-Fattah and T. J. Pinnavaia, Chem. Commun. 665–666 (1996). W. Zhang and T. J. Pinnavaia, Chem. Commun. 1185– 1186 (1998). B. Echchadhed, A. Moen, D. Nicholson, and L. Bonneviot, Chem. Mater. 9:1716–1719 (1997). A. Corma, Chem. Rev. 97:2373–2419 (1997). K. Moller and T. Bein, Chem. Mater. 10:2950–2963 (1998). A. Stein, M. Fendorf, T. P. Jarvie, K. T. Mueller, A. J. Benesi, and T. E. Mallouk, Chem. Mater. 7:304– 313 (1995). G. G. Janauer, A. Dobley, J. Guo, P. Zavalij, and M. S. Whittingham, Chem. Mater. 8:2096–2101 (1996). U. Ciesla, D. Demuth, R. Leon, P. Petroff, G. Stucky, K. Unger, and F. Schu¨th, J. Chem. Soc. Chem. Commun. 1387–1388 (1994). N. Ulagappan and C. N. R. Rao, Chem. Commun. 1047–1048 (1996). K. G. Severin, T. M. Abdel-Fattah, and T. J. Pinnavaia, Chem. Commun. 1471–1472 (1998). U. Ciesla, S. Schacht, G. D. Stucky, K. K. Unger, and F. Schu¨th, Angew. Chem. Int. Ed. Engl. 35:541–543 (1996). A. Y. Kim, P. J. Bruinsma, Y. L. Shen, and J. Liu, Mater. Res. Soc. Symp. Proc. 435:131 (1996). J. S. Reddy and A. Sayari, Catal. Lett. 38:219 (1996). A. Kim, P. Bruinsma, Y. Chen, L. Q. Wang, and J. Liu, Chem. Commun. 161–162 (1997). J. A. Knowles and M. J. Hudson, J. Chem. Soc. Chem. Commun. 2083–2084 (1995). V. Luca, D. J. MacLachlan, J. M. Hook, and R. Withers, Chem. Mater. 7:2220–2223 (1995).

850 166. 167. 168. 169. 170. 171.

172. 173. 174.

175. 176. 177.

178. 179. 180. 181. 182. 183. 184.

185.

186. 187. 188. 189.

Stein and Melde P. Liu, I. L. Moudrakovski, J. Liu, and A. Sayari, Chem. Mater. 9:2513–2520 (1997). P. Liu, J. Liu, and A. Sayari, Chem. Commun. 577 (1997). F. Vaudry, S. Khodabandeh, and M. E. Davis, Chem. Mater. 8:1451–1464 (1996). M. Yada, M. Machida, and T. Kijima, Chem. Commun. 769–770 (1996). J. Luo and S. L. Suib, Chem. Commun. 1031–1032 (1997). S. H. Tolbert, P. Sieger, G. D. Stucky, S. M. J. Aubin, C.-C. Wu, and D. N. Hendrickson, J. Am. Chem. Soc. 119:8652–8661 (1997). P. Liu, J. S. Reddy, and A. Sayari, Mater. Res. Soc. Symp. Proc. 431:101 (1996). M. S. Wong, D. M. Antonelli, and J. Y. Ying, Nanostructured Mater. 9:165–168 (1997). (a) B. T. Holland, P. K. Isbester, C. F. Blanford, E. J. Munson, and A. Stein, J. Am. Chem. Soc. 119:6796– 6803 (1997). (b) D. A. Kron, B. T. Holland, R. Wipson, C. Maleke, A. Stein, Langmuir 15:8300–8308 (1999). S. Oliver, N. Coombs, and G. A. Ozin, Adv. Mater. 7: 931–935 (1995). A. Chenite, Y. L. Page, V. R. Karra, and A. Sayari, Chem. Commun. 413–414 (1996). A. Sayari, I. Moudrakovski, J. S. Reddy, C. I. Ratcliffe, J. A. Ripmeester, and K. F. Preston, Chem. Mater. 8:2080–2088 (1996). D. Zhao, Z. Luan, and L. Kevan, Chem. Commun. 1009–1010 (1997). P. Feng, Y. Xia, J. Feng, X. Bu, and G. D. Stucky, Chem. Commun. 949–950 (1997). T. Abe, A. Taguchi, and M. Iwamoto, Chem. Mater. 7:1429–1430 (1995). T. Doi and T. Miyake, Chem. Commun. 1635 (1996). G. A. Ozin and S. Oliver, Adv. Mater. 7:943–947 (1995). S. Oliver, A. Kuperman, N. Coombs, A. Lough, and G. A. Ozin, Nature 378:47–50 (1995). G. A. Ozin, N. Varaksa, N. Coombs, J. E. Davies, D. D. Perovic, and M. Ziliox, J. Mater. Chem. 7:1601– 1607 (1997). A. Stein, M. Fendorf, T. P. Jarvie, K. T. Mueller, M. E. Garcia, and T. E. Mallouk, in Advances in Porous Materials (S. Komarneni, D. M. Smith, and J. S. Beck, eds.), Materials Research Society, Pittsburgh, 1995, pp. 69–79. G. G. Janauer, A. D. Dobley, P. Y. Zavalij, and M. S. Whittingham, Chem. Mater. 9:647–649 (1997). B. T. Holland, P. K. Isbester, E. J. Munson, and A. Stein, Mater. Res. Bull. 34:471–482 (1999). G. Fu, C. A. Fyfe, W. Schwieger, and G. T. Kokotailo, Angew. Chem. Int. Ed. Engl. 34:1499–1502 (1995). R. A. Vaia, R. K. Teukolsky, and E. P. Giannelis, Chem. Mater. 6:1017–1022 (1994) and references therein.

190. 191. 192. 193. 194.

195.

196.

197. 198.

199. 200. 201. 202. 203.

204. 205. 206. 207. 208.

209. 210. 211.

212. 213. 214.

A. Galarneau, A. Barodawalla, and T. J. Pinnavaia, Nature 374:529–531 (1995). A. Galarneau, A. Barodawalla, and T. J. Pinnavaia, Chem. Commun. 1661–1662 (1997). M. E. Leonowicz, J. A. Lawton, S. L. Lawton, and M. K. Rubin, Science 264:1910 (1994). A. Corma, V. Fornes, S. B. Pergher, T. L. M. Maesen, and J. G. Buglass, Nature 396:353–356 (1998). W. J. Roth, C. T. Kresge, J. C. Vartuli, M. E. Leonowicz, A. S. Fung, and S. B. McCullen, Stud. Surf. Sci. Catal. 94:301–308 (1995). C. T. Kresge, W. J. Roth, K. G. Simmons, and J. C. Vartuli, U.S. Patent 5,229,341, Mobil Oil Corp. (1993). G. A. Ozin, E. Chomski, D. Khushalani, and M. J. MacLachlan, Curr. Opin. Colloid Surf. Sci. 3:181–193 (1998). T. Maschmeyer, F. Rey, G. Sankar, and J. M. Thomas, Nature 378:159–162 (1995). J. V. Walker, M. Morey, H. Carlsson, A. Davidson, G. D. Stucky, and A. Butler, J. Am. Chem. Soc. 119: 6921–6922 (1997). R. Burch, N. Cruise, D. Gleeson, and S. C. Tsang, Chem. Commun. 951 (1996). M. Morey, A. Davidson, H. Eckert, and G. Stucky, Chem. Mater. 8:486–492 (1996). B. J. Aronson, C. F. Blanford, and A. Stein, Chem. Mater. 9:2842–2851 (1997). T. Yanagisawa, T. Shimizu, K. Kuroda, and C. Kato, Bull. Chem. Soc. Jpn. 63:1535–1537 (1990). J. S. Beck, D. C. Calabro, S. B. McCullen, B. P. Pelrine, K. D. Schmitt, and J. C. Vartuli, U.S. Patent 5,145,816, Mobil Oil Corp. (1992). S. D. Sims, S. L. Burkett, and S. Mann, Mater. Res. Soc. Symp. Proc. 431:77–82 (1996). S. L. Burkett, S. D. Sims, and S. Mann, Chem. Commun. 1367–1368 (1996). D. J. Macquarrie, Chem. Commun. 1961–1962 (1996). C. E. Fowler, S. L. Burkett, and S. Mann, Chem. Commun. 1769–1770 (1997). (a) M. H. Lim, C. F. Blanford, and A. Stein, J. Am. Chem. Soc. 119:4090–4091 (1997). (b) M. H. Lim, A. Stein, Chem. Mater. 11:3302–3308 (1999). F. Babonneau, L. Leite, and S. Fontlupt, J. Mater. Chem. 9:175–178 (1999). M. H. Lim, C. F. Blanford, and A. Stein, Chem. Mater. 10:467–470 (1998). W. M. Van Rhijn, D. E. De Vos, B. F. Sels, W. D. Bosaert, and P. A. Jacobs, Chem. Commun. 317–318 (1998). M. H. Lim and A. Stein, Mater. Res. Soc. Symp. Proc. 519:89–94 (1998). K. Moller and T. Bein, Stud. Surf. Sci. Catal. 117:53– 64 (1998). B. C. Dave, B. Dunn, J. S. Valentine, and J. I. Zink, Anal. Chem. 66:1120A–1127A (1994).

Synthesis of Porous Inorganic Solids 215. 216.

217. 218. 219. 220. 221. 222.

I. Honma and H. S. Zhou, Chem. Mater. 10:103–108 (1998). R. Hoppe, A. Ortlam, J. Rathousky, G. Schulz-Ekloff, and A. Zukal, Microporous Mater. 8:267–273 (1997). B. T. Holland, C. Walkup, and A. Stein, J. Phys. Chem. B 102:4301–4309 (1998). J. F. Diaz and K. J. Balkus Jr., J. Mol. Catal. B Enzymatic 2:115 (1996). H. Yang, N. Coombs, and G. A. Ozin, Adv. Mater. 9: 811–814 (1997). M. Antonietti, B. Berton, C. Go¨ltner, and H. P. Hentze, Adv. Mater. 10:154–159 (1998). B. T. Holland, C. F. Blanford, and A. Stein, Science 281:538–540 (1998). B. T. Holland, C. F. Blanford, T. Do, and A. Stein, Chem. Mater. 11:795–805 (1999).

851 223.

224. 225. 226. 227. 228. 229. 230.

C. F. Blanford, T. N. Do, B. T. Holland, and A. Stein, in Mater. Res. Soc. Symp. Proc. (P. W. Lednor, D. A. Nagaki, and L. T. Thompson, eds.), MRS, Pittsburgh, 549:61–66 (1999). J. E. G. J. Wijnhoven and W. L. Vos, Science 281: 802–804 (1998). O. D. Velev, T. A. Jede, R. F. Lobo, and A. M. Lenhoff, Nature 389:447–448 (1997). O. D. Velev, T. A. Jede, R. F. Lobo, and A. M. Lenhoff, Chem. Mater. 10:3597–3602 (1998). A. Imhof and D. J. Pine, Nature 389:948–951 (1997). A. Imhof and D. J. Pine, Adv. Mater. 10:697–700 (1998). B. T. Holland, L. Abrams, and A. Stein, J. Am. Chem. Soc. 121:4308–4309 (1999). D. Zhao, P. Yang, D. I. Margolese, B. F. Chmelka, G. D. Stucky, Chem. Commun. 2499–2500 (1998).

Index

N-Acetyl-N-alkylglycosylamine, 112 N-Acetyl-N-alkyllactosyl amines, 113 CMC, 116 N-Acetyl-N-decyllactosylamine, 113 N-Acetyl-N-dodecyllactosylamine, 116, 117, 120 micelles, 119, 120 4-Acetyl-1-phenoxyalkyl salts electroreduction at Hg cathode, 316 micellar effects on pinacol/carbinol product distributions upon reduction at Hg cathode, 317, 318 Acetyl salicylate, 188 Acetylacetone, 833 Acetylphenoxyammonium salts suppression of autoinhibition by surfactants, 317 Acid Blue 25, 586 Acid catalysis of heterodimer surfactant cleavage, 83 Acid catalyzed hydrolysis of betaine esters, 47 Acid chlorides hydrolysis of, 197 Acid Yellow 1, 586 ACPA, 488 ACPD 4,4⬘-azobis-4-cyanopentanoic acid, 488 Acrylamide, 471, 474–476, 480, 482, 483, 485, 486, 488–490, 492, 495, 507, 531, 532, 533, 561, 562, 566 AM, 477 inverse emulsion polymerization of, 137 Acrylamide emulsion in o-xylene, 484 Acrylamidoundecanoate condensation onto hydroxylphenyldimethylsulfonium methyl sulfate, 559 Acrylate, 553

12-2-1, 2Br aggregate structure by AFM, 73 12-4-12, 2Br aggregate structure by AFM, 73 16-s-16, 2Br effect of spacer length on micellar morphology, 79 Abalone shell, 780 ABC templating, 806 ABC-templated silicates, 802 ABS acrylonitrile-butadiene-styrene, 547 see alkylbenzene sulfonates, 4 Acetal surfactants decomposition of, 53 Acetalization of glucose, 26 Acetals alkyl glucosides, 51 hydrolysis of, 189 Acetamide, 272 chemical trapping of, 291 in chemical trapping, 290 Acetate, 272, 603 Acetic acid, 272 Acetic anhydride in alkyl polyglycoside production, 26 Acetone, 521, 588, 594, 603 Acetonitrile, 588, 589 Acetophenone cathodic reduction of, 299 reduction on Hg cathode, 314 reduction on Pb cathode, 314 N-Acetyl-N-alkyl-glucosyl amines, 112 N-Acetyl-N-alkyl-lactosyl amines, 112 853

854 Acrylate emulsion polymerization, 568 Acrylic acid, 476, 488, 491, 495, 512, 551, 552 inverse emulsion polymerization in Isopar M, 489 Acrylic acid esters, 431 Acrylonitrile, 256, 559 in synthesis of ether carboxylic acids, 3 Acrylonitrile-butadiene-styrene ABS, 547 suspension polymerization, 563 Acryloyl, 503, 504 N-Acryloyl-1, 6-diaminohexane, 495 11-(Acryloyloxy)undecyl trimethylammonium (AUTMAB) in nanolatex formation, 559 Actin effect on vesicle morphology, 403 Active control of interfacial properties, 155 N-Acyl-N-alkylamino-1-deoxyglycitols, 112 N-Acyl-N-alkylamino-1-deoxy lactitols, 121 HIV activity, 121 N-Acyl amino acids, 13 1-Acyl-sn-glycerophosphocholines, 676 N-Acyl sarcosinates, 13 Acyclic acetal surfactants synthesis of, 52 Acyclic alcohols, 51 N-Acylthiazolidine-2-thiones, 112 Acylation of amino acids, 13 of glycosylamine, 112 of protein hydrolysates, 13 of sodium glutamate, 13 Addressable dewetting, 169 Admicellar polymerization, 537–544 Admicelle formation, 537, 538, 779 Admicelles of geminis, 72 Adogen 464, 377 ADPA p-aminodiphenylamine, 315 Adsolubilization, 537 of monomers, 538 Adsorption isotherms 12-2-12, 2Br gemini, 72 at solid-water interface, 71 DTAB, 72 Adsorption studies, 836 ADVN, 475, 476 2,2⬘-azpbis(2, 4-dimethylvaleronitrile-2), 485 Wako V-65, 485 AIBA, 474 AE see aliphatic polyoxyethylene alcohols, 18 PIT of, 18 Aerosol OT, 353, 596, 597

Index AES see alcohol ether sulfates, 1 see alkyl ether sulfates, 9 AFM, 541, 645, 650 12-s-12, 2Br aggregate structure, 73 atomic force microscopy, 510 bilayer formation, 72 in LB films, 48 of gemini adsorption, 72 Ag, 644 in LB films, 648 Ag nanoparticles, 635 AgBr, 615 AgBr particle precipitation, 614 AgBr particles diameter of, 612, 613 AgBr precipitation in reverse microemulsion, 612 AgCl, 617 AGE see alkyl polyglycoside esters, 29 Aggregate formation, 569 Aggregate structures on mica by AFM, 73 Aggregates supramolecular, 806 Aggregation nucleation in emulsion polymerization, 435 Aggregation number, 250, 706 of cationic surfactant oligomers, 80 AgI, 644 in LB films, 648 AgNO3, 611 AIBN, 131, 134, 137, 474, 4476, 483, 485, 489, 504, 566, 567 azobisisobutyronitrile, 481 AIDS, 111, 120 AIHEA, 474 Air–water interface nanoparticle synthesis at, 633–638 Air/DDO/TEG liquid crystal microemulsions, 839 Al, 838 Al(NO3)3 ⭈ 9H2O, 837 Al13, 840 Al2O3, 838 Al2Si6, 841 Al3⫹, 838 Al3Si5, 841 Al4Si4, 841 Al4Si4 (OH)O4⫺ 12 , 841 Alcohol by cathodic reduction of acetophenone, 299 Alcohol condensation in sol-gel processing, 803 Alcohol distribution in bicontinuous microemulsions, 288 in water-in-oil microemulsions, 288

Index Alcohol distribution constants in cationic microemulsions, 286 Alcohol ether sulfates (AES), 1 Alcohol ethoxylates, 2, 45, 48 conversion to alkyl ether sulfates, 9 Alcohol sulfates (AS), 1 Alcohols aliphatic, 1 ethoxylation of, 18 propoxylation of, 18 alkyl glucosides from, and glucose, 24 by oxo process, 18 by Ziegler process, 18 derived from natural fats, 18 derived from oils, 18 ethoxylation of, 15 Alcoholysis in sol-gel processing, 803 Aldehydes by hydrolysis of acetals, 51 Aldol group transfer polymerization, 555 Aliogen Red L 3870HD perylene vermillion, 409 Aliphatic alcohols, 1 by esterification of fatty acids and reduction, 18 by transesterification with methanol, 18 ethoxylation of, 18 propoxylation of, 18 Aliphatic ether sulfates from amidosulfonic acid sulfonation, 4 Aliphatic polyoxyethylene alcohols (AE), 18 cloud point of, 18 Aliphatic sulfonates, 6 Alkali-labile surfactants, 46 normal ester quats, 46 Alkaline hydrolyses, 210–211 Alkane sulfonates, 3 biodegradability, 6 by sulfochlorination, 6 by sulfoxidation, 6 Alkane thiolates, 845 Alkanes sulfochlorination of, 6 Alkanol amide sulfates from monoethanol amines, 11 Alkanol amide sulfation to give amide ether sulfates, 11 high viscosity, 12 Alkanol amides, 20 Alkanol XC, 581, 582, 595 Alkanolamine salts of phosphoric acid esters, 14 Alkenyl sulfonates in sulfonation of ␣-olefins, 7 1-Alkyl-4-alkylpyridinium halides, 192 N-Alkylamino-1-deoxyglycitols, 112

855 N-Alkylamino-1-deoxy lactitols, 112, 113, 121, 123 N-Alkylaminolactitols, 117 CMC, 116 micellization, 116 N-Alkyl-N-methyl-N,N-bis(3-carboxy-4iodoso)benzylammonium bromide, 378 N-Alkylglycosylamines, 112 N-Alkylpyridiniocarboxylate, 678 Alklylation with alkyl halides in preparation of phenolic ethers, 364 Alkoxylation to yield nonionic surfactants, 14 Alkyl acrylates, 508 Alkyl alcohol cosurfactant, 783 Alkyl allyl sulfonic acid HSAAS, 551 Alkyl aryl ketone photocleavage, 56 Alkyl aryl ketone sulfonate, 55 Alkyl benzene sulfonates, 45, 55 Alkyl chain length toxicological effects of, 34 3-Alkylcyclohexanones from alkyliodides, 310 Alkyl dimethylamine oxides, 20 Alkyl epoxides reaction with quaternary tertiary amines, 32 Alkyl ether sulfates, 27 AES, 9 by conversion of alcohol ethoxylates, 9 stability in detergent pastes, 28 Alkyl glucosides, 24, 51 from alcohols and glucose, 24 Alkyl halides, 427 hydrolysis of, 197 Alkyl maleate alkyl pyridinium bromide, 552 Alkyl maleate propyl sulfonate, 52 ␣-Alkylmaltoside, 117 Alkyl methacrylates, 508, 510 Alkyl phenols polymerization of, 516 Alkyl polyethylene glycol ethers, 27 stability in detergent pastes, 28 Alkyl polyglucosides in detergents combined with monoglyceride sulfates, 11 Alkyl polyglycoside derivatives, 1, 28 Alkyl polyglycoside esters AGE, 29 citrates, 29 sulfosuccinates, 29 tartrates, 29 Alkyl polyglycoside phosphates, 28 Alkyl polyglycoside sulfates, 28

856 Alkyl polyglycosides, 1, 24–26 applications of, 23 by acetalzation of glucose, 26 physicochemical properties, 27 production capacity, 23 stability in detergent pastes, 28 Alkyl polyoxyethylene carboxylic acids, 3 Alkyl pyridinium micelles, 181 Alkyl sulfates (AS), 9, 45 crystallization, 6 Alkyl tributylammonium bromides, 671 Alkyl(poly-1-oxapropen)oxaalkene carboxylic acids, 3 Alkyl-cobalt complexes, 328 Alkylamidobetaines stability in detergent pastes, 28 Alkylamidopropyl betaine structure, 34 Alkylarylsulfonates, 4 Alkylation of phenol, 365 Alkylbenzene sulfonates linear, 1 Alkylbenzenes sulfonation of, 5 Alkylene oxides, 14 Alkylphenol ethoxylates, 45 Alkylphenols polyoxyethylene, 1 Alkylphenyl ethers, 427 Alkylphosphate geminis, 63 N-(Alkyl)taurines from sodium 2-bromoethane-1-sulfonate with fatty amines, 63 in synthesis of taurine geminis, 63 Allyl, 844 2-Allyl-2-cyclohexenone, 310 Allylic surfmers, 551 AlSi7, 841 Alumina, 820 pseudoboehmite alumina, 838 Alumina fibrils, 653 Alumina-coated titanium dioxide, 563 Aluminophosphates, 839 lamellar, 839 Aluminum lakes, 586 Aluminum sulfate, 586, 820 AM, 477, 483 acrylamide, 477 polymerization, 481 Ambidextrous surfactants, 137, 138 in W/CO2 emulsions, 357 Amide ether sulfates alkanol amide sulfation, 11 Amide sulfates from alkanol amides, 11

Index Amidosulfonic acid ‘‘sulfamic acid,’’ 4 sulfonation of alkyl phenols, 4 sulfonation with, 4 Amine functionalized latexes, 482 Amine oxides, 20, 225 intermediates in betaine syntheses, 34 thermal decomposition, 20 Amine surfactants, 838 Amino acid–based geminis, 63, 64 4-Aminoantipyrene from electroreduction of NAP, 316 Amino headgroups, 832 2-Aminooctane, 274 Aminopropyl, 843 Ammonium peroxydisulfate APS, 480 Ammonium persulfate, 489 Amorphous, 577 Amphipathic polymers, 565 Amphiphilic block copolymers, 797–816 Amphiphilic color couplers, 598 Amphiphilic dendrimer G(3)G, 346 Amphoseife, 436 Amphoteric surfactants, 2, 34 as cosurfactants, 38 betaines, 34 ecological properties, 38 in shampoo combined with monoglyceride sulfates, 11 physicochemical properties, 38 properties of, 38 toxicological properties, 38 AMPS, 531 Andogen, 378, 464 Aniline, 476 inverse emulsion polymerization of, 494 Anionic alkyl polyglycosides applications of, 23 Anionic geminis, 61, 63 CMC, 98–102 structural types, 62 with hydrophilic spacers, 63 Anionic inisurfs, 552 2,2⬘-azobis(N-2⬘-methylpropanoyl-2-amino-alkyl-1sulfonate)s, 552 bis[2-(4⬘-sulfophenyl)alkyl]-2,2⬘-azodiisobutyrate ammonium salts, 552 Anionic Keggin ions, 839 Anionic pathway in carbon-carbon bond formation, 331 Anionic polymerization of 4-vinyl pyridine and t-butyl methacrylate, 563 Anionic polymerization stabilizers, 566

Index Anionic surfactants, 829 acetals, 51 alkyl benzene sulfonates, 45 alkyl ether sulfates, 2 alkyl sulfates, 2, 45 carboxylates, 2 linear alkyl sulfates, 2 soaps, 2 sulfosuccinates, 8 Anionic surfmers, 552 alkyl maleate propyl sulfonate, 552 hemiester of maleic anhydride, 552 sodium 11-crotonoyl undecan-1-oyl sulfate, 552 sodium 11-methacryloyl-undecan-1-oyl sulfate, 552 Anionic–nonionic geminis, 65 Anisaldehyde, 300 Anodic cyanation of aromatics in microemulsions, 309 of 1,3-dimethoxybenzene to give 2,4-dimethoxybenzonitrile, 308 of 1,2-DMB effects of product partitioning, 317 Anodic nitration of aromatics, 307 of naphthalene in Brij 35 micelles, 308 of NDMA, 315 of N,N-dimethylaniline, 311 Anodic oxidation, 298 of butylbenzene, 299 of MBT to yield DBDS, 315 of SCN-, 302 of toluene, 306 Anodic thiocyanation of aromatic amines and phenols, 307 Antarox CO880, 38 Anthracene, 603 Anti-HIV activities of catanionic geminis, 126 Antifungal activity, 120 Antioxidants membrane localized, 145 Antistat additives ethoxylated amines, 20 Antistats ether carboxylic acids, 3 Antiviral activity, 120 Antiviral drugs, 112 AOMe-14, 198, 225 myristyldimethylamine oxide, 176 myristyldimethylamine N-oxide, 236 AOPr-14, 198 myristyldipropylamine N-oxide, 236

857 AOS see ␣-olefin sulfonates, 6 AOT, 236, 477, 478, 483, 484, 488, 515, 517, 520, 533, 602, 614–616, 622, 699 sodium bis(2-ethylhexyl sulfosuccinate), 475 micelles, 191, 481 AOT/heptane/water systems, 609 APE see polyoxyethylene alkyl phenols, 18 APG, 1, 2 see alkyl polyglycosides, 1 APS, 481, 488, 566, 567 ammonium peroxydisulfate, 480 Aquatic toxicity ester quats, 46 Aqueous micellar aggregates, 177 Aquersymer dispersion process, 551 Arabinofuranosyl cytosine (AraC), 49 AraC see arabinofuranosylcytosine, 149 cytotoxicity, 151 Arachidic acid, 635, 644 monolayer, 635 Aragonite, 813 Arcs, 834 Arctic Syntex L coconut monoglyceride, 11 Arctic Syntex M coconut monoglyceride, 11 Area-difference elasticity model of bilayer membranes, 397 Arenediazonium ion, 272 chemistry, 268 Arginine-based geminis, 70 Arlacel 83, 478 sorbitan sesquiolate, 474 16-ArN2⫹, 274 1-ArN2BF4, 268 16-ArN2BF4, 268 Aromatics anodic nitration of, 307 Array colloidal crystalline, 806 Aryl-2,2,2-trichloroethanols, 182 decomposition of para-substituted, 191, 192 AS, 1 see alkylsulfates, 9 Ascorbic acid vitamin C, 290 AscP, 587 Aspergillus fumigatus, 111, 120 Association colloids, 266 Associative thickeners, 561 ASTM D2024, 18 Asymmetric gemini cationic surfactant mesophase, 825

858 Asymmetric geminis, 67 Atomic force microscopy, AFM, 72, 510 ATR-FTIR, 822 Au, 644, 653 Au nanoparticles, 635, 655 TEM, 645 AUTMAB 11-(acryloyloxy)undecyl trimethylammonium in nanolatex formation, 559 Autocatalysis micellar, 413–428 of lipid aggregation, 403 Autoclaving, 596 Auxiliary solvent, 579–581, 584, 588, 592 influence on precipitation in microemulsions, 627 toluene, 583 Azo dye method for measurement of dediazonation rate constants, 277 Azobenzene, 678 photoactivity, 166 Azobenzene-based surfactants, 165, 171 4,4⬘-Azobis-4-cyanopentanoic acid ACPD, 488 2,2⬘-Azobis(2,4-dimethylvaleronitrile-2) ADVN, 485 Azobisisobutyronitrile AIBN, 481 2,2⬘-Azobis(N-2⬘-methylpropanoyl-2-amino-alkyl-1-sulfonate)s, 552 AZOH 4-[(4-hexylphenyl)azo]phenol in electroless plating, 407 AZPEG, 410, 411 in CuPc film preparation, 409 preparation from AZOH, 407 synthesis scheme, 408

B, 838 BA see butylacrylate, 132 Bacterial adhesion, 112 Bacteriocides cationic geminis, 59 BAM N,N⬘-methylenebisacrylamide, 483 Bancroft rule, 350, 473 Band gap energy CdS, 646 Base catalyzed hydrolysis of betaine esters, 47 Batch emulsion polymerization of styrene, 555 Batch process emulsion polymerization, 433 Batch solvent shifting precipitation, 590

Index BCAT synthesis, 153 Behenic acid, 643, 644 Belousov–Zhabotinsky reaction, 222 Bending modulus, 467 Benzaldehye oxidation to benzoic acid, 301 Benzene, 476, 782, 785, 786 Benzene/water interface, 786, 789–792 Benzensulfonates, 181 Benzoic acid, 425 from oxidation of benzaldehyde, 301 Benzyl alcohol electrooxidation on nickel anode, 305 indirect oxidation to benzaldehyde, 300 N-␣-Benzoyl-DL-arginine-4-nitroaniline, 845 Benzoyl chloride hydrolysis in W/CO2 microemulsions, 351 Benzoyl peroxide, 486 BPO, 480 Benzyl chloride conversion to benzyl bromide in W/CO2 microemulsions, 352 Benzyl chloride and KBr reaction in W/CO2 microemulsions, 363 Benzylideneaniline, 678 BET, 541 BET surface area, 840 BET surface area of silicas, 805 Betaine ester hydrolysis, 47 Betaine esters, 47 as PTC, 31 sensitivity to hydrolysis, 33 Betaines, 34 alkylamidopropyl, 34 structure of, 34 BHA, 290 Bibenzyl formation from benzyl bromide, 331 Bicontinuous cubic liquid crystals, 527 Bicontinuous cubic phase, 669, 674, 785 polymerization in, 530 Bicontinuous gels polymerization in, 530 Bicontinuous microemulsions, 374, 376, 455, 477, 602 alcohol distribution in, 288 continuous hydrogel synthesized in, 495 electroorganic synthesis in, 296 polymerization in, 530 templating, 532 Bilayer, 228, 634 formation, 679 forming amphiphiles, 685 templating, 839

Index Bilayers coaxial cylindrical, 838 Bimolecular eliminations by hydroxide, 209 Bimolecular nucleophilic substitutions, 201–208 Bimolecular reactions, 199 kinetic analysis, 251 other, 212–220 Binary phase diagrams, 808 block copolymer/water, 807 of DDAB, 683 of N-dodecylpyridinio-3-carboxylate, 679 of N-dodecylpyridinio-4-carboxylate, 679 of trisiloxane surfactants, 677 PB202PEO360/water, 809 Binders latex, 548 Biocides ester quats, 34 Biodegradability, 1 ester quats, 31, 34, 46 of alkane sulfonates, 6 of dioxolane surfactants, 53 of sulfosuccinic acid dialkyl esters, 9 of sulfosuccinic acid monoalkyl esters, 9 Biodegradable surfactants, 45 Biomimetic crystallization, 813, 816 Biomimetic mineralization, 813 Biomineralization of sea shells, 814 Biosurfactants, 2 Biphasic hydrolysis of ethyl hexanoate, 421 BIPO 1,3-bis(1-imidazolyl)-2-propyl octadecanoate, 671 N,N⬘-Bisacrylamide, 495 1,3-Bis(N-cetyl-N,N-dimethyl-ammonium)-butane dibromide (CDA)2C4 2Br, 236 1,3-Bis(N-cetyl-N,N-dimethyl-ammonium)-propane dibromide (CDA)2C3 2Br, 236 Bis(2-chloroethyl)sulfide mustard (HD), 374 Bis(2-ethylhexyl) sodium sulfosuccinate AOT, 236 Bis(dimethylamino)heptamethine, 605 Bisfurylalkanes, 844 Bis-gluconamido alkanes, 114 N,N-Bishydroxyethyl tall oil amide, 489 1,3-Bis(1-imidazolyl)-2-propyl octadecanoate BIPO, 671 Bis-lactobioamido alkanes, 114 Bis-lactobionamido alkanes surface tension, 117 Bis[2-(4⬘-sulfophenyl)alkyl]-2,2⬘-azodiisobutyrate ammonium salts, 552 Bjerrum length in cationic surfactant oligomers, 81

859 BLL reaction, 413 Block copolymerization living anionic ring opening of butylene oxide/ethylene oxide, 555 Block copolymers for titanium dioxide stabilization, 563 self-assembled particles, 590 nanostructure design with, 797–816 Blood serum colloidal stabilizer, 562 Bola-amphiphiles, 113 dissymmetric synthesis of, 115 Bolaform disulfide containing, 155 Bolaform (n) X2 Me3N⫹(CH2)nN⫹Me3 2X⫺, 236 Bolaform disulfide surfactants, 161 Bolaform surfactant, 111 loss of conformational entropy, 77 Bone mimetic system, 839 Borohydride reduction of dicarbonyls, 379 of monocarbonyls, 379 Borosilicate glass, 779, 781, 789, 794 mesoporous silica films on, 788 Bottom-up synthesis, 797 Bovine serum albumin (BSA) in W/CO2 microemulsions, 353 BPO, 475, 481 benzoyl peroxide, 480 Brewster angle, 634 Bridging flocculation, 552, 569 Brij, 176 Brij 30 polyethylene glycol dodecylether, 475 Brij 35, 312, 411 Brij 96, 377 Bromination in titration of double bonds, 459 Bromoacetal electroreduction of, 332 radical cyclization of, 332 1-Bromobutane, 363, 364, 367 alkylation of phenol with, 365 conversion to butanol, 366 (4-Bromobutyl)-2-cyclohexene-1-one conversion to 1-decalone in microemulsions, 331 2-(4-Bromobutyl)-2-cyclohexenone intramolecular cyclization, 310 o-3-Bromopropoxyphenoxide, 196 2-(3-Bromopropyl)-2-cyclohexenone 5 endo trig cyclization of, 310 Bronstead equation, 190, 191

860 Bronze Violet GI Methyl violet Lake, 409 BTHA, 166 BuA butyl acrylate, 555 Butadiene, 436, 503, 550, 540 1,3-Butadiene, 540 1-Butanol, 186, 366, 376–379 Butanol distribution in CTAB microemulsions, 287, 288 Butyl acrylate, 131, 256, 551, 552, 554 t-Butyl alcohol, 476, 566 p-t-Butylbenzaldehyde by anodic oxidation of butylbenzene, 299 Butylbenzene anodic oxidation of, 299 t-Butyl-2-benzothiazolesulfenamide TBBS a rubber accelerator, 315 Butyl bromide reduction in DDAB/water/dodecane microemulsions, 330 N-Butyl formamide NBF, 77 t-Butylhydroquinone TBHQ, 290 Butyl methacrylate, 532 n-Butyl methacrylate, 434, 467, 468, 566 t-Butyl methacrylate, 467, 468 t-Butylmethylether TBME, 298 2-t-Butylphenol ECH of in emulsions, 313 Butylene oxide, 549 block copolymerization of, 555 Butylphenyl ether, 363, 365 synthesis of, 364 BVEP 1,2-di-O-(1⬘,9⬘-octadecadienyl)-sn-glycero-3-poly(␻methoxyethylene[115]glycol)ate, 150, 152 C10E4, 183, 279 decyltetraoxyethylene glycol ether, 236 C10MA didecyldimethylammonium methacrylate, 476 C11–15H23–31O(CH2CH2O)12H Tergitol 15-S-12, 828 C12E6, 279 phase diagram in water, 670 C12E7 dodecylheptaoxyethylene glycol ether, 198, 236, 254 C12E10 dodecyldecaoxyethylene glycol ether, 236 C12E12 phase behavior, cubic phases in, 672 C12E23, 195 dodecyltricosanoxyethylene glycol ether, 236

Index C12Ey, 259 C12TAC, 781–783, 786, 789 C12TMA⫹, 835 C14NPe3Br tetradecyl tripentylammonium bromide, 671 C14TAC, 781, 783, 786, 789 C16E8, 279 C16E20 cetyleicosanoxyethylene glycol ether, 236 C16H33(CH3)2N, 828 C16PhyPC, 690 C16TAC, CTAC, 784, 786–788, 789 C16TMABr, 843 C20PhyPC, 690 C4EO-water-dodecane, 675 C6EO2-water phase diagram, 704 C6EO3-water phase diagram, 704 C7EO3-water phase diagram, 704 C7F15CH(OSO3Na)C7H15, 139 C7H15CH(SO3⫺ Na⫹)C7H15, 350 CAC, 694 Cadmium arachidic films H2S reaction, 643 Calcein, 149 leakage from DPPlsC liposomes, 150 photorelease from liposomes, 148 release kinetics, 152 Calcination, 808, 821, 830, 835, 836, 843 Calcite, 813 Calcium carbonate, 813 hollow spheres, 815 rhombohedral crystals, 815 spheres, 814, 815 twins, 815 Calcium dodecylphosphate lamellar phase, 839 CAM cetylammonium, 841 CAM/Al4Si4, 841 Capillary arrays, 155 Capillary hydrodynamic chromatography particle sizing by, 460 Carbohydrate-based geminis, 63 Carbohydrate-based surfactants, 1, 20 glucose esters, 2 sorbitan esters, 2 sucrose esters, 2 Carbon black, 410 Denka black, 409 Toka black 7550F, 409 Carbon bond formation by electrochemical catalysis in microemulsions, 310

Index [Carbon bond formation] in microemulsions electrochemically driven, 309, 310 Carbon dioxide, 591, 592 Carbon-carbon bond formation, 331, 332 cyclizations, 331 mediated electrochemical synthesis of, 328 unsymmetrical, 331 Carbonates monoalkyl, 48 5(6)-Carboxyfluorescein, 690 6-Carboxy fluorescein, 605 Carboxy functionalized latexes, 482 Carboxylate in anionic geminis, 61 Carboxylate geminis, 71 Carboxylation of fatty acid derivatives, 2 of phosphoric acid derivatives, 2 Carboxylic acids, 123 alkyl(poly-1-oxapropen)oxaalkene, 3 alkyl polyoxyethylene, 3 ether, 3 short ether, 3 Carboxylic groups conductometric titration of, 555 Carboxymethyl cellulose dispersion polymerization stabilizer, 566 Carboxymethylation of fatty alcohol ethoxylates with monochloroacetic acid, 3 Carbozole, 603 ␤-Carotene, 603 ␤-Carotenoids, 587 as fat constituents, 3 Carpet shampoos sulfosuccinate dialkyl esters, 9 Carvonce ECH of, 312 Cascade release of calcein from liposomes, 150 of Ca2⫹ from liposomes, 150 Cascade triggering in liposomes, 149 Cast bilayer films, 653 Casting lost-wax, 807 Castor oil ethoxylation of, 20 sulfation of, 10 Catalysis micellar, 377 Catalysts, 609 Catalytic electrodes in microemulsions, 333

861 Catalytic films on electrodes in microemulsions, 324 Catalytic hydrogenation of D-glucose, 64 Catalytic hydrolysis, 378 Catalytic reduction of DBCH in bicontinuous microemulsions, 328 Catanionic geminis anti-HIV activities, 126 synthetic scheme, 125 Catanionic glycolipids, 123 Catanionic surfactants, 166 CATC, 379 Cathodic reduction of acetophenone, 299 Cationic surfactants, 829 Cationic geminis, 63 arginine based, 70 CMC, 88–97 ferrocenyl, 65 structural types, 61 synthesis, 60 Cationic initiator (2,2⬘-dimethyl-2,2⬘-azo-N-benzylpropionamidine) hydrochloride, 569 Cationic micelles degree of ionization, 283 Cationic microemulsions alcohol distribution constants, 286 Cationic surfactant mesophase asymmetric gemini, 825 conventional alkyltrimethylammonium, 825 conventional dialkyldimethylammonium, 825 symmetric gemini, 825 Cationic surfactants, 30 alkyl quats, 45 dialkyl quats, 45 ecological behavior, 33 physicochemcial behavior, 33 polymeric, 31 separation of ergot alkaloids by MEKC, 86 toxicological behavior, 33 Cationic surfmers, 552 alkyl maleate alkyl pyridinium bromide, 552 alkyl maleate trimethylamino ethyl bromide, 552 Cationic vinyl ether lipids, 152 Cationic-anionic geminis, 65 CB1-14 myristyldimethylammonium carboxybetaine, 195, 236 CB1-16 cetyldimethylammonium carboxybetaine, 195, 236 CCl4/water emulsions, 305 (CDA)2C2 2Br, 195 (CDA)2C3 2Br 1,3-Bis(N-cetyl-N,N-dimethyl-ammonium)-propane dibromide, 236

862 (CDA)2C4 2Br, 229 1,3-Bis(N-cetyl-N,N-dimethyl-ammonium)-butane dibromide, 236 Cd arachidic film, 646 FTIR of, 649 Cd behenate, 651 Cd behenate films, 645 Cd nonacosa-10, 12-diyonate LB films, 643 Cd stearate, 651 Cd(DTG)2, 653 Cd(OH)2, 660 CdB2, 644 CdC2, 644 CdI2, 644 CdO, 643 CdS, 519, 630, 643, 644, 653, 654, 660, 800 films, UV-vis spectra, 655 grown in Cd arachidate films, 647 in arachidate films, UV-vis spectra, 647 in LB films, 648 in Nafion films, 657 nanoparticles, 635 synthesis in W/CO2 microemulsions, 354 UV-vis spectra in Nafion films, 652 UV-Vis spectra in W/CO2 microemulsions, 355 particles in Nafion films, 652 stabilized by mercaptoethanol, 658 CdS/arachidate films, 650 CdS/CdSe, 644 CdS/glutaraldehyde films, 657 CdS/HgS, 644 CdS/HMP films, 658 CdS/ME films, 658 CdS/ME/PDADMAC LbL films, 659 CdS/Nafion films, 659 CdS/PbS, 644 CdS/Pt particles in Nafion films, 652 CdS/ZnS, 644 particles in Nafion films, 652 CdSe, 643, 644, 653 nanoparticles, 635 particles in Nafion films, 652 CdTe, 643, 644 Ce, 838 Ce(III)/Ce(IV) couple, 300 CEES, 380 2-chloroethylethyl sulfide, 379 Cell surface oligosaccharides, 112 Cellulose acetate butyrate dispersion polymerization stabilizer, 567 Centrifugation particle sizing by, 460 CeO2, 653 CER, cohesive energy ratio, 478 Ceramic materials, 609

Index Cerebrosides as fat constituents, 3 Ceric ion redox systems, 567 Cetyl alcohol in miniemulsion polymerization, 560 Cetylammonium CAM, 841 Cetyldimethylamine, 828 Cetyldimethylammonium carboxybetaine CB1-16, 236 Cetyleicosanoxyethylene glycol ether C16E20, 236 Cetylpyridinium chloride CPCl, 236 Cetylquinuclidinium chloride CQCl, 236 Cetyltrimethylammonium 4-vinylbenzote CTVB, 600 Cetyltrimethylammonium sulfate CTA(SO4)0.5, 236 Cetyltrimethylammonium tosylate CTAT, 601 CF-MPA dimorpholinophosphoramidate, 680 CH2Cl2, 302 [C12H25N(CH3)3]0.5(MoO3.25), 839 [C12H25N(CH3)3]2/3V2O5.⭈33.H2O, 839 [C12H25N(CH3)3]6(H2W12O40)⭈xH2O, 839 (C19H42N)6(H2W12O40), 839 Chain transfer agent, CTA, 444 Chainlike polymerization of silica, 826 Charge density matching, 822 CHCl3/water emulsions, 305 Chemical activation in surfactant solutions, 337–347 Chemical capping, 643 Chemical detoxification in surfactant systems, 373–393 Chemical potential during swelling of polymer particles, 440 of monomer is the micelles, 467 of surfactants, 69 Chemical reduction of disulfide, 162 Chemical stabilization, 599 Chemical trapping, 265–291 alcohol distribution constants from, 286 in ionic surfactants, 280 Chimeric lipids C16PhyPC, 692 C20PhyPC, 692 Chiral biphenyl in synthesis of chiral cationic geminis, 65 Chiral geminis, 65 Chloracetic acid esters quaternization of tertiary amines, 33

Index Chloramphenicol, 603 Chlorination of amine hydrochlorides electrochemical, 305 Chloroacetate as alkylating agent in betaine synthesis, 34 p-Chlorobenzoates, 181 2-Chloroethylethyl sulfide CEES half mustard, 379 Chlorofluorocarbons, 129 1-Chloro-2-hydroxypropane sulfonate in preparation of sulfobetaine as alkylating agent, 35 3-Chloro-2-hydroxypropyltrimethylammonium chloride reaction with alcoholic groups alternative quaternization route, 33 2-Chloronitrobenzene, 316 Chlorosulfonates in preparation of sulfobetaines, 35 Chlorosulfonic acid, CSA, 4 in sulfonation, 4 Chlorotrifluoromethane, 591 Chlorotrimethylsilane, 843 CnH2n⫹1NH(CH2)2NH2, 835 Cholesterol, 625 nanoparticles, 624 Cholesteryl acetate, 583 Choline esters, 46 hydrolysis of, butyrylcholinesterase catalysis of, 46 structure of, 47 Choline tosylate, 147 Chrysotile, 838 CnH2n⫹1-trimethylammonium, 823 Citrates alkyl polyglycoside esters of, 29 Classical nucleation theory in emulsion polymerization, 435 Clay particles, 653, 656 Clays, 841 contaminated dechlorination of, 380 pillared, 831 Cleavable heterodimer surfactant, 83 Cleavable surfactants, 45, 65 acetals, 51 decomposition of, 53 acid-labile, 49 acyclic alcohols, 51 alkali-labile, 46 alkyl glucosides, 51 chemodegradable, 56 cyclic acetals, 49 dialkylester quats, 46 hydrolysis of N — —C containing surfactants, 56 hydrolysis of sulfone containing surfactants, 49 ketals, 53 Norrish type II cleavage, 55

863 [Cleavable surfactants] ortho esters, 54 ozone-cleavable spacer, 65 photodegradation of diazosulfonates, 57 second-generation, 53 hydrolysis of, 54 splittable, 56 triggering of phase transitions, 145 UV labile, 55 with ethylenesulfone moiety, 48 with N — —C bond, 54 with polyoxyethylene chains, 52 with Si — O bond, 48 Cloud point, 279, 376 ASTM D2024, 18 CLSM, 511 confocal laser scanning microscopy, 510 Clusterlike agglomeration, 826 CMC, 177, 416, 538, 667, 680, 804, 825 8-s-8, 2Br, 88 10-s-10, 2Br, 89 12-s-12, 2Br, 89 12-s-12, 2Cl, 89 16-s-16, 2Br, 90 N-acetyl-N-alkyllactosylamines, 116 N-alkylaminolactitols, 116 anionic geminis, 98–102 cationic geminis, 88–97 effect of alkyl chain length, 77 effect of headgroup on gemini, 76 effect of oligomerization degree, 78 effect of spacer length in gemini, 76 Monte Carlo simulation of gemini, 76 nonionic geminis, 102, 103 of bolaform surfactants effect of alkyl chain length, 77 of gemini surfactants, 76, 416 alkyl chain length dependence, 74 effect of spacer length, 77 of surfactant dimer, 75 oligomeric surfactants anionic trimers, 104 cationic trimers, 103 CMD see critical micelle density, 140 CO, 642 Co(DS)2, 258 Co(salen), 328 CO2 phase diagram, 130 supercritical, 129 Co2⫹, 838 Coagulants, 494 Coagulation concentration, 569 Coagulum formation in dispersion polymerization, 560 Coalescence in emulsion polymerization, 445

864 [Coalescence] in inverse emulsion polymerization, 487, 488 of latexes, 548 Coalescence rate effect on by cationic geminis, 79 Coating dip, 780 spin, 780 Coatings conductive waterborne, 562 Coaxial cylindrical bilayers, 838 Cobaloximes, 328 Cobalt boride, 618, 620 Cobalt-nickel boride particle size, 621 Cocoamidopropyl betaine properties of, 39 Cocoamphoacetate properties of, 39 Cocobetaine properties of, 39 Coconut monoglyceride sulfate in shampoo, 11 Coconut oil in isethionates, 12 sulfation of, 10 Cocoyl sarcosinate, 13 Cohesive energy ratio (CER), 473 Coin reactions, 188 Colloid mills, 581 Colloidal assembly of latexes, 806 Colloidal crystalline array, 806 Colloidal metal particle synthesis in gemini solutions, 86 Colloidal silica, 820 Colloidal stabilizers blood serum, 562 egg albumin, 562 gelatin, 562 starch, 562 Color filters by contact plating, 411 Color Index pigments, 577 Color instant image dyes, 587 Comminution, 577, 595, 596 Compartmentalization, 377, 577, 578 Component exchange among pseudophases in electroorganic synthesis, 325 Composites conductive, 543 containing heteroatoms, 838 epoxy-glass mat, 543 nickel flake, 544 polymer matrix, 542 Condensates protein/fatty acid, 13

Index Condensation, 580 esterification, 554 of carboxylic acids onto hydroxylphenyldimethylsulfonium methyl sulfate, 559 of fatty acid derivatives, 2 of glucose and long-chain alcohols, 51 of phosphoric acid derivatives, 2 of TAOS, 844 Condensation polymerization, 446 Condensation reactions, 844 Conductimetric titration of carboxylic groups, 555 Conductimetry, 491 Conductive composites, 543 Conductive microemulsion suitability for electrochemical syntheses, 324 Conductivity continuous phase characterization in emulsions, 366 electrical in organic phases, 301 in emulsion polymerization, 435 Confocal laser scanning microscopy, CLSM, 510 Confocal microscopy, 395 of giant vesicles of mixed phospholipids, 401 Conformational entropy of gemini headgroup, 76 Contact angles, 171 Contact plating, 408 Continuous particle nucleation, 480 Continuous process emulsion polymerization, 433 Contrast agents radiographic, 596 Control of particle size, 643 Controlled crystallization, 813 Controlled-pore glass, CPG, 801 Conventional alkyltrimethylammonium cationic surfactant mesophase, 825 Conventional dialkyldimethylammonium cationic surfactant mesophase, 825 Cooperative nucleation, 821 Copolymerization inverse emulsion, 489 of hydrophilic mon0mers, 482 of vinyl acetate/N-vinyl formamide, 569 Copper nanoparticles in ethane extinction vs time, 355 in liquid isooctane extinction vs time, 355 synthesis in W/propane microemulsions, 354 ␤-Copper phthalocyanine (CuPc) in electroless plating, 408 Copper triflate in boomerang scrolls, 694 Coprecipitation, 586

Index Core shell polymerization seeded, of styrene/butyl acrylate, 555 Core-shell styrene/butyl acrylate/acrylic acid, 552 Core-shell latex, 550 Corrosion inhibitors ether carboxylic acids, 3 Cortisone, 603 CoS, 644 Cosurfactants, 378 alcohols as, 482 alkyl alcohol, 783 amphoteric surfactants as, 38 Coulomb interactions, 797 Coulombic, 826 Counter ion exchange and affinity in micelles, 285 Counter ions polymerizable in vesicles, 507 Coupler dispersion particles, 580 Coupler dispersions, 582 Couplers photographic, 581, 588 amphiphilic, 598 Coupling with oxidized developers, 580 CPCl, cetylpyridinium chloride, 236 CPG controlled-pore glass, 801 CQCl, cetylquinuclidinium chloride, 236 Critical micelle concentration (CMC), 73 Critical micelle density (CMD), 140 Critical packing parameter, 702 Cromofine blue 4920 phthalocyanine blue G, 409 Cromofine blue B145 phthalocyanine blue R, 409 Cromofine Red 6820 Dioxazine violet, 409 Cromofine yellow 5910 cromophtal yellow GR, 409 Cromophtal Red A3B dianthraquinoyl red, 409 Cromophtal blue A3R Indanthron blue, 409 Cromophtal yellow GR Cromofine yellow 5910, 409 Cross-linked micelles in catanionic gemini solutions, 84 Cross-linked poly(alkyl methacrylates), 511 Cross-linking in vesicular polymerization, 510 Crosslinker BAM, 483 Cryo-TEM, 461, 595, 681, 695, 810, 822 of gemini wormlike micelles, 83

865 [Cryo-TEM] of liposomes, 148 of surfactant oligomeric micelles, 79 Crystal violet, 188 Crystalline, 577 Crystalline array colloidal, 806 Crystallinity, 791 Crystallization, 577, 583 biomimetic, 813 of alkyl sulfates, 6, 10 CTA, chain transfer agent, 444 CTA ions, 840 CTA surfactants, 844 CTA(SO4)0.5, 195 cetyltrimethylammonium sulfate, 236 CTA⫹, 828 CTA/Al4Si4, 841 CTAB, 176, 181, 183, 185, 186, 188, 195, 196, 198, 226, 233, 253, 259, 267, 284, 312, 314, 316, 324, 376–378, 379, 380, 475, 478, 559, 695–697, 779, 824, 825, 828, 834 cetyltrimethylammonium bromide, 236 Kraft point, 276 micelles p-menthane from D-limonene, 313 phase diagram, 668 CTAB-SOS-water ternary phase diagram, 696 CTAC, 181, 185, 186, 191, 195, 198, 232, 280, 283, 327, 363–368, 377, 379, 781, 783, 822, 828, 832, 834, 835, 837, 844 cetyltrimethylammonium chloride, 236 CTANO3, 195 cetyltrimethylammonium nitrate, 236 CTAOAc, cetyltrimethylammonium acetate, 236 CTAOH, 183, 185, 186, 226, 232, 601, 697, 822 CTAOMs, 198 CTAT, 696, 697 cetyltrimethylammonium tosylate, 601 CTAT-SDBS-water phase diagram, 698 CTAX, 314 CTBAB, 196, 198 CTBAX, 225 CTEAB, 196, 198 CTEABr, 186 CTPAB, 196 CTPAOH, 226 CTPAX, 225 CTVB, cetyltrimethylammonium 4-vinylbenzote, 600 rodlike micelles, 601 Cu, 644 Cu behenate, 651 films, 645 Cu(AOT)2, 354 Cu(DS)2, 258, 259

866 Cu(II), 603 Cubes, 813 Cubic, 668 Cubic bicontinuous phase of geminis, 85 Cubic films mesoporous silica, 788 Cubic MCM-48 phase, 823 Cubic mesoporous silica films, 790 Cubic phase of lauroyl lysophosphocholine, 677 of myristoyl lysophosphocholine, 677 of palmitoyl lysophosphocholine, 677 Cubic surfactant structures, 784 CuPc, 411 ␤-copper phthalocyanine, 408 films, 409 Current efficiency effects of solubility, 298 in emulsions, 316 Curvature spontaneous, 703 Curvature control in microemulsion polymerization, 460 CuS, 644 CuS nanoparticles, 653 Cutting oils sulfated oils, 10 CYAB, 540 Cyanide, 378 Cyanoethyl, 843 Cyclic acetals, 49 Cyclic voltammograms CdS nanoparticles in arachidic films, 657 Cyclization reactions, 195 Cyclohexane, 475, 476, 490, 491 Cyclohexanol, 475, 478 Cyclohexanone, 580 Cyclohexylcarbodiimine, 548 Cyclopentadiene, 248, 252, 256 Cylindrical micelles, 808 of nonionic sugar-based geminis, 80 silica coated, 821 Cytochrome c, 845 Cytotoxicity of AraC, 151

Daxad 11G, 585 DBCH trans-1,2-dibromocychlohexane, 328 DBDS di-2-benzothiazole, 315 reaction with TBA to give TBBS, 315 DBF, 378 DBS, dodecylbenzenesulfonate, 318 DBSA, dodecyl benzenesulfonic acid, 839 DCAT, 153

Index DDAB, 312, 314, 324, 327, 397, 457, 460, 651, 683, 684, 698 didocecyldimethylammonium bromide, 296 giant vesicles, 397 phase diagram, 683 systems, p-menthane from D-limonene, 313 vesicles, 402 DDAB-AOT-water phase diagram, 699 DDAB-LC11C9-water phase diagram, 700, 701 DDAB-SDS-D2O phase diagram, 698 DDAB-SDS-water system, 699 DDAB-water binary phase diagram, 699 DDAB/AOT mixture reverse hexagonal phase, 700 DDAB/SDS mixture lamellar phase, 700 DDAC, dioctyldecylammonium chloride, 643 DDAO, 365–368 dimethyldodecylamine oxide, 363 DDAOT, didodecyldimethylammonium bis(2ethylhexyl)sulfosuccinate, 699 hydrated crystals, 699 DDDACl, didodecyldimethylammonium chloride, 176 Dimyristoyl phosphatidylcholine, DMPC, 511 DDP, decylammonium dihydrogenphosphate, 839 DDT, 1,1,1-trichloro-2,2-bis( p-chlorophenyl)ethane, 188 Deacylation, 197 Deamination of 1-octamine, 235 Debenzylation, 694 Debye-Hu¨ckel approach, 191 1-Decalone from intramolecular cyclization of 2-(4-bromobutyl)-2cyclohexenone, 310 Decane, 475 n-Decanol, 781 Decarboxylation, 196, 231 counter ion effect, 194 dicationic surfactants as catalysts, 196 of bound substrates, 192 of 6-NBIC, 191, 192 of tetradecyloxy derivative of 6-NBIC, 230 Decene-1-yl condensation onto hydroxylphenyldimethylsulfonium methyl sulfate, 559 Dechlorination 4,4⬘-dichlorobiphenyl catalytic electrochemical, 380 of arochlor-contaminated clays, 380 Decyl trimethylammonium bromide, 165 1-Decyl-3-amido pyridine, 378 Decylammonium dihydrogenphosphate, DDP, 839 Decyltetraoxyethylene glycol ether, C10E4, 236

Index N-Decyl deoxy-1-lactitol amine, 116 N-Decylaminolactitol, 120 Dediazonation rate constants measurement of, 277 Dediazoniation, 265 Dediazoniation reactions, 268 Defect-free supramolecular system, 802 Deformation energy of latex films, 554 Dehalogenation of organohalides in microemulsions, 309 Dehydration of 2-methylbut-3-yn-2-ol, 842 Dehydrochloronation, 185 Dehydrohalogenation base catalyzed, 302 Dendrimer amphiphilic G(3)G, 346 Dendritic micelles, 139 Dendritic surfactants, 139 Denka black carbon black, 409 DePEGylation, 151 DePEGylative triggering of DOPE: vinyl ether-PEG liposomes, 150 Dephosphorylation of bound substrates, 192 Depletion flocculation, 562 Depletion stabilization, 562 Design of inorganic nanostructure with block copolymers, 797–816 of porous ceramics, 801 Detergency high sulfosuccinic acid monoalkyl esters, 9 of AE, 18 Detergent lysis of vesicles, 510 Detergent market, 1 Detergent powders LAS in, 5 Detergents, 1 AE as, 18 alkyl sulfates, 10 ether carboxylic acids, 3 fatty acid N-methyl glucamides, 23 HLB of, 18 Dewetting, 171 addressable patterned, 169 patterned, 155 DHAB, dihexadecyldimethylammonium bromide, 684 DHP, dihexadecylphosphate, 324 1,12-Diaminododecane, 833 Di-2-benzothiazole, DBDS, 315 1,2-Dichloroethane, 338 1,2-Dicyanoethylene, 252

867 Di-esterification of tri-(beta-ethanol amines), 31 Di-HCF4, 53 Di-n-butyl phthalate, 581, 582 Di-Na-glucoside citrate, 29 Di-Na-glucoside sulfosuccinate, 29 Di-sec-butylether, DSBE, 298 Diacetylene, 503 Diacetylene lipids, 504 1,3-Diacyl-rac-glycero-2-phosphocholines, 692 Diacylphospholipids, 689 Dialkyldimethylammonium bromides phase boundaries, 684 Dialkylester quats as rinse cycle softeners, 46 Dialkylphospholipids, 689 Dialysis, 580 Dianthraquinoyl red Cromophtal Red A3B, 409 Diastereofacial selectivity, 248 Diatom microskeletons, 839 Diazonium salt, 267 Dibenzoyl peroxide, 478 Dibenzyl phosphate, 694 ␣,␻-Dibromo alcohols in synthesis of cationic geminis, 60 trans-1,2-Dibromocyclohexane DBCH, 328 ␣,␻-Dibromo oligo(oxyethylene) in synthesis of cationic geminis, 60 Dibutyl ether synthesis of, 364 N,N-Dibutyl formamide, 377, 380 Dicarboxylate geminis, 63 synthesis of from diols and bromoacetic acid, 63 Dicarboxylic dichloride, 476 Dicephalic surfactant, 671 Dicetylester of bis(2-hydroxylethyl)ammonium Cl hydrolysis of, 47 4,4⬘-Dichlorobiphenyl, catalytic dechlorination, 80 Dicyclohexylcarbodiimide, 549 Didecyldimethylammonium methacrylates C10MA, 476 DMAMA, 480 Didodecyldimethylammonium bis(2-ethylhexyl)sulfosuccinate, DDAOT, 699 Didocecyldimethylammonium bromide, DDAB, 296 Didocecyldimethylammonium chloride, DDDACl, 176 Didodecyl gemini surfactants, 687 Diels-Alder reactions, 234, 235, 247–260 activation parameters, 253 hetero, 254 Lewis acid catalysis of, 249, 255 micellar rate effects, , 255 retro, 253 Diesters of phosphoric acid, 14 Diethoxymethane, 599

868 Diethyl fumarate, EF, 480 Differential scanning Calorimetry, DSC, 482 Diffusion of monomer, 480 of solutes in micellar solutions, 303 Diffusion coefficients, 326 lateral in lipid bilayers, 506 of gemini micelles by FRAP, 82 Diffusion-limited condensation, 578 Digitonin, 397, 399 Diglycerides ethoxylation of, 19 Diglycidyl ether, 476 Dihexadecyldimethyammonium bromide, DHAB, 684 Dihexadecylphosphate, DHP, 324 2,4-Dihydroxybenzilidine-4⬘-(hexadecylamino)-benzylamine, 644 2,6-Dihydroxynaphthalene, 520 1,1⬘-Dihydroperfluorooctyl acryloate (FOA), 132 Diisoproplyether, DIPE, 298 Dimensional stability of latex films, 548 Dimeric surfactants, 195 ferrocenyl, 160 Dimerization of cyclopentadiene, 248 Dimerization of naphthalene to yield binaphthalene, 308 (2S,3S)-2,3-Dimethoxy-1,4-bis(N-hexadecyl-N,Ndimethylammonium)butane dibromide, 196 1, 4-Dimethoxybenzene anodic nitration of, 307 3,4-Dimethoxybenzonitrile, 3,4-DMBN from anodic nitration of 1,2-DMB, 317 2,2⬘-Dimethyl-2,2⬘-azo-N-benzylpropionamidine) hydrochloride cationic initiator, 569 2,6-Dimethylcyclohexanol by ECH of 2,6-dimethylphenol, 314 (S)-(⫹)-2,2-Dimethyl-1,3-dioxolane-4-methanol, 153 Dimethyl distearyl ammonium chloride as PTC, 31 Dimethyl ethanolamine acrylic esters of, 31 methacrylic esters of, 31 2,6-Dimethylphenol ECH of to give 2,6-dimethylcyclohexanol, 314 Dimethyl sulfate quaternization of trialkyl triazine, 66 reaction with primary amines, 31 Dimethyl sulfoxide, 588 Dimethylacetamide, 588, 589 Dimethylation of primary amines by dimethyl sulfate, 31 Dimethyldioctadecylammonium bromide, 644 Dimethyldodecylamine oxide, DDAO, 363 Dimethylformamide, 593 Dimethylketal in phosphatidylcholines, 691

Index Dimethylsulfide, 379 N1,N3-Dimethyl urocanic methyl ester, 672 N,N-Dimethyl-1-naphthyl amine, DMN, 302 N,N-Dimethylacetamide, 272 N,N-Dimethylaniline anodic nitration of, 311 N,N-Dimethyldodecylamine, 427 N,N-Dimethyldodecylamine-N-oxide, 427 N,N-Dimethylformamide, 566 Dimorpholinophosphoramidate, 680 CF-MPA, 680 2,4-Dinitro-1-chloronaphthalene, 185 2,4-Dinitrophenyl phosphate dianion, DNPP2⫺, 191 1,2-Di-O-(1⬘,9⬘-octadecadienyl)-sn-glycero-3-poly(␻methoxyethylene[115]glycol)ate see BVEP, 152 Dioctyldecylammonium bromide, DDAB, 643 Dioctyldecylammonium chloride, DDAC, 643 Dioctadecyldimethylammonium bromide, DODAB, dodabR, 226, 324 Dioctadecyl dimethylammonium chloride, DODAC, 507 Di(1H,1H,5H-octafluoro-n-pentyl) sodium sulfosuccinate di-HCF4, 350 Diol lipids as fat constituents, 3 1,2-Dioleoyl-sn-glycero-3-phosphoethanolamine, DOPE, 145, 152 Dioxazine violet Cromofine Red 6820, 409 1,3-Dioxolanes from long-chain aldehyde, 50 from 1,2- and 1,3-diols, 50 from ethyl esters of keto acids, 53 Dip coating, 780, 788, 789, 805 for nanolaminated thin films, 780 sol-gel, 834 Dipalmitoylphosphatidylcholine, DPPC, 120, 149 DIPE, diisopropylether, 298 2,3-Diphenyl-2,3-butanediol from reduction of acetophenone on Pb cathode, 314 1,1-Diphenyl-2,2,2-trichloroethane, dyhydrochloronation, 185 Diphosphate geminis vesicles of, 84 N,N⬘-Diphthalamidyldiethylenetriamine, 153 DiPhyPC, 690 vesicles, 692 Diplasmenylcholine DPPlsC, 149 cascade triggering of, 149 synthesis from solketal, 147 Dipotassium dodecylmalonate, K2DoM, 670 Dipyridinium surfactant synthesis, 60 Dipyridyl carbonate, DPC, 153 Diquaternary ammonium synthesis, 60 Direct dispersions, 581 Direct electrochemical processes in emulsions, 297

Index Direct oxidation of NaDTC in biphasic emulsions, 305 Direct recombination, 659 Directed polymerizations, 526 Disazo yellow AAMX Seikafast Yellow 2600, 409 Disazo yellow HR Seikafast Yellow 2700, 409 Discoidal micelles of nonionic sugar-based geminis, 80 Discoids, 834 Disklike micelles, 697 Disks, 813 Dispersion, , 429 Dispersion polymerization, 429, 472, 565 Aquersymer, 551 encapsulation of inorganics, 566 in supercritical CO2, 566 in supercritical microemulsions, 356 inverse, 492 PVP in, 560 styrene in CO2, 134 styrenic macromonomers of polyethylene oxide in, 560 Dispersion polymerization stabilizers carboxymethyl cellulose, 566 cellulose acetate butyrate, 567 2-ethylhexyl methacrylate, 566 ethylhydroxyethyl cellulose, 566 methacrylate-terminated phthalate glycol polyester, 566 ␻-methoxy-PEG-undecyl-␣-methacrylate, 566 methyl cellulose, 566 Na alginate, 567 Na dioctyl sulfosuccinate, 566 nonylphenol-PEG-monomaleate, 566 PEG-maleate, 566 PEG-maleate-alkyl, 566 PEO-PPO, 566 poly(t-butylstyrene), 566 poly(1,1-dihydroperfluorooctylacrylate), 566 poly(1,1-dihydroperfluorooctyl methacrylate), 566 poly(2-(dimethylamino)ethylmethacrylate)-balkylmethacrylate, 566 polyepiclorhydrin, 566 poly(dimethylsiloxane)-methyl methacrylate, 566 poly(1H,1H,2H,2H-perfluorooctyl methacrylate-b-PMMA), 566 poly(methacrylic acid), 567 poly(methacrylic acid)-co-ethylacrylate, 566 poly(vinyl alcohol), 566 poly(vinyl methyl ether), 566, 567 poly(N-vinyl pyrrolidone), 566 poly(N-vinylpyrrolidone)-co-(vinyl acetate), 566 PS-b-polybutadiene, 566 polyacrylic acid, 566 Dispersions coupler, 582

869 [Dispersions] direct, 581 from emulsions, 579 NS, 581 organic, 584 pharmaceutical, 588, 590 1,2-Disubstituted phosphate surfactants, 693 Distearoylphosphocholine, DSPC, 690 Distribution constants estimation by chemical trapping in microemulsions, 286 estimation by fluorescence quenching in microemulsions, 286 estimation by vapor pressure methods in microemulsions, 286 Distribution of propyl gallate, 290 Distribution of TBHQ, 290 Distribution of vitamin C, 290 Distribution of vitamin E, 290 1,3-Disubstituted phosphate surfactants, 693 Disulfide based surfactants, 160 Disulfide reduction chemical, 162 electrochemical, 162 photochemical, 162 Disulfide-based surfactants, 162 5,5⬘-Dithiobis-(2-nitrobenzoic acid), DTNB, 229 Dithiothreitol (DTT), 150, 162 Di(10-undecenyl)sulfosuccinate, DUSS, 476 Divinyl benzene, 508, 511, 566 DLPC, dilaurylphosphocholine, 398 DLS, dynamic light scattering, 141, 482 DMA, dodecyl methacrylates in miniemulsion polymerization, 560 DMAEA, 490 dimethylaminoethylacrylate, 489 DMAEM, dimethylaminoethylmethacrylate, 489 DMAMA, didecyldimethylammonium methacrylate, 480 DMN N,N-dimethyl-1-naphthyl amine, 302 electrodimerization of, 302 DMPC dimyristoyl phosphatidylcholine, 511 phase diagram, 689 DMSO, 589 DNA, 153, 398, 845 DNA-lipid interactions, 400 DNA: cationic lipid complexation, 152 DNPP2⫺, 2,4-dinitrophenyl phosphate dianion, 191 DODAB, 507, 510, 511 DODABr, 226 dioctadecyldimethylammonium bromide, 324 DODAC, 510 dioctadecyl dimethylammonium chloride, 507 DODACl vesicles, 228 DODAX, 227 n-Dodecanol, 781, 787

870 Dodecanolactam, 591, 592 Dodecyl aliphatic surfactants, 832 Dodecylamine/niobium(V) ethoxide, 832 N-Dodecylamino-1-deoxylactitol, 121 N-Dodecylaminolactitol, 120 micelles, 120 Dodecylammonium chloride-SDS mixture, 703 4-Dodecylaniline, 832 Dodecylbenzensulfonate, DBS effect on indirect oxidation of anthracene, 318 Dodecyl benzenesulfonic acid, DBSA, 839 Dodecyl bromide reduction in DDAB/water/dodecane microemulsions, 330 Dodecyldecaoxyethylene glycol ether C12E10, 236 N-Dodecylglycinate in chemical trapping, 290 Dodecylheptaoxyethylene glycol ether, 197 C12E7, 236 N-Dodecyl-lactobionamide, 120 micelles, 120 Dodecyl-␣-maltoside, 120 Dodecyl-␤-maltoside, 120 ß-1-n-Dodecyl-D-maltoside, 116 Dodecyl methacrylates, DMA, 560 N-Dodecyl-N-methylglycinate in chemical trapping, 290 N-Dodecyl-4-methylpyridinium bromide, 254 Dodecylpentamethyl-1, 3-propylenebis-(ammonium chloride), DoPPDAC, 670 N-Dodecylpyridinio-3-carboxylate, 679 N-Dodecylpyridinio-4-carboxylate, 679 Dodecyltricosanoxyethylene glycol ether, C12E23, 236 DOPE see 1,2-dioleoyl-sn-glycero-3-phosphoethanolamine, 145 liposomes, 150 DOPE: BVEP liposomes acid-triggered release, 151 DoPPDAC dodecylpentamethyl-1,3-propylenebis-(ammonium chloride), 670 phase diagram, 672 DOTMA/Chol, 153 Double chain surfactants synthetic scheme, 114 Double jet precipitation, 595 Double-chain histidine surfactants, 693 Double-chain surfactants phase behavior, 667 Double-headed surfactants, 829 Dowex 2, 181 DPC, dipyridyl carbonate, 153 DPPC dipalmityoylphosphocholine, 149, 398, 688 phase diagram, 689 vesicles, 692 DPPE, 688 phase diagram, 689

Index DPPlsC see diplasmenylcholine, 149 liposomes, endosomal uptake model, 151 DPPlsC/DOPlsC synthesis, 153 Dressed micelle theory, 178 Drug delivery galactose, 112 glucose, 112 mannose, 112 DSBE, di-sec-butylether, 298 DSC, 683, 685 differential scanning calorimetry, 482 DSPC, distearoylphosphocholine, 690 DTA, 839 DTA4H2V10O28⭈8H2O, 839 DTAB, 181, 188, 198, 457, 460, 467, 694, 695, 696 adsorption isotherms, 72 trimers, 66 DTAB-SDS-water, 695 ternary phase diagram, 696 DTAB/DDAB, 463, 464 DTAC, 71, 694, 696 asymmetric micelles, 695 in water phase diagram, 670 DTAC-SN-D2O phase diagram, 694, 695 DTAC-SN-water system, 699 DTAOH, 181 DTG, 659 tetradecyl-N-[4-[6-(N,N⬘,N⬘-ethylenediamino)-hexyl]oxy]benzoyl-L-glutamate, 653 DTNB, 5,5⬘-dithiobis-(2-nitrobenzoic acid), 229 DTT, dithiothreitol, 150, 162 du Nuoy ring method, 167 Dupanol ME, 600 DUSS, 480 di(10-undecenyl)sulfosuccinate, 476 Dye forming efficiency of coupler dispersions, 580 Dynamic light scattering, DLS, 141, 166, 482 Dynamic scanning electrochemical microscopy, SECM, 329 Dynamic surface tension, 157, 167 of C12E8, 162

E1cb decompositions, 191 ECH electrocatalytic hydrogenation, 298 of 2-t-butylphenol in buffered emulsions, 313 of carvone, 312 of limonene, 298, 312 of phenanthrene, 312 at Raney nickel cathodes, 298 Ecological properties of amphoteric surfactants, 38 EDTA, 832, 835 EF, diethyl fumarate, 480 Effects of mediator potential on DBH reduction rates, 329

Index Efficiency of electroorganic synthesis effects of heterogeneous solutions, 305 Egg albumin colloidal stabilizer, 562 Egg phosphatidylcholine, EPC, 700 Eicosyl chains, 690 Elastic modulus of gemini solutions, 82 Electric fields effects on silica formation, 826 Electrical conductivity, 521 of organic phases, 301 Electrocatalytic hydrogenation, ECH, of unsaturated organics, 298 Electrochemical chlorinations of amine hydrochlorides, 305, 306 Electrochemical conversion of NDPA to ADPA, 316 effects of organic emulsions on passivation effect, 315 Electrochemical epoxidation of hexene, 303 Electrochemical generation of silver films, 634 Electrochemical measurement of dediazonation rate constants, 278 Electrochemical processes in micelles, 303, 304 in microemulsions, 303, 304 in O/W emulsions mechanisms of, 296 Electrochemical reduction of disulfide, 162 Electrochemical reductions of 4-acetyl-1-phenoxyalkyl salts at Hg cathode, 316 Electrochemistry in microheterogeneous solutions, 295 Electrode modification effects, 311 Electrode wetting, 297 by organic phases in O/W emulsions, 301 Electrodimerization of DMN, 307 into TMN2⫹, 302 Electroless plating, 407–412 rate of film growth, 409 Electroluminescent organic LCD, 792 Electron diffraction PbS particulate films, 636 Electron microscopy, 509 Electron transfer in micelles, 303 Electroorganic synthesis, 295–318 in microemulsions, 323 Electrooxidation of benzyl alcohol on nickel anode, 305, 306 Electrophilic bromination of olefins, 234 Electrophoretic mobility of silica, 71 Electropolymerizations, 640 of W/O microemulsions, 309 Electroreduction bromoacetal, 332 of DDT, 311 of hexachlorobenzene, 311 of NAP at Pb cathode, 316 Electrorheological fluids, 495 Electrosteric stabilization, 549, 563

871 Electrosynthesis of conducting polymers in micellar solutions, 318 EmpiLan NP5 (polyoxyethylene)5–9nonyl phenol, 476 Emulsification, 84 Emulsification efficiency of cationic geminis, 79 Emulsifiers AE as, 18 amine oxides, 20 castor oil ethoxylates, 20 ether carboxylic acids, 3 ethoxylated amines, 20 ethoxylated glycerol esters, 20 in emulsion polymerization photolabile surfactants, 55 phosphoric acid triesters in cosmetic emulsions, 13 sorbitan esters, 22 sulfosuccinic acid monoalkyl esters, 9 W/O, HLB of, 18 Emulsion droplets, 577 Emulsion polymerization, 362, 429–449, 471, 509, 542, 565 acrylate, 568 batch, 433 of styrene, 555 continuous, 433 emulsifiers in sorbitan esters, 22 sulfosuccinic acid monoalkyl esters, 9 feed, 433 in cationic gemini microemulsions, 87 in critical fluids, 363 kinetics, 432 Monte Carlo modeling of, 489 of vinyl acetate, 567 photolabile emulsifiers in, 55 polymeric surfactants in, 547 polymerizable surfactants in, 547 transport, 562 Emulsions, 527 direct electrochemical processes in, 297 effects on efficiency in electroorganic synthesis, 305 effects on selectivity in electroorganic synthesis, 305 electroorganic synthesis in, 295 indirect electrochemical processes in, 297 transformation to dispersions, 580 Enantioselectivity, 252 induced by chiral surfactant, 259 micellar effects on, 258 micelle induced, 235 Encapsulating spheres precipitation in, 604 Encapsulation of inorganics, 66 End cap energy of cationic surfactant oligomers, 81 of gemini wormlike micelles, 82 Endo pathway, 248 Endo-templating, 801, 812

872 Endocytosis, 400 Endocytotic events, 400 Endosomal uptake pathway for targeted DPPlsC liposomes, 151 Enzymatic lysis of vesicles, 505 Enzymatic reactions in W/CO2 microemulsions, 353 Enzymes immobilization in hydrogels, 495 EO see ethylene oxide, 14 EO(4)NP, polyoxyethylene(4) nonylphenol, 475 EO5PO70EO5, 805 EO13PO70EO13, 805 EO17PO55EO17, 805 EO19PO33EO19, 805 EO20PO30EO20, 805 EO20PO70EO20, 805, 830, 838 EO26PO39EO26, 805 EPC-OG-water phase diagram, 701 Epichlorohydrin, 363 esterification to form glycidyl ethers, 364 etherification, 367 in synthesis of cationic trimers, 67 Epitaxial growth of semiconductor nanoparticles, 635 Epitaxial reactions at monolayers, 642 Epoxidation of alkenes, 234 Epoxidation of hexane electrochemical, 303 Epoxy, 844 Epoxylation of aliphatic alcohols, 18 Epoxy-glass mat composites, 543 Equilibrium solubility, 610 Erythrocytes human, 605 Eschweiler–Clark reaction, 67 ESR, 478 Ester alkanoate solubilization in sodium alkanoate micelles, 418 Ester amines unsuitable for quaternization, 31 Ester quats aquatic toxicity, 46 as biocides, 34 biodegradability, 34, 46 fatty soaps by hydrolysis of, 46 sensitivity to hydrolysis, 33 Ester surfmers by condensation, 559 functionalization of polystyrene latexes, 559 Esterification, 554 in sol-gel processing, 803 of epichlorohydrin to form glycidyl ethers, 364 of fatty acids with polyethylene glycol, 19 of o-phosphoric acid, 14 of polyethylene glycol with ␣-sulfonated fatty acids, 63 of sucrose, 22

Index Esters polyol, 844 Esters of keto acids to yield ketals, 53 Estersulfonates, 4 ␤-Estradiol, 591, 592 Ethanol, 476, 603, 791, 824, 830, 831, 834 Ether, 603 Ether carboxcylic acids, 3 as antistats, 3 as corrosion inhibitors, 3 as emulsifiers, 3 from fatty alcohol ethoxylates, 3 in cleaning, 3 in cosmetics, 3 in washing, 3 Ether sulfates alcohol, 1 alkaline stability, 10 as pastes, 10 Etherification of epichlorohydrin, 367 Ethoxylated amines, 20 Ethoxylated fatty acids, 19 Ethoxylated fatty esters, 9 Ethoxylated glycerol esters in cosmetics, 20 Ethoxylated surfactants alcohol ethoxylates, 2 fatty alkanolamides, 2 fatty amine oxides, 2 Ethoxylates homologue distribution, 17 Ethoxylation of alcohols, 15 of alkanol amides to give amide ether sulfates, 11 of castor oil, 20 of diglycerides, 19 of monoglycerides, 19 of sorbitan esters, 22 of tertiary amines with ethylene oxide, 32 polyethylene glycol as untoward side product in, 16 reactor, 17 Ethylene oxide (EO), 14 Ethyl acetate, 411, 579–581 Ethyl acrylate, 495 Ethyl alcohol, 425 Ethyl alkanoate esters dissolution rates, 423 Ethyl alkanoates, 426 aqueous solubility, 424 hydrolysis in liquid-liquid systems, 363 Ethyl benzoate hydrolysis of, 420 Ethyl cellulose, 474, 491 o-Ethyl-S-diisopropylaminoethylmethyl phosphothiolate VX, 374 Ethyl glucoside in transacetalization, 51 Ethyl hexanoate biphasic hydrolysis of kinetics, 420, 421

Index Ethyl octanoate, 427 hydrolysis of, 414, 420 Ethylene, 131, 431, 591 Ethylene glycol diglycidyl ether in synthesis of taurine geminis, 63 Ethylene oxide, 549 block copolymerization of, 555 in Alkoxylation, 14 reaction with primary amines, 31 reaction with tertiary amines, 32 Ethylenesulfone moiety in cleavable surfactants, 48 Ethylethylene, 444 2-Ethylhexyl methacrylates dispersion polymerization stabilizer, 566 Ethylhydroxyethyl cellulose dispersion polymerization stabilizer, 566 4-Ethylphenol, 517, 520 Evaporation, 580 auxiliary solvent removal, 584 Exo pathway, 248 Exo-templating, 799, 801, 812 External fields effects on silica formation, 826 F(CF2)8–10CH2CH2O(CH2OCH2O)3 FSO-100, 139 FAA see fatty alkanolamides, 2 Falling-film reactor monoglyceride sulfation in, 11 sulfonation in, 4 FAO see fatty amine oxides, 2 Fast Rose Lake B Rhodamine B Lake, 409 Fat liquor sulfated oils in leather processing, 10 Fat-soluble vitamins as fat constituents, 3 Fats saponification of, 2 Fatty acid condensates with proteins, 13 Fatty acid alkanolamides stability in detergent pastes, 28 Fatty acid amides conversion from fatty acid methyl esters, 25 Fatty acid ethoxylates by esterification with polyethylene glycol, 19 by ethoxylation of fatty acids, 19 Fatty acid glucamides, 2, 25, 26 physicochemical properties, 27 stability in detergent pastes, 28 two-step synthesis, 27 Fatty acid methyl esters conversion to fatty acid amides, 25 saponification of, 2

873 Fatty acid monoglyceride sulfates by sulfation and transesterification of glycerol, 11 Fatty acid N-methyl glucamides applications of, 23 production capacity, 23 Fatty acids ethoxylated, 19 from saponification, 2 saponification of, 2 Fatty alcohol ethoxylates conversion to ether carboxylic acids, 3 Fatty alkanolamides, 2 Fatty amine ethoxylates, 20 Fatty amine oxides, 2 Fatty esters ethoxylated, 19 Fatty soaps by hydrolysis of ester quats, 46 Fe, 838 Fe2⫹, 838, 839 Fe3⫹, 838, 839 Fe3O4, 653 Fe3O4 particles, 566 Ferrite nanoparticles, 519 Ferrocene-based surfactants, 155 Ferrocene diffusion in microemulsions, 326 redox potential, 157 Ferrocenyl cationic geminis, 65 Ferrocenyl redox chemistry, 157 Ferrocenyl surfactants, 157, 407 as mediators, 327 dimeric, 160 Gibbs monolayers of, 159 surface tension, 158 FeSe particles in Nafion films, 652 Fiber-to-vesicle transformation, 680 Fibers, 834 Fichlor, 379 Field flow fractionation particle sizing by, 460 Filaments, 688 Film characterization, 654 cubic mesoporous silica, 785 formation in electroless plating, , 408 forming latexes, 570 mesoporous silica, 785 mesostructures, 791 preparation by LbL assembly, 653 silica hexagonal mesoporous, 786 silica lamellar mesoporous, 787 thickness, 656 lamellar mesoporous silica, 789 Films cast bilayer, 653

874 [Films] Cd behenate, 645 Cu behenate, 645 mesoporous silica films on borosilicate glass, 788 mesoporous silica films on Teflon, 788 nanoparticulate silver, 634 of cadmium arachidate, 643 photoelectrochemistry of, 657 physicochemical properties, 657 PSS/PVP by LbL assembly, 654 semiconductor particulate, 635 silica at fluid–fluid interfaces, 779–794 Zn behenate, 645 Fine particle morphology, 830 First-order rate constants, 82 Flexible tubules, 708 Flocculants, 494, 562 bridging, 552, 569 depletion, 562 of latexes, 547 of W/CO2 emulsions, 352 Flory-Huggins equation, 467 Flory-Huggins interaction parameter, 442 Flory-Huggins model, 425, 467 Flory-Huggins solution theory, 437 Flory-Huggins theory, 442, 508 in emulsion polymerization, 435 Flotation quaternary ammonium surfactants in, 2 Flow systems, 585 RESS, 592 Fluid-energy milling, 577 Fluorescence depolarization, 780 microscopy of GV, 396 of 1-pyrenenonanoic acid, 227 Fluorescence micrographs of pyrene, 604 Fluorescence microscopy, 511 Fluorescence quenching estimation of micellar ionization, 283 studies of micellar shape, 79 Fluorescence recovery after photobleaching, FRAP, 82 Fluorescent probes membrane soluble, 400 Fluorinated methacrylates, 566 Fluorination to change HLB, 692 Fluorocarbon acrylamido surfmers, 562 Fluorohectorite, 841 Fluoropolymer surfactants, 131 FOA see 1,1⬘-dihydroperfluorooctyl acryloate, 132 Foam stability, 71 Foam stabilizers alkyl olyglycosides, 27 Foamers alkyl dimethylamine oxides, 20

Index Foaming highly, sulfosuccinic acid monoalkyl esters, 9 weakly, sulfosuccinate dialkyl esters, 9 Foaming ability, 71 Foams, 381 Force, hydration, 700 Force balance measurements with AFM, 72 Formamide, 455 Formation of porous materials mechanistic pathway, 824 Formation of surfactant phases, 667–710 Four-chain surfactants, 686 FPEG nonionic ferrocenyl surfactants, 407 FRAP diffusion coefficient measurements of gemini micelles, 82 Free energy driving force for particle formation, 578 of micellization, 75 of geminis, 78 of stabilization of colloidal particles, 563 of transfer of methylene from water to micellar core, 75 Free radical polymerization in microemulsions, 455–468 in vesicles, 503–507 Free radicals surface active oligomers, 456 Freeze fracture TEM of liposomes, 148 Freon see 1,1,2-trifluorotrichloroethane, 132 Frontier molecular orbital theory, FMO, 247 Fructose, 49 FSM-16, 836–838 FSM-A, 837 FSM-C, 837 FSM-D, 837 FSM-n, 836 FTIR, 478, 649, 648, 651, 782, 841 Fumarate surfmers, 553 Functional surfactants, 45 Functionalization of polystyrene latexes with ester surfmers, 559 Functionalized latexes amine, 482 carboxy, 482 hydroxyl, 482 mercapto, 482 sulfonate, 482 Functionalized microgels, 495 Functionalized surfactants, 829 Fungicides cationic geminis, 59 Furan, 249 Fusogenic liposomes, 145

Index G1086 polyethylene (EO)40 sorbitol hexaleate, 474 Ga, 838 Ga3⫹, 838 GaAl12, 840 Galactocerebrosides sulfated, 112 Galactonamide ribbon formation, 706 Galactonic headgroup, 706 Galactose, 112 Galactosphingolipid, 123 Galactosyl ceramide, 111 Galcer, 123 Gallery templating, 842 Galvani potential, 302 Gamma radiolysis, 548 GAS, 594 gas antisolvent process, 592 Gas antisolvent process, GAS, 592 Gas catalyzed thin-film synthesis, GCTFS, 780 Gas chromatography, 459 Gas condensation, 603 of pyrene, 604 Gauche defects, 792 GB sarin isopropyl methyl fluorophosphonate, 374 GCTFS, gas catalyzed thin-film synthesis, 780 Gel effect in emulsion polymerization, 434 Gel permeation chromatography, GPC, 482 Gel phase, 670 Gelatin, 579, 581, 587, 596 colloidal stabilizer, 562 Gemini admicelles, 72 adsorption to laponite, 78 to silica, 78 to titanium oxide, 78 adsorption isotherms, 72 anionic, 61 catanionics catanionic glycolipids, 123 cationic, 60, 61 CMC, 73, 75 effect of headgroup, 76 effect of spacer length, 76 didodecyl, 687 diphosphate, 687 disodium sulfonates from 1,3-propanesultone, 62 from diols, 62 glycolipids, 123 micelles micropolarity, 78 microviscosity, 79

875 [Gemini] solubilization capacity, 78 solubilization of hexane, 78 solubilization of toluene, 78 nonionic, 61 surfactants, 2, 56, 59, 195, 829 aggregate geometry, 72 aggregate morphology, 79 alkylphosphate, 63 amino acid based, 63, 64 anionic, 63 anionic-nonionic, 65 as templating agents, 87 asymmetric, 67 carbohydrate based, 63 carboxylate, 71 cationic, 63 cationic-anionic, 65 cationic ferrocenyl, 65 chemoenzymatic routes, 63 chiral, 65 dicarboxylate, 63 foaming properties, 71 from L-cysteine, 63 glycerophosphate–pressure-area isotherms, 71 hexagonal phase, 82 interfacial packing, 72 lamellar phase, 82 liquid crystalline phases, 85 nonionic-nonionic, 65 on graphite, 779 on MoS2, 779 phosphate, 71 serine based, 63 short spacer, 70 sugar based, 64 sulfate, 71 sulfonate, 71 taurine, 63 vesicles, 83 wormlike micelles, 83 Gene delivery cationic vinyl ether lipids in, 152 Giant phospholipid vesicles, 395 Giant vesicles, 226, 688 as chemical vessels, 395 of dimyristoyl phosphatidylcholine, 511 POPC, 400 self-replication, 227 Gibbs equation, 68, 70 Gibbs free energy of sodium alkanoate aggregates, 425 Gibbs monolayer of ferrocenyl surfactants, 159 Gibbs phase prism, 456 Gibbs-Thompson equation, 579 Glass cleaners sulfosuccinate dialkyl esters, 9

876 Glass surfaces, 781 Glass transition effects in microemulsion polymerization, 467 Glass transition temperature, 548 Gliaden particles, 586 Glucamides fatty acid, 25 Gluconamide helices, 707 Gluconic headgroup, 706 Glucose, 48, 49, 112 catalytic hydrogenation, 64 production volume, 22 Glucose-based surfactants, 56 Glucose-derived surfactants, 24 Glucose 6-dodeanoate, 50 Glucose esters, 2 Glucosidation reaction, 24 Glutamate acylation of sodium salt, 13 Glutaraldehyde cross linking with, 586 Glutaraldehyde films, 657 Glycerides, 10 Glycerine from saponification, 2 Glycerol, 145 sn-Glycerol-3-phosphate-acyltransferase, 400 Glycerophosphate geminis pressure-area isotherms, 71 Glycidyl ether kinetics of preparation, 367, 368 synthesis of, 364 effect of alkalinity, 369 effect of surfactant type, 369 Glycidyl trimethylammonium chloride reaction with alcoholic groups alternative quaternization route, 33 Glycol-based solvents, 839 Glycolipid N-dodecanoyl-N-nonyl lactitol LC11C9, 700 Glycolipids, 111–126 antifungal activity, 122 Glycosidic surfactants, 235 Gold colloids, 800 Gouy–Chapman layer, 177, 180, 190 GPC, gel permeation chromatography, 482 GPEC, gradient polymer elution chromatography, 549 Gradient polymer elution chromatography, GPEC, 549 Graphite, 781 Guinea Green B, 586 Gulonamide, 707 Gulonic headgroup, 706 Gum arabic, 568 GV, giant vesicles, 395 Gyroid phases, 802, 833, 834 H2O2, 517 H2S, 635, 642, 643, 651

Index H2Se, 642, 643 H2SO4, 829 H2Te, 642, 643 H3PO4, 829 Half mustard 2-chloroethylethyl sulfide, 379 o-3-Halopropoxyphenoxide bromide, 196 Hard spheres synthesized from silica, 780 Hartley micelle, 177 HB239, polyester-polyethylene oxide, 476 HB246, 489 polyester-polyethylene oxide sorbitan monooleate, 476 HBr, 642, 829 HCB, hydrophile-CO2-phile balance, 350 HCl, 642, 820, 829 HD, mustard, bis(2-chloroethyl)sulfide, 374 HDPC, hexadecylphosphorylcholine, 284 Headgroup spacer, 59 Headgroups amino, 832 phosphate, 832, 833 Helices, 706 left handed, 709 right handed, 709 Heliogen blue G Heliogen blue L6700F, 409 Heliogen blue L6700F phthalocyanine blue E, 409 Heliogen green D9360 phthalocyanine green 6Y, 409 HEMA, 476, 495 Hemiacetal formation in glucosidation, 24 Hemiester of maleic anhydride, 552 Hemimicelles, 304, 779 Heptaethyleneglycol, 197 HER, hydrogen evolution reaction, 298 Heterodimer surfactants, 66 Hetero Diels Alder reactions, 254 Heterodimer surfactants, 65 Heterogemini surfactants, 54 Hexadecane, 378, 379, 476, 490, 491 Hexadecane in water microemulsions, 377 Hexadecanyl chains, 690 Hexadecyl gulonamide, 708 Hexadecyldiglycerol ether, 226 Hexadecylphosphorylcholine, HDPC, 284 N-1-Hexadecyl-3-carbamoylpyridinium bromide, 273 N-Hexadecyl-2-chloropyridinium iodide hydrolysis in 1, 2-dichloroethane, 339 in lactamization, 338 lactonization, 338 synthesis of, 338 1,4-(N-Hexadecyl-N,N-dimethylammonium)butane dibromide, 196 n-Hexane, 476 Hexagonal, 668

Index Hexagonal films mesoporous silica, 788 Hexagonal mesophases, 679 Hexagonal mesoporous silica films, 790 Hexagonal mesoporous silica particles, 791 Hexagonal phase, 527, 669, 674, 676, 825 of 12-2-12, 2Br geminis, 82 Hexagonal phases polymerization in, 530 Hexagonal silica film mesoporous, 786 Hexagonal silica films on mica, 781 Hexagonal silica/surfactant nanocomposites, 780 Hexagonal surfactant structures, 784 Hexagonally close packed spheres see P63/mmc, 826 Hexametaphosphate, HMP, 658 Hexane, 147, 475 solubilization by cationic geminis, 78 Hexanol, 284, 475, 478 Hexanol distribution in CTAB microemulsions, 287, 288 3-(N-Hexadecyl-N,N-dimethylammonio)-propane sulfonate, HPS, 284 4-[(4-Hexylphenyl)azo]phenol, AZOH, in electroless plating, 407 1-Hexene, 302 N-Hexyl methacrylate, 459, 460, 463 condensation on disaccharide, 559 Hf, 838 HFDePC, 1,1,2,2-tetrahydroperfluorodecyl-pyridinium chloride, 680 HfO2, 838 HgS, 643, 644 in LB films, 648 HI, 642, 829 HI phase, 145 Hierarchically structured ceramic oxides, 806 High-density magnetic recording media, 609 HII phase, 145 Hills process in sulfoxidations, 6 L-Histidine-based geminis vesicles of, 84 HIV, 111, 121 HLB, 286, 375, 473, 478, 484, 549, 554, 555, 563, 570, 674, 675, 706 see hydrophile-lipophile balance, 18 relation to emulsion structure, 473 HLB values sorbitan esters, 22, 23 sorbitan ester ethoxylates, 22 HMP, hexametaphosphate, 658 HMPA, hydroxypropyl methacrylate, 559 HNO3, 829 Hoechst light water technology in sulfoxidations, 6 Hollow fibers synthesized from silica, 780

877 HOMO, 247 Homochiral quaternary salts, 235 Homogeneous nucleation theory, 432 in emulsion polymerization, 435 Homogenization, 584 hot, 582, 583 Homogenizers, 581 Homopolymers of surfmers, 549 Horseradish peroxidase, HRP, 515 Hot homogenization, 582, 583 (H2PW11O39)⫺3, 840 HPLC, 544 HPLC analysis of didiazoniation products, 276, 277 HPLC measurement of dediazonation rate constants, 278 HPS, 3-(N-hexadecyl-N,N-dimethylammonio)-propane sulfonate, 284 HPS micelles, 285 HREM, 836, 837 HRP, 517 horseradish peroxidase, 515 HSAAS, alkyl allyl sulfonic acid, 551 HSC11H22O(CH2CH2O)nH, 548 HSC11H22SO3Na, 548 HUFT theory, 432 Hyamine 2389 mainly methyldodecylbenzyltrimethylammonium chloride, 312 Hyamine 2389 films, 312 Hybrid organic/inorganic structures, 812 Hydroxyethyl cellulose, 567 4-Hydrindanone, from 2-(3-bromopropyl)-2-cyclohexene-1-one from intramolecular cyclization of 2-3-bromopropyl)-2cyclohexenone, 310 in bicontinuous microemulsions, 332 2-Hydroxyethylmethacrylate-co-ethylenedemethacrylate, 567 2-Hydroxy-5-nonylaceteophenone, 603 2-Hydroxy-1,1,2,3,3-pentahydroperfluoroundecyldiethylammonium chloride, I-C11, 680 Hydroxypropyl cellulose, 563 Hydrated DDAOT crystals, 699 Hydration force, 700 Hydration numbers, 280 Hydration numbers by chemical trapping, 289 of nonionic micelles, 278 Hydrazine, 622 Hydrogel particles superparamagnetic, 495 Hydrogen bonding, 797 Hydrogen evolution reaction, HER, 298 Hydrogen peroxide, 187, 427 Hydrogenation in titration of double bonds, 459 Hydrolysis acid catalyzed of plasmenylcholine, 146 catalytic, 378 in sol-gel processing, 803

878 [Hydrolysis] in W/CO2 microemulsions of benzoyl chloride, 351 of p-nitrophenyl chloroformate, 351 lipase catalyzed, 353 of acetals, 51, 189 acid catalyzed in alkyltrimethyl ammonium micelles, 188 of acid chlorides, 197 of alkyl halides, 197 of N-␣-benzoyl-DL-arginine-4-nitroaniline, 845 of benzoyl chloride, 353 of betaine esters, 47 of t-butyl methacrylate to sodium methacrylate, 563 of 2,4-dinitrophenyl phosphate dianion, 191 of esters, 378 of ether sulfates, 10 of ethyl alkanoates, 416 in two-phase liquid-liquid systems, 363 of ethyl benzoate, 420 of ethyl esters, 413 of ethyl octanoate, 414, 420 of N-hexadecyl-2-chloropyridinium iodide in 1,2dichloroethane, 339 of N — —C containing surfactants, 56 of p-nitrophenylphosphate, 495 of octanoic anhydride, 427 of oleic anhydride, 427 catalyzed by oleic acid vesicles, 399 of organophosphorous compounds, 375 of ortho esters, 55 of OTOS, 844 of phosphate esters IBA catalyzed, 378 of PNDP, 375, 377 of polyoxyethylene surfactants, 52 of second-generation cleavable surfactants, 54 of sulfonic esters, 197 of TAOS, 844 of TEOS, 823 vinyl ether acid catalyzed, 152 Hydrolyzed TEOS, 830 Hydrophile-CO2-phile balance HCB, 350 Hydrophile-lipophile balance (HLB), 18 detergents, 18 of wetting agents, 18 of w/o emulsifiers, 18 o/w emulsifiers, 18 solubilizers, 18 Hydrophobic additive in miniemulsion stabilization, 559 Hydrophobic interactions, 797 Hydrophobic spacers, 71 Hydrophobicity micellar rate effects, 221

Index Hydrothermal reactions of sodium metatungstate with CTAOH, 839 with cationic alkylammonium surfactants, 820 Hydrothermal stability of Ti-TMS1, 833 Hydrothermal synthesis, 845 Hydrotropes, 381 Hydroxyalkane sulfonates in sulfonation of ␣-olefins, 7 Hydroxyaluminum bis[poly(hexafluoropropylene oxide)carboxylate], 137 Hydroxyapatite, 814, 839 o-Hydroxybenzoate, 181 Hydroxyethyl cellulose, 565, 568 Hydroxyethyl methacrylate, 491 Hydroxyl functionalized latexes, 482 Hydroxylphenyldimethylsulfonium methyl sulfate in condensation with carboxylic acids, 559 Hydroxypropyl methacrylates, HMPA, 559 4-Hydroxy-2, 2, 6, 6-tetramethyl piperidino-1-oxy 4-hydroxy-TEMPO, 351 4-Hydroxy-TEMPO, 4-hydroxy-2,2,6,6-tetramethyl piperidino1-oxy in FPECOO-NH4⫹ microemulsions, 351 4-Hydroxythiophenol, 520 Hysteresis in nitrogen adsorption, 831 (H2W12O40)⫺6, 840 I-C11, 2-hydroxy-1,1,2,3,3-pentahydroperfluoroundecyldiethylammonium chloride, 680 Ia3d, 785, 823 IBA, iodosobenzoates, 378 IBX sodium 2-nitro-4-iodoxy benzoate as hydrolysis catalyst, 379 Igepal, 176 Igepal CO-430 polyoxyethylene(4) nonylphenol, 475 Igepal RC-760, 831 Im3m, 786, 829 cubic, 838 Image dye formation, 580 Imidazole, 147, 844 4-Imidazole acrylic acid, 672 Imidazole headgroups, 671 Imidazoline amphoterics diacetate, 37 monoacetate, 37 Imidazolines (imidazolinium betaines), 36 Imidazolinium betaine structure of, 37 Imidazolinium betaines (imidazolines), 36 Immobilization of enzymes, 495 Incompatible materials, 797 Incorporation of metal particles into LB films, 641 Incorporation yield in dispersion polymerization, 560 Indanthron blue cromophthal blue A3R, 409 Indirect electrochemical processes in emulsions, 297

Index Indirect oxidation of anthracene to anthraquinone, effect of DBS on, 318 of benzyl alcohol to benzaldehyde, 300 with PTC, 301 of p-methoxytoluene, 300 of NaDTC in biphasic emulsions, 305 of organics in microemulsions, 309 of toluene, 300 Indofast brilliant scarlet (R-6335) perylene vermillion, 409 Indofast brilliant scarlet R-6500 Perylene scarlet, 409 Infinite periodic minimal surface, IPMS, 526, 527 Inhibitors in microemulsion polymerization, 458 Inisurfs, 548, 551 anionic, 552 Initiation azo-carboxy, 550 by irradiation, 489 efficiency of, 548 redox, 504 water soluble, 472 Initiators KPS, 466 potassium vinylbenzyl alcoholate, 555 water soluble, 430 Intercalated micellar templating, 845 Intercalation, 837 Interface benzene/water, 789 ethyl ester–aqueous, 415 Interface of two immiscible electrolyte solutions, ITIES, 302 Interfaces benzene/water, 786 liquid–liquid, 779 water-CO2, 138 Interfacial anion concentration, 280 Interfacial area per unit volume, 805 Interfacial free energy, 579 Interfacial hydration by chemical trapping, 289 Interfacial interactions in surfactant templating of porous solids, 827 Interfacial nucleophile concentration by chemical trapping, 289 Interfacial packing of geminis, 72 Interfacial properties of surfactant solutions, 155 Interfacial states active control of, 157 Interfacial structures at electrodes, 326 Interfacial tension between water and supercritical CO2, 349, 350 Interfacial water, 178, 179 Interfacial water concentration, 280 Internal olefin sulfonates (IOS), 6 Intramolecular cyclization of 2-(4-bromobutyl)-2cyclohexenone in microemulsions, 310

879 Inverse dispersion polymerization, 492, 493 Inverse emulsion polymerization, 472, 483, 485, 489 of acrylamide, 137 of aniline, 494 in supercritical CO2, 490 Inverse heterophase polymerization, 473 Inverse microemulsion polymerization, 473 surfactants for, 477 Inverse miniemulsion polymerization, 490 Inverse suspension polymerization, 491, 492 Inverse systems polymerization in, 471–496 Iodipamide ethyl ester, 589, 590 Iodosobenzoates, IBA, 378 Ionic polymerization, , 568 Ionization degree of cationic micelles, 283 Ionization of micelles degree of (␣), 180 IOS see internal olefin sulfonates, 6 IPMS, infinite periodic minimal surface, 526, 527 IR, 783, 819, 823 Isethionates, 12 Isocyano, 503 Isodecyl acrylate conversion in vesicular polymerization, 509 Isoelectric points, 587 Isooctane, 284, 475, 476, 520, 533 Isopar M, 474–476, 489 Isoparaffinic mixture, 474 Isoprene, 540 Isopropanol, 588 Isopropyl methyl fluorophosphonate Sarin (GB), 374 N-Isopropylacrylamide polymerization in vesicles, 512 N-Isopropylamide, 567 Isotherms pressure-area, 69 ITIES, interface of two immiscible electrolyte solutions, 302 ITO, 411, 658, 781 ITO coated glass, 792 ITO coated quartz, 657 ITO glass, 789, 794 Jeff-amines, 20 K2DoM dipotassium dodecylmalonate, 670 phase diagram, 672 K2DoM-potassium tetradecanoate-D2O phase diagram, 704 Kanemite, 835, 837, 838 transformation to hexagonal FSM-16, 836 KCl, 833, 835 Keggin ions, 840 anionic, 839 Keggin salt, 839

880 Kenyaite, 838 Kerosene, 474, 475, 603 Ketals, 53 Ketal surfactants rate of biodegradation, 54 KHSO3, 379 Kinetic ‘‘cmc,’’ 229 Kinetic reactivity of coupler dispersions, 580 Kinetic salt effects, 211 Kinetic stabilization, 597 Kinetics of water absorption in latex films, 556 KLE3729 poly[(ethylene-butylene)-co-ethylene oxide], 476 KOH, 379 KPS, 474–476, 484, 487, 488–490, 550, 567, 569 KPS, potassium persulfate, 434 Kraft boundary, 670, 671 in gemini surfactant phase diagrams, 85 Kraft temperature, 177, 436 Kraton liquid, 807 L3 phase of DDAB, 684 La, 838 LABS see linear alkylbenzene sulfonates, 4 Lactamization of 12-aminododecanoic acid, 340 mechanism of activation, 340 Lactonization in reverse micelles, 338 mechanism of activation, 340 of HOC15H31COOH, 340 Lactose, 112 Lakes, 585 Lamellar, 668 Lamellar aggregates, 784 Lamellar aluminophosphates, 839 Lamellar crystals, 706 Lamellar dispersions electrochemical processes in, 309 Lamellar films mesoporous silica, 788 Lamellar gel phase, 688 Lamellar liquid crystalline, LLC phase, 381 Lamellar mesoporous silica, 789 Lamellar mesoporous silica films, 790 Lamellar mesoporous silica particles, 791 Lamellar phase, 527, 669, 674, 676, 825, 826 gel, 688 of geminis, 85 of 12-2-12, 2Br geminis, 82 polymerization in, 530 rippled, 688 Lamellar silica film, mesoporous, 787 Lamellar-hexagonal phase transitions cleavable surfactants triggered by, 145

Index Lamellar-hexagonal phase transition, 822 LaMer diagram, 609–611 Langmuir–Blodgett film transfer, 641 Langmuir equation, 186 Langmuir isotherm application to ion binding, 282, 283 Langmuir–Blodgett films, 402, 634, 657 particle synthesis in, 639 preparation, 640 Laponite gemini adsorption, 78 Large unilamellar vesicles, LUV, 227 LAS, 1, 4 see linear alkyl sulfonates, 4 in detergents, 5 Lateral diffusion coefficient in lipid bilayers, 506 Latex, 845 core shell, 550 flocculation, 547 polystyrene, 442 PS, 811 styrene butadiene, 550 Latex films deformation energy, 554 stress-strain of, 554 maleic hemiester stress strain of films, 556 succinic hemiester stress strain of films, 556 Latex particles, 653 Latex sphere manipulation with optical tweezers, 405 Latex stability, 570 Latexes film forming, 570 by emulsion polymerization, 495 Lauroyl lysophosphocholine, 677 N-Lauroyl glutamate, 13 Lauryl ether sulfate, 28 Lauryl polyoxyethylene(3) alcohol in sulfosuccinic acid monoalkyl esters, 9 Layer-by-layer assembly LbL assembly, 639, 653 polymer particle templating, 604 Layered silica/surfactant nanocomposites, 780 LB films, 644, 646 LbL assembly layer-by-layer assembly, 640, 654 LbL films, 658 LC11C9, glycolipid N-dodecanoyl-N-nonyl lactitol, 700 LCD, 781 Lead nitrate, 635 Lecithin, 36, 480, 520, 582, 591 ␣-Lecithin, structure of, 35 LED, light emitting diodes, 653 LED from LbL assembly, 653 Left-handed helices, 709 Lennard-Jones fluid, 704 Lewis acids, 249 Li⫹-fluorohectorite, 842 Ligand-assisted templating, 832

Index Light addressable release of liquid from capillaries, 170 Light emitting diodes, LED, 653 Light scattering dynamic, 166 static, 166 Light-active surfactants, 155 Limiting surface area of 12-2-12, 2Br at silica/water interface, 73 Limonene ECH of, 298 in various media, 312 Linear alkylbenzene sulfonates (LAS), 1 Linoleic acid, 118 lipoxygenase catalysis peroxidation in W/CO2 microemulsions, 353 oxidation by soybean lipoxygenase, 118 Lipase catalysis of hydrolysis of p-nitrophenol butyrate in W/CO2 microemulsions, 353 of fatty acid esters of sugars, 49 for polyester synthesis, 516 Lipids diol as fat constituents, 3 Lipid bilayers polymerization in of hydrophobic monomers, 508 swelling with hydrophobic monomers, 508 Lipid membranes with hydrophobic polymer scaffold, 509 Lipid packing morphology, 146 Lipid polymerization, 505 Lipid synthesis, 146 Lipid tubes, 834 Lipid vesicles stabilization, 502 Lipids diacetylene, 504 lipoyl functionalized, 503 polymerizable, 399, 502 reactive, 503 Lipophilic receptors, 86 Liposaccharide grafting to polystyrene latex, 559 Liposomes, 11145, 226, 296, 501, 684, 668 calcein photorelease from, 148 fusogenic, 145 magnetic, 398 membrane fusion mechanisms, 145 stealth, 502 targeting mechanisms, 145 Lipoxygenase catalysis of linoleic acid peroxidation in W/CO2 microemulsions, 353 Liquid crystal display, multilayer organic electroluminescent, 792 Liquid crystal lamellar phases, 527 Liquid crystal phases hexagonal, 527

881 Liquid crystal templating (LCT), 820, 821 Liquid crystalline display, LCD, 411 Liquid crystals cubic, bicontinuous, 527 lyotropic, 381 Liquid-gel transition, in AOT-lecithin system, 521 Liquid-liquid interfaces silica films at, 779 Liquid-liquid two-phase reactions, 363 Living anionic block copolymerization, 555 Living polymerization anionic ring opening, 555 LLC, lamellar liquid crystalline phase, 381 Loop size distribution, in gemini solution, 84 Lost-wax casting, 807 Ludox CL, 586 LUMO, 247 LUV, large unilamellar vesicles, 227, 228 Lyotropic liquid crystals, 381 Lysolipids, 400 Lysophosphocholines, 676 M41S, 780, 790, 802, 819, 820, 826, 829, 832, 833, 839 MA, methyl acrylate, 477 MAA, 489, 495 Macroinitiators, 567 Macrosurfactants, 59 MADQUAT 2-methacryloyl oxyethyl trimethylammonium chloride, 478, 480 Magadite, 837, 841 Magnetic fields effects on silica formation, 826 Magnetic liposomes, 398 Magnetic vesicles, 399 Magnetite particles in phospholipid GV, 398 Maleic acid, 249 sulfosuccinates from, 8 Maleic anhydride in sulfo derivatization of alkyl polyglycosides, 29 Maleic hemiester latex films stress strain of, 556 Maleic latex films water absorption kinetics, 556 Maleic surfactants, 555 Maleic surfmers, 553 Malthion, 374 Manganese decacarbonyl, 843 Mannich reaction to yield phosphonate betaine, 36 Mannich-type reactions of aldehydes, 233 of amines, 233 of silyl enolates, 233 to prepare beta-amino ketones or esters, 233 Mannonamide planar bilayer sheets, 706, 707

882 Mannonic headgroup, 706 Mannose, 112 Marangoni effects electrochemical control of, 168 Mass action approach, 177 Mass action model, 186 Mass transfer effects on electrochemical processes in O/W emulsions, 299 Mass transport of electroactive solutes in microemulsions, 325 Mass transport in microemulsions effects of structure on, 324 Mass transport of surfactants, 167 Materials incompatible, 797 Materials synthesis by polymerization, 525–534 Matrix stabilization, 599, 603 Maximum bubble pressure method, 157, 158 MBA, 493 MBBA, N-(4-methoxybenzylidene)-4-butylaniline, 678 MBT, 2-mercaptobenzothiazole anodic oxidation of, 315 MCM-22, 842 MCM-41, 525 MCM-41, 787, 805, 820–828, 831, 835–838, 842–845 mechanism of formation, 820 organically functionalized, 844 MCM-48, 819–821, 823–825, 842 MCM-50, 819, 820, 824, 832 ME, mercaptoethanol, 658 Me(EO)45(caprolactone)10CONHC(CH3)2C6H4C(CH3)CH2 surfmer, 553 Me(EO)45(caprolactone)10OCOCHCHCOOH surfmer maleic, 553 Me(EO)45[(CH2)4O]10H, 553 Me3N⫹(CH2)nN⫹Me3⭈2X⫺ bolaform (n) X2, 236 MECC, micellar electrokinetic capillary chromatography, 232 Mechanical properties stress strain curves, 555 Mechanism of electrooxidation of benzyl alcohol, 307 of electrochemical chlorination of amine hydrochlorides, 306 Mediated electrochemical synthesis in microemulsions, 325 in surfactant films, 325 Mediator catalyst in electroorganic synthesis, 325 Mediator formal potential control, 328 MeEO45BO12OCNHCOCH(CH3)CH2 surfmer (methacyloyl isocyanate), 553 MeEO45BO12OCOCH2SH transurf, 553 MeEO45BO15CH2C(C6H5)CHCH2 surfmer, styrenic, 553

Index MeEO45BO8OCOCHCH2 surfmer, acrylic, 553 MeEO45BO9CONHC(CH3)2C6H4C(CH3)CH2 surfmer, 553 MeEO45BO9SC(C6H5)CHCH2 transurf, 553 MEKC, micellar electrokinetic chromatography, 86 Membrane bending, 397 curvature, 397 elasticity, 397 energy, 397 expansivity, 397 morphology, 397 Membrane electrodes, 86 Membrane mimetic, 634 Membrane protein extraction, 117 Membrane protein function, 502 Membranes, 634 synthesized from silica, 780 (⫹)-p-Menthene by ECH of D-limonene, 312 MeONS hydrolysis of, 199 2-Mercaptobenzothiazole, MBT, 315 Mercapto functionalized latexes, 482 Mercaptoethanol ME, 658 stabilization of CdS, 658 Mercaptopropyl, 844 11-Mercaptoundecanoic acid, 169 MES see ␣-sulfo fatty acid methyl esters, 7 Mesitylene, 827, 833 Mesophases electroorganic synthesis in, 296 Mesopores through supramolecular templating, 802 Mesoporous films, 781 platinum on gold, 781 Mesoporous materials templated by gemini surfactants, 87 Mesoporous solids morphology, 833 Metal colloids, 495, 799 Metal oxide nanoparticles synthesis in W/CO2 microemulsions, 354 Metal nanoparticles synthesis in W/CO2 microemulsions, 354 Metal phthalocyanine, MP copper or iron, 410 Metal phthalocyanines, MPC, 330 Metallated porphyrin, 845 Metallic soaps, 2 Metallized pigments, 585 Metallosupramolecular coordination polyelectrolytes, 562 Methacrylate, 457 condensation onto hydroxylphenyldimethylsulfonium methyl sulfate, 559

Index Methacrylate-terminated phthalate glycol polyester dispersion polymerization stabilizer, 566 Methacrylic acid, 476, 489, 493 Methacrylic acid esters, 431 Methacryloyl, 503, 504 2-(Methacryloyloxy)-ethyltrimethylammonium chloride, MADQUAT, 483 Methanol, 476, 482, 791, 820, 824, 825 2-Methacryloyl oxyethyl trimethylammonium chloride, 490 MADQUAT, 480 copolymerized with acrylamide, 489 p-Menthane by ECH of D-limonene, 312 p-Methoxybenzaldehyde PMBA, anisaldehyde, 300 2-Methoxybenzonitrile, 2-MBN, from anodic cyanation of 1,2DMB, 317 N-(4-Methoxybenzylidene)-4-butylaniline MBBA, 678 p-Methoxytoluene, PMT, 300 indirect oxidation of, 300 Methoxy-halide ion exchange in trimethyl ammonium halides, 32 ␻-Methoxy-PEG-undecyl-␣-methacrylate dispersion polymerization stabilizer, 566 N-Methylacetamide, 272 chemical trapping of, 291 in chemical trapping, 290 Methyl acrylate, MA, 477 N-Methyl-N-alkyl-urocanic esters, 672 Methyl amine to give N-methyl glucamine, 27 Methyl benzyl surfactants, 557 2-Methylbut-3-yn-1-ene by dehydration of 2-methylbut-3-yn-2ol, 842 2-Methylbut-3-yn-2-ol, 842 Methyl cellulose, 567 dispersion polymerization stabilizer, 566 N-Methyl-2-chloropyridinium iodide as carboxyl activating agent, 338 N-Methyl-4-cyanopyridinium ion alkaline hydrolysis of, 228 N,N⬘-Methylenebisacrylamide, BAM, 483 N,N⬘-Methylenediacrylamide, 507 Methyl esters, of fatty acids, 2 N-Methylglucamine, 26 Methyl glucoside esters, 28 by transesterification of methyl glucosides, 29 N-Methyllactobionamide polymerization of, 344, 345 Methyl methacrylates, MMA, 131, 447, 531, 532 suspension polymerization of, 564 Methyl methacrylate-butyl acrylate copolymer, 555 Methyl naphthalene-2-sulfonate, 186, 188 hydrolysis of, 199

883 Methyl orange, 132 in dendritic micelles, 140 Methyl pyrrolidone, 588 N-Methyl-2-pyrrolidone, 379 Methyl vinyl ketone, 248 Methyl violet Lake Bronze Violet GI, 409 Methylacrylate, 248 Methylamine glucamides from and glucose, 25 Methylammonium chloride conversion of methyldichloroamine, 305 N-Methyl glucamine acetylated with fatty acid methyl ester, 27 Methylglucoside esters applications of, 23 production capacity, 23 N-Methyl glycine see Sarcosine, 13 N-Methyl-N-nitroso-p-toluenesulfonamide, MNTS, 190 N-Methylnorbornylgluconamide polymerization of, 344, 345 2-Methyl pyrrolidinone, MP, 377 Mg2⫹, 838 MgS, 644 Mica, 781, 834 Micellar counter ion exchange and affinity, 285 Micellar aggregates, 824 Micellar autocatalysis, 413 Micellar catalysis, 250, 362, 377, 414 of geminis, 86 role in electrochemical synthesis, 307 single phase, 360 stereospecific catalysis, 361 two-phase, model for, 369 Micellar cubic phase, 679, 698 Micellar effects on enantioselectivity, 258 on endo-exo selectivity, 256, 257 on reaction rates, 175 on regioselectivity, 257 with catalytic counterions, 258 Micellar electrokinetic capillary chromatography, MECC, 232 Micellar electrokinetic chromatography, MEKC, 86 of geminis, 85 Micellar emulsion polymerization, 561 Micellar growth of cationic surfactant oligomers, 80 Micellar inhibited reactions counter ion effects on, 283 Micellar inhibition, 260 role in electrochemical synthesis, 307 Micellar nucleation, 434 Micellar phase transfer catalysis, 233, 362 Micellar rate effects on Diels–Alder reactions, 252 pseudophase model, 182

884 [Micellar rate effects] substrate hydrophobicity, 221 Micellar solubilization, 537 Micellar solution, 676 isotropic, 669 Micellar-emulsion polymerization, 560 Micellar-enhanced ultrafiltration separation by, 86 Micellar/hexagonal boundary of geminis, 85 Micelle properties micropolarity, 78 solubilization capacity, 78 Micelle shape, 668 Micelle to vesicle transition, 696, 700 Micelle-mediated transport, 419 Micelles, 577, 634, 784, 822 N-acetyl-N-dodecyllactosylamine, 119, 120 N-alkyl-aminolactitols, 116 AOT, 481 cationic, degree of ionization of, 283 curvature, 831 cylindrical, 808 N-dodecylaminolactitol, 120 N-dodecyllactobionamide, 120 electroorganic synthesis in, 296 formation, 832 mixed, 792 HPS, 285 monomer swollen, 480 of PFOA-g-PEO, 133 spherical, 798 unimolecular dendritic, synthesis of, 139 wormlike, 798 zwitterionic, interfacial halide concentrations in, 284 Micelles as nanoreactors, 798, 799 Micellization, in pH shifting, 597 Michael addition of methyl acrylates to fatty amines, 37 Michaelis-Menton equation, 182 Microcapsules of pigments poly(vinyl alcohol) as stabilizer, 564 Microelectronic devices, 609 Microemulsion, 429 bicontinuous, 602 oil-in-water, 602 water-in-oil, 602 water/AOT/heptane, 630 water/PEDGE/hexane, 609 Microemulsion ‘‘phases,’’ 374 Microemulsion droplets, 577 Microemulsion polymerization, 429, 471, 509, 528, 529 free radical, 455–468 of styrene/gemini systems, 87 Microemulsion structure bicontinuous, 324 O/W, 324 Microemulsions, 45, 477, 480, 527 catalytic electrodes in, 333

Index [Microemulsions] conductive, 324 electrochemical processes in, 309 electroorganic synthesis in, 296, 323 polymerizable surfactants in, 559 precipitation in, 609–630 reverse counter ion concentrations in, 284 water concentrations in, 284 solubilizing capacity for synthesis, 323 transesterification in, 23 water/AOT/heptane, 609, 611, 617, 622, 624, 626 water/CTAB/hexanol, 609, 616, 620, 625, 630 water/PEDGE/hexane, 622, 623 Microgels functionalized, 495 Microinjection techniques for studying GV, 397 Microlatexes, 481 Micropolarity of cationic surfactant oligomers, 78 Micropores through molecular templating, 801 Microreactors vesicles, 227 Microscopy atomic force (AFM), 510 confocal laser scanning (CLSM), 511 fluorescence, 511 optical, 532 phase contrast, 511 polarizing, 512 scanning electron, 511 video enhanced interference contrast, 695 Microsuspension, 827 Microsuspension polymerization, 429, 472 Microviscosity of gemini surfactant micelles, 79 Mild surfactants ether carboxylic acids, 3 Mineral oil, 376 Miniemulsion, 429 Miniemulsion polymerization, 429, 472, 553 cetyl alcohol in, 560 in nanocolorant formation, 605 SDS in, 560 Miniemulsions polymerizable surfactants in, 559 Minimum surface area as function of gemini spacer length, 71 Miscible solvent mixing, 587 Miscible solvent shifting, 589 Mixed micellar precipitation, 599 MKA equation, 441 MMA, 132, 483, 555, 559, 566, 567 methyl methacrylate, 477 Mn, 838 Mn2⫹, 838 Mo, 838 MO4Al12(OH)24(H2O)12⫹7, 839

Index Mobility electrophoretic of silica, 71 Models describing phase behavior, 702–706 Molecular dynamics, 704 of C12EO2-water system, 705 Molecular tectonics, 634 Molecular templating, 801, 802, 823, 824 Molecular volume, 579 Molecular weight distribution in microemulsion polymerization, 459, 463 Monad G, coconut monoglyceride, 11 Monoalkyl carbonates, 48 Monoesters of phosphoric acid, 14 Monoethanol amines to give alkanol amide sulfates, 11 Monoglyceride sulfates, 11 by continuous process, 10 in shampoo, 10 combined with aminophosphate surfactant, 11 combined with amphoteric surfactants, 11 combined with phosphoric acid esters, 11 combined with succinic acid, 11 skin compatibility, 11 Monoglycerides conversion to monoglyceride sulfates, 11 ethoxylation of, 19 Monolithic solids synthesized from silica, 780 Monomer adsolubilization, 538 diffusion, 480 partitioning, 460 Monomer particles biradical termination, 466 Monomer solubility of surfactants, 667 Monomer starvation in emulsion polymerization, 433 Monomer swollen micelles, 480 Monooleoylphosphocholine, MOPC, 404 Monopalmitin route to plasmenylcholine, 147 Monsanto process for production of adiponitrile emulsion basis, 323 Montane 83, 484, 486 sorbitan sesquiolate polyoxyethylene sorbitan trioleate, 475 Montanox 80 sorbitan sesquiolate polyoxyethylene C18 terminated acrylamide polymer, 475 Montanox 85, 486 Monte Carlo simulation, 71, 178, 704 emulsion polymerization modeling, 489 of gemini CMC, 76, 77 Monyanox 85, 484 MOPC, monooleoylphosphocholine, 404 3-Mordent Blue, 586 Morgen model in microemulsion polymerization, 462

885 Morphology arcs, 834 discoids, 834 fibers, 834 gyroids, 834 lipid tubes, 834 of mesoporous solids, 833 rods, 834 ropes, 834 sheets, 834 MP, 2-Methyl pyrrolidinone, 377, 378 MP, metal phthalocyanine, 410 MSU-V, 831 MSU-X, 828, 831 Multifunctional surfactants, 2 Multigranular spheres, 833 Multilamellar vesicles, 808, 831 Mustard, bis(2-chloroethyl)sulfide, 374 Mustard simulant b, 401 Mylar, 779 MYR145 polyoxyethylene(8) stearic acid, 475 Myristic acid, 601 Myristoyl lysophosphocholine, 677 Myristyl polyoxyethylene(3) alcohol in sulfosuccinic acid monoalkyl esters, 9 Myristyldimethylamine N-oxide OMe-14, 236 Myristyldimethylamine oxide AOMe-14, 176 Myristyldimethylammonium propanesulfonate SB3–14, 176 Myristyldimethylammonium carboxybetaine CB1–14, 236 Myristyldipropylamine N-oxide AOPr-14, 236 N2 adsorption, 831 N2H4, 642 Na alginate dispersion polymerization stabilizer, 567 Na dioctyl sulfosuccinate dispersion polymerization stabilizer, 566 Na-glucoside tartrate, 29 Na2O, 824 NaAA, sodium acrylate, 483 NaAAS sodium 10-acrylamidostearate, 550 sodium 9-acrylamidostearate, 550 NaAlO2, 837 NaAMPS, sodium 2-acrylamido-2-methylpropanesulfonate, 483 NaAMPS, 474 NaCl, 835 NaCl-type structure, 636 Nacre, 780 NaDTC, sodium dimethyldithiocarbamate, 305

886 Nafion, 640, 651 films, 657 NaHSi2O5: 3H2O, 835 NaHSO3, 475 NaMA, sodium methacrylate, 476 Nanocast, 807, 808 Nanocasting, 807, 810 Nanochemical structures, 797 Nanochemistry, 797 Nanocolorant precipitation, 605 Nanocomposites hexagonal silica/surfactant, 780 layered silica/surfactant, 780 Nanocosa-10, 12-diyonic acid, 644 Nanocrystalline silver particulate films, 634 Nanodisks, 601 Nanolaminated films by dip coating, 780 Nanolatexes produced with polymerizable surfactants, 559 Nanoparticle films schemes for preparation of, 640 Nanoparticle precipitation by pH shifting, 599 Nanoparticle stabilization in microemulsions, 613 Nanoparticle synthesis in amphiphilic films, 639–660 in microemulsions, 609 in W/critical fluid microemulsions metal and metal oxide, 354 Nanoparticles CdS, 519, 657 ferrite, 519 from gluconamides, 344 in LB films by incorporation of particles, 641 by metal ion reduction, 641 in situ formation, 642 schemes for, 642 poly(DL-lactide-co-glycolide), 567 recovery, 628 silica, 586 TiO2, 519 Nanoreactors, 804 micelles as, 799, 798 Nanostructure design with block copolymers, 797–816 Nanostructured aluminosilicate, 811 Nanostructured porous silica, 808 Nanostructured precipitates, 807 NaOH, 825 NAP, 4-nitrosoantipyrene, 316 Naphthalimides HIV inhibitors, 122 2-Naphthol, 520 ␤-Naphthol, solubilization by cationic geminis, 78 1,4-Naphthoquinone, 252 Navy Blue, 591, 592 Nb, 838

Index 6-NBIC, 6-nitrobenzisoxazole-3-carboxylate, 191, 196, 229 Nb(Oet)5, 833 Nb(Oet)5-dodecylamine mixtures, 833 Nb(Oet)5-octadecylamine mixture, 833 Nb-TMS1, 833 niobium transition metal oxide molecular sieve, 832 Nb-TMS2, 832 Nb-TMS3, 833 Nb-TMS4, 832 Nb-TMS5, 833 Nb2O5, 838 NBF, N-butylformamide, 377 NDPA, 4-nitrosodiphenylamine cathodic reduction of, 308 Needles, 813 Neoglycolipids, 112–115 Nerve agents, 374 Neutral amine surfactants, 838 Neutral surfactants, 829 Neutron reflectivity nonionic sugar geminis, 71 of cationic geminis, 71 (NH4)2S2O8, 476 Ni(DS)2, 258 Ni2⫹, 838 NIAD, 551 Nickel boride, 618, 620 Nickel flake, 544 Niobium oxide, 833 Niobium transition metal oxide molecular sieve Nb-TMS-1, 832 Niobotungstate clusters, 840 Nitrile rubber, 547 Nitrobenzene/electrode interface, 307 Nitrobenzene/water emulsion, 302 Nitrogen adsorption isotherms, 808 Nitroguanidine, 593 Nitrolignin, 567 p-Nitrophenol butyrate lipase catalysis of hydrolysis in W/CO2 microemulsions, 353 p-Nitrophenoxide, 375 p-Nitrophenyl chloroformate hydrolysis in W/CO2 microemulsions, 351 p-Nitrophenyl diphenyl phosphate, 187 PNDP, 375 p-Nitrophenylphosphate, 185 enzymatic hydrolysis in microgels, 495 Nitrosamines, 26 4-Nitrosoantipyrene, NAP reduction at Pb cathode, 316 4-Nitrosodiphenylamine, NDPA, 308 ␤-Nitrostyrene, 507 Nitrous oxide, 591 NLO, nonlinear optical materials, 516 NMR, 478, 509, 520, 522, 527, 548, 549, 555, 613, 615, 616, 702, 819, 820, 824, 827, 838, 840

Index [NMR] chemical shifts, 614 magic angle spinning, 783, 830, 836 of styrenic anionic block copolymers, 558 self-diffusion measurements, 457 29 Si, 836 solid state, 812 NMR spectra of PS-b-PFOA, 136 Noncyclic acetal surfactants, synthesis of, 52 Nonionic ferrocenyl surfactants FPEG in electroless plating, 407 Nonionic geminis, 61 CMC, 102, 103 Nonionic nucleophiles, 271 Nonionic styrenic surfmer, 554 Nonionic sugar-based geminis cylindrical micelles of, 80 discoidal micelles, 80 Nonionic surfactants, 14, 829 alcohol ethoxylates, 45 alkylphenol ethoxylates, 45 by alkoxylation, 2, 14 by ethoxylation, 14 by ethoxylation of alcohols, 18 by oxethylation, 14 by propoxylation of alcohols, 18 from aliphatic alcohols, 18 glucoside geminis, 65 Nonionic surfmers, 554 Nonionic-anionic geminis, 65 Nonionic-cationic geminis, 65 Nonionic-nonionic geminis, 65 Nonlinear optical materials NLO materials, 516 Nonmicellar aggregates reactions in, 226 Nonpercolating inverse systems polymerization kinetics in, 481 Nonseeded emulsion polymerization, 446 Nonsoap surfactants, 1 N-Nonylaminolactitol, 117 Nonylphenol-PEG-monomaleate dispersion polymerization stabilizer, 566 Norbornene polymerization of, 341–344 Norrish type II cleavage, 55 Norrish-Trommsdorff effect in emulsion polymerization, 433, 434 NOS 25, 557 NP 30, 557 NS dispersions, 581 Nucleation, 579, 610 continuous, 480 in emulsion polymerization, 438, 439 rates, 588 Nuclei, 579

887 Nucleophiles strongly basic, 274 Nucleophilic substitution in derivatizing alkyl polyglycosides, 28 Nylon 12, 591 O/W, oil-in-water, 527 OC, octylglucoside, 700 [(OCF2CF(CF3))n(OCF2)m]OCF2COO⫺NH4⫹ in reverse microemulsions, 139 Octadecylamine, 635, 833 Octanoic anhydride hydrolysis of, 427 Octanol, 478 n-Octanol, 781 N-Octylamide tail, 706 N-Octylaminolactitol, 120 ␤-1-n-Octyl-D-glucopyranoside, 116 Octyl glucoside, 398 Octyl gulonamide, 708 Octylglucoside, OC, 700 t-Octyl-phenoxy-PEO10 methacrylate T10, 475 t-Octylphenoxy-poly(oxyethylene) methacrylate, 483 OHP, organophosphorous hydroxylase, 380 Oil-in-water, O/W, 527 Oil-in-water emulsions containing micelles, 362 electrochemical processes in, mechanisms, 296 Oil-in-water microemulsions, 374, 455, 477, 602 Oil-water interface, 779 Olefin sulfonates, 6 ␣-Olefin sulfonates (AOS), 6 from ethylene oligomerization, 6 Oleic acid vesicles, 399 Oleic anhydride hydrolysis of, 427 1-Oleoyl-sn-glycero-3-phosphocholine in water phase diagram, 670 Oleoyl lysophosphocholine, 678 Oleoyl sarcosinate, 13 Oleyl alcohol, 673 Oligomeric silica clusters, 820 Oligomeric surfactants, 59 Oligomerization degree effect on gemini CMC, 78 Oligomers, 66, 67 Oligosaccharides cell surface, 112 Olive oil sulfation of, 10 OP10, 489 OPA, organophosphorous acid anhydrase, 380 Optical latex sphere manipulation, 405 microscopy, 532 polymerization, 640

888 [Optical] switches, 659 trapping, 395, 404 tweezers Organic compound solubilization in micellar solutions, 303 Organic dispersions, 584 Organic in CO2 microemulsions, 350 Organic phase wetting of electrodes, 301 Organic pigments, 594 Organic reactions in W/CO2 microemulsions, 351 Organic solvents, use in solubilizing reactants, 359 Organically functionalized MCM-41, 844 Organophosphorous acid anhydrase, OPA, 380 Organophosphorous compounds hydrolysis, 375 Organophosphorous hydroxylase, OHP, 380 Organosilane surfactants, 829 Organotrialkoxysilanes, OTOS, 844 Ortho esters, 54 synthesis of, 55 Osmotic agents, 472 compressibility, 441 pressure gradient, 560 pressure measurements, 700 Osmotically stabilized droplets, 490 Ostwald ripening, 472, 579, 583, 605, 652 in miniemulsions, 559, 560 Ostwald–Freundlich equation, 579 OTOS, organotrialkoxysilanes, 844 Oxalid acid, 603 Oxidation of benzaldehyde, 306 of chemical agents, 379 of Fe(CN)2 (bpy)2, 191 of mustard, 379 organics catalyzed by high-valent oxides effects of surfactants on, 318 of unsaturated fatty acid by soybean lipoxygenase, 120 of V-type phosphorothiolates, 379 of VX, 379 Oxidative polymerization in dispersion polymerization of aniline/APS, 566 of aniline/SPS, 566 of phenol, 566 of pyrrole/APS, 566 of 3,5-xylidine/APS, 566 Oxo process alcohols from, 18 Oxone, 379 Oxonols, 594 Oxyethylated fatty alcohol in synthesis of ether carboxylic acids, 3 Oxyethylation to yield nonionic surfactants, 14 Ozone-cleavable spacers in anionic geminis, 65 Ozonolysis in titration of double bonds, 459

Index P2VP, poly(2-vinylpyridine), 799 P62/mmc, 826, 829, 832, 834 Packing at air-water interface, 69 Packing parameter, 526, 668, 678, 680, 683, 684, 694, 702, 705, 706 Paliogen Red L 3530HD pyranthrone red, 409 Paliogen Red L 3910HD perylene red, 409 Palisade layer, 675 Palmitoyl chloride, 147 Palmitoyl lysophosphocholine, 677, 678 Papain, 845 Paraffins sulfochlorination of, 6 Parameter critical packing, 526 surfactant packing, 526 Paraoxon, 374 Partial solubility parameters, 473 Particle coalescence in emulsion polymerization, 445 Particle concentration, 656 Particle condensation, 577 Particle formation in emulsion polymerization, 433 in LB films, 649 Particle growth in emulsion polymerization, 433, 443 in films, 647 Particle nucleation, 567 in emulsion polymerization, 434 Particle polydispersity in microemulsion polymerization, 458 Particle precipitation, 577 Particle shape, 648 Particle size, 830 of cholesterol, 625–627 of cholesteryl acetate dispersions, 585 of cobalt nickel boride, 621 of nickel boride, 620 of platinum particles, 622 of Pt-ReO2, 624 of rhodiarome, 629, 630 of rhovanil, 627 with surfmer, 551 Particle size analysis, 583 Particle size control, 643 Particle size determination TEM, 644 x-ray diffraction, 644 Particle size distribution in microemulsion polymerization, 460 Particle size monodispersity in dispersion polymerization, 560 Particle sizing by capillary hydrodynamic chromatography, 460 by centrifugation, 460 by quasielastic light scattering, 460 by TEM, 460

Index Particles Ag, 635, 644 AgI, 644 Au, 635, 644, 653, 656 ␤-carotenoid, 587 CdBr2, 644 CdCl2, 644 CdI2, 644 Cd-MnS, 644 CdS, 635, 644, 653 in Nafion films, 652 CdS/CdSe, 644 CdS/HgS, 644 CdS/PbS, 644 CdS/Pt in Nafion films, 652 CdS/ZnS, 644 in Nafion films, 652 CdSe, 644, 653 in Nafion films, 652 CdTe, 644 CeO2, 653 cholesterol, 624 clay, 653, 656 core shell latex, 550 CoS, 644 coupler dispersion, 580 Cu, 644 CuS, 644 Fe3O4, 653 encapsulation, 566 FeS2 in Nafion films, 652 gliaden, 586 hexagonal mesoporous silica, 791 HgS, 644 lamellar mesoporous silica, 791 latex, 653 MgS, 644 nickel boride, 618, 620 oxidized graphite, 653 PbI2, 644 PbS, 635, 644, 653 in Nafion films, 652 Pd, 644 PdS, 644 platinum, 623 platinum synthesis, 622 polypyrrole by emulsion polymerization, 495 porcupine, 569 proteins, 653 Pt in Nafion films, 652 PtS, 644 rhenium dioxide, 623 silica, 653 encapsulation, 566 SiO2 in Nafion films, 652 superparamagnetic hydrogel, 495

889 [Particles] TiO2, 644, 653 in Nafion films, 652 virus, 653 zirconia, 653 ZnS, 635, 644 Partitioning pseudophase model, 304 Passivation by emulsions, 315 by surfactant films, 315 of electrodes, 315 solvent effects, 317 specific interaction effects, 317 Patch clamp experiments, 400 Patterned dewetting, 169 Pb stearate, 651 PB-P2VP, 800 PB-PEO templated silica, 809 Pb2⫹, 838 PB202PEO360/water binary phase diagram, 809 PBE, 187, 188, 228 Poisson–Boltzmann equation, 181 PbS, 643, 644, 653 in LB films, 648 in Nafion films, 657 nanocrystallites, 636 nanoparticles, 635 particles epitaxially oriented, 636 grown under arachidic acid monolayers, 638 grown under hexadecylphosphate monolayers, 638 in Nafion films, 652 PbS particulate films electron diffraction, 636 TEM, 636 PbS/stearic acid films, 648 PbSe nanoparticles, 635 PCB, 373 Pd, 643, 644 Pd(Ac)2, 799 PdCl4/DDA2 films, 651 PDMS, 131, 137, 806 stabilizer in critical fluids, 357 stamp, 806 PDMS-b-P(MMA-co-MA) PMMA latex stabilizer in W/CO2, 357 PDMS-b-P(t-BA-co-AA) PMMA latex stabilizer in W/CO2, 357 PDMS-b-PAA, 350, 352 PDMS-b-PMA, 352 PDMS-b-PMMA-b-PAA PMMA latex stabilizer in W/CO2, 357 PDMS-b-PVAc stabilizer in critical fluids, 357

890 PDMS-PAA block copolymers dispersants for water in CO2 emulsions, 350 PEDGE, 622 penta(ethylene glycol) dodecyl ether, 609 PEDTA, poly(ethyleneimine tetraacetate), 814 PEE, polyethylethylene, 404 PEG, 565–567 PEG grafts on bilayers, 402 PEG-maleate dispersion polymerization stabilizer, 566 PEG-maleate-alkyl dispersion polymerization stabilizer, 566 PEG600, 350 PEI, 655 PEM, pentaerythriolmyristate, 475 Pendant drop method, 163 Pendant droplet release light induced, 155, 171, 172 Penta(ethylene glycol) dodecyl ether, PEDGE, 609 Pentaerythriolmyristate, PEM, 475 1-Pentanol, 376 PEO, 373, 812, 829 PEO-b-MMA-Asp, 814 PEO-b-PEDTA, 814 PEO-b-PMMA-Phos, 814 PEO-PEE block copolymers giant vesicles from, 404 PEO-PPO dispersion polymerization stabilizer, 566 PEO-PPO-PEO, 804, 829, 835 Percolating inverse systems polymerization kinetics in, 481 Perfluorocarbon fluids in suspension polymerization, 564 Perfluoropolyether surfactants, 137 Perfluoropolyethers sorbitol ester derivative, 138 sulfate derivatives, 138 sulfonate derivatives, 138 Perindo Maroon R-6424 Perylene maroon, 409 Permeability of vesicles switchable, 505 Peroxidation of linoleic acid in W/CO2 microemulsions catalyzed by lipoxygenase, 353, 354 Persistence length in wormlike micellar solution, 84 Personal care castor oil ethoxylates, 20 Perylene vermillion Aliogen Red L 3870HD, 409 Perylene maroon Perindo Maroon R-6424, 409 Perylene red Paliogen Red L 3910HD, 409 Perylene scarlet Indofast brilliant scarlet R-6500, 409 Perylene vermilion films on ITO SEM of, 410 Petroleum ether, 476

Index PFOA, 490 poly(1,1-dihydroperfluorooctyl acrylate), 355 dispersion polymerization stabilizer, 566 stabilizer in critical fluids, 357 synthesis in supercritical CO2, 131 PFOA-b-PS micelles in supercritical CO2, 136 PFOA-b-PVAc, stabilizer in critical fluids, 357 PFOA-g-PEO, 132 PFOMA see poly(fluorooctylmethacrylate), 141 PFPE-Mn surfactants, 351 PFPECOO-NH4⫹ in water-in-CO2 microemulsions, 350 pH in water/CO2 microemulsions, 350 pH shifting, 594 pH shifting precipitation, 597 Pharmaceutical dispersions, 588, 590 Phase behavior of branched chain surfactants, 680 of CiEOj surfactants, 672 of double-chain surfactants, 667, 680 of multiple-chain surfactants, 667, 680 of polymerizable microemulsions, 456 of single-chain surfactants, 667 of surfactant mixtures, 694–702 Phase contrast microscopy of phospholipid GV, 396 Phase contrast microscopy, 511 Phase diagrams C12E6 in water, 670 C6EO2-water, 704 C6EO3-water, 704 C7EO3-water, 704 C13/C15EOx surfactants, 673 CTAB-SOS-water, 696 CTAT-SDBS-water, 698 DDAB-AOT-water, 699 DDAB-LC11C9-water, 700, 701 DDAB-SDS-D2O, 698 decyl trimethylammonium bromide and sodium decylsulfate mixtures, 165 DTAB-SDS-water, 696 DDAB-water, 699 DMPC, 689 DoPPDAC, 672 double chain surfactants, 682 DPPC, 689 DPPE, 689 DTAC, 695 DTAC in water, 670 DTAC-SN-D2O, 694, 695 EPC-OG-water, 701 HFDePC, 681 K2DoM, 672 K2DoM-potassium tetradecanoate-D2O, 704 oleoyl lysophosphocholine, 678 palmitoyl lysophosphocholine, 678

Index [Phase diagrams] SDS-water, 699 SN, 695 sodium 2-methyldecanoate in water, 670 SSPOM, 672 stearoyl lysophosphocholine, 678 ternary of microemulsions, 376 water, oil, emulsifier, 381, 382 tetradecyl tripentylammonium bromide, 671 zwitterionic 1-oleoyl-sn-glycero-3-phosphocholine in water, 670 Phase inversion temperature of AE, 18 PIT, 18 Phase prism C12EO5-water-decane, 675 Phase separation in gemini vesicle systems, 84 Phase separation model, 177 Phase structures of block copolymers, 812 Phase transfer catalysis, 295, 297, 350, 360 PTC, 31 by micelles, 233 micellar, 362 Phase transfer reactions in W/CO2 microemulsions, 352 Phase transition cleavable surfactants, triggered by, 145 lamellar to hexagonal, 822 Phase transition temperature for DSPC and derivatives, 690 Phenanthrene ECH of, 312 Phenobarbital, 596 Phenobarbitone phenobarbital, 596 Phenol, 48 alkylation of, 365 Phenol-formaldehyde resins, 516 Phenolic ethers synthesis of unsymmetrical, 364 Phenolic glycidyl ether synthesis of, 364 Phenoxides, 196 1-Phenylethanol from reduction of acetophenone on Pb cathode, 314 2-(2-Phenyl-2-propenylthio)propanoic acid, 549 Phosphoric acid esters as alkanolamine salts, 14 as potassium salts, 14 Phos, poly(phosphate), 814 Phosphatation to make geminis with polyphosphoric acid, 62 Phosphate in anionic geminis, 61 Phosphate esters IBA catalyzed hydrolysis, 378 Phosphate geminis, 71 Phosphate headgroups, 832, 833

891 Phosphatides as fat constituents, 3 Phosphatidic acid, 690 Phosphatidyl choline, 592 Phosphatidyl ethanolamine, 592 Phosphatidyl inositol, 592 Phosphatidyl nucleosides, 399 Phosphatidylcholine, 690 egg, (EPC), 700 Phosphatidylethanolamine, 591, 690 Phosphatidylglycerol, 690 Phosphatidylinositol, 591 Phosphatidylserine, 690 Phosphocholine, 690 GV, 398 Phospholipase, 145 Phospholipase A2, 149, 284 Phospholipase D, 400 Phospholipase PL-A2 snake venom, 400 Phospholipids, 226, 501, 688, 839 plasmenylcholine, 145 Z-vinyl ether linked, 145 Phosphonate betaine by Mannich reaction, 36 Phosphoric acid, 838 Phosphoric acid derivatives, 13 Phosphoric acid esters, 13 esterification with o-phosphoric acid, 14 in shampoo, combined with monoglyceride sulfates, 11 Photo-optic applications, 660 Photoactive surfactants, 166 Photobleaching, 659 Photochemical reduction of disulfide, 162 Photochemistry in microemulsions, 309 Photocleavage of alkyl aryl ketone, 56 Photodegradation of diazosulfonate surfactants, 57 Photoelectrochemical cell, 657 Photoelectrochemistry of films, 657 Photoelectrodes, 659 Photographic couplers, 588 amphiphilic color forming, 581 Photoinitiator, 550 oil soluble, 559 Photoisomers of azobenzene surfactants, 166 Photolabile surfactants, 55 Photooxidation plasmenylcholine, 146 Photovoltage as function of particle size of CdS in arachidic acid films, 658 CdS/PDADMAC LbL films, 659 produced by LbL particle films of CdS/ME particles, 658 Phthalocyanine, 603, 845 Phthalocyanine blue E Heliogen blue L6700F, 409 Phthalocyanine blue G Cromofine blue 4920, 409

892 Phthalocyanine blue R Cromofine blue B145, 409 Phthalocyanine green, 409 Phthalocyanine green 6Y Heliogen green D9360, 409 N-Phthaloylglycine, 190 Phy, phytanyl chain, 690 Physical state amorphous, 577 crystalline, 577 Physicochemical properties of amphoteric surfactants, 38 Physicochemical properties of films, 657 Phytanyl chains Phy, 690 PIE model, 185 pseudophase ion exchange model, 180 Pigments, 588 Pillared clays, 831 Pinacol by cathodic reduction of acetophenone, 299 PIT see phase inversion temperature, 18 Planar bilayers, 668 Plasenylcholine synthesis from monopalmitin, 147 Plasmalogen see plasmenylcholine, 145 Plasmenyl lipid pool, 145 Plasmenylcholine phospholipids, 145 Plasmenylcholine photooxidation, 146 Platelet-shaped seeds, 814 Platelike morphologies, 831 Platinum particles, 622, 623 PLL, poly-L-lysine, 333 PLL-mediator films on electrodes, 334 Pluronic-derived silicas, 805 Pluronic-type triblock copolymers, 804 Pm3n, 785, 786, 790, 826, 829, 833, 834 PMAc, 799 PMBA, p-methoxybenzaldehyde, 300 PMMA, 134, 137, 138, 411, 483, 555, 567 poly(methyl methacrylate), 356 PMMA-b-PEG, 568 PMMA-b-poly(acrylic acid), 568 PMT, p-methoxytoluene, 300 PNDP, 380 p-nitrophenyldiphenyl phosphate, 375 hydrolysis of, 377 in microemulsions, 375 PNIPAM, poly(N-isopropylacrylamide), 512 PO see propylene oxide, 14 POE-(20)-sorbitan monoleate, 583 Point of zero charge (PZC), 72, 537 of electrodes, 304 Poisson–Boltzmann approximation, 703 cell model, 703

Index Poisson–Boltzmann equation, 186 PBE, 181 Polar substituents micellar rate effects, 223 Polarizing microscopy, 512 Poly(((methacryloyloxy)undecyl)-N,N⬘-dimethylamino-N-2hydroxyethyl ammonium bromide), 569 Poly(1,1⬘-dihydroperfluorooctyl acrylate) PFOA, 131 as steric stabilizer in W/CO2 microemulsions, 354 dispersion polymerization stabilizer, 566 stabilization of PEHA emulsions in CO2, 355 Poly(1,1-dihydroperfluorooctyl methacrylate) dispersion polymerization stabilizer, 566 Poly(1H,1H,2H,2H-perfluorooctyl methacrylate-b-PMMA) dispersion polymerization stabilizer, 566 Poly(2-(dimethylamino)ethyl methacrylate) macromonomers, 65 Poly(2-(dimethylamino)ethylmethacrylate)-b-alkylmethacrylate dispersion polymerization stabilizer, 566 Poly(2-ethylhexyl acrylate) [PEHA] emulsions sterically stabilized in CO2 with poly(1,1-dihydroperfluorooctyl acrylate), 355 Poly(2-hydroxyethylmethacrylate-co-styrene-4-sulfonic acid sodium salt), 562 Poly(2-vinylnaphthalene-alt-maleic acid)-graft-polystyrene, 568 Poly(2-vinylpyridine) P2VP, 799 Poly(4-vinyl pyridine), 569 Poly(acrylic acid), 512, 568 Poly(alkyl acrylate), 130 Poly(alkyl methacrylate), 510 Poly(alkyl methacrylate-b-sulfonated glycidyl methacrylate), 568 Poly(alkylene oxide), 829, 838 Poly(alkylene oxides), 130 Poly(allylamine hydrochloride), 605 Poly(butadiene), 569, 807 PB, 799 Poly(butadiene)-b-poly(2-vinylpyridine), 799 Poly(diallyldimethyl ammonium chloride), 653 Poly(diallyldimethylammonium chloride) shells, 562 Poly(dimethylsiloxane), 130 Poly(dimethylsiloxane)-methyl methacrylate dispersion polymerization stabilizer, 566 Poly(DL-lactide-co-glycolide) nanoparticles, 567 Poly(ethyl ethylene)-b-poly(styrene sulfonate), 568 stabilizers, 569 Poly(ethylethylene vinyl acetate) latex, 136 Poly(ethylene glycol), 350, 444, 562, 564, 804, 805, 807, 811 in emulsion polymerization, 447 Poly(ethylene-co-butylene), 807 Poly(ethyleneimine tetraacetate), PEDTA, 814 Poly(fluorooctylmethacrylate), PFOMA, 141 Poly(FOA), 132 Poly(FOA-co-BA), 132

Index Poly(FOA-co-ethylene), 132 Poly(FOA-co-MMA), 132 Poly(FOA-co-styrene), 132 Poly(hexafluoropropylene oxide), 131 Poly(hexafluoropropylene oxide) carboxylic acid, 137 Poly(isoprene), 569, 811 Poly(lithium acrylate) by inverse emulsion polymerization, 495 Poly(methacrylic acid), 568 dispersion polymerization stabilizer, 567 Poly(methacrylic acid)-co-ethylacrylate dispersion polymerization stabilizer, 566 Poly(methyl methacryate) (PMMA), 549 dispersion polymerization, 356 Poly(MMA-co-hydroxylethyl methacrylate)-g-Krytox, 138 Poly(N-isopropylacrylamide), PNIPAM, 512 Poly(N-vinyl pyrrolidone), 566 dispersion polymerization stabilizer, 566 Poly(N-vinylpyrrolidone)-co-(vinyl acetate) dispersion polymerization stabilizer, 566 Poly(oxyethylene)alkyl ethers, 669 Poly(oxyethylene)-based polymerizable surfactants, 548 Poly(perfluoropropylene oxide) as steric stabilizer in W/CO2 microemulsions, 354 Poly(phenylquinoline), PPQ, 590 Poly(phenylquinoline)-b-PS amphiphiles, 404 Poly(phosphate) Phos, 814 Poly(styrene), 807 latex, 811 Poly(styrene sulfonate)-b-poly(ethylethylene), 444 Poly(styrene sulfonate)-b-polystyrene, 569 Poly(styrene-b-ethylene oxide), 807 Poly(styrene-b-methacrylic acid), 799 Poly(styrene-co-acrylic acid), 568 Poly(t-butylstyrene) dispersion polymerization stabilizer, 566 Poly(t-butylmethacrylate), PTBM, 141 Poly(vinyl acetate), 568 dispersion polymerization, 356 latex, 136 PVAc, 354, 564 Poly(vinyl acetate)-poly(vinyl alcohol), 567 Poly(vinyl alcohol), 563 as stabilizer, 564 dispersion polymerization stabilizer, 566 vinyl chloride suspension polymerization as stabilizer in, 564 Poly(vinyl alcohol)-co-poly(vinyl amine), 569 Poly(vinyl benzyl chloride)-b-polystyrene, 569 Poly(vinyl chloride), PVC, 431 Poly(vinyl methyl ether) PVME, 476 dispersion polymerization stabilizer, 566, 567 Poly-L-lysine (PLL) in catalytic films, 333 Poly-MADQUAT, 495

893 Poly-t-butylacrylate saponification of, 512 Poly[(ethylene-butylene)-co-ethylene oxide] KLE3729, 476 Poly[(ethylene-co-butylene)-b-(ethylene oxide)], 807 Poly[2-(N-ethylperfluorooctane sulfonamido)]ethyl acrylate, 131 Poly[2-(N-methylperfluorooctanesulfonamido)ethyl methacrylate], 131 Poly[2-(N-methylperfluorooctane sulfonamido)]ethylacrylate, 131 Polyacrylamide, 471, 561 Polyacrylic acid dispersion polymerization stabilizer, 566 Polyallyl hydrochloric acid, 653 Polyaniline, 494, 495 Polyarabic acid, 568 Polyaromatic amines, 516 Polybutadiene, 549 Polycarboxylic acids, 563 Polychloroprene, 547 Polycondensation of long-chain amino acid esters for polypeptide vesicles, 503 Polyepiclorhydrin dispersion polymerization stabilizer, 566 Polyemersomes, 404 Polyester synthesis using lipases, 516 Polyester-polyethylene oxide HB239, 476 Polyester-polyethylene oxide sorbitan monoleate HB246, 476 Polyethylene, 603, 779 Polyethylene (EO)40 sorbitol hexaleate G1086, 474 Polyethylene glycol esterification of, 63 side product in ethoxylation, 16 Polyethylene glycol dodecylether Brij 30, 475 Polyethylene glycol monomethyl ether, 554 Polyethylene glycol sorbitan monoleate Tween 80, 474 Polyethylene oxide alcohols, 18 Polyethylene sorbitan trioleate Tween 85, 474 Polyethyleneglycol sorbitan esters, 22 Polyethyleneglycol-20-sorbitan stearic acid esters, 23 Polyethylethylene, PEE, 404 Polyglycosides alkyl, 1 Polymer gels, 802 Polymer particles swelling, 439 Polymer synthesis in reverse micelles, 517 Polymer-matrix composites, 542 Polymeric bead formation, 584 Polymeric cationics, 31

894 Polymeric films formation from conductive o/w microemulsions, 309 Polymeric stabilizers, 562–570, 598 amphipathic polymers, 565 poly(2-hydroxyethylmethacrylate-co-styrene-4-sulfonic acid sodium salt), 562 Polymeric surfactants, 2, 547–570 Polymerizable counter ions, 600 in vesicles, 507 Polymerizable lipids, 399, 502 Polymerizable surfactants, 541, 547–570 in emulsion polymerization, 547 in microemulsions, 559 poly(oxyethylene)-based, 548 Polymerization living anionic ring opening block, 555 Polymerization acrylamide, 481 aldol group transfer, 555 batch emulsion of styrene, 555 chainlike of silica, 826 condensation, 446 directed, 526 dispersion, 565 emulsion, 429–449, 542, 565 kinetics, 432 in admicelles, 537–544 in bicontinuous cubic phases, 530 in bicontinuous gels, 530 in dispersions, 472 in emulsions, 471 in hexagonal phases, 530 in inverse emulsions, 472 in inverse systems, 471–496 in lamellar phases, 530 in lipid bilayers of hydrophobic monomers, 508 in microemulsions, 471 in miniemulsions, 472 in surfactant mesophases, 525–534 in suspensions, 472 in vesicle bilayers, 529 inverse dispersion, 492, 493 inverse emulsion, 483, 485 surfactants for, 484 inverse microemulsion, 473 inverse miniemulsion, 490 inverse suspension, 491, 492 ionic, 568 kinetics, 459 microemulsion, 455–468, 528, 529 miniemulsion, 553 of alkyl phenols, 516 of dodecanolactam, 591 of 5-hydroxymethyl bicylco [2.2.1]-2-heptene, 343, 344 of lipids in vesicles, 503–507 of methyl acrylate, 567

Index [Polymerization] of norbornene, 341–344 of reactive counter ions in vesicles, 506 of silicate, 823 of styrene/divinylbenzene, 564 of vinyl chloride, 445 radical, 431 ring opening in vesicles, 503 seeded core shell of styrene/butyl acrylate, 555 silicate, 784 suspension, 429, 563–565 template at vesicle interfaces, 506 template breakthrough, 532 vesicular, 501 within fluid bilayers, 401 Polymerization rate with surfmer, 551 Polymerized vesicles detergent stability, 505 Polymorphs, 577 of phenobarbital, 596 Polynucleic acids, 515 Polyol esters, 844 Polyoxyethylene chains in cleavable surfactants, 52 (Polyoxyethylene)5–9nonyl phenol EmpiLan NP5, 476 Polyoxyethylene (20) sorbitan monopalmitate Tween 40, 376 Polyoxyethylene adduct of polyoxypropylene diamine adduct Tetonic 1102, 475 Polyoxyethylene alkyl phenols, 1 APE, 17 Polyoxyethylene sorbitol hexaoleate, 478 Polyoxyethylene(4) nonylphenol, 484, 491 Igepal CO-430, 475 Polyoxyethylene(8) stearic acid, 484 MYR145, 475 Polyphenols, 515 at oil-water interface, 523 enzymatic synthesis of, 516 synthesis using peroxidases, 516 Polyphenylenevinylene, PPV, 653 Polypropylene, 592, 593 Polypyrrole particles by emulsion polymerization, 495 Polysaccharide synthesis using cellulases, 516 Polysiloxane surfactants, 137 Polysoaps, 549, 569 Polysorbates polyethyleneglycol sorbitan esters, 22 Polystep B23, 596 Polystryrene step growth functionalization, 555

Index Polystyrene, 510, 569, 603 PS, 34 cores, 562 latex, 442, 549 grafting to, 559 oligomers, 350 Polystyrene-b-PEG, 568 Polystyrene-b-poly(ethylene oxide), 549 Polystyrene-polyethylene, SE3030, 476 4-Poly(styrene sulfonate, sodium salt), 605 Polytetrafluoroethylene, PTFE, 365 Polyvinyl alcohol, 555, 579, 603 Polyvinylpyrrolidone, 579 POPC giant vesicles, 400 Porcupine particles, 569 Pore channels, 787 Pore diameter of silicas, 805 Pore dimensions MCM-41 organically functionalized, 844 Pore size distribution, 802, 831 Pore systems, 801 Porogens, 801 Porosity by porogen displacement, 801 Porous ceramics design of, 801 glasses, 802 inorganic solids, 819–845 nobia films, 780 silica films, 780 titania films, 780 Porphyrin/FSM-16, 838 Porphyrins, 845 Potassium alginate, 567 dodecanoate, 436 octadecanoate, 436 permanganate, 379 persulfate KPS, 434 Potassium vinylbenzyl alcoholate, 555 Potato starch dextrin, 565 Potential window increases in emulsions, 311 in micellar solutions, 311 in microemulsions, 311 Powder x-ray diffraction, 839 PPIE, pseudophase ion exchange model, 252 PPO, 373 PPQ, poly(phenylquinoline), 590 PPQ-b-PS, 590 PPV, polyphenylenevinylene, 653 Precipitation batch solvent shifting, 590 by gas condensation, 603 by pH shifting, 594, 597

895 [Precipitation] by sol-gel, 803 by solvent shifting, 584, 597 double jet, 595 hydrothermal, 803 in encapsulating spheres, 604 in microemulsions, 602, 609–630 in reverse emulsions, 603 of inorganic-ABS structures, 804 of nanocolorants, 605 of silver bromide, 611 of silver chloride, 611 of silver halide, 611 within aerosol droplets, 578 within emulsion droplets, 578 Precipitation mechanism in emulsion polymerization, 435 Premicelles, 229, 231 Premicellization of geminis, 76 Press cakes, 577 Pressure-area isotherms, 69 Primary amines hexagonal mesoporous silica templating, 830 reaction with ethylene oxide, 31 Probes membrane soluble fluorescent, 400 Texas Red-DOPE, 400 Product adsorption passivation suppression by organic phases in emulsions, 315 Propane sultone, 555 1,3-Propane sultone, 565 n-Propanol, 476, 600 1-Propanol, 250 2-Propanol, 478 Propoxylation of aliphatic alcohols, 18 Propyl gallate, 290 Propylene supercritical, 592 Propylene oxide, PO, 14 copolymerization with ethylene oxide, 16 in alkoxylation, 16 Proteins, 653 condensates with fatty acids, 13 PS see polystyrene, 134 PS-b-PFOA, 140, 490 core-shell micellar aggregates, 135 proton NMR, 136 surfactants, 134 PS-b-polybutadiene dispersion polymerization stabilizer, 566 PS-co-PEO, 476 Pseudoboehmite alumina, 838 Pseudoisocyanine, 616 Pseudoisocyanine hexafluorophosphate, 605 Pseudomonas diminuta, 380 Pseudophase ion exchange model, 252 PIE model, 180

896 Pseudophase model, 177, 296, 374 Pseudophase partitioning model, 304 PSS, 653, 655 PSS/PVP films, 654 Pt particles in Nafion films, 652 Pt clusters, 838 Pt-ReO2 particle size, 624 Pt-ReO2 particles, 623 PTBM see poly(t-butylmethacrylate), 141 PTBM-b-PFOMA, , 141, 142 PTC, 31, 300, 364–366 immobilization on polymer, 301 phase transfer catalysis, 297 PTES, 844 PTES/TEOS condensation of, 844 PTFE, 541, 543 polytetrafluoroethylene, 365 PtS, 644 Pulsed laser polymerization, 460 PVAc, 564 poly(vinyl acetate), 356 PVAc-b-PFOA CMD transition, 141 PVAc-b-poly(1,1 2-tetrahydroperfluorooctyl acrylate) CMD transition, 141 PVAc-b-PTAN, 141 PVC, 564 particles, 564 poly(vinyl chloride), 431 PVME, poly(vinyl methyl ether), 476 PVP, 588, 589 (PW12O40)⫺3, 840 1-Py, 1-pyrenenonanoic acid, 227 Pyranthrone red Paliogen Red L 3530HD, 409 1-Pyrenenonanoic acid, 1-Py, 227 1-Pyrenol, 520 Pyridine, 139, 147 Pyrolytic graphite, 834 Pyrolytic sublimation, 833 Pyrrole, 541 PZC, 304, 537 adsorption of 12–2-12, 2Br, 72 point of zero charge, 72 Quaternization of tertiary amines with dimethyl sulfate, 31 QCM, quartz crystal microbalance, 654 QCM analysis of CdS/PDADMAC LbL films, 655 Quantum size effects, 609, 633 Quartz crystal microbalance, 649 QCM, 654 Quasielastic light scattering particle sizing by, 460

Index Quaternary ammonium salts, 30, 801 Quaternization of tertiary amines with chloroacetic acid esters, 33 in polymers by methyl halides, 32 Quaternization reaction, 30 with alkylene oxides, 31 Quaternization and ethoxylation of dimethyl tertiary amines with ethylene oxide, 32 Radical chain reaction in sulfoxidation of alkanes, 6 Radical coupling with electrochemically formed NO2, 308 Radical cyclization of bromoacetal, 332 Radical pathway in carbon-carbon bond formation, 331 Radical polymerization, 431 Radiolarian microskeletons, 839 Radius of curvature in Ostwald ripening, 560 Raffinose, 48 Raffinose 6-dodecanoate, 50 Raman spectroscopy, 819 Randles–Sevcik equation, 325 Random mesh phase, 680 Rapid expansion of supercritical fluids RESS, 591 Rate constants second order, 377 Rates of polymerization in microemulsion polymerization, 459 Reactant compartmentalization, 307 Reactant partitioning control, 330 Reactant preconcentration control on electrodes, 330 Reactant transport in microemulsions, 324 Reaction calorimeter, 459 Reaction rates of particle formation in films, 650 Reactions condensation, 844 electrochemical, of toxic agents, 380 electrochemical dechlorination, 380 enzymatic in W/CO2 microemulsions, 353 of toxic agents, 380 in multiphase micellar systems, 359–370 in nonmicellar aggregates, 226 in two-phase micellar systems, 362 in vesicles, 226 in W/CO2 microemulsions between nucleophiles and CO2soluble reactants, 363 liquid-liquid two-phase, 363 of anionic in micelles, 189 of z-ArN⫹2, 269 salt-gel, 840 Williamson, 364 within films, 642 Reactive counter ions polymerization of in vesicles, 506 Reactive olefins from thermal decomposition of amine oxides, 20

Index Reactive stabilizers, 566 Reactive surfactants, 551 Reactivity control by aqueous amphiphilic systems, 175 Reactors ethoxylation, 17 Recombination, 659, 660 Recrystallization, 577 Rectorite, 841 Red Dye No. 6, 585, 586 Redox initiated free radical polymerization, 504 Redox initiation H2O2-ascorbic acid, 559 Redox potential of ferrocene, 157 Redox-active surfactants, 155, 157 Reducing sugars, 112 Reduction of alkyl vicinal dibromides to olefins using adsorbed MPC, 330 of benzyl bromide to yield bibenzyl, 331 of chemical agents, 379 of 1,2-dibromocyclohexane to cyclohexene, 333 of disulfide group, 161 of 4-nitrosodiphenylamine in cationic micelles, 308 of vicinal dibromides in microemulsions, 330 Reductive alkylation, 67 of methylamine Raney nickel catalyzed, 27 Refatting ethoxylated glycerol esters, 20 Reformatsky reaction ␤-hydroxy esters by the, 235 Regiomeric isomers of sulfosuccinic acid monoalkyl esters, 9 Regioselectivity, 235 micellar effects on, 257 Regioselectivity control in Diels-Alder reactions, 234 Release from capillaries of liquid, 170 Release pathway for targeted DPPlsC liposomes, 151 RESS, rapid expansion of supercritical fluids, 591 RESS flow systems, 592 trans-Retinoic acid, 586 Retro Diels-Alder reaction, 253 Reverse emulsions precipitation in, 603 Reverse hexagonal liquid crystal, 674 Reverse micelles, 516 Reverse microemulsions alcohol distribution in, 288 counterion concentrations in, 284 water concentrations in, 284 Reverse vesicles, 176, 674 Rhenium dioxide particles, 623 Rheology of cationic surfactant oligomers, 82 Rheology measurements, 836 Rhodamine B Lake Fast Rose Lake B, 409 Rhodamine 6G, 605

897 Rhodiarome, 602, 629 nanoparticles, 625 structure, 625 Rhovanil, 602, 625 particle size, 627 Ribbons, 706 Ricinoleic acid esterification by ethoxylation, 20 Right-handed helices, 709 Rigid-colloid templating, 806 Ring opening polymerization, 555 in vesicles, 503 Ringlet adsorption patterns, 569 Rippled lamellar phase, 688 Rodlike aggregates, 669 Rodlike micelles, 669 CTVB, 601 Rods, 814, 834 aggregated, 812 nanoscopic, 812 Rolled-up planar sheets, 706 Ropes, 834 Rubber synthetic, 430 SAAS, sodium alkyl allyl sulfonate, 551 Salicylideneaniline, 678 Salmeterol xinafoate, 594 Salt-gel reaction, 840 Salting out, 585 SAM, self-assembled monolayers, 845 SANS, 134, 460, 461, 467, 491, 697 of monomer partitioning in microemulsion polymerization, 457 of PFOA in CO2, 131 of PFOA-g-PEO in CO2, 133 of surfactant oligomer micelles, 79 water-in-CO2 microemulsions, 350 Saponification, 2 of fatty acid metal esters, 2 of fatty acids, 2 of poly-t-butylacrylate, 512 of triglycerides, 2 Sarcosinates, 13 Sarcosine, 13 Sarin GB, 374 SAU, 551 sodium acrylamido undecanoate, 550 SAXS, 134, 531, 532, 822 small angle x-ray scattering, 527 SB3-14, 195, 198 myristyldimethylammonium propanesulfonate, 176 SB3-16, 195, 225 SBA-1, 826 SBA-2 3D hexagonal, 826

898 SBA-12, 829 SBA-16, 829 SBBu3-14, 198 SBPr3-14, 195 SC CO2, 594 Scaffold hydrophobic monomer in lipid membranes, 509 Scanning electron microscopy, SEM, 482 Schemes for preparation of nanoparticle films, 640 Schiemann reaction, 275 Schotten-Baumann reaction sorcosinates from acid chlorides, 13 Schultz distribution, 461 SCS, sodium cetylsulfate, 376 SDBS, 696, 697 sodium dodecylbenzene sulfonate, 601 SDHP, sodium dihexadecyl phosphate, 226 SDS, 157, 167, 171, 176, 189, 190, 198, 226, 252, 254, 312, 324, 327, 363, 365, 366, 368, 379, 434, 436, 448, 475, 478, 539, 540, 547, 552, 554, 557, 561, 589, 694–696, 698, 702, 839, 840 in miniemulsion polymerization, 560 SDS micelles effect on 4-nitrobenzenediazonium ion, 274 SDS-water binary phase diagram, 699 SE3030 polystyrene-polyethylene, 476 SECM dynamic scanning electrochemical microscopy, 329 Second order rate constants, 377 Second-generation cleavable surfactants, 53 SEDS, 594 solution enhanced dispersions by supercritical fluids, 593 Seed particles in emulsion polymerization, 455 Seeded core shell polymerization of styrene/butyl acrylate, 555 Seeded emulsion polymerization, 554 Seeds platelet shaped, 814 styrene-butylacrylate, 552 SEHP, 507 Seikafast Yellow 2600 disazo yellow AAMX, 409 Seikafast Yellow 2700 disazo yellow HR, 409 Selectivity control through pseudophase distribution of substrate, 308 Selectivity of electroorganic synthesis effects of heterogeneous solutions, 305 Self-aggregation of surfactants, 667 Self-assembled monolayers, 634 SAM, 845 Self-assembling films, 651 Self-assembly of fluorocarbon surfactants, 680 of polymeric stabilizers, 599

Index [Self-assembly] of surfactants, 599 supramolecular, 797 Self-emulsifiable oils sulfated oils, 10 Self-replication of giant vesicles, 227 SEM, 510, 511, 518, 522, 589, 656, 783, 789, 831, 836 calcium carbonate, 815 cubic lamellar mesoporous films, 791 cubic mesoporous silica films, 793 hexagonal mesoporous silica film, 792, 793 lamellar mesoporous silica films, 790, 793 micromolded silica structure, 807 scanning electron microscopy, 482 Semiconductor nanoparticles epitaxial growth, 635 Semiconductor particulate films, 635 Semicontinuous process (feed) emulsion polymerization, 433 Semidilute regime in gemini surfactant solutions, 81 Sensor surface acoustic wave, 780 Sentamid-5, 484, 487 amide of stearic acid polyoxyethylated N,N-bishydroxyethyl tall oil amide, 476 Separations of toxic agents, 381 Serine-based geminis, 63 SESD process spontaneous emulsification solvent diffusion process, 567 Seven-chain surfactant, 686 Shampoo coconut monoglyceride in, 11 monoglyceride sulfates in, 10 sulfated oils in, 10 Shear fields effects on silica formation, 826 Shear thickening, 483 Shear thinning, 483 Sheets, 834 Short-spacer geminis, 70 Si(OR)4, 803 Si8, 841 Si8O8⫺ 20 , 823, 841 Sieve tray column, 588 Silane coupling agents, 843 Silica gemini adsorption, 78 Silica, 653 sol-gel processing of, 803 PB-PEO templated, 809 Pluronic derived, 805 Silica coated cylindrical micelles, 821 Silica films at fluid-fluid interfaces, 779–794 Silica gel, 779, 820 Silica monolith, 810 Silica particles, 562, 566, 653

Index Silicate gel thin film precursor, 782 Silicate polymerization, 784, 823 Silicon electronic switches, 659 Silver halide precipitation, 611 Silver nanoparticle synthesis in W/CO2 microemulsions, 354 Simulations Monte Carlo, 71 Single-chain surfactants phase behavior, 667 SiO2 films, 656 SiO2 particles in Nafion films, 652 Size quantization, 643 Size quantized semiconductor particles, 659 Skeletonized vesicles, 505, 506 Skin compatible surfactants ether carboxylic acids, 3 Skin compatibility good, sulfosuccinic acid monoalkyl esters, 9 of monoglyceride sulfates, 11 combined with alkyl polyglucosides, 11 SMA, stearyl methacrylate, 560 Small angle neutron scattering, SANS, 79 Small unilamellar vesicles, SUV, 227 Smith Ewart case, 486, 539 in emulsion polymerization, 433 SMO, sorbitan monooleate, 474 Sn, 838 SN, sodium nonanoate, 694 SN2 reactions of sulfonate esters, 234 Snake venom phospholipase PL-A2, 400 SnO2, 838 SO3 see sulfur trioxide, 4 Soaps, 2 high grade, 3 metallic, 2 sensitivity to water hardness, 3 Sodium (R)-2-methyldecanoate, 669 Sodium 10-acrylamidosstearate, NaAAs, 550 Sodium 11-crotonoyl undecan-1-oyl sulfate, 552 Sodium 11-methacryloyl-undecan-1-oyl sulfate, 552 Sodium 2-acrylamido-2-methylpropanesulfonate, NaAMPS, 483 Sodium 2-bromoethane-1-sulfonates in preparation of N(alkyl)taurines, 63 Sodium 2-methyldecanoate in water phase diagram, 670 Sodium 2-nitro-4-iodoxy benorate IBX, 379 Sodium 9-acrylamidostearate, NaAAS, 550 Sodium acrylamido undecanoate, SAU, 550 Sodium acrylate, NaAA, 482, 483 Sodium alkanoate micelle size distribution, 426 Sodium alkanoate aggregates mole fraction vs aggregate number, 417 Sodium alkyl allyl sulfonate, SAAS, 551

899 Sodium alkyl sulfates, 436 Sodium alkyl sulfonates, 437 Sodium aluminate, 820 Sodium bis(2-ethylhexyl sulfosuccinate) AOT, 475 Sodium borohydride, 379 Sodium carbonate, 820 Sodium carboxymethyl cellulose, 567 Sodium cetylsulfate, SCS, 376 Sodium decanoate, 669 rate of biodegradation, 54 Sodium decylsulfate, 165 Sodium diatrazoate, 596 Sodium dihexadecyl phosphate, SDHP, 226 Sodium dimethyldithiocarbamate, NaDTC anodic conversion to TMT, 305 Sodium dodecyl sulfate see SDS, 45 Sodium dodecylbenzene sulfonate, 564 SDBS, 601 Sodium glutamate acylation, 13 Sodium hypochlorite, 379, 605 Sodium methacrylates, NaMA, 480 Sodium methacrylate, 563 Sodium nitroprusside reaction with H2S in W/CO2 microemulsions, 354 Sodium nonanoate, SN, 694 Sodium octadecyl sulfate, 436 Sodium p-vinylbenzene, 474 Sodium perfluoroheptanoate, 540 Sodium poly(hexafluoropropylene oxide) carboxylate, 137 Sodium silicate, 820, 837 Sodium sulfopropyl octadecyl maleate, SSPOM, 670 Sol-gel, 845 dip coating, 834 evaporation for silica film synthesis, 780 precursor, 806 process, 794 processing in ABC bulk phases, 811 processing of silica, 803 silica chemistry, 826 synthesis of silica, 807 Solid-water interface adsorption isotherms, 71 Solketal route to diplasmenylcholine, 147 Solubility, 579 high aqueous sulfosuccinic acid monoalkyl esters, 9 of alkyl esters saturation, 415 saturation of ethyl octanoate, 416 surfactant, 706 Solubility enhancement of ethyl alkanoates by ethanol, 424 by sodium alkanoates, 424 Solubilization in micellar aggregates, 179 in micelles, 296, 537

900 [Solubilization] in microemulsions, 296 of esters in micelles, 417 of intermediates in electrochemical conversions, 307 of substrates in electrochemical conversions, 307 Solubilization capacity in geminis of transazobenzene, 78 per alkyl chain, 79 Solubilization equilibria in micelles and microemulsions, 303 Solubilization studies of micellar shape, 79 Solubilizers castor oil ethoxylates, 20 ethoxylated amines, 20 ethoxylated glycerol esters, 20 HLB of, 18 Solution enhanced dispersion, SEDS by supercritical fluids, 593 Solvent effects on dediazoniation rates, 270 Solvent shifting, 587, 591 in microemulsions, 602 precipitation, 584, 597 Solvents auxiliary, 579–581, 588, 592 high vapor pressure auxiliary, 580 Sonoelectrochemistry modified electrodes in 1-octanol/water emulsions, 299 Sorbitan ester ethoxylates HLB values, 22 Sorbitan esters, 2, 21 applications of, 23 ethoxylation, 22 from sorbitol, 22 HLB values, 21, 23 hydrophilicity of, 23 polyethyleneglycol-, 22 production capacity, 23 Sorbitan laurate, 603 Sorbitan monoleate Span 80, 474 Sorbitan monostearate, 226 Span 60, 474 Sorbitan sesquiolate Arlacel 83, 474 Sorbitan sesquiolate polyoxyethylene C18 terminated acrylamide polymer Montanox 80, 475 Sorbitan sesquiolate polyoxyethylene sorbitan trioleate Montane 83, 475 Sorbitol, 49 hydrogenated glucose derivative, 2 intramolecular dehydration intermediate, in fatty acid esterification, 22 production volume, 22 Sorbyl, 503 Sorcosinates via Schotten–Baumann reaction, 13 SOS, 696, 697

Index Spacers chemical nature effect on CMC, 77 effect of hydrophilicity on phase diagram, 79 effect of length on micelle morphology, 79 headgroup, 59 oxyalkylene, 60 hydrophilic effect on aggregation number, 79 in anionic geminis, 63 hydrophobic, 71 oligo(oxyethylene) in geminis, 77 oxyethylene, 70 short, 70 Span 20 sorbitan laurate, 603 Span 60 sorbitan monostearate, 474 Span 80, 486, 488, 489, 491 sorbitan monooleate, 474 Specific surface area, 805 Spectroscopic measurement of dediazonation rate constants, 277 Spherical micelles, 798 Spherical to rodlike micellar transition, 669 Sphingosine vesicles, 400 Spin casting, 640 Spin coating, 780 Spinning oils sulfated oils in textile processing, 10 Spiral ribbon morphologies, 831 Splittable surfactants, 2 Sponge phase, 674 Spontaneous curvature, 467, 703 Spontaneous emulsification solvent diffusion process (SESD), 567 Spontaneously formed vesicles, 507 Sputter coating, 656 SSDSE, styrene sodium dodecyl sulfonate ether, 550 SSPOM, sodium sulfopropyl octadecyl maleate, 670 phase diagram, 672 Stability hydrolytic of dicetylester of bis(2-hydroxylethyl)ammonium chloride, 47 latex, 570 of detergent pastes, 28 of foam, 71 of sulfonate over range of pH, 7 of phosphoric acid esters to hydrolysis, 13 of vesicles, 703 Stability diagram, 600 for W/CO2 emulsions, 351 Stabilization, 597 by polymerization, 600 chemical, 599

Index [Stabilization] depletion, 562 electrosteric, 549 kinetic, 597 matrix, 599, 603 of lipid vesicles, 502 of nanoparticles, in microemulsions, 613 steric, 597 Stabilization of latexes in W/CO2 microemulsions, 354 Stabilizer steric, 581 Stabilizers for dispersion polymerization in critical fluids, 357 Stachyose, 48 Stachyose 6-dodecanoate, 50 Starch colloidal stabilizer, 562 Static light scattering, 166 Stealth liposomes, 502 Stearic acid, 643, 644 Stearoyl lysophosphocholine, 678 Stearyl methacrylates, SMA, 560 Stereoselectivity, 235 of cyclizations in microemulsions, 309 Steric constraints, 667–710 Steric stabilization, 563, 597 of poly(2-ethylhexyl acrylate) [PEHA] emulsions in CO2, 355 Steric stabilizer, 581, 587, 812 Stereoselectivity of carbon-carbon bond formation in microemulsions, 331 Stern layer, 177, 190, 200, 378 Sterols as fat constituents, 3 Stress strain, 555 maleic hemiester latex films, 556 of latex films, 554 succinic hemiester latex films, 556 Structure of micelles, 177 Structure-directing proteins, 813 Styrene, 131, 431, 436, 444, 467, 483, 508, 511, 531, 532, 539, 540, 550–554, 566–568 in gemini surfactant microemulsion polymerization, 87 microemulsion polymerization, 465 in emulsion polymerization, seeded, 554 Styrene polymerization latexes by, 559 Styrene sodium dodecyl sulfonate ether, SSDSE, 550 Styrene-butadiene, 547 latex, 550 Styrene-butylacrylate seeds, 552 Styrene-co-glycidylmethacrylate, 567 Styrene-co-HEMA, 566 Styrene-co-urethane acrylates, 567 Styrene-divinylbenzene copolymerization, 564 Styrene/divinyl benzene, 511 Styrene/divinylbenzene polymerization, 564

901 Styrenic anionic block copolymers, 558 Styrenic anionic surfmers, 555 Styrenic cationic surfmers, 561 Styrenic macromonomers of polyethylene oxide in dispersion polymerization, 560 Styrenic nonionic surfmers, 555 Styryl, 503 Sublimation pyrolytic, 833 N-Substituted-1, 8-haphthalimides, 124 3-( p-Substituted-phenyl)-1-(2-pyridyl-2-propen-1-one dienophiles, 253 Substrate solubilization, 179 Succinic hemiester latex films stress strain of, 556 Succinic latex films water absorption kinetics, 556 Succinic surfactants, 555 Sucrose, 23, 48 esterification of, 22 production volume, 22 Sucrose 6-dodecanoate, 50 Sucrose esters, 2, 22, 23 applications of, 23 by transesterification with fatty acid methyl ester, 24 production capacity, 23 production processes, 25 Sugar esters, 48 enzymatic synthesis of, 49 Sugar-based geminis, 64 Sugar-based surfactants applications of, 23 glucose esters, 2 production capacity, 23 sorbitan esters, 2 sucrose esters, 2 Sugar-substituted norbornenes polymerization of, 344 Sulfamic acid see amidosulfonic acid, 4 Sulfate in anionic geminis, 61 Sulfate geminis, 71 Sulfated alkanol amides, 11 Sulfated fatty acid monoglycerides in soap-free shampoo, 10 Sulfated galactocerebrosides, 112 Sulfated oils, 10 castor oil, 10 coconut oil, 10 composition of, 10 olive oil, 10 Sulfates alcohol, 1 alcohol ether, 1 Sulfation, 3 in falling-film reactor of monoglycerides, 11

902 [Sulfation] of fatty acid derivatives, 2 of phosphoric acid derivatives, 2 Sulfide nanoclusters, 520 Sulfobetaine-based macromonomers, 565 Sulfobetaine micelles, 225 hydrolysis in, 199 Sulfobetaines sultaines, 35 Sulfochloride in sulfochlorination, 6 Sulfochlorination, 3 to convert paraffins, 6 to give alkane sulfonates, 6 ␣-Sulfo fatty acid methyl esters (MES), 7 from fatty acid methyl esters, 7 Sulfolane tetramethylene sulfone, 380 Sulfonate in anionic geminis, 61 Sulfonate functionalized latexes, 482 Sulfonate geminis, 71 Sulfonate group pH stability, 7 Sulfonate surfactant trimers, 67 Sulfonates alkylbenzene, 1 linear alkylbenzene, 1 Sulfonation, 3 falling-film reactors in, 4 multi-tube reactor, 4 of alkylbenzenes, 5 of esters reaction mechanisms, 8 of glycidyl methacrylate, 568 of ␣-olefins, by sulfur trioxide, 7 with amidosulfonic acid, 4 with chlorosulfonic acid, 4 with sulfur trioxide, 4 Sulfones in sulfonation of alkylbenzenes, 5 Sulfonic esters hydrolysis of, 197 Sulfosuccinates, 8 alkyl polyglycoside esters of, 29 from maleic acid, 8 sulfosuccinic acid esters, 8 Sulfosuccinic acid esters see sulfosuccinates, 8 Sulfosuccinic acid monoalkyl esters based on ethoxylated fatty alcohols, 9 based on lauryl polyoxyethylene(3) alcohol, 9 based on myristyl polyoxyethylene(3) alcohol, 9 emulsifiers in emulsion polymerization, 9 Sulfosuccinic acid monoester regioisomers, 8

Index Sulfoxidation, 3 to give alkane sulfonates, 6 Sulfur hydrosols from thiosulfate HCl catalyzed, 435 Sulfur trioxide in sulfonation of alkylbenzenes, 5 in sulfonation of fatty acid methyl esters, 7 reaction with tertiary amine, 35 sulfonation of ␣-olefins, 7 sulfonation with, 4 Sultaines sulfobetaines, 35 1,2-Sultones in sulfonation of ␣-olefins, 7 1,3-Sultones in sulfonation of ␣-olefins, 7 1,4-Sultones in sulfonation of ␣-olefins, 7 Supercritical CO2, 129 inverse emulsion polymerization in, 490 in dispersion polymerization, 566 Supercritical fluid methods particle precipitation, 591 Superparamagnetic hydrogel particles, 495 Supersaturated solutions, 578 Supersaturation, 579, 588 Suppression of NDMA polymerization in cationic micelles during anodic nitration of NDMA, 317 Supramolecular, 802 aggregates, 806 self-assembly, 797 templating, 802, 823, 824 Surface acoustic wave sensor, 780, 794 Surface area, 840 Surface areas of ferrocenyl surfactants in monolayers, 160 Surface patterning, 845 Surface potentials, 378 Surface tension, 68 active control of, 155 by du Nouy ring method, 167 by maximum bubble pressure method, 158 of disulfide surfactants, 164 by pendant drop method of disulfide surfactants, 163 dynamic of SDS, 157 lowering, 598 measurement by maximum bubble pressure method, 157 measurements, 491 of azobenzene surfactants, 168 effects of agglomeration, 165 of bis-lactobionamido alkanes, 117 of ferrocenyl surfactants, 158, 161 of geminis as function of gemini spacer length, 71 of SDS, 168 Wilhelmy plate, 158 Surface-active oligomeric free radicals, 456

Index Surfactant aggregates, 784 aggregation behavior, 706 desorption from latex particles, 548 residence time in micelles, 250 solubility, 706 Surfactant admicelles AFM imaging of, 779 Surfactant adsorption at electrodes, 304 Surfactant assembly interface, 267 Surfactant-based gels synthesis in, 520 Surfactant dimers, synthesis, 60 Surfactant mass transport, 167 Surfactant mixtures phase behavior, 694–702 phase diagrams, 165 Surfactant morphologies platelike, 831 spiral ribbon, 831 Surfactant oligomers, 59, 67 as alkaline earth cation ionophores, 87 structure labeling, 60 Surfactant phase behavior models describing, 702–706 Surfactant phases formation of, 667–710 Surfactant structure micellar rate effects, 224 Surfactant synthesis by carboxylation of fatty acid derivatives, 2 carboxylation of phosphoric acid derivatives, 2 condensation of fatty acid derivatives, 2 sulfation of fatty acid derivatives, 2 sulfation of phosphoric acid derivatives, 2 Surfactant-templated silicates, 802 Surfactant templating, 802 Surfactants ambidextrous, 137, 139 amine, 838 amphoteric, 2, 34, 37 betaines, 2, 34 anionic, 829 as drug delivery vehicles, 232 azobenzene based, 165 betaines, 34 bilayer forming as membrane mimetic models, 232 biodegradability, 45 bolaform, 111 carbohydrate based, 1, 20 glucose esters, 2 sorbitan esters, 2 sucrose esters, 2 carboxylates soaps, 2 cationic, 30, 829 ecological behavior, 33 physicochemical behavior, 33 toxicological behavior, 33

903 [Surfactants] chemical potential, 69 chemically labile, 233 cleansers N-acyl amino acids, 13 cleavable, 45, 65, 145 dendritic, 139 1,3-dioxolanes, 51 disulfide based, 160 dodecyl aliphatic, 832 double chain N-acyl-N-alkylamino-1-deoxyglycitols, 112 double-chain histidine, 693 double-headed, 829 ecological properties, 2 effects on styrene emulsion polymers, 557 ether carboxylic acids, 3 ferrocene based, 155 as mediators, 327 ferrocenyl, 157 in electroless plating, 407 fluoropolymer, 131 foaming N-acyl amino acids, 13 for inverse emulsion polymerization, 484 for inverse microemulsion polymerization, 477 for supercritical fluids, 129–142 four-chain, , 686 functional, 45 functionalized, 829 gemini, 2, 59, 829 geometrical shape, 667 glucose-based, 24, 56 glycosidic, 235 good wetting sulfosuccinate dialkyl esters, 8 hemiamides, 557 hemiesters, 557 heterodimer, 65, 66 hydroxyaluminum bis[poly(hexafluoropropylene oxide)carboxylate], 137 in emulsion polymerization, 447 interactions with antigenic proteins, 232 interactions with eukaryotic cells, 232 interactions with mineral surfaces, 232 interactions with prokaryotic cells, 232 intermolecular interactions, 667 light active, 155 maleic, 555 mild N-acyl amino acids, 13 ether carboxylic acids, 3 monomer solubility, 667 multifunctional, 2 neutral, 829 nonionic, 829 by alkoxylation, 2

904 [Surfactants] nonionic ferrocenyl in electroless plating, 407 nonionics by alkoxylation, 14 nonpolymeric in CO2, 138 nonsoap, 1 oligomers, 59, 66 organosilane, 829 packing at air-water interface, 69 perfluoropolyether, 137 phase behavior, 667 physical properties, 2 poly(hexafluoropropylene oxide) carboxylic acid, 137 polymeric, 2, 547–570 polymerizable, 541, 547–570 DMAMA, 480 poly(phenylquinoline)-b-PS, 404 polysiloxane, 137 PS-b-PFOA, 134 reactive, 551 redox active, 155 self-aggregation, 667 self-organization, 667 seven chain, 686 skin compatible ether carboxylic acids, 3 sodium poly(hexafluoropropylene oxide) carboxylate, 137 splittable, 2 styrene sodium dodecyl sulfonate ether, 550 succinic, 555 sugar based glucose esters, 2 sorbitan esters, 2 sucrose esters, 2 sulfated oils as nonsoaps, 10 sulfonate trimers, 67 surface activity, 68 surface area of, 70 toxicological properties, 2 triple chain, 67 vinyl ether, 145–154 weakly foaming sulfosuccinate dialkyl esters, 8 zwitterionic, 2, 557, 829 Surfmers, 548, 549, 551 activated ester functionalization of PS latexes, 559 alkyl allyl sulfonic acid, 551 allylic, 551 anionic, 552 cationic, 552 with crotonic group, 551, 552 with maleic group, 552 with methacrylate group, 551 fluorocarbon acrylamido, 562 fumarate, 553 in latexes for biotechnologies, 555–559

Index [Surfmers] in polystyrene latexes, 547 maleic, 553 Me(EO)45(caprolactone)10CONHC(CH3)2C6H4C(CH3)CH2, 553 Me(EO)45(caprolactone)10OCOCHCHCOOH, 553 Me(EO)45(BO)8OCOCHCH2, 553 MeEO45BO9CONHC(CH3)2C6H4C(CH3)CH2, 553 MeEO45BO15CH2C(C6H5)CHCH2, 553 nonionic, 554 styrenic, 554 sodium acrylamido undecanoate, 550 sodium alkyl allyl sulfonate, 551 styrenic anionic, 555 styrenic nonionic, 555 Surfynol 465 in gold and silver nanoparticle synthesis, 68 Suspension polymerization, 429, 472, 563–565 controlled radical polymerization in, 565 inverse, 492 of acrylonitrile-butadiene-styrene, 563 of methyl methacrylate, 564 SUV, small unilamellar vesicles, 227 Swelling of polymer particles, 439, 440 in emulsion polymerization, 443 Symmetric gemini cationic surfactant mesophase, 825 Synchrotron x-ray analysis of arachidc aicd monolayers, 636 Syndet bars isethionates in, 12 Syndet soaps coconut monoglycerides in, 11 Synkinons for membranes, 707 Synthesis bottom-up, 797 by gallery templating, 842 electroorganic, 295–318 enzymatic using surfactant assemblies, 515 gas catalyzed thin film, 780 in surfactant-based gels, 520 in W/critical fluid microemulsions, 354 materials, by polymerization, 525–534 of BCAT, 153 of butylphenyl ether, 364 of CdS nanoparticles in W/CO2 microemulsions, 354 of copper nanoparticles in W/propane microemulsions, 354 of dibutyl ether, 364 of films at fluid-fluid interfaces, 781 of glycidyl ether, 364 effect of alkalinity, 369 effect of surfactant type, 369 of N-hexadecyl-2-chloropyridinium iodide, 338 of inorganic porous solids, 819–845 of nanoparticle copper in W/propane microemulsions, 354 of nanoparticles in amphiphilic films, 639–660 of nickel boride particles, 618, 620 of platinum particles, 622 of phenolic ethers

Index [Synthesis] unsymmetrical, 364 of phenolic glycidyl ether, 364 of polyesters use of lipases for, 516 of polymers in reverse micelles, 517 of polyphenol use of peroxidases, 516 of polysaccharides use of cellulases, 516 of porous inorganic solids, 819–845 of silica sol-gel, 803, 807 of silver nanoparticles in W/CO2 microemulsions, 354 of vinyl ether PEG lipid conjugates, 150 of zeolites, 819 particle, 634 top-down, 797 Synthetic detergents, 1 Synthetic pathway control in microemulsions, electroorganic, 323 Synthetic rubber, 430 Synthetic scheme double chain surfactants, 114 T10, 483 t-octyl-phenoxy-PEO10 methacrylate, 475 Ta, 838 Ta-TMS1, 833 Ta2O5, 838 Talonamide twisted fibers, 707 Talonic headgroup, 706 Tamol 731, 588 Tantalum oxides, 832 TAOS, tetraalkoxysilanes, 844 Tartrates alkyl polyglycoside esters of, 29 Taurates, 12, 13 fatty acid condensation with Na-N-methyltaurate, 12 Taurine geminis, 63 TBA, 493 TBAB, 365–367 tetrabutylammonium bromide, 363 TBBS, t-butyl-2-benzothiazolesulfenamide, 315 TBHQ, t-butylhydroquinone, 290 TBME, t-butylmethylether, 298 TBP, tributylphosphate, 376 TEABr, 834 Tee-mixing, 585 Teflon, 779, 781, 788, 789, 794 TEG, tetraethylene glycol, 839 TEM, 519, 531, 577, 581, 648, 624, 679, 784, 789, 805, 808, 819, 831, 839 transmission electron microscopy, 482

905 [TEM] Au nanoparticles, 645 aqueous gluconamide, 708 aqueous gulonamide, 708 aqueous mannonamide, 708 aqueous n-octyl galactonamide, 708 aqueous talonamide, 708 boomerang structures, 693 ceramic objects, 813 freeze fracture, 783, 785 hexadecyl gulonamide flexible tubules, 709 hexadecyl gulonamide twisted ribbons, 709 hydroxyapatite, 816 latex-templated silica structure, 807 MCM-41, 843 octadecyl mannonamide helices, 709 of CdS nanoparticles prepared in W/CO2 microemulsions, 356 of coupler dispersions, 582 of gold colloids, 800 of MCM-type structures, 820 of nanocasts after calcination, 809 of vesicles, 686 of tubules, 686 particle sizing by, 460 PbS particulate film, 636 pentadecyl gluconamide helices, 709 pentadecyl gluconamide twisted ribbons, 709 polymer gel, 810 silica nanocast, 810 tetradecyl gluconamide helices, 709 vesicle bilayers, 691 Template breakthrough, 532 Template emulsion droplet as particle, 577 Template polymerization at vesicle interfaces, 506 Templates enzyme crystals, 562 latex particles, 562 Templating ABC, 806 bicontinuous microemulsions, 532 bilayer, 839 by nonionic PEO surfactants, 831 by primary amines of hexagonal mesoporous silica, 830 endo, 801, 812 exo, 799, 801, 812 gallery, 842 ligand assisted, 832 liquid crystal, 821 LCT, 820 molecular, 801, 802, 823, 824 of silicates with cationic surfactants, 819 rigid colloid, 806 supramolecular, 823, 824

906 [Templating] surfactant, 802 vesicle, 839 with intercalated micelles, 845 TEMPO 2,2,6,6-tetramethylpiperidine-N-oxyl, 565 TEOS, 781, 782, 803, 804, 806, 823–825, 830, 831, 834, 835, 840–842, 844 tetraethylorthosilicate, 780 TEOS hydrolysis, 823 Tetonic 1102, 484, 486, 487 polyoxyethylene adduct of polyoxypropylene diamine adduct, 475 Tergitol 15-S-12, 831 see C11–15H23–31O(CH2CH2O)12H, 828 Termination biradical, 466 Ternary phase diagram, 609, 610 surfactant, polymer, and water, 602 water/styrene/C12 cationic gemini, 79 Tetra(t-butyl)ammonium hydroxide, 379 Tetraalkoxysilanes, TAOS, 844 Tetraalkylorthosilicates, 820 Tetrabutyl ammonium fluoride, 147 Tetrabutylammonium bromide, TBAB, 363 Tetrachloroauric acid, 799 Tetrachloroethylene, 379 Tetradecyl tripentylammonium bromide C14NPe3Br, 671 phase diagram, 671 Tetradecyl-N-[4-[6-(N,N⬘,N⬘-ethylenediamino)hexyl]oxy]benzoyl-L-glutamate DTG, 653 Tetradecylamine, 568 Tetraethylene glycol, 197 TEG, 839 Tetraethylorthosilicate, 525 TEOS, 780 N,N,N⬘,N⬘-Tetraethylphthalamide, 599 Tetrafluoroethylene, 540 Tetrahedral aluminum, 837 Tetraheptylammonium bromide PTC in benzyl chloride conversion to benzyl bromide, 352 2,2⬘,4,4⬘-Tetrahydroxybenzophenone, 589, 590 Tetramethylammonium bromide TMAB, 197 TMABr, 272 Tetramethylammonium chloride, 837 TMACl, 272 p-(1,1,3,3-Tetramethylbutyl)phenyl-polyethoxyethanol Triton X-100, 610 Tetramethylene sulfone sulfolane, 380 N,N,N⬘,N⬘-Tetramethyl-1, 1’-naphthydine dication TMN2⫹, 302 Tetramethylorthosilicate, TMOS, 780

Index 2,2,6,6-Tetramethylpiperidine-N-oxyl, TEMPO, 565 Tetramethylthiuram disulfide, TMT, 305 Tetramethylammonium silicate, 820 Tetrapropylenebenzene sulfonate from ␣-dodecylene, 4 Tetronic T-908, 596, 597 Tetronics, 20 Texas Red-DOPE probe, 400 Textile softeners cationic geminis, 59 quaternary ammonium surfactants, 2 Thermotropic behavior of gemini mesophases, 85 THF, 799 Thickeners alkyl dimethylamine oxides, 20 ethoxylated glycerol esters, 20 Thin film synthesis gas catalyzed, 780 Thin films synthesized from silica, 780 Thiol-based surfactants, 162 Thiol-MCM-41, 844 Threadlike micelles, 680 Threadlike micelles of I-C11, 681 Threshold pressure, 592 THP, 594 Thymol blue, 138 Ti, 838 Ti-TMS1, 833 TiCl4, 643, 843 Time resolved fluorescence quenching TRFQ, 695 TiO2, 519, 643, 644, 653, 832, 838, 843 electrophoretic deposition, 657 particles in Nafion films, 652 TiO2/PSS films, 654 Titania, 843 Titania grafting, 843 Titanium dioxide alumina coated, 563 dispersion stabilization, 562 gemini adsorption, 78 Titration, conductometric of carboxylic groups, 555 Titration of double bonds by bromination, 459 by hydrogenation, 459 by ozonolysis, 459 TMA⫹, 828 TMAB, tetramethylammonium bromide, 197 TMABr, tetramethylammonium bromide, 272 TMACl, 280 tetramethylammonium chloride, 272 TMAOH, 828 TMN2⫹ N,N,N⬘,N⬘-tetramethyl-1,1⬘-naphthydine dication, 302 TMOS, 803, 808, 835, 844 tetramethylorthosilicate, 780

Index TMT, tetramethylthiuram disulfide, 305 Toka black 7550F carbon black, 409 Toluene, 474–477, 483, 485, 566, 583, 585 indirect oxidation of, 300 solubilization by cationic geminis, 78 2-p-Toluidino-naphthalene-6-sulfonate fluorescence of effects of submicellar aggregates on, 231 Top-down synthesis, 797 ␣-Topophenol vitamin E, 290 Toxicity of sulfosuccinic acid dialkyl esters, 9 of sulfosuccinic acid monoalkyl esters, 9 Toxicological effects of alkyl chain length, 34 Toxicological properties of amphoteric surfactants, 38 TPS see tetrapropylenebenzene sulfonate, 4 Transacetalization yielding alkyl glucosides from short-chain alkyl glucosides, 51 Transazobenzene solubilization in gemini micelles, 78 Transesterification in dimethyl formamide, 23 in microemulsions, 23 of methyl glucosides with fatty acid methyl esters, 29 sucrose esters by, 23 with fatty acid methyl esters to give sucrose esters, 24 Transfecting agents, 59 Transfection agent, 153 Transfer constant, 549 Transient bleaching spectra of nanoparticulate CdS in Nafion, 659 Transient photobleaching of CdS particles, 660 Transmission electron microscopy, TEM, 482 Transurf, 548, 549, 551 MeEO45BO12OCOCH2SH, 553 MeEO45BO9SC(C6H5)CHCH2, 553 Trapped water, 616 TREM-LF 40 sodium alkyl allyl sulfonate, 551 TRFQ, time resolved fluorescence quenching, 695 Trialkyl triazine quaternization with dimethyl sulfate, 66 Tributylphosphate, TBP, 376, 380 1,1,1-Trichloro-2,2-bis(p-chlorophenyl)ethane DDT, reactions of hydroxide with, 188 1,1,2,2-Tetrahydroperfluorodecyl-pyridinium chloride HFDePC, 680 Tricresylphosphate, 582 Tridodecylmethylammonium bromide, 684 Triesters of phosphoric acid, 14 Trifluoromethane, 591

907 1,1,2-Trifluorotrichloroethane, 132 Triggering acid-catalyzed in liposomes, 149 cascade in liposomes, 149 dePEGylative, 150 Triglycerides saponification of, 2 Triiodobenzoate esters, 596 Trimers of DTAB, 66 Trimethyl alkyl amine, 569 Trimethyl amine, 512 Trimethylsilyl derivatives, 843 Tri(octyldecyl)methylammonium chloride, 380 Triple-chain surfactants, 67 Triton, 176 Triton SP-175, 311 Triton X-100, 254, 831 p-(1,1,3,3-tetramethylbutyl)phenyl-polyethoxyethanol, 610 Trommsdorff effect see Norrish-Trommsdorff effect, 433 True amphoteric surfactants, 36 based on fatty amines, 37 by addition of acrylic acid, to ring-opened imidazolines, 38 structure of, 37 Trypsin, 845 Tubules, 688 Tumor metastasis, 112 Turbidity in emulsion polymerization, 435 of dispersion polymerization of PMMA and poly(vinyl acetate), 356 Tween 20, 118 Tween 40 polyoxyethylene (20) sorbitan monopalmitate, 376 Tween 80, 486 polyethylene glycol sorbitan monooleate, 474 Tween 85, 489 polyethylene sorbitan trioleate, 474 Twisted fibers, 706 Two-phase micellar catalysis model for, 369 Ultrafiltration, 580, 599 Undecyltrimethylammonium bromide, 679 Unilamellar vesicles, 396, 502, 692 Unimolecular reactions of anionic substrates, 191, 193, 194 Unit cell size, 791 Unnatural phosphatidylcholines, 691 Unsymmetrical carbon-carbon bonds, 331 Urocanic acid, 672 UV labile surfactants, 55 UV spectroscopy, 509 UV-vis, 845 UV-vis spectra of CdS films, 655 of Pd containing LB films, 651

908 V, 838 V10O6⫺ 28 , 839 van der Waals, 826 Vanadium tetrakisisopropoxide, 843 Vectorial transport of droplets, 155 VEM, video enhanced interference contrast microscopy, 695 Vermiculite, 841 Vesicle dispersions electrochemical processes in, 309 Vesicle fusion, 83 Vesicle-micelle transition, 84 Vesicle polymerization, 529 Vesicle templating, 839 Vesicles, 45, 296, 501, 601, 680, 684, 668, 834, 838 as microreactors, 227 DDAB, 402 detergent lysis of, 510 diPhyPC, 692 DPPC, 692 enzymatic lysis, 505 free radical polymerization in, 503–507 giant, 395 in drug delivery, 528 interfacial halide concentrations, 284 multilamellar, 808, 831 of asymmetric phosphate geminis, 84 of gemini surfactants, 83 of diphosphate geminis, 84 polymerization of lipids in, 503–507 polypeptide, 503 reactions in, 226 reverse, 176 skeletonized, 505, 506 sphingosine, 400 spontaneously formed, 507, 698 stability, 703 unilamellar, 502, 692 with switchable permeability, 505 Vesicular morphologies, 591 Vesicular polymerization, 501 cross-linking in, 510 Vesosomes, 402 Video enhanced interference contrast microscopy VEM, 695 Vinyl, 503, 843 Vinyl acetate, 441, 553 Vinyl acetate emulsion polymerization, 567 p-Vinylbenzene sulfonate inverse emulsion polymerization of, 487 Vinylbenzoate condensation onto hydroxylphenyldimethylsulfonium methyl sulfate, 559 Vinyl benzyl surfactants, 557 Vinyl chloride, 431, 563 Vinyl esters, 431 from dimethyl ethanolamine esters, 20

Index Vinyl ether degradative reactions for diplasmenylcholine, 150 for plasmenylcholine, 150 Vinyl ether hydrolysis, 151 Vinyl ether PEG lipid conjugate, synthesis of, 150 Vinyl ether surfactants, 145–154 Vinyl polymerization of norbornene in aqueous dispersion, 342 in SDS/water microemulsion, 343 Vinyl-MCM-41, 844 4-Vinyl pyridine, 563, 566 Vinylpyrrolidone, 474, 489 Vinylsulfone, 48 Viral infection, 112 Virus particles, 653 Viscoelasticity, 483 Viscosity, 521 of gemini surfactant micellar solutions, 81 Vitamin E ␣-topophenol, 290 Vitamin B12, 328 Vitamin B12 hexacarboxylate, 333 Vitamin C ascorbic acid, 290 Vitamins fat soluble as fat constituents, 3 VOC, volatile organic component, 579 Volmer isotherms, 187 Volume fraction of hexagonally-packed cylinders, 805 VTAS/TAOS condensation of, 844 VTES, 844 VTES/TEOS, 844 VTMS/TMOS, 844 VX o-ethyl-S-diisopropylaminoethylmethyl phosphothiolate, 374 Vycor glass, 801

W, 838 W/O, water-in-oil, 527 Wako V-65 ADVN, 485 Washing, 580 Water trapped, 616 Water absorption of films from latexes, 556 Water addition to form naphthoquinones, 308 Water catalyzed reactions, 191, 198 Water-CO2 interface, 138 Water condensation in sol-gel processing, 803 Water in CO2 emulsions, 350 Water-in-oil, W/O, 527 Water-in-oil microemulsions, 374, 455, 477, 515, 516, 602, 609

Index Water/AOT/heptane microemulsion, 609, 617, 622, 624, 626, 630 AgBr precipitation, 611 Water/AOT/p-xylene microemulsions, 616, 617 Water/benzene interface see benzene/water interface, 789 Water/carbon dioxide emulsions, reactions in, 349–357 Water/carbon dioxide microemulsions, reactions in, 349–357 Water/CTAB/hexanol microemulsion, 609, 616, 620, 624, 625, 630 Water/DDP/TEG liquid crystal microemulsions, 839 Water/PEDGE/hexane microemulsions, 609, 622, 623 Waterborne conductive coatings, 562 Water uptake by films prepared using hemiamide surfactants, 557 prepared using hemiester surfactants, 557 prepared using zwitterionic surfactants, 557 Waxes as fat constituents, 3 Weight average aggregation number of sodium alkanoate micelles, 418 Wetting agents alkyl dimethylamine oxides, 20 HLB of, 18 White spirit, 475 Wilhelmy plate method, 158, 167 Williamson reaction, 364 WO3, 838 Wormlike micelles, 669, 798 Wormlike micelles, of cationic surfactant oligomers, 80 Wormlike micelles, of gemini surfactants, 82 X-ray diffraction, 586 X-ray plasmon spectroscopy, 649 X-ray scattering, 670

909 XRD, 655, 789, 822, 830, 833, 836, 837 cubic mesoporous silica film, 787 hexagonal mesoporous silica film, 788 mesoporous silica film, 784 spectra, 650 m-Xylene, 674 o-Xylene, 474, 475, 484 Xylitol, 49 Y, 838 Young–Laplace equation, 442 z-ArN2BF4, preparation, 276 Z-vinyl ether linked phospholipids, 145 Zeolite films, 780 Zeolite synthesis, 819 Zeolites, 633, 801, 802 Ziegler process alcohols from, 18 in ethylene oligomerization, 6 Zirconium oxides, 832 Zn behenate, 651 films, 645 Zn(DS)2, 258 Zn2⫹, 799, 838 ZnO, 800 ZnS, 644 nanoparticles, 635 ZnS/stearic acid films, 648 Zr, 838 ZrO2, 838 ZSM-48, 823 ZSM-5, 823, 824 Zwitterionic micelles interfacial halide concentrations in, 284 Zwitterionic surfactants, 829

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Cationic Surfactants (Surfactant Science)

Colloids in Biotechnology (Surfactant Science)

Computational Methods in Surface and Colloid Science (Surfactant Science Series)

Protein-Based Surfactants (Surfactant Science Series)

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Thermal Behavior of Dispersed Systems (Surfactant Science)

Analysis of Surfactants (Surfactant Science Series)

Physical Chemistry of Polyelectrolytes (Surfactant Science Series)

Bicontinuous Liquid Crystals (Surfactant Science)

Microporous Media: Synthesis, Properties, and Modeling (Surfactant Science)

Wetting and Spreading Dynamics: 138 (Surfactant Science)

Coagulation and Flocculation, Second Edition (Surfactant Science)

Molecular and Colloidal Electro-optics (Surfactant Science)

Surfactants in Cosmetics (Surfactant Science), 2nd ed

Molecular and Colloidal Electro-optics (Surfactant Science)

Emulsions and Emulsion Stability (Surfactant Science)

Adsorption: Theory, Modeling, and Analysis (Surfactant Science Series, Volume 107)

Emulsions and Emulsion Stability: Surfactant Science Series 61

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Reactions and Synthesis in Surfactant Systems (Surfactant Science Series)