3d, 4d and 5d Elements, Alloys and Compounds (Landolt-Bornstein: Numerical Data and Functional Relationships in Science and Technology - New Series Condensed Matter)

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Author: H.P.J. Wijn | H.P.J. Wijn | K. Kanematsu | S. Misawa | M. Shiga | H. Wada

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ISSN

og@-7988(CondensedMatter)

ISBN

3-540-60334-4Springer-VerlagBerlin Heidelberg NewYork

LibraryofCongress Catalogingin Publication Data Zahlenrrerteund Funktionen ausNaturwissenschaftenundTechnik,NeueSerie Editor in Chief: W. Martienssen Vol. 111/3zA:Editor:H.P.J.Wijn At headof title: Landolt-BGrnstein.Addedt.p.:: Numerical data and functional relationships in scienceand technology. Tableschiefly in English. Intended to supersedethe Physikalisch-chemischeTabellenby H. Landolt and It. BOrnsteinof which the 6th ed.began publication in 1950under title: Zahlenwerteund Funktionen ausPhysik,Chemie,Astronomie,Geophysikund Technik. Vols.publishedafterv. 1of group I haveimprint: Berlin,NewYork,Springer-Verlag Includesbibliographies. s.Physics--Tables.z.Chemist~--Tables.).Engineering--Tables. I. B8mstein.R.(Richard),@-1gn II. Landolr,H. (Hans),1831-1g1o. III. Physikalisch-chemischeTabellen.IV.Title: Numerical dataand functional relationshipsin scienceand technology. QC61.23 ~02'.12

6253136

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Preface

The intrinsic magnetic properties of metals, alloys and metallic compounds have been systematically compiled in the various subvolumes 19A–F of the Landolt-Börnstein New Series Group III. Each subvolume is devoted to a separate and, from a point of view of the Periodic System of the Elements, coherent group of substances. The amount of experimental data that became available since the publishing of each of these subvolumes gave us every reason to ask the various authors to consider the appropriateness of preparing supplements to their original work. As a result, in this present and first subvolume LB III/32A, the magnetic properties of substances consisting of 3d, 4d and 5d elements, and of alloys between these elements, as well as alloys and compounds between 4d or 5d elements and main group elements, have been compiled as they were described in the literature since about the beginning of the 1980's. This subvolume is a supplement to LB III/19A, and to section 1.6 of LB III/19B, which is supplemented in section 1.3 of the present volume. Many thanks are due to the authors for the continued agreeable cooperation, Frau G. Burfeindt and Dr. W. Finger of Landolt-Börnstein's editorial office for the great help in the editorial work, especially in preparing the camera-ready pages of this volume from the electronic files submitted by the autors, and, last but not least, Springer-Verlag for the carefulness with respect to the publication of this volume. Aachen, September 1996

The Editor

List of symbols

Symbol

Unit

Quantity

a, b, c as B B Cp CV cij cL

nm, Å

lattice parameters asymmetry ratio bulk modulus magnetic induction heat capacity at constant pressure heat capacity at constant volume elastic constants elastic constant for longitudinal sound wave, cL = (c11 + c12 + 2c44)/2 diffusion coefficient q2-expansion coefficient of the spinwave energy energy cohesive energy Young´s modulus q4-expansion coefficient of the spinwave energy Fermi energy anisotropy energy electrons per atom nuclear electric quadrupole coupling constant frequency de Haas van Alphen frequency shear modulus g-factor magnetic field magnetic anisotropy field applied magnetic field critical magnetic field effective magnetic field magnetic hyperfine field Planck's constant Planck's constant divided by 2π spin wave energy Miller indices intensity isomer shift intensity direction of electrical current Knight shift

D D E Ecoh E E EF Ea e/a e2qQ f f G g H HA Happl Hcr Heff Hhyp h ω h, k, l I IS J J K

Pa T, G J kg–1 K–1 J kg–1 K–1 Pa Pa m2 s–1 eV Å2, THzÅ2 J, erg, eV, Ry eV Pa THzÅ4 eV J m–3 mm s–1, MHz Hz T Pa A m–1, Oe A m–1, Oe A m–1, Oe A m–1, Oe A m–1, Oe A m–1, Oe Js Js eV

mm s–1

List of symbols Symbol

Unit

Quantity

K K1 Ku1, Ku2 k, kB ki– kf ∆l/l m* M Ms n(E) P(H) p p p

Pa J m–3, erg cm–3, Pa J m–3, erg cm–3, Pa J K-1

bulk modulus first-order magnetocrystalline anisotropy constants uniaxial magnetic anisotropy constants Boltzmann constant photon scattering vector linear magnetostriction effective electron mass magnetization saturation magnetization density of states of energy E probability distribution pressure atomic magnetic moment average atomic magnetic moment magnetic moment per atom z-component of linear momentum reduced wavevector direction of atomic displacements in ultrasonic wave spin-density wavevector thermoelectric power electrical resistance Hall coefficient electrical resistance ratio thermoelectric power Stoner factor scattering function temperature annealing temperature Curie temperature critical temperature spin-freezing temperature spin-glass transition temperature incommensurate-commensurate transition temperature Néel temperature quenching temperature spin-flip temperature superconducting transition temperature longitudinal nuclear spin relaxation time reduced temperature time zz-component of electric field gradient volume velocity composition

pat pz q qii Q Q R R r S S S(q, ω) T Ta TC Tcr Tf Tg TIC TN TQ TSF Ts T1 t t Vzz V v x, y a a b

A m-1, T, G A m-1, T, G states/eV atom Pa, bar µΒ µΒ µΒ kg m s–1

nm–1, Å–1 V K–1 Ω m3/C VK–1 K–2 K, °C K K K K K K K K K K s s V cm–2 m3 m s-1

K

–1

critical exponent of specifc heat linear thermal expansion coefficient critical exponent of magnetization

XI

XII

List of symbols

Symbol

Unit

Quantity

b Γ, γ Γ2 Γ γ γ ∆ δ ε ς η qD l l100, l111 l l||

deg

angle Grüneisen constant transverse nuclear spin relaxation rate linewidth critical exponent of magnetic susceeptibility electronic specific heat coefficient quadrupole splitting incommensurability factor, δ = 1 – Qa/2π linear strain reduced wavevector asymmetry parameter of the electric field gradient Debye temperature magnetostriction magnetostriction constants longitudinal spin relaxation rate magnetostriction parallel to the direction of the magnetization magnetostriction perpendicular to the direction of the magnetization relative permeability permeability permeability of the vacuum nuclear Bohr magneton electron density of states at the Fermi energy frequency spin rotation frequency of positive muons

s–1 meV J mol–1 K–2 mm s–1

K

s–1

l⊥

µ µ µ0 µn n(EF) n nµ+ ∆r/ r r s s s τ cg cHF cV cm χ' χ'' χ~n ω ω

Tm A-1 Tm A-1

s–1, Hz s–1

magnetoresistance Wm Am2kg–1, Vsmkg–1, Gcm3g-1 Am2mol–1, Vsmmol–1, Gcm3mol-1 Pa s m3kg-1, cm3g-1

electrical resistivity bulk magnetic moment per unit of mass

m3mol-1, cm3mol-1

magnetic susceptibility per mole real part of the complex magnetic susceptibility imaginary part of the complex magnetic susceptibility nonlinear magnetic susceptibility, n = 2, 3, … volume magnetostriction angular precession frequency

rad s–1

bulk magnetic moment per mole stress time interval magnetic susceptibility per unit of mass high-field magnetic susceptibility magnetic susceptibility per unit of volume

List of abbreviations

a.u. ac AF AS at bcc c.w. CPA cr CSDW dc dHvA diff el F FC fcc FIFM FM FMAR FR hcp IC INS ISDW KKR

atomic unit alternating current antiferromagnetic asperomagnetism atom body-centered cubic cold-worked coherent potential approximation critical commensurate spin-density wave direct current de Haas – van Alphen diffuse electronic ferromagnetic field-cooled face-centered cubic field-induced ferromagnetism ferromagnetism ferromagnetic antiresonance ferromagnetic resonance hexagonal close-packed commensurate – incommensurate inelastic neutron scattering incommensurate spin-density wave Kramers – Kronig – Rostocker

LDOS LISDW max µSR NIS NMR orb P PAC ph ppm RSG RT s SAF SDW SF SG SP SPKKR SUP supercond TAS TCT TISDW wt ZFC

local density of states longitudinal incommensurate spin-density wave maximum muon spin resonance neutron inelastic scattering nuclear magnetic resonance orbital paramagnetic perturbed angular correlation phonon parts per million reentrant spin glass room temperature spontaneous; saturation superantiferromagnetism spin-density wave spin-flip spin glass superparamagnetism spin-polarized KKR method superconductivity superconducting triple-axis spectrometer tricritical temperature transeverse incommensurate spin-density wave weight zero-field cooled

Definitions, units and conversion factors

Units are given for the cgs/emu system and SI, for defining relations of the magnetization, B = H + 4πM, B = µ0(H + M) and B = µ0H + M, respectively. µ0 = 4π⋅10–7 VsA–1m–1, A: molar mass, ρ : mass density. Quantity

cgs/emu

SI

B

G = (erg cm–3)1/2 1G≡ 1 Oe = (erg cm–3)1/2 1 Oe ≡ B = H + 4πM G 1G≡

T = Vs m–2 10–4 T A m–1 103/4π A m–1 B = µ0(H + M) A m–1 103 A m–1

B = µ0 H + M T 4π⋅10–4 T

P = MV G cm3 1 G cm3 ≡ σ = M/ρ G cm3 g–1 1 G cm3 g–1 ≡ σm = σA G cm3 mol–1 1 G cm3 mol–1 ≡

P = MV A m2 10–3 A m2 σ = M/ρ A m2 kg–1 1 A m2 kg–1 σm = σA A m2 mol–1 10–3 A m2 mol–1

P = MV Vsm 4π⋅10–10 V s m σ = M/ρ V s m kg –1 4π⋅10–7 V s m kg –1 σm = σA V s m mol–1 4π⋅10–10 V s m mol–1

χ

P = χH cm3 1 cm3 ≡

P = χH m3 4π⋅10–6 m3

P = χ µ0 H m3 4π⋅10–6 m3

χV

χV = χ/V cm3 cm–3 1 cm3 cm–3 ≡

χV = χ/V m3 m–3 4π m3 m–3

χV = χ/V m3 m–3 4π m3 m–3

χg

χg = χV/ρ cm3 g–1 1 cm3 g–1 ≡

χg = χV/ρ m3 kg–1 4π⋅10–3 m3 kg–1

χg = χV/ρ m3 kg–1 4π⋅10–3 m3 kg–1

χm

χm = χg A cm3 mol–1 1 cm3 mol–1 ≡

χm = χg A m3 mol–1 4π⋅10–6 m3 mol–1

χm = χg A m3 mol–1 4π⋅10–6 m3 mol–1

R0 , Rs

ρH = R0B + 4πRsMs Ω cm G–1 1 Ω cm G–1 ≡

ρ H = R 0 B + µ0 R s M s m3 C–1 100 m3 C–1

ρH = R0B + RsMs m3 C–1 100 m3 C–1

H M

P

σ σm

Ref. p. 281

1.1.1. Ti, V, Cr, Mn

1

1 Magnetic properties of 3d, 4d, and 5d elements, alloys and compounds

1.1 3d elements This is an updating and an extension of the comprehensive compilations of the magnetic properties of Ti, V, Cr and Mn by Franse and Gersdorf in LB 111/19A[86F2] and of Fe, Co and Ni by Steams [86Sl] in the samevolume, covering the literature after about the year of 1982. The major part of this later work deals with the investigation of the influence of small additions of other elements on the magnetic properties of the 3d elements.

1.1.1 Ti, V, Cr, Mn Survey

Metal

Properties

Cr*)

SDW 15-18 magnetic phasediagram 1,3, 5,7-9, 11-14 19,20 X(13 2,4,6, 10, 12 TN@>P> latent heat 37 ANI vs. T 25,26 elastic properties 27-3 1 Miissbauer data 21a,b nuclear properties 22 muons 23,24 electrical resistivity 32a,b-36 Mossbauer data 38 lattice constants 39 nuclear properties 40,43 Mijssbauer data 41,42 phasediagram, T,(x) 44 latent heat 45 All1 vs. T 46

clMn PMn yMn

Fig.

Table

1,2 1,2

3

4

*) Included are alloys of Cr with minor additions of the elements Al, Ga, Si, Ge, Mn, Fe, Pt. Ru or Re.

Landolt-BOrnstein New Series W32A

2

1.1.1 Ti, V, Cr, Mn

[Ref. p. 28

1.1.1.1 Ti See LB 111/19A,p. l-5

1.1.1.2 v See LB III/l9A, p. 6

1.1.1.3 Cr Supplement to LB III/l 9A, p. 6-l 6 A comprehensive theoretical and experimental survey of the spin-density-wave (SDW) antiferromagnetism of chromium has been given by E. Fawcett [88Fl]. The NCel temperature of pure Cr has again been derived from thermal expansion and bulk modulus measurements:T,.,= 3 11 K [83Al], and from critical neutron scattering experiments: TN= 3 10.1 f 0.1 K, showing a weak first-order transition [90Nl, 90N2]. The transition is continuous in the caseof Cr diluted with V, MO or Mn [86Fl]. In the caseof doping with Co no true location of the NCel temperaturecould be determined [83Al]. The magnetic phase diagrams of dilute antiferromagnetic Cr alloys have been derived from the results of measurementsof the thermal expansion, elastic constant, electrical resistivity, magnetic susceptibility, X-ray or neutron diffraction properties of samples with small concentrations of the elements: Al (Fig. I), Ga (Fig. 3), Si (Fig. 5), Ge (Fig. 7), Mn (Fig. 9), Fe (Fig. 1la), Pt (Fig. 13), Ru and Re, see also Tables 1 and 2. For a survey see [92F2]. The Ntel temperature is generally taken as the point where the curve for the bulk modulus as a function of temperature, B(T), has a minimum. It is also considered to be the temperature at which the linear expansion curve a(7) has an inflection point (at a temperature above its minimum) in the caseof ISDW-P transitions, or to be the temperature where the curve a(T) shows a very steep minimum in the case of CSDW-P transitions. Also has been measuredthe influence of externally applied pressureon the NCel temperature TN,the temperature Tc, of the phasetransition between commensurate(C) and incommensurate(I) spin-density waves (SDW), and on the spin-flip temperature TSFbetween transverse (T) and longitudinal (L) incommensurate SDW phases,TISDW (or AF,) and LISDW (or AF,), respectively: Cr-1.4 at% Al (Fig. 2 and Table I), Cr-Ga (Fig. 4 and Table I), Cr-Si (Fig. 6 and Table 1), Cr-Ge (Fig. 8) Cr-Mn (Fig. lo), Cr-Fe (Fig. 11b), Cr-0.3 at% Ru (Fig. 13). For ternary alloys of Cr (Fe) and Cr (Si) with V or Mn see also [92F 1, 93Fl]. Fig. 14 gives an example. Neutron inelastic scattering measurementsof pure Cr and Cr doped with 0.2 at% V give more information on the magnetic structure in the neighborhood of the NCel temperature [83B2, 85G1, 90Nl,90N2, 9lF2]. The incommensurability factor 6= 1 - (Qu)/27t of the SDW vector Q ‘has been measured as a function of temperature and pressure for small additions of Al (Fig. 15) Si (Figs. 5, 16), V (Fig. 17) and Fe (Fig. 18) to chromium. A survey and extension of high-resolution neutron scattering measurements in relation to propagating modes in the TSDW system of single-Q chromium is given in [93Sl]. For the magnetic susceptibility of pure Cr and Cr diluted with Ni or V see Figs. 19 and 20. It appearsthat nickel up to a concentration of 2 at% in Cr-Ni does not have a local magnetic moment. The local moment of vanadium in Cr-V alloys is 1.8 uB and 1.12 ue for a concentration of 0.5 at% and 1.52 at%, respectively [8lKl]. For magnetic fields on “‘Cd and “‘Ta nuclei in chromium see Figs. 21a,b. The diluted-impurity hyperfine field on “‘Cd in ISDW chromium at 4 K is 60.3 + 2.0 kOe [8OVl]. For the nuclear spin relaxation rate of ?r seeFig. 22. For spin precession properties of positive muons in LSDW chromium see Figs. 23 and 24. The low-temperature limit of the zero-field angular precession frequency is ‘Y529.0.106 rad s-‘, Land&-Bamtcin New Series 111132A

1.1.1. Ti, V, Cr, Mn

Ref. p. 281

3

corresponding to an internal magnetic field of = 6.21 kOe. The muon diffusivity at 4 K is estimated to be D1,+= 2.4.1014m’s’ [86Ml, 90Tl]. Small additions of Al, V or Mn have much influence on the muon spectrum [92Nl]. For pure Cr the linear thermal expansion coefficient a is shown as a function of temperature in Fig. 25. Small concentrations of other elements can have a drastic influence on the a(T) curve. For substitutions of Al see [84Al], Ga [85Al], Si [88Al], Ge [87Rl], V [85Kl, 85K2, 88Cl] and Fig. 25, Mn [87Al], Ru [88A3] and Pt [88A2]. For substitutions of V or Mn in Fe- or Si-doped Cr see [92Fl, 93Gl]. The temperature dependenceof the elastic constants cii of a chromium crystal in various magnetic states is given in Figs. 27-30. The insets of these figures illustrate the experimental set up in each case. The vectors labelled qii represent the direction of the atomic displacements as a consequenceof the ultrasonic waves. For a detailed behavior of the attenuation of the sound waves around TSFsee [87M2, 88F2, 9OCl]. Small concentrations of substituted elements have much influence on the elasticity moduli. For substitutions of Al see [84Al], Ga [85Al], Si [88Al]*), Ge [87Rl]*), V [82Cl, 88Cl] and Fig. 31, Co [82A2], Mn [87Al], Ru [88A3,93Bl], Re [93Bl] and Pt [88A2]. Data on the electrical resistivity of Cr are given in Figs. 32a,b. For the influence of minor substitutions on the resistivity of chromium see in the case of Ga [83Al, 84A2] and Fig. 33, Si [9lFl]*), Ge [86Rl]*) and Fig. 34, Ru [9382] and Figs. 35, 36, Re [85Bl] and OS[85Bl]. For ternary Cr--(Fe-V) and Cr-(Fe-Mn) see [93Gl]. Specific heat of Cr and Cr-0.5 at% V see Fig. 37. For a survey of various properties of Cr above room temperature seeTable 3.

*) Seealso LB 111/19C,subsect. 1.5.4.3, p. 7 for earlier data.

For Table 1 seenext page Table 2. Cr-x at% M, M = Ru, Re, single crystals. NCel temperature TN,spin-flip temperature TsF,and the transition temperatures T,, and T,, between ISDW and CSDW on heating and cooling, respectively, as derived from ultrasonic (US) and neutron diffraction (N) data [93Bl]. X

TNWI

r,, WI

TCIWI

TSFWI us

us

N

us

N

N

0.3 0.5

402+_5 465+8

406+5 462+5

257 f 5 146 z!z8

255 + 4 143 f 6

240+4 92 zk6

Cr lo&ex 0.3 0.5

328 ?I 8 414 k 8

Land&-Bbmstein New Series III132A

250 IL 9

85 zk5

119f8 87 f 9

N

75 f 9

4

1.1.1 Ti, V, Cr, Mn

[Ref. p. 28

Table 1. Cr-x at?/oM, M = Al, Ga, Si, V. NCel temperature TN and transition temperature between incommensurate and commensuratephases, T,, , as derived from thermal expansion and from bulk elasticity measurements,a(Q and B(7), respectively. X

T,.,[K] derived from

T,, [K] derived from

Ref.

a(n

BUJ

Cr ,0&X4 0 0.67 1.06 1.70 2.19 2.74 3.20

311 255 185 95 215 260 299

311 246 184 98 216 272 303

83A3 84Al 84AI 84Al 84Al 84A 1 84Al

Cr 100-rGax 0.15 0.42 0.72 0.83 1.oo 1.42 1.72 1.88 3.00

297 290 282 335 342 388 404 435 445

295 285 280 355 370 400 415 435 450

85A1 85Al 85Al 85Al 85Al 85A1 85A1 85A1 85AI

Cr loa-rSix 0.50 0.74 0.90 1.04 1.42 1.79 3.43

277*5 255 f 5 237&5 233 f 2 245*2 242*2 176&2

275 f 2 250*2 230~1~8 235 k.5 245 f 5 240 f 5 185 *25

a(T)

258 255 175 170

203~~5 123*5

B(T)

255 240 155

88A1 88Al 88Al 88Al 88Al 88Al 88Al

Landolc-BBmrtein New Seria W32A

Ref. p. 281

1.1.1. Ti, V, Cr, Mn

5

Table 3. Cr. Most probable values for the linear thermal expansion coefficient a, heat capacities C, and CV,bulk modulus B and Grtineisen parametery, as derived from various literature data by [86Wl]. T

a

CP

CV

B

Kl

[ 10dK-‘1

[J mol-‘K-‘1

[J mol-‘K-‘1

Wal

350 400 450 500 550 600 650 700

7.43 8.12 8.61 9.00 9.30 9.58 9.82 10.10

24.5 25.2 26.0 26.5 27.0 27.5 28.0 28.5

24.3 24.9 25.6 26.0 26.4 26.8 27.2 27.6

1.77 1.87 1.92 1.94 I,94 1.94 1.94 1.93

0

Cr

Land&-Bbmstein New Series 111132A

1

2

3 x-

4

Y

1.12 1.32 1.39 1.44 1.46 1.48 1.50 1.50

Fig. 1. Cr-x at% Al. Magnetic phase diagram [84Al]. P : paramagnetic,TISDW: transverse incommensurate SDW phase, LISDW: longitudinal incommensurate SDW phase,TCSDW: transverse commensurateSDW phase. Derived from 1: thermal expansion 2: elastic constant measurements [84Al]; measurements [84Al]; 3,4: electrical resistivity measurements [78A 1, 80s 11; 5: elastic constants [83Rl].

6

1.1.1 Ti, V, Cr, Mn 225 K

[Ref. p. 28

I

,

I

Cr-1.9ot%Al

200

!

175

150

125 0

2

3

4 kbor 5

P-

1

2

3

4 kbor 5

P-

TN as derived from neutron diffraction spectra for a x = 1.4 and b x = 1.9 [82Ml].

Fig. 3. Cr-x at% Ga. Magnetic phase diagram, similar to Fig. I [84A2, seealso 82Kl). 1: neutron diffraction [83Bl]; 2: electrical resistivity [79Fl]; 3: electrical resistivity [84A2]; 4: thermal expansion [79Fl]. Triple point at x EJ0.5 at% Ga and T= 277 f 5 K [84A2].

ISOW 0.5

0

b

Fig. 2. Cr-x at% Al, x = 1.4, 1.9. Influence of externally applied pressurep on the Ntel temperature

200 0 Cr

171; 125 .&”

1

1.0

1.5 x-

2.0

2.5

3.0

3.5

Lmdolt-Barnstein New Serb IW32A

Ref. p. 281

1.1.1. Ti, V, Cr, Mn

500 K

I

500

I

K

Cr-x at % Go

0

2

4

a

6

8

kbar 10

Fig. 4. 0-x at% Ga. Influence of externally applied pressure p on the Ntel temperature TN for various concentrations x as derived from the electrical

I

I

Cr - 1.06 at %Go

0

b

P-

7

2

4

6

8

kbar IO

P-

resistivity. a Ntel transitions to CSDW and ISDW phases, TNc and TN,, respectively. b (p, Q-phase diagram for x = 1.06 [82Kl, seealso 83Al].

Fig. 5. Cr-x at% Si. Magnetic phase diagram as derived from various physical properties and assembledin [93Fl]. 1: Electrical resistivity [67Al]; 2: thermoelectric power [71Al]; 3: magnetic susceptibility [73Hl]. 4: electrical resistivity, thermal expansion [75Fl]; 5: electrical resistivity [76Jl]; 6: neutron diffraction [77Cl]; 7: electrical resistivity [77Sl]; 8: specific heat [77Al]; 9: magnetic susceptibility [80Dl]; 10: neutron diffraction [8OCl]; JJ: neutron diffraction [82El]; 12: specific heat, 13: neutron magnetic susceptibility [82Bl]; diffraction [86M2]; J4: thermal expansion, ultrasonic velocity [88Al]. Insets: a Magnetic phase diagram around the triple point. b SDW incommensurability parameterCT=1 - QuRn along the dashedline in a for x = 0.85.

0 Cr

Landolt-BOrnstein New Series 111/32A

1

2

3 x-

4

5

8

1.1.1 Ti, V, Cr, Mn

[Ref. p. 28

325 K 300

I 275 I LT= 250

225

a

200 0

1

2

P-

3

4

kbor 5

Fig. 6. Cr-x at% Si, x = 0.5, 0.9, 1.4. a Influence of externally applied pressurep on the NCel temperature TN, as derived from neutron diffraction data. b Phase diagram for x = 1.4. The hatched region indicates

0

0.4

0.8

1.2 x-

b

0

1

2

P-

3

4 kbor 5

coexistence of ISDW and CSDW phases.For x 2 1.9 and up to p = 3 kbar only the CSDW phase exists [82Mj].

Fig. 7. Cr-x at% Ge. Magnetic phase diagram as derived from measurementsof (I) thermal expansion, (2) bulk elasticity moduli [87Rl], and (3) electrical resistivity [87R2]. The solid curves are best fits obtained from theory given in [84Ml]. 1.6

2.0

Land&-Bbmrtein New Scria W32A

Ref. p. 281

1.1.1. Ti, V, Cr, Mn I

I

I

9

I x =0.51

Cr-x ot%Ge 325 I

300

300

csow

I b. 275

I

L 250

250 200

225 200 0

0.5

a

1.0

1.5 2.0 P-

2.5

3.0

150 0

kbar 4.0

1

2

b

3

4

5 kbar 6

PK 400 YY,

x =d.89 P

350 II

h

300 I I h 250

csow

200 I

c

Fig. 8. Cr-x at% Ge, x = 0.5 1, 0.70, 0.89. Magnetic phase diagram for various compositions as derived

Landolt-Bbmstein New Series 111/32A

100r 0

I 1

I 2

P-

I 3

I 4

I I 5 kbar 6

from the influence of pressure on the electrical resistivity of the alloy [86Rl].

[Ref. p. 28

1.1.1 Ti, V, Cr, Mn

10

500

500

I

I

I

K Cr-xat%Mn I

K

,

(1

LSrl

I

I

I

Cr- 0.5 at %Mn 1

--I 1x1 pI I 1

400114

0,

csolv I

I

I

I

ZOOI

t I.

\I

.\

350.

300

9/p

0

0.15

0.30

0.15

0.60

liO/ 0.75

0.90

x-

Cr-

I x of%

Fe

300

00 V’ ( TCSOW v

250

!

200

;f

150

'7 s8 0 9 - 10 0 11 x 12

100 50

a

0 Cr

1

2

x-

I

1

I 2

ISOW

I

I

I 3

I

I

I

4

5 kbor 6

P-

Fig. 9. Cr-x at% Mn. Magnetic phase diagram as derived from (I) thermal expansion and (2) bulk modulus measurements. (3) [84Y I]. (4) Spin-flip temperaturesderived from bulk moduli measurements. Triple point x = 0.20 f 0.02 and T= 330 f 15 K [87Al, seealso 82Ml, 84Yl].

400 K

200’ 0

I

3

, 0 13 014 _ 0 15

Fig. 10. Cr-0.5 at% Mn. Influence of pressure p on the NCel temperatureTN and the transition temperature T,, between CSDW and ISDW [82Ml].

Fig. 11 a. Cr-x at% Fe. Magnetic phase diagram, as derived from various physical properties and assembled by [93Fl]. I: Magnetic susceptibility [66Sl]; 2: neutron diffraction [6711]; 3: neutron diffraction [67A2]; 4: electrical resistivity [70Al]; 5: thermoelectric power [7lAl]; 6: thermal expansion [74Fl]; 7: ultrasonic velocity, electrical resistivity [75El], neutron diffraction [82Fl]; 8: X-ray diffraction [76Ml]; 9: specific heat [76Sl]; IO: thermal expansion, ultrasonic velocity [77Hl]; II: [77H2]; 12: magnetic electrical resistivity susceptibility [73Hl]; 13: specific heat [75Kl]; 14: electrical resistivity [79Kl]; 15: neutron diffraction [82Ml]; 16: specific heat, magnetic susceptibility [82Bl]; f 7: thermal expansion [89Bl].

+ 16 e17

4

_

15 Lmdolt-Bbrntrcin New Series llV32A

Ref. p. 281

1.1.1. Ti, V, Cr, Mn I

Cr- 2.8 at% Fe

I

h-2.1 at%Fe 260

I

0

2

b

4

6

kbor

8

P-

Fig. 11 b, c. Cr-x at% Fe. Influence of externally applied pressurep on the NCel temperature TN and the transition temperature TIC between ISDW and CSDW. The latter transition shows some irreversibility, indiElectron concentration (Cr =6) 6.02 6.04 6.06 I

6006'oo

K

100

6.08

fr

\

0

0.5

1.0

1.5

2.0

x-

Fig. 12. Cr-x at% Pt. Magnetic phase diagram, as derived from susceptibility data (open circles [75Nl]) and neutron diffraction spectra(solid circles [78Bl]).

Land&-Bbrnstein New Series 111/32A

1.0

1.5

2.0

2.5 kbor 3.0

P-

cated by the arrows. b Results for x = 2.8 derived from electrical resistivity and ultrasonic velocity data [93Fl], c for x = 2.1 from neutron diffraction data [82Ml].

296

I

260

I

256

I

2LOY 0

h

0

0.5

I

K Cr-0.3 at%Ru

Cr-xat%Pt

HSDW‘i

0 0

0.25

II

/I

0.50 P-

IY

I

I

I

0.75

1.00

I

1.25 kbor 1.50

Fig. 13. Cr-0.3 at% Ru, single crystal. Influence of pressurep on the transition temperature TIC between CSDW and ISDW phase. The lower curve applies to increasing, the higher curve to decreasing pressure. Transition points derived from longitudinal ultrasonic wave velocities [92Al].

1.1.1 Ti, V, Cr, Mn

12

[Ref. p. 28

600 K

600 K

500

0

0.2

0.4

a

x-

0.6

0.8

1.0

1.2

Magnetic phase Fig. 14. (Cr-z at% Fe),-,Mn,. diagram as derived from thermal expansion data for a z = 1.5 and b z= 0.5. TN: Neel temperature; T,, and Tc : temperaturesfor transitions from TISDW to 0.035,

I

I

I

Cr-xat%Al

I

0

b

I

I

I

I

0.2

0.4

0.6

0.8

I

1.0

I

1.2

x-

TCSDW phases at higher temperature and from TCSDW to TISDW phases at lower temperature, respectively [92Fl].

I

I Cr-xi

%Si I

I

I

I

I 3

I 4 kbor

ao301 T-Y-4 0.030

0.035

w

.4

1

0

o.0505 0

1

2

3

0.040

4 kbor 5

P-

,,,u” 0.045’ Fig. 15. Cr-1.4 at% Al. Pressure dependence of the incommensurability parameter 6= 1 - Qa12n of the spin density wave vector Q at TIT, = 0.99, as derived from neutron diffraction spectra. For comparison the curve for pure Cr is given [82Ml].

0

I 1

2

PFig. 16. Cr-1.4 at% Si. Pressure dependence of the incommensurability parameter S= 1 - QuRx of the spin density wave vector Q at T/T, = 0.99, as derived from neutron diffraction spectra. For comparison the curve for pure Cr is given [82Ml].

Landolr-Bamrtein New Series IIIl3tA

Ref. p. 281

1.1.1. Ti, V, Cr, Mn

13

r-x at %Fe

I

I

1

3

4

I

0.030 I

0.055 I

I

IR

I 0 0

0

0

COO8

+

0.050 I

Y, o.035

‘

-

I 0.040

75

.

115

155 T-

195

235

0.045I 0

K 275

Fig. 17. Cr-0.5 at% V. Temperature dependence of the incommensurability parameter 6 as derived from neutron diffraction spectra. Points without error bar have uncertainties of the size of the symbols [88Nl].

2

kbar

5

P-

Fig. 18. Cr-x at% Fe, x = 2.1, 3.0. Pressure dependence of the incommensurability parameter 6= 1 - Qu/2n of the spin density wave vector Q at TIT N = 0.99, as derived from neutron diffraction spectra.For comparison the curve for pure Cr is given [82Ml, seealso 82Fl].

3:. . 40-6 cm3 e

IO *IO6 9 cm3 8

3.i

6 I ?? 5: 4

2.1

i

a

125

175

225 T-

215

325

375 K 425

Fig. 19. Cr-x at% V, x = 0, 0.58, 1.04, 1.52. Magnetic mass susceptibility xy a and its inverse b as a

Land&-Bsmstein New Series IIV32A

175

b

225 T-

215

function of temperatureT [81Kl].

325

375 K 425

14

1.1.1 Ti, V, Cr, Mn

[Ref. p. 28

Cr- x at %Ni

2.9

I 1

125

I 175

225

275

325

I 375 K 4

Fig. 20. Cr-x at% Ni, x = 0, 0.43, 1.5. Magnetic mass susceptibility ~a vs. temperatureT [81Kl].

15.0 kOe

70

kOe 60

12.5

2.5

0

a

50

100

150

200

250

300

K 350

l-

Fig. 21. a Cr doped with “‘Cd. Magnetic hyperfine field H,,,.r vs. temperature T as derived from nuclear resonance experiments. The broken curve shows the magnetisation of pure Cr, obtained by [67Wl] from neutron diffraction experiments, with data normalised to the value of HhYpat 128 K [8OVl].

b

l-

b Cr doped with ‘*‘Ta. Maximum hyperfine field of Ta nuclei, Hhyp,vs. temperature 7’. The inset is an enlargement for the critical temperature region Triangles represent (normalised) [78Tl]. magnetisation data as derived from neutron diffraction spectra[67W I].

Lmdolt-Bbmstein New Series llV32A

15

1.1.1. Ti, V, Cr, Mn

Ref. p. 281 0.35 (SKI-'

&IO2

, , I

1

0.30

0.25

t

I

’ c

0.20

L h 5 0.15

IO2 6 6 4 2

IO R " 4

0.10

t 0 IkOe -I

0.05 k.10-2E10-’ 2

4 6 81

2

I 6 810

2

4 6 ~10~ K 4.10'

T0

100

200

300

400

K 500

Fig. 22. Cr; Cr-2 at% V. Nuclear spin relaxation rate expressed as (T,T)-’ vs. temperature T for 53Cr at 15.0 MHz NMR in a magnetic field of 61.9 kOe. The solid curves are theoretical, the dashed line is the expected Korringa rate (T,,/T)-’ for 53Cr[83Kl].

Fig. 23. Cr, single crystal. Impurity content in at ppm: H = 50, C = 90, N < 20, Si = 18, Fe = 11, rest vs. Q in [ 11l] direction as obtained from polarised neutron scattering at several temperatures T abovethe Curie temperature Tc. The Q=O points were derived from the static susceptibility [86Bl].

0.005 0.010 0.015 0.020 0.025 0.030K20.035

9* -

P-

Fig. 55. %i. Spin wave energies tiw vs. square of wavevector length q at temperaturesjust below the Curie temperature Tc as derived from polarised neutron scattering experiments.. The corresponding spin wave stiffness constantsD are indicated [91Bl].

1.1.2.10 g factors and ferromagnetic resonance properties SeeLB III/19A, p. 85-90 Ferromagnetic antiresonance (FMAR) transmission experiments in Fe at 73 GHz confirmed the microscopic relaxation parameter(see eq. (I) in LB III/19A, p. 85) /z = 0.7.10* s-’ at room temperature, increasing to 1.4.10’ s-’ at 140 K [88Rl]. For the temperature range above room temperature see Fig. 56. From the linewidth of the ferromagnetic resonance absorption the n(7) curve of Fig. 57 is obtained. Similar curves for Co and Ni in Figs. 58 and 59.

Lsndolt-Btmsrein New Series 111132A

[Ref. p. 72

1.1.2 Fe, Co, Ni

64

5-

I

meV60Ni11111

0

0.2

0.4

0.6

0.8

1.0

1.2 x-’ 1.4

0

Fig. 54. ‘%i. Energy-integrated neutron scattering function <M’(Q)> vs. Q in [ 11l] direction as obtained from polarised neutron scattering at several temperatures T abovethe Curie temperature Tc. The Q=O points were derived from the static susceptibility [86Bl].

0.005 0.010 0.015 0.020 0.025 0.030K20.035

9* -

P-

Fig. 55. %i. Spin wave energies tiw vs. square of wavevector length q at temperaturesjust below the Curie temperature Tc as derived from polarised neutron scattering experiments.. The corresponding spin wave stiffness constantsD are indicated [91Bl].

1.1.2.10 g factors and ferromagnetic resonance properties SeeLB III/19A, p. 85-90 Ferromagnetic antiresonance (FMAR) transmission experiments in Fe at 73 GHz confirmed the microscopic relaxation parameter(see eq. (I) in LB III/19A, p. 85) /z = 0.7.10* s-’ at room temperature, increasing to 1.4.10’ s-’ at 140 K [88Rl]. For the temperature range above room temperature see Fig. 56. From the linewidth of the ferromagnetic resonance absorption the n(7) curve of Fig. 57 is obtained. Similar curves for Co and Ni in Figs. 58 and 59.

Lsndolt-Btmsrein New Series 111132A

Ref. p. 721

1.1.2 Fe, Co, Ni

I

-250

350

450

550

650

0

750 K 850

65

I

I

50

I

100

200

I

250 K 300

T-

.I -

Fig. 56. Fe. Landau-Lifshitz damping parameterR vs. temperature T as derived from FMAR transmission amplitudes at 72.43 GHz. The error bar (* 0.06.108 Hz) applies to all measuring points [91Cl].

I

150

Fig. 57. Fe. Relaxation parameter /z at 693 GHz resonancefrequency as a function of temperature T as derived from FR absorption experiments [90B 13.

2.5 *lo8

0

50

100

150

200

250

K 300

I!

\

2.

\

! l

0

50

100

150 T-

200

.

.

6810

2

11 1

01

q

250K 25K

250 K 300

Fig. 58. Co. Relaxation parameter /z at 763 GHz resonancefrequency as a function of temperature T as derived from FR absorption measurements[90Bl].

12

4

4

6 810’

2

6 GHz8103

f res -

Fig. 59. Ni. Relaxation parameter R at 250 K and 25 K vs. resonancefrequency f,,, as derived from FR absorption experiments. Inset: temperature dependence of il at various frequencies [90B 11.

Land&-BOrnstein New Series 111/32A

[Ref. p. 72

1.1.2 Fe, Co, Ni

66

1.1.2.11 Fermi surfaces, band structures, exchange energies and electron spin polarisations SeeLB III/l9A, p. 91-l 12 Many, more or less successful, attempts have been made to calculate by first-principle band theory methods the possible magnetic statesof the 3d metals in their various crystallographic configurations, see e.g. [85Hl, 86M1, 88M1, 89LI, 90K1, 90M1, 91P1,93211. A first study of the Fermi surface topology using two-dimensional angular correlation of polarised positron annihilation radiation is given in [88Gl]. For the results of an extended calculation of density of states and spin densities of hcp Co see [88Bl, 92S1,93Sl]. For the calculated densities of states of 3d substitutional impurities in Fe seeFig. 60. For s, p and 4d impurities see [85A2, 87221. For 3d and 4d impurities in Ni seeFigs. 61 and 62.

-iv

Mn in Fe

Cr in Fe

2-

-3-

I

spin -

I

L

$a&

spin +

spin 4

spin +

states3 Fe - 3d Vin Fe

spin -

3

eV

2

I

1

z .o

0

I

-1 -2 spin -

-3 1

I

-8

-6

I

,-4 f-ff-

I

I

I

-2

0

2 eV 4-8

I

I

I

-6

-4

f-ff-

Fig. 60. Fe with substitutional 3d impurities. Local density of electron states LDOS at the nucleus of the impurity as derived from a self-consistent spin-

I

1

I

-2

0

2 eV4. eV -8

I

I

I

I

-6

-4

-2 E-fF-

spin I

0

2 eV

polarised muffin-tin Green function method calculation [85A2].

Landolt-Bomsrein New Seria 111132A

Ref. p. 721

1.1.2 Fe, Co, Ni

g&2Ni-3d SCin Ni eV

spin +

67

spin +

spin+ V in Ni

Ti in Ni

2-

-2 -3 -

$l& eV

3-

2-

spin +

spin +

ti

Mn

3-

spin -

spin -

spin +

spin t

spin-

spin +

I

L

spin -

spin +

Cu in Ni

Ni in Ni

Co in Ni

I

Fe in Ni

-I

-3 -

2-

spin -

Cr in Ni

-2 -

9

spin -

ii

.

+

-2 -

I

spin -3 -8

-6

I -1,

I -2 E-E, -

0

2 eV 4 -8

I -6

I -4

Fig. 61. Ni with substitutional 3d impurities. Local density of electron states LDOS at the nucleus of the

Land&-BBmstein New Series IIV32A

I -2 0 E-E, -

I I 2 eV 4

-8

-6

-4

-2 E-E,

impurity. Cf. also Fig. 60 [8722].

0

-

spin I I 2 eV4

I

1.1.2 Fe, Co, Ni

68

3 stafes eV 2

spin t

spin t 2r in Ni

Nb in Ni

1

I

i2 “,

[Ref. p. 72

0 -1 -2

spin +

3go& eV

2-

spin -

spin -

-3

MOin Ni

spin t

I

spin -

I

spin t

lc in Ni

I

spin -

II

rninr

I I

spin -

spin t

I

Ag in Ni

spin -8

-6

-4

-2

0

2

eV4 -8

-6

-4

f-

Fig. 62. Ni with substitutional 4d impurities. Local density of electron states LDOS at the nucleus of the

-2

0

2 eVL

I -4

f-

impurity. Cf. also Fig. 60 [8722].

1.1.2.12 Optical constants, magneto-optic Kerr and Faraday effect SeeLB III/19A, p. 113-l 18

I -6

I -2

f-

0

I I 2 eV4

Ref. p. 721

1.1.2 Fe, Co, Ni

69

1.1.2.13 Specific heat, resistivity SeeLB 111/19A,p. 118-133 Specific heat Co In Fig. 63 the specific heat of Co is representedtogether with a proposed separation into contributions of various parts. The paramagnetic contribution is calculated with a Debye temperature O;, = 375 K and the electronic specific heat coefficient y= 2 .02.10m3 J mol-1K-2[79Bl]. Specific heat Ni New survey of specific heat data seeFigs. 64a, b and c. In [81M2] the various contributions to the heat capacity are given for the temperature range 0.. .1726 K. For the magnetic heat capacity seeFig. 65. Electrical resistivity of Fe and Ni High-pressure and high-temperature electrical resistivity of Fe and Ni in Figs. 66 and 67.

55 J

mol K 50 45

900

1100

1300 K 150

Fig. 63. Co. Specific heat C, vs. temperature7’. Paramagnetic ( Cr ) and magnetic( Cmag ) contributions to the experimentalheat capacity Crp. Inset: 201 300

500

700

900 T-

Landolt-BMnstein New Series IW32A

1100

1300 K 151 IO

excessheatcapacity CF vs. temperature.Solid line: experimental;dashedline: calculated[79Bl].

70

1.1.2 Fe, Co, Ni

250

a

300

350

400

450

500

311 600

550 K 600 b

3

[Ref. p. 72

I

I

I

I

610

620 T-

630

640

I K 650

42

molK 40

36

32 301 600 C

I 800 800

1000 1000 1200

I I 1400 1400 1600 K 1800

Fig. 64 a-c. Ni, polycrystalline. Specific heat C, vs. temperature T. (I) Set I: 99.89 wt% pure Ni with 800 ppm Fe, 150 ppm Si, 90 ppm Cr, 50 ppm Co as major impurities, using a pulse calorimetry method. (2) Set II: 99.95 wt% pure Ni with < 1000 ppm Co and ~100 ppm Cu, Fe, Si and Al, using adiabatic calorimetry. Measuring points (3) are earlier data from [36Bl, 36B2, 38S1, 66Vl, 55K1 gatheredby 81M2].

T-

Landoff-Barnstein New Series 111/32A

Ref. p. 721

1.1.2 Fe, Co, Ni

71

130 pQcm 110

t 90 of 70

0

200

400

600 l-

800

1000 1200 K 1400

Fig. 65. Ni, magnetic heat capacity CFag vs. temperature T as calculated from two different sources: solid curves [81M2], dashedcurves [56Hl].

30 550

650

750

850 T-

950

1050 1150 K 1250

Fig. 66. Fe, 99.999 wt% pure foil, Johnson Mathey, England. Electrical resistivity p vs. temperature T at two pressuresp [86Y2].

31 pCkli

Ni 25

2:

21 581 3

Fig. 67. Ni, 99.999 wt% pure foil, Johnson Mathey, England. Electrical resistivity p vs. temperature 7’ at three pressuresp [86Y2]. Tc: Curie temperature. 600

Landolt-BOrnstein New Series 111132A

620

640 T-

660

680 K 700

72

Referencesfor 1.1.2

1.1.2.14 References for 1.1.2 36B1 3682

Bronson, H.L., Wilson, A.J.C.: Can. J. Res.A 14 (1936) 181 Bronson, H.L., Hewson, E.W., Wilson, A.J.C.: Can. J. Res. A 14 (1936) 194

38S1

Sykes, C., Wilkinson, H.: Proc. Phys. Sot. (London) 50 (1938) 834

55Kl

Kraus, F., Warncke, H.: Z. Metallkd. 46 (1955) 61

56HI 56S1

Hofmann, J.A., Paskin, A., Tauar, K.J., Weiss, R.J.: J. Phys. Chem. Solids 1 (1956) 45 Shull, C.G., Wilkinson, M.K.: Phys. Rev. 97 (1956) 304

62K1

Koi, Y., Tsujimara, A., Hihara, T., Kushida, T.: J. Phys. Sot. Jpn. 17 Suppl. B-l (1962) 96

63Cl 63C2 63L1

Collins, M.F., Forsyth, J.B.: Philos. Mag. 8 (1963) 401 Collins, M.F., Wheeler, D.A.: Proc. Phys. Sot. 82 (1963) 633 Low, G.G.E., Collins, M.F.: J. Appl. Phys. 34 (1963) 1195

65C1 65Kl 65Vl

Collins, M.F., Low, G.G.E.: Proc. Phys. Sot. 86 (1965) 535 Kouvel, J.S., Hartelius, C.: J. Phys. Chem. Solids 25 (1965) 1357 Veerman, J., Rathenau,G.W.: Proc. Int. Conf. Magn. Nottingham (1965) 737

66Bl 6651 66Vl

Bhagat, S.M., Anderson, J.R., Hirst, J.J.: Phys. Rev. Lett. 16 (1966) 1099 James,D.W., Leak, G.M.: Philos. Mag. 14 (1966) 701 Vollmer, O., Kohlhaas, R., Braun, M.: Z. Naturforsch. A 21 (1966) 181

68Cl 68Hl

Comly, J.B., Holden, T.M., Low, G.G.: J. Phys. C 1 (1968) 458 Heumann, Th., Imm, R.: J. Phys. Chem. Solids 29 (1968) 1613

69Cl

Cable, J.W., Wollan, E.O., Child, H.R.: Phys. Rev. Lett. 22 (1969) 1256

7OCl

Cable, J.W., Child, H.R.: Phys. Rev. B 1 (1970) 3809

7lCl 71Fl

Cable, J.W., Child, H.R.: J. Phys. (Paris) Suppl. C 1 (1971) 67 Franse, J.J.M.: J. Phys. (Paris) 32 (1971) Cl-186

72Ll

Leger, J.M., Loriers-Susse,C., Vodar, H.: Phys. Rev. B 6 (1972) 4250

73Al 73Fl 7311

Aldred, A.T., Rainford, B.D., Hicks, T.J., Kouvel, J.S.: Phys. Rev. B 7 (1973) 218 Foy, M.L.G., Heiman, N., Kossler, W.J., Stronach, C.E.: Phys. Rev. Lett. 30 (1973) 1064 Ito, Y., Akimitsu, J.: J. Phys. Sot. Jpn. 35 (1973) 1000

74Bl 74Cl 74F 1 74F2 7411 74Pl

Brezin, E., Le Guillou, J.-C., Zinn-Justin, J.: Phys. Lett. A 47 (1974) 285 Cable, J.W., Child, H.R.: Phys. Rev. B 10 (1974) 4607 Fujiwara, H., Ohishi, K., Kadomatsu, H., Nomura, J.: J. Phys. Sot. Jpn. 36 (1974) 909 Fisher, M.E.: Rev. Mod. Phys. 46 (1974) 597 Ito, Y., Akimitsu, J.: J. Phys. Sot. Jpn. 36 (1974) 43 1 Patterson,B.D., Crowe, K.M., Gygax, F.N., Johnson, R.F., Portis, A.M.: Phys. Lett. A 46 (1974) 453

76Bl

Bervillier, C.: Phys. Rev. B 14 (1976) 4964 Land&-Bmwein New Series W32A

Referencesfor 1.1.2 76Cl 76G1 7662 7663

76Hl 76Ll 76Ml 76N 1 77Cl 77C2 77c3 77c4 77Kl 77K2 77Ll 77Nl 77N2, 77N3 77Wl 7811 78Ml 78M2 78Nl 78Sl 78Vl 78W1 79B1 79Hl 79H2 79Jl 79Kl 79Pl 79Rl 80Gl 80Kl

73

Cable, J.W., Medina, R.A.: Phys. Rev. B 13 (1976) 4868 Graf, H.: Phys. Rev. Lett. 37 (1976) 1644 Graf, H., Kiindig, W., Patterson,B.D., Reichart, W., Roggwiller, P., Camani, M., Gygax, F.N., Rtiegg, W., Schenck, A., Schilling, H., Meier, P.F.: Phys. Rev. Lett. 37 (1976) 1644 Gurevich, I.I., Klimov, AI., Maiorov, V.N., Melashko, E.A., Nikolskii, B.A., Selivanov, V.I., Suetin, V.A.: Zh. Eksp. Teor. Fiz. 69 (1975) 439; Sov. Phys. JETP 42 (1976) 222 (Engl. Transl.) Hamagaki, H., Nakai, K., Nojiri, Y., Tanihata, I., Sugimoto, K.: Hyperfine Interact. 2 (1976) 187 Livet, F., Radhakrishna, P.: Solid State Commun. 18 (1976) 33 1 Mm-nick, D.E., Hass, M., King, H.T., Ventura, E.: Hyperfine Interact. 1 (1976) 367 Nagamine, K., Nagamiya, S., Hashimoto, O., Nishida, N., Yamazaki, T., Patterson,B.D.: Hyperfine Interact. 1 (1976) 5 17 Callaway, J., Wang, C.S.: Phys. Rev. B 16 (1977) 2095 Camani, M., Gygax, F.N., Rtiegg, W., Schenck,A., Schilling, H.: Phys. Lett. A 60 (1977) 439 Cable, J.W.: Phys. Rev. B 15 (1977) 3477 Cable, J.W., Wollan, E.O.: Physica B 86-88 (1977) 745 Kollie, T.G.: Phys. Rev. B 16 (1977) 4872 Keus, H.E., Huiskamp, W.J.: Physica B 85 (1977) 139 Livet, F., Radhakrishna, P.: J. Phys. Chem. Solids 38 (1977) 275 Nishida, N., Hayano, R.S., Nagamine, K., Yamazaki, T., Brewer, J.H., Garner, D.M., Fleming, D.G., Takeuchi, T., Ishikawa, Y.: Solid StateCommun. 22 (1977) 235 Niesen, L., Kikkert, P.J., de Waard, H.: Hyperfine Interact. 3 (1977) 109 Nojiri, Y., Hamagaki, H., Sugimoto, K.: Phys. Lett. A 60 (1977) 77 Wakoh, S., Kubo, Y.: J. Magn. Magn. Mater. 5 (1977) 202 Ingalls, R., van der Woude, F., Sawatzky, G.A., in: Mbssbauer Isomer Shifts (Shenoy, G.K., Wagner, F.E., eds.), Amsterdam: North Holland Publ. Comp. (1978) p. 361 Madhav, R.L., Chakravarty, R., Jirak, Z., Satya Mm-thy, N.S.: Phys. Rev. B 18 (1978) 6275 Moruzzi, V.L., Janak, J.F., Williams, A.R.: Calculated Electronic Properties of Metals, New York: Pergamon Press(1978) Nojiri, Y., Hamagaki, H., Sugimoto, K.: Hyperfine Interact. 4 (1978) 465 Schenck, A.: Hyperfine Interact. 4 (1978) 282 Viilkl, J., Alefeld, A.: Topics in Applied Physics: Hydrogen in Metals I, Berlin: Springer 28 (1978) 329 Witt, H.P., Niesen, L., de Waard, H.: Hyperfine Interact. 5 (1978) 233 Bendick, W., Pepperhoff, W.: J. Phys. F 9 (1979) 2185 Hamagaki, H., Nojiri, Y., Sugimoto, K., Nakai, K.: J. Phys. Sot. Jpn. 47 (1979) 1806 Hearmon, R.F.S., in: Landolt-Bbrnstein, New Series,Vol. III/II, (Hellwege, K.-H., ed.), Berlin, Heidelberg, New York: Springer (1979) p. 100 Janak, J.F.: Phys. Rev. B 5 (1979) 2206 Kajzar, F., Parette, G.: Phys. Rev. B 20 (1979) 2002 Parette, G., Kajzar, F.: J. Phys. F 9 (1979) 1867 Rao, G.N.: Hyperfine Interact. 7 (1979) 141 Graf, H., Balzer, G., Recknagel, E., Weidinger, A., Grynszpan, R.I.: Phys. Rev. Lett. 44 (1980) 1333 Kajzar, F., Parette,G.: J. Magn. Magn. Mater. 17-19 (1980) 87

Land&-Biirnstein New Series IIY32A

74 81Cl 81Kl 8lK2 8lK3 81Ml 8lM2 81Rl 81Yl 8lY2

Referencesfor 1.1.2 Chakravarty, R., Madhav, R.L.: J. Phys. F 11 (1981) 2071 Kopp, M., Klein, E.: Hyperfine Interact. 11 (1981) 153 Kopp, M., Kazami-Far, B., Klein, E.: Z. Phys. B 44 (1981) 73 Kobeissi, M.A.: Phys. Rev. B 24 (1981) 2380 Minamisono, T., Nojiri, Y.: Hyperfine Interact. 9 (1981) 437 Meschter, P.J., Wright, J.W., Brooks, C.R.: J. Phys. Chem. Solids 42 (1981) 861 Riedi, P.C., Webber, G.D.: J. Phys. F 11 (1981) 1669 Yaouanc, A., Chappert, J., Hartmann, O., Norlin, L.O., Karlsson, E.: Hyperfine Interact. 8 (1981) 667 Yagi, E., Bossy, H., Daring, K.P., Gladisch, M., Herlach, D., Matsui, H., Orth, H., Putlitz, G. zu, Seeger,A., Vetter, J.: Hyperflne Interact. 8 (1981) 553

82Kl 82Wl

Keus, H.E., Huiskamp, W.J.: Physica B 114 (1982) 269 Webber, G.D., Riedi, P.C.: J. Phys. F 12 (1982) 2047

83Kl 83K2 83K3 83Ml

Krane, K.S.: Hypertine Interact. 15-16 (1983) 1069 Kasamatsu,Y., Hihara, T., Kojima, K., Kamigaichi, T.: J. Phys. Sot. Jpn. 52 (1983) 263 Klein, E.: Hyperfine Interact. 16 (1983) 557 Mbslang, A., Graf, H., Balzer, G., Recknagel, E., Weidinger, A., Wicker-t,Th.: Phys. Rev. B 27 (1983) 2674 Rennert, P., Carl, G., Hergert, W.: Phys. StatusSolidi (b) 120 (1983) 273 Rijswijk, W. van, Berg, F.G. van den, Joosten,W.R., Huiskamp, W.J.: Abstracts 6th Int. Conf. Hyperfine Interact., Groningen (1983) H14

83Rl 83R2 84Al 84A2 84B 1 84Yl

Ackermann, B., Feder, R., Tamura, E.: J. Phys. F 14 (1984) L173 Akai, H., Akai, M., Bltigel, S., Zeller, R., Dederichs, P.H.: J. Magn. Magn. Mater. 45 (1984) 291 Boysen, J., Brewer, W.D., But-es,K.D., Kettschau, A., Klein, E., Kopp, M., Wilson, G.V.H.: J. Magn. Magn. Mater. 43 (1984) 267 Yagi, E., Flik, G., Ftirderer, K., Haas,N., Herlach, D., Major, J., Seeger,A., Jacobs,W., Krause, M., Krauth, M., Mundinger, H.-J., Orth, H.: Phys. Rev. B 30 (1984) 441

85Al 85A2 85Dl 85Hl 85Ml 85Wl

Akai, M., Akai, H., Kanamori, J.:‘J. Phys. Sot. Jpn. 54 (1985) 4246 Akai, H., Akai, M., Kanamori, J.: J. Phys. Sot. Jpn. 54 (1985) 4257 Dederichs, P.H., Zeller, R., Akai, H., BlUgel, S., Oswald, A.: Philos. Mag. B 51 (1985) 137 Hathaway, K.B., Jansen,H.J.F., Freeman,A.J.: Phys. Rev. B 31 (1985) 7603 Martinez, J.L., Biini, P., Shirane, G.: Phys. Rev. B 32 (1985) 7037 Wang, C.S., Klein, B.M., Krakauer, H.: Phys. Rev. Lett. 54 (1985) 1852

86Al 86Bl

Akai, H., Bltigel, S., Zeller, R., Dederichs, P.H.: Phys. Rev. Lett. 56 (1986) 2407 Brown, P.J., Capellman, H., Deportes,J., Givord, D., Johnson, S.M., Ziebeck, K.R.A.: J. Phys. (Paris) 47 (1986) 49 1 Cooper, M.J., Laundy, D., Cardwell, D.A., Timms, D.N., Holt, R.S.: Phys. Rev. B 34 (1986) 5984 Kasamatsu,Y., Hihara, T., Kojima, K., Kamigaichi, T.: J. Magn. Magn. Mater. 54-57 (1986) 1107 Kellner, W.-U., Albrecht, T., Flhnle, M., Kronmtiller, H.: J. Magn. Magn. Mater. 62 (1986) 169 Moruzzi, V.L., Marcus, P.M., Schwarz, K., Mohn, P.: Phys. Rev. B 34 (1986) 1784 Mook, H.A., Lynn, J.W.: Phys. Rev. Lett. 57 (1986) 151 Stiisser, N., Rekveldt, M.Th., Spruijt, T.: Phys. Rev. B 33 (1986) 6423

86C 1 86Kl 86K2 86Ml 86M2 86Sl

Referencesfor 1.1.2 86Wl 86Yl 86Y2 87Al 87Bl 87B2 87Ml 87M2 87Rl 87Sl 8782 87Tl 8721 8722 88Al 88Bl 88El 88F1 88Gl 88Hl 8851 88L1 88Ml 88M2 8801 88Pl 88Rl 88Sl 88Tl 88T2 89Cl 89Dl 89Ll 89Ml 8901 8902 89Sl 89T1

75

Whittle, G.L., Campbell, S.J., Calka, A.: Hyperfine Interact. 28 (1986) 993 Yousuf, M., Sahu, P.Ch., Jajoo, H.K., Rajagopalan, S., Govinda Rajan, K.: J. Phys. F 16 (1986) 373 Yousuf, M., Sahu, P.C., Govinda Rajan, K.: Phys. Rev. B 34 (1986) 8086 Akai, M., Akai, H., Kanamori, J.: J. Phys. Sot. Jpn. 56 (1987) 1064 Budzynski, M., Simecek, P., Lesner, T., Gizek, P., Prochazka,I., Simeckova, E., TsupkoSitnikov, V.M., Ehn, L., Janout, Z.: Hyperfine Interact. 34 (1987) 3 15 Bltigel, S., Akai, H., Zeller, R., Dederichs, P.H.: Bhys. Rev. B 35 (1987) 3271 Mills, D.: Phys. Rev. B 36 (1987) 6178 Minamisono, T., Nojiri, Y., Matsuta, K., Iwayama, T., Fujinaga, M.: Hyperflne Interact. 34 (1987) 299 Riedi, P.C., Dumelow, T., Rubinstein, M., Prinz, G.A., Qadri, S.B.: Phys. Rev. B 36 (1987) 4595 Sakai, N., Sekizawa, H.: Phys. Rev. B 36 (1987) 2164 Shirane, G., Boni, P., Martinez, J.L.: Phys. Rev. B 36 (1987) 88 1 Tsunoda, Y., Kunitomi, N., Nicklow, R.M.: J. Phys. F 17 (1987) 2447 Zarestky, J., Stassis,C.: Phys. Rev. B 35 (1987) 4500 Zeller, R.: J. Phys. F 17 (1987) 2123 Akai, H.: Hyperfine Interact. 43 (1988) 255 Blaha, P:, Schwarz, K., Dederichs,,P.H.: Phys. Rev. B 38 (1988) 9368 Ebert, H., Strange, P., Gyorffy, B.L.: J. Phys. F 18 (1988) L135 Faisst, T.: J. Phys. (Paris) Colloq. Suppl. C 8 (1988) 65 Genoud, P., Singh, A.K., Manuel, A.A., Jarlborg, T., Walker, E., Peter, M., Weller, M.: J. Phys. F 18 (1988) 1933 Heiming, A., Steinmetz, K.H., Vogl, G., Yoshida, Y.: J. Phys. F 18 (1988) 1491 Jansen,H.J.F., Peng, S.S.: Phys. Rev. B 37 (1988) 2689 Lindgren, B., Sjbstriim, J.: J. Phys. F 18 (1988) 1563 Moruzzi, V.L., Marcus, P.M.: J. Appl. Phys. 64 (1988) 5598 Mook, H.A., Paul, D.M., Hayden, S.: Phys. Rev. B 38 (1988) 12058 Ono, F., Maeta, H.: J. Phys. (Paris) C8 Suppl. 49 (1988) 63 Paul, D.McKenzie, Mitchell, P.W., Mook, H.A., Steigenberger,U.: Phys. Rev. B 38 (1988) 580 Rudd, J.M., Cochran, J.F., Urquhart, K.B., Myrtle, K., Heinrich, B.: J. Appl. Phys. 63 (1988) 3811 Sundararajan,V., Asokamani, R., Kanhere, D.G.: Phys. Rev. B 38 (1988) 12653 Tsunoda, Y., Kunitomi, N.: J. Phys. F 18 (1988) 1405 Timms, D.N., Brahmia, A., Collins, P., Collins, S.P., Cooper, M.J., Holt, R.S., Kane, P.P., Clark, G., Laundy, D.: J. Phys. F 18 (1988) L57 Collins, S.P., Cooper, M.J., Timms, D., Brahmia, A., Laundy, D., Kane, P.P.: J. Phys. Condens. Matter 1 (1989) 9009 Drittler, B., Stefanou,N., Bltigel, S., Zeller, R., Dederichs, P.H.: Phys. Rev. B 40 (1989) 8203 Liu, F., Press,M.R., Khanna, S.N., Jena,P.: Phys. Rev. B 39 (1989) 6914 Moruzzi, V.L., Marcus, P.M., Ktibler, J.: Phys. Rev. B 39 (1989) 6957 Ono, F.: Physica B 161 (1989) 129 Ono, F., Maeta, H.: Physica B 161 (1989) 134 Svare, I.: Phys. Rev. B 40 (1989) 8641 Tsunoda, Y.: J. Phys. Sot. Jpn. 58 (1989) 1648

Landolt-BOrnstein New Series 111/32A

76

Referencesfor 1.1.2

89T2

Tsunoda, Y.: J. Phys. Condens.Matter 1 (1989) 10427

90Al

Akai, H., Akai, M., Bliigel, S., Drittler, B., Ebert, H., Terakura, K., Zeller, R., Dederichs, P.H.: Prog. Theor. Phys. Suppl. 101 (1990) 11 Bargen, N. von, Boehler, R.: High PressureRes. 6 (1990) 133 Dederichs, P.H., Drittler, B., Zeller, R., Ebert, H., Weinert, W.: Hypertine Interact. 60 (1990) 547 Daalderop, G.H.O., Kelly, P.J., Schuurmans,M.F.H.: Phys. Rev. B 41 (1990) 11919 Ebert, H., Zeller, R., Drittler, B., Dederichs, P.H.: J. Appl. Phys. 67 (1990) 4576 Eriksson, O., Johansson,B., Albers, R.C., Boring, A.M., Brooks, M.S.S.: Phys. Rev. B 42 (1990) 2707 Krasko, G.L., Olson, G.B.: J. Appl. Phys. 67 (1990) 4570 Moruzzi, V.L., Marcus, P.M.: Phys. Rev. B 42 (1990) 8361 Timms, D.N., Brahmia, A., Cooper, M.J., Collins, S.P., Hamouda, S., Laundy, D., Kilboume, C., Saint-Lager, M-C.: J. Phys. Condens.Matter 2 (1990) 3427

90Bl 90D1 90D2 90E1 90E2 90K1 90M1 90T1 91Bl 91Cl 91D1 91Ml 91P1 91P2 91P3 91P4 91Rl 91s1 91T1 92B1

Bbni, P., Martinez, J.L., Tranquada, J.M.: Phys. Rev. B .43(1991) 575 Cochran, J.F., Rudd, J.M., Muir, W.B., Trayling, G., Heinrich, B.: J. Appl. Phys. 70 (1991) 6545 Dederichs, P.H., Zeller, R., Akai, H., Ebert, H.: J. Magn. Magn. Mater. 100 (1991) 241 Mryasov, O.N., Liechtenstein, A.I., Sandratskii, L.M., Gubanov, V.A.: J. Phys. Condens. Matter 3 (1991) 7683 Peng, S.S., Jansen,H.J.F.: Phys. Rev. B 43 (1991) 3518 Podgorny, M., Goniakowski, J.: Nuovo Cimento 13 (1991) 311 Peng, S.S., Jansen,H.J.F.: J. Appl. Phys. 69 (1991) 6132 Pet-ring,T.G., Boothroyd, A.T., Paul, D.M., Taylor, A.D., Osbom, R., Newport, R.J., Blackman, J.A., Mook, H.A.: J. Appl. Phys. 69 (1991) 6219 Ruuskanen, P., Kettunen, P.: J. Magn. Magn. Mater. 98 (1991) 349 Sundararajan,V., Kanhere, D.G., Singru, R.M.: J. Phys. Condens.Matter 3 (1991) 1113 Taylor, R.D., Pasternak,M.P., Jeanloz, R.: J. Appl. Phys. 69 (1991) 6126

9282 92H 1 92Sl

Brown, P.J., Deportes, J., Neumann, K.-U., Ziebeck, K.R.A.: J. Magn. Magn. Mater. 104107 (1992) 2083 Brookas, N.B., Clarke, A., Johnson,P.D.: Phys. Rev. B 46 (1992) 237 Hirai, K.: J. Magn. Magn. Mater. 104-107 (1992) 749 Singh, D.J.: Phys. Rev. B 45 (1992) 2258

93Bl 93H1 93s1 9321

Barradas,N.P., Rots, M., Melo, A.A., Soares,J.C.: Phys. Rev. B 47 (1993) 8763 Haglund, J.: Phys. Rev. B 47 (1993) 566 Sandratskii, L.M., Kiibler, J.: Phys. Rev. B 47 (1993) 5854 Zhong, W., Ovemey, G., Tombnek, D.: Phys. Rev. B 47 (1993) 95

Land&-Barnstein New Series IW32A

Ref. p. 1131

1.2.1 Alloys between Fe, Co or Ni

77

1.2 Alloys between 3d elements 1.2.1 Alloys between Fe, Co or Ni This is a supplement to Landolt-Bornstein, New Series,Volume 111/19A(1986) p. 142-281. Survey Property

Phasediagrams, lattice parameters Paramagnetism Spontaneousmagnetisation Miissbauer data Muons Spin waves Magnetic moments High-field magnetic susceptibility ‘) Magnetocrystalline anisotropy Magnetostriction Density of states Elastic, magnetoelastic constants Thermal expansion Specific heat Electrical resistivity, magnetoresistance

Fe-Co

Fe-Ni

Co-Ni

Fig.

Fig.

Fig.

1

2, 3 4 5-7

839

10-14 15 16-18

20-23

19 22

24-3 1 32

40

33-36 41-44 45-5 1

37-39 52,53

54-56 57 58-60

61;62

‘) SeealsoTables1 and2. 1.2.1.1 Phase diagrams, lattice parameters Fe-Co system Short range local atomic order parametersin dilute FeCo alloys at temperaturesaround T, have been derived from zero-field NMR data at 59Conuclei [83P2]. Ferromagnetically induced chemical ordering in Fe,,,O-xCoX alloys as a consequenceof the effect of ferromagnetism on the electronic band structure of the alloy components is treated in [88H2]. A more phenomenological approach for the ordering, including chemical and magnetic interactions, is given in [85M4], and is in good agreement with observations in the range 30 < x < 70. For the short-range order parametersof dilute FeCo alloys see Fig. 1 and [85Pl]. Kinetics of short-range and long-range ordering for the equiatomic compound FeCo have been investigated by Mossbauer spectroscopy[91F2].

Landolt-Bornstein New Series II1132A

1.2.1 Alloys between Fe, Co or Ni

78

[Ref. p. 113

Fe-Ni system

The martensitic transformation in Fe-Ni alloys in the region of 30 at% Ni has recently been studied by X-ray absorption fine structure (XAFS) measurements.Already above the martensitic transformation temperature a certain volume fraction of local bee structure can be detected. The temperature where this change in the alloy starts is higher around the Fe atom than around the Ni atom [90Fl], see also [86Rl]. Mean-square atomic displacements derived from X-ray diffraction measurementson a 30.5 at% Ni-Fe single crystal alloy show a decreaseas the sample temperature increases to the martensitic transition temperature of 198.3 K [85Cl]. This is in contrast to reported increases derived from MSssbauerspectroscopy [7lYl, 80El]. Since some kind of directional chemical order is also found in Ni-Fe alloys when cooled through their Curie point in the presenceof a magnetic field, it may be expectedthat concentration fluctuations in the distribution of the various atoms of the alloy are related to magnetic order. A first-principles electron theory of concentration fluctuations applied to these alloys is given in [87Sl, 89Al]. For the influence of external pressure on the lattice parametersof Fe,OO-xNix alloys see Fig. 2 and for the influence of electron radiation Fig. 3. O-4-2

--. L Feloo-xCox ----

x =20 .-

- 0.2

- 0.1 neutron

I

I-

- 0.6

Fig. 2. Fe,,Ni,,, feeandbeecrystalstructure.Relative change of the lattice constant a under applied pressure p at 295 K. a, is the lattice constant at atmospheric pressure[88Hl]. 7,/r -

Fe,oo-xCo,y x = 2, 20, annealed until equilibrium is attained and quenched to room temperature. Short-range order parameter (SRO) Z,* Ix vs. relative reciprocaltemperatureTcIT where Tc is the Curie temperature,i& = @al+6q)/14

Fig. 1.

with ai the SRO parameters in the Cowley sense. Measured either b> neutron diffuse scattering experiment or by NMR [86 PI].

Landoh-Bbmrlein New Series 111132A

Ref. p. 1131

1.2.1 Alloys between Fe, Co or Ni

79

Fig. 3. FeloO,Ni,, Invar-type alloys. Roomtemperature lattice parameter a vs. composition as dependenton 2 MeV electron radiation intensity I and irradiation temperature T [84Ml].

1 2 3 4

.I 02 A.3 A4 v5 r6

25

30

35

x-

45

40

5 6

T

I

WI

[electron cmM2]

470 520 353 523 673 -

4.10’” 3.4.1020 4.1019 4.1019 4.1019

annealed

Ref.

84Ml 84Ml 79c1

79Cl 79Cl 79Cl

50

1.2.1.2 Paramagnetic properties Fe-Ni system Paramagnetic spin fluctuations in Fe,,Ni,, Invar-type alloy, see Fig. 4. For disordered crystalline Fe,,Ni,, the asymptotical critical exponent p= 0.37 [86Kl]. 100 &

T=1.257,

wi35

80

I

I'\ .-

60

/\ 2 s ” 40

i

Fig.b. Fe,,Ni,,, single crystal. The amplitude <M2(q) > of the spin fluctuations obtained at T= 1.25 T, by integration of the scattering function S(q,u), where the wavevector q and frequency w are related to the transfers of linear momentum and energy, respectively, of the polarized neutrons in the neutron scattering experiment. Scans along [l 1l] and [IOO] crystallographic directions, for which the qvalues at the Brillouin-zone boundary are 1.52 A-’ and 1.75 A-‘-], respectively. The dot-dash line represents ideal paramagnetic scattering with

\ .' \ $

, 0 [I111

'0.

l

\O

\

20

\

l\

. lo -.*

-.-.-.--.-:1.

0

0.2

P2eff O-Ti,

0.4

[IO01

0.6

W--

. -a

0.8 A-'

peff= 3.3 pB [87Tl]. 1.0

1.2.1.3 Magnetic phase diagram, spontaneous magnetisation Fe-Ni system The temperature dependence of the low field dc [89Rl, 89R2, 90Rl] and ac magnetisation curves [85M2, 86M2, 86M3] show a rather complicated behaviour in the range 4.2...250 K. From the latter Miyazaki et al. [85M2] derived the magnetic phase diagram of Fig. 5a, which differs in details from Landolt-Barnstein New Series 111132A

Ref. p. 1131

1.2.1 Alloys between Fe, Co or Ni

79

Fig. 3. FeloO,Ni,, Invar-type alloys. Roomtemperature lattice parameter a vs. composition as dependenton 2 MeV electron radiation intensity I and irradiation temperature T [84Ml].

1 2 3 4

.I 02 A.3 A4 v5 r6

25

30

35

x-

45

40

5 6

T

I

WI

[electron cmM2]

470 520 353 523 673 -

4.10’” 3.4.1020 4.1019 4.1019 4.1019

annealed

Ref.

84Ml 84Ml 79c1

79Cl 79Cl 79Cl

50

1.2.1.2 Paramagnetic properties Fe-Ni system Paramagnetic spin fluctuations in Fe,,Ni,, Invar-type alloy, see Fig. 4. For disordered crystalline Fe,,Ni,, the asymptotical critical exponent p= 0.37 [86Kl]. 100 &

T=1.257,

wi35

80

I

I'\ .-

60

/\ 2 s ” 40

i

Fig.b. Fe,,Ni,,, single crystal. The amplitude <M2(q) > of the spin fluctuations obtained at T= 1.25 T, by integration of the scattering function S(q,u), where the wavevector q and frequency w are related to the transfers of linear momentum and energy, respectively, of the polarized neutrons in the neutron scattering experiment. Scans along [l 1l] and [IOO] crystallographic directions, for which the qvalues at the Brillouin-zone boundary are 1.52 A-’ and 1.75 A-‘-], respectively. The dot-dash line represents ideal paramagnetic scattering with

\ .' \ $

, 0 [I111

'0.

l

\O

\

20

\

l\

. lo -.*

-.-.-.--.-:1.

0

0.2

P2eff O-Ti,

0.4

[IO01

0.6

W--

. -a

0.8 A-'

peff= 3.3 pB [87Tl]. 1.0

1.2.1.3 Magnetic phase diagram, spontaneous magnetisation Fe-Ni system The temperature dependence of the low field dc [89Rl, 89R2, 90Rl] and ac magnetisation curves [85M2, 86M2, 86M3] show a rather complicated behaviour in the range 4.2...250 K. From the latter Miyazaki et al. [85M2] derived the magnetic phase diagram of Fig. 5a, which differs in details from Landolt-Barnstein New Series 111132A

80

1.2.1 Alloys between Fe, Co or Ni

[Ref. p. 113

Menshikov’s [89M4] in Fig. Sb. The origin of the anomalies has been related to the coexistence of ferro- and antiferromagnetic like regions as a consequenceof statistical compositional fluctuations in the alloy, which opens the possibility of thermally activation of pinned domain walls.The ground magnetic state of Fe,,Ni,, below about 20 K is a noncollinear FM state, also called asperomagnetic [90Tl]. For a calculation of the role of spin and phonon fluctuations on the temperature dependenceof the spontaneous magnetisation of Fe-Ni Invar-type alloys, see [91S2]. The influence of externally applied pressure and of electron irradiation on the spontaneousmagnetisation, is shown in the Figs. 6 and 7, respectively. 1000 K 800

600 111 F

I

600 200

k 500

b

a Fe

-. x-

_ 4 0 -LF-0 Fe

40

x-

60

80

100

Ni

-.

Fig. 5. Fe,,,_,Ni,. Magnetic phase’ diagram. a Ferromagnetic Curie temperatures F and I&J of the a and y phase, respectively. SG denotes the proposed spin-glass phase. Neel points and transition

temperatures TB are indicated [85M2]. b Magnetic phase diagram as suggested by [89M3] and based upon the experimental points of [63CJ] (circles), [64B l] (downward triangles) and [69Al] (triangles).

Landolt-Btmstein New Series llV32A

Ref. p. 1131

1.2.1 Alloys between Fe, Co or Ni

81

I.45 kG 1.40

1.35 I P 1.30

1.25

1.20

0

2

4

6

8 kbar

IO

LJ-'

Fig. 6. Fe,,,,Ni,,,,, annealed polycrystalline sample. Influence of externally applied pressure p on the spontaneous magnetisation M, at two temperatures T and the magnetisation A& in a magnetic field of 40 kOe [9001].

T-

Fig. 7. Fe,,,,,-XNi,.Spontaneousmassmagnetisation o, vs. temperature T. Solid curves after irradiation at 470 K with 4.10” electrons cm-* and dashed curves after subsequentannealing at 1000K [84Ml].

1.2.1.4 Hyperfine magnetic fields. Isomer shift, muons Fe-Co system Hyperfine fields in.bcc Fel,,O-x Co, alloys seeFig. 8. Spin-echo spectraseeFigs. 9a, b.

Fe-Ni system For “Fe isomer shift in the paramagneticregion of Fe,,,-,Ni, Invar-type alloys, seeFig. 10; Mijssbauer spectra and hypertine field distribution histograms Figs.lla, b; the influence of pressure on the Mbssbauer spectra Figs. 12a, b. “Fe Mijssbauer spectroscopy with polarized radiation gives information on the hyperfine field vectors, seeFig. 13. Components of the Mijssbauer spectra due to iron on nickel and nickel on iron sites in FeNi, have been identified, see Fig. 14. It was found that when an iron atom on an iron site has a first-neighbour iron atom, the magnitude of its hyperfine field increasesby 7 kOe. When such an atom has only five second-neighbour iron atoms instead of six, its hyperfine field increasesby 12 kOe [87Cl] in contrast to the usually accepted values of 11 and - 2.5 kOe, respectively [77Dl, 85121. For properties of muons in fee Fe,,Ni,, Invar and Fe,,,Ni,, non-Invar alloys seeFigs. 15a,b.

Landolt-Bhrnstein New Series IW32A

Ref. p. 1131

1.2.1 Alloys between Fe, Co or Ni

81

I.45 kG 1.40

1.35 I P 1.30

1.25

1.20

0

2

4

6

8 kbar

IO

LJ-'

Fig. 6. Fe,,,,Ni,,,,, annealed polycrystalline sample. Influence of externally applied pressure p on the spontaneous magnetisation M, at two temperatures T and the magnetisation A& in a magnetic field of 40 kOe [9001].

T-

Fig. 7. Fe,,,,,-XNi,.Spontaneousmassmagnetisation o, vs. temperature T. Solid curves after irradiation at 470 K with 4.10” electrons cm-* and dashed curves after subsequentannealing at 1000K [84Ml].

1.2.1.4 Hyperfine magnetic fields. Isomer shift, muons Fe-Co system Hyperfine fields in.bcc Fel,,O-x Co, alloys seeFig. 8. Spin-echo spectraseeFigs. 9a, b.

Fe-Ni system For “Fe isomer shift in the paramagneticregion of Fe,,,-,Ni, Invar-type alloys, seeFig. 10; Mijssbauer spectra and hypertine field distribution histograms Figs.lla, b; the influence of pressure on the Mbssbauer spectra Figs. 12a, b. “Fe Mijssbauer spectroscopy with polarized radiation gives information on the hyperfine field vectors, seeFig. 13. Components of the Mijssbauer spectra due to iron on nickel and nickel on iron sites in FeNi, have been identified, see Fig. 14. It was found that when an iron atom on an iron site has a first-neighbour iron atom, the magnitude of its hyperfine field increasesby 7 kOe. When such an atom has only five second-neighbour iron atoms instead of six, its hyperfine field increasesby 12 kOe [87Cl] in contrast to the usually accepted values of 11 and - 2.5 kOe, respectively [77Dl, 85121. For properties of muons in fee Fe,,Ni,, Invar and Fe,,,Ni,, non-Invar alloys seeFigs. 15a,b.

Landolt-Bhrnstein New Series IW32A

82

[Ref. p. 113

1.2.1 Alloys between Fe, Co or Ni

0

a

20

60

40

Fe

x-

80

100 co b

Fig. 8. Fen,&o, alloys. Magnetic hyperfine fields for a Fe and b Co atoms. Experimental for Fe: (I) [63J I]; (2) disordered, T= 77 K [89HI 1; (3) ordered, T= 77 K [89Hl]; experimental for Co: (I) [59Al]; (2) disordered [76M3]; (3) ordered [76M3]. The theoretical curves calculated by means of the charge

0 Fe

20

60

40 x-

80

100 co

self-consistent Korringa-Kohn-Rostoker coherent potehtial approximation (KKR-CPA). (4) denotes the core hyperfine field and (5) the total nonrelativistic hyperfine field. The total relativistic hyperfine fields are given by the dashed-pointedcurve [90El].

0

mm T - 0.1

I u c

mm -s-

-0.1

-0.51 400

Fig. 10. Fe,,Ni,,, Fe,,Ni,,, fee disordered Invar-type alloys. 57Feisomer shift IS vs. temperature T in the paramagneticstate. The curves are drawn according to a model calculation. IS relative to a-Fe source at 300 K [84Wl].

500

600

T-

700

800

900 K 1000

1.2.1 Alloys between Fe, Co or Ni

Ref. p. 1131

83

Fe- x at % Co

330

335

340

345

I

I

I

45

46

47

a

H-

350 I

48

355

360kOe365

I 49 MHz

I 50

I

Y-

I I 170 275 I 270. 275 L

b

Fig. 9. Fe-x at% Co. Spin-echo NMR spectra of 57Fe and 5gCo at 4.2 K in zero external magnetic field. Open circles: experimental data. Curves calculated

Land&-Bbmstein New Series IIV32A

280 I 280

28% I 285

I 290

l-f-

0 I 295

I 300

I

J

305MHz310

according to various models. a for “Fe, b for 5gCo [71Sl].

84

1.2.1 Alloys between Fe, Co or Ni

[Ref. p. 113

57Fe

150 200 Hhyp -

I -8

I

I

I

I

I

I

I

-6

-‘+

-2

0

2

4

6 mm/s 10

250

300kOe350

I

Fig. 11. Fe,,Ni,,. fee disordered Invar-type alloy. a

“Fe MLissbauer spectra at various temperatures.

Curves fitted from the hyperfine field distribution histograms of b [84Sl, seealso 83M2].

Landolt-Barnstein New Series 111/3?A

1.2.1 Alloys between Fe, Co or Ni

Ref. p. 1131

p=o

\

4.1 GPO

7.0GPa

. p released

I

-8.3

p released

I

I

I

I

-6

-3

0

3

a

c

6 mm/s 8.3

V--c-

Fig. 12. Fe,,Ni,,, fee disordered Invar-type ‘alloy. Influence of increasing and releasing pressurep on a

Landalt-BOrnstein New Series IW32A

100 b

200 H hyp-

300

kOe

4 I

the 57Fe Mijssbauer spectra at 4.2 K and b the hyperfine field distribution [88Al, 89A2].

86

1.2.1 Alloys between Fe, Co or Ni 601

I

I

I

I

FeNi,

I

Fe64Ni36

[Ref. p. 113

,,

50 CO

5UI

I

I

I

I

I

1

Fe68Ni3Z 1-t

40 t I

A I

I

I 3OFY I,

!’

:.

I ‘r- \ ‘:O” K , \

280

b

290

300

H-hyp

‘310

320 kOe330

Fig. 14. FeNi,, ordered single crystal. Distribution of the hyperfine magnetic fields derived from “Fe Mossbauer spectra according to two different models, a [77Dl, 77D2] and b [87Cl], respectively. The symbols (i, j) denote an Fe atom with i first-neighbour Fe atoms andj second-neighbour Fe atoms, similar for the Ni atoms.

Fig. 13. Fe,,,,Ni,, fee disordered Invar-type alloys. Hypertine field distributions at two temperatures derived from Mossbauer spectra for polarized yradiation, giving information on the component of the hyperfine field vector in the direction of the quantization axis. The total intensities of the distributions are normalized to the samevalue [84Ul].

Landolt43amstein New Series llV32A

Ref. p. 1131

87

1.2.1 Alloys between Fe, Co or Ni

. .

A

1 MHf 2- A # 7

t I b

0.12 I

0.08

0.08

I -ilo. -* ‘.” -

0.12

Tc AAAl

t

---,

0

0

0”

0.04 0

5 0650

700

a

750 T-

800

850 K 90:

Fig. 15. a Non-Invar Fe,,Ni,,; b Invar Fe,,Ni,,. Temperature dependknce of zero-field positive r&on pSR relaxation rate q’ above Curie temperature rc, the muon spin precession frequency w,/2n below Tc

350

b

400

450

T-

500

550 K 600

and the initial asymmetry ratio CI, of the positron count between forward and backward direction [89Ml].

1.2.1.5 Spin wave properties Fe-Ni system For Fe,,Ni,, neutron scattering experiments al 4 K result in a spin wave stiffness constant D = 58 + 2 THz A’, if the spin wave energy’is expressedas E=Eo+Dq2+Eq4,

(1)

with E, = 0.094 + 0.007 THz and E r 433 + 41 THz A4 [92Hl] . The spin wave stiffness constant D of Fe,,,-,Ni, Invar-type alloys and its temperature dependenceaccording to D=D,(l-D,

T’),

(2)

as derived from magnetisation curves are given in Table 1and Figs. 16-18. Calculations of D on the basis of a coherent potential approach [88Ml] and on its relation with the band structure parameters[85El]. Co-Ni system D(x) for Co,OO-xNix at 4.2 K and 293 K: Fig. 19.

Land&-Bihstein New Series 111/32A

Ref. p. 1131

87

1.2.1 Alloys between Fe, Co or Ni

. .

A

1 MHf 2- A # 7

t I b

0.12 I

0.08

0.08

I -ilo. -* ‘.” -

0.12

Tc AAAl

t

---,

0

0

0”

0.04 0

5 0650

700

a

750 T-

800

850 K 90:

Fig. 15. a Non-Invar Fe,,Ni,,; b Invar Fe,,Ni,,. Temperature dependknce of zero-field positive r&on pSR relaxation rate q’ above Curie temperature rc, the muon spin precession frequency w,/2n below Tc

350

b

400

450

T-

500

550 K 600

and the initial asymmetry ratio CI, of the positron count between forward and backward direction [89Ml].

1.2.1.5 Spin wave properties Fe-Ni system For Fe,,Ni,, neutron scattering experiments al 4 K result in a spin wave stiffness constant D = 58 + 2 THz A’, if the spin wave energy’is expressedas E=Eo+Dq2+Eq4,

(1)

with E, = 0.094 + 0.007 THz and E r 433 + 41 THz A4 [92Hl] . The spin wave stiffness constant D of Fe,,,-,Ni, Invar-type alloys and its temperature dependenceaccording to D=D,(l-D,

T’),

(2)

as derived from magnetisation curves are given in Table 1and Figs. 16-18. Calculations of D on the basis of a coherent potential approach [88Ml] and on its relation with the band structure parameters[85El]. Co-Ni system D(x) for Co,OO-xNix at 4.2 K and 293 K: Fig. 19.

Land&-Bihstein New Series 111/32A

[Ref. p. 113

1.2.1 Alloys between Fe, Co or Ni

88

Table I. Fe,,_,Ni,, Invar-type single crystal alloys. Results of iterative least-squares analysis of specific magnetisation vs. temperature curves for magnetic fields up to 16.9 kOe. Alloy density p at room temperature, specific mass magnetisation CTat H = 16.5 kOe and T = 4.2 K; estimated average magnetic moment per atom derived from this value, par, and the high-field magnetic susceptibility under the same conditions, xnr. See further eqs. (l-3) for the definition of the spin wave constants D,, D,, /I = E/D, and the Stoner coefficient S [83N2,90Nl]. X

34.2 34.7 35.4 37.0 38.6 40.2 45.0

CT

tg cm-7

P cmk’l M

[IO-’ cm’g-‘1 [meVA*]

[I Om6 K-*1 [A*]

[ 1O-6K-*1

8.131(5) 8.131(5) 8.130(5) 8.131(5) 8.140(5) 8.145(5) 8.210(5)

173.37 173.47 174.96 178.33 179.09 177.23 171.55

3.07(10) 2.25(10) 1.86(10) 1.51(10) 1.23(10) 0.79(7) 0.62(7)

1.4(2) 1.7(2) 2.05(5) 2.2(2) 2.2(2) 2.2(2) 2.2(2)

1.324(100) 1.490(100) 1.650(50) 1.279(100) 0.834(100) 0.673(70) 0.385(50)

Pat

1.764 1.765 1.781 1.817 1.826 1.809 1.755

XHF

4

4

85(10) 110(10) 122(lO) 140(10) 155(10) 165(10) 200( 10)

4 -10-6 K-2

300-

II&?

S

P

Fe,,,O-xNi,

3

250.

xFig. 16. FeloO_,Ni,,Invar-type alloys. Spin-wave stiffness constant D, vs. composition as derived from

magnetisationcurves[83N2] and comparedto results

P

0.04(4) O.lO(lO) 0.03(3) O.OO(5) 0.50(10) 0.35(10) 0.40(10)

8 -10-e K-512

6

Fig. 17. Fe,,,_,Ni,. Temperature coefficientD, andD, vs. Ni concentration. D, is defined in eq. (2). For the alloy x = 50.4 the quantity D varies as D = D,( 1D2p'*). Results are from [83N2] (circles), [75Hl] (triangles), [7911] (downward triangles).

of neutron scattering experiments indicated by: I

[75HI]. 2 [7911],3 [64Hl], 4 [68Ml], 5 [7OWl], 6 [76Ml]. The solid line represents the MathonWohlfahrt plot for D,.

Landolt-Barnstein New Series 111Ll2A

Ref. p. 1131

1.2.1 Alloys between Fe, Co or Ni

89

700 meVA'

600

n -30

35 -

40

x-

45

50

55

Fig. 18. Fe,,,-XNi,. Coefficient of the quartic term in the spin-wave dispersion relation, fl= E/D,, vs. Ni concentration. Results are from [83N2] (circles), [68Ml] (solid triangle), [7911] (open triangle).

n -30

40

50

60 x-

70

80

90

100 Ni

Fig. 19. Co,OO-xNix.Spin-wave stiffness constant D vs. Co concentration x. (I) -(3): T= 293 K, (4): T= 4.2 K. (1) and (2) are results of inelastic neutron scattering from [76Ml] and [79Hl], respectively. Results (3) of [76M2] are derived from magnetisation measurements.Dashed curve: spin-wave resonance at T= 293 K [72Hl, 79Hl].

1.2.1.6 Atomic magnetic moments Fe-Co system For Fe-Co ordered alloys spin density calculations based on the linearised augmented plane-wave (LAPW) method have been performed by [8482], resulting in spin densities well confined to the atomic regions. This allows to associate the magnetic moments of each atomic sphere with its respective element, as given in Figs. 20 and 21. For results from first principles calculations of the spin and orbital moments of Fe-Co and Co-Ni alloys using the linear muffin-tin orbital method and the virtual-crystal approximation see Fig. 22. For disordered Fe-Co alloys the orbital and spin magnetic moments are given in Fig. 23. The magnetic structure factors of ordered FeCo with the CsCl structure have been determined by coherent scattering experiments of a polarized neutron beam from a single crystal [89D 11.

Land&-BBmstein New Series 111132A

Ref. p. 1131

1.2.1 Alloys between Fe, Co or Ni

89

700 meVA'

600

n -30

35 -

40

x-

45

50

55

Fig. 18. Fe,,,-XNi,. Coefficient of the quartic term in the spin-wave dispersion relation, fl= E/D,, vs. Ni concentration. Results are from [83N2] (circles), [68Ml] (solid triangle), [7911] (open triangle).

n -30

40

50

60 x-

70

80

90

100 Ni

Fig. 19. Co,OO-xNix.Spin-wave stiffness constant D vs. Co concentration x. (I) -(3): T= 293 K, (4): T= 4.2 K. (1) and (2) are results of inelastic neutron scattering from [76Ml] and [79Hl], respectively. Results (3) of [76M2] are derived from magnetisation measurements.Dashed curve: spin-wave resonance at T= 293 K [72Hl, 79Hl].

1.2.1.6 Atomic magnetic moments Fe-Co system For Fe-Co ordered alloys spin density calculations based on the linearised augmented plane-wave (LAPW) method have been performed by [8482], resulting in spin densities well confined to the atomic regions. This allows to associate the magnetic moments of each atomic sphere with its respective element, as given in Figs. 20 and 21. For results from first principles calculations of the spin and orbital moments of Fe-Co and Co-Ni alloys using the linear muffin-tin orbital method and the virtual-crystal approximation see Fig. 22. For disordered Fe-Co alloys the orbital and spin magnetic moments are given in Fig. 23. The magnetic structure factors of ordered FeCo with the CsCl structure have been determined by coherent scattering experiments of a polarized neutron beam from a single crystal [89D 11.

Land&-BBmstein New Series 111132A

90

1.2.1 Alloys between Fe, Co or Ni

PIP,1 Fe

2.14

Fe,Co

2.30

FeCo (CSCI)

2.21

FeCo

2.15

1ZintlI

PFe [Id

[Ref. p. 113

PCJhJ

co, FeCo,

1.90 zco,

Cotbcc) 1.65

Fig. 20. Fe-Co alloys, ordered structures. Calculated local and average spin magnettc momentsprc,, pcOand p, respectively, see text above. For both Fe and Co the first near neighbours are shown in each structure. For Fe&o two types of Fe atoms exist, i.e. with four and with eight near neighbour ions. The same holds vice versa for the Co atoms in the FeCo, compound [84S2].

Landoh-Barnstein New Series 111132A

Ref. p. 1131 2.71

1.2.1 Alloys between Fe, Co or Ni I

2.3

1

,

\\.

I,*’2’

1 2.17

/

I

k , Fe,oo~xCox / 2.5 ‘\., / \ / ;’ ,I-;;.

I

I

1

I

I

I

,’

10.50

I

Fe,oo-x’Cox boo-x Nix I ‘\\ I a\\ Pspin\ -\

2.00 *.

pq \I I

\I\ ’

IQ

1.75

\

I I

I

pg 0.45

-I 0.40 0.35

I ‘1

1.9.

1.50

\ \ \\

1.7 -

2.50I

91

I.E 1.25 $1.00

0 experiment o theory

0.30

----

0.25 I 0.20990

experiment theory ‘,

1.5 0

20

Fe

40

x-

60

80

100

co

Fig. 21. FeioO-$o,, ordered alloys. Average spin magnetic moments p per atom vs. composition parameter x. Results are experimental [69Bl], corrected for orbital magnetism, and calculated, see Fig. 20 [8482].

01

Fig. 22. Fe-Co, Co-Ni. Calculated and experimental spin and orbital magnetic moments per atom pspinand porb,respectively [92Sl]. For experimental data see LB III/l 9A.

0

0 experiment o theory 1.5

0 Fe

Land&-Biirnstein New Series 111/32A

*

I 20

40 x-

60

80

100 co

Fig. 23. Fe,OO&oX, disordered alloys. Average magnetic spin moment per atom j5 vs. compostion parameter x. Experimental results are from [69Bl] and [82Tl] with g factors from [61Ml]; theoretical results using a tight-binding schemeare from [84Vl].

92

1.2.1 Alloys between Fe, Co or Ni

[Ref. p. 113

1.2.1.7 High-field susceptibility Fe-Ni system Magnetisation curves of Fe-Ni Invar-type alloys at various temperatures in strong magnetic fields: Figs. 24-26.The spin-wave stiffness constants derived from these curves are, within the indicated errors, equal to those given in Table 1.Apart from the spin-wave contribution to the magnetisation an additional contribution is found in high fields, described as a non-spin-wave part or a Stoner-type contribution causedby the excitation of single-particle spin flips: Acrr=STn

(3)

s = so (I -s, H),

(4)

with where S,,and S are constantsand H is the applied effective magnetic field [83N2, 90N1,92Nl]. For the Stoner constantsS seeFigs. 27a, b and Table 2. From the high-field hysteresis curves of Figs. 28 and 29, it is evident that hysteresis occurs only at a relative low temperature, dependent on the composition of the alloy. High-field susceptibilities are shown in Fig. 30. For the influence of externally applied pressure on the magnetisation curve see Fig. 31. Table 2. Fe,OO.,Ni,single crystals. Stoner parameters of eq. (3) used for fitting the curves to the experimental points of the Figs. 24-26. Seealso Fig. 27. X

37.0 35.4 34.2

&I

Sl

[ 10” K-*1

[ 10” Oe-‘1

1.286(20) 1.678(20) 1.347(20)

1.04(10) 1.34(10) 1.23(10)

Ref.

92N 1 90N 1 90N 1

Landolt-Btmrtein New Series 111132A

Ref. p. 1131

1.2.1 Alloys between Fe, Co or Ni

93

180 A.Tkg 175

160

I

I

I

I

155

b

150

Fig. 24. %s.8Ni34.2,single crystal alloy. Specific mass magnetisation (TVS.applied effective magnetic field H at various temperatures in the crystallographic [ 1001 direction. Solid curves are the result of a calculation using the parametersof Tables 1 and 2 [90Nl].

135 130

0

1

2

3

4

5

T

6

POH176.0 J T kg 175.5

180

I

I

I

I

166.0 -L T kg 165.5

175 170

174.0

I 165 b

I 153.5 b

164.5

160

153.0

164.0

155'

152.5

163.5

152.0

163.0

165.0 I b

145 14oL 0 a

I 1

I 2

I 3 PoH -

I 4

I 5

Fig. 25. Fe,,,,Ni,,,,, single crystal alloy. a Specific mass magnetisation cr vs. applied effective magnetic field Hat various temperaturesin the crystallographic

Landolt-Biirnstein New Series IIU32A

151.0

T

b

12

3

4

5T

6

,uoH [loo] direction. Solid curves are the result of a calculation using the parametersof Tables 1 and 2. b shows an enlargement of a [90Nl, 83Pl].

[Ref. p. 113

1.2.1 Alloys between Fe, Co or Ni

170 I 165 b 160 155 Fig. 26. Fe,,Ni,,, single crystal alloy. Specific mass magnetisation crvs. applied effective magnetic field H at various temperatures in the crystallographic [loo] direction. Solid curves are the result of a calculation using the parametersof Tables I and 2 [92N I].

l501-1/1

1451 0

I 1,

I 8

I 12

I 16

I 20 I

POH-

’

1.68

40-l 1.k 1.64 1.62 1.60

-I *I 1.05

1.56 1.5&

b

1.00I 0

4

El

12

16

1

20

POH -

a Fig. 27. Fe,OO_,Ni,,single crystal alloys. Coefficient S of the Stoner-type contribution to the magnetisation (see eq. 4) vs. applied field H, as derived from the

magnetisation curves of Figs. 24-26. The solid circles show results from [83N2]. For the parametersof the straight lines seeTable 2. a [90Nl], b [92Nl].

Land&-Barnstein New Series 111132A

Ref. p. 1131

1.2.1 Alloys between Fe, Co or Ni

95

18 &J 9 18

i' 43’A I,.’6.0R

1781

18

176

17

t b

174 I

17

b 174

176' 0

17'

/

' 4

I 8

I 12

I 16

T

i

Pu,HFig. 28. Fe,,,,Ni,,,,. High-field hysteresis curves at various temperatures T for increasing and decreasing field strengths H [85Ml, 86Ml].

Landolt-BOrnstein New Series IW32A

4

8

12

16

T

POH 7

Fig. 29. Fe,,,,Ni,, Invar-type single crystal alloys. Magnetic hysteresis curves at 4.2 K, measuredwith an effective field H parallel to the crystallographic [loo] axis. The magnetisation sequence is indicated by arrows for each composition of the alloy [86Ml].

1.2.1 Alloys between Fe, Co or Ni

96 40 'L$

I Fe,OO-x

[Ref. p. 113

I

Ni,

H II l1001

9

/

35'

25 I

20

r N

15

10 0

5

0

15

30

45

60

75

K 90

l-

1

2 POH -

3

4

15

Fig. 31. Fe,, ,,N& 6, annealed polycrystalline sample. Influence of externally applied pressure on the magnetisation curves at 4.2 K (open symbols) and 77 K (solid symbols) [9001].

Fig. 30. FeloO_,Ni,. Invar-type single crystal alloys. High-field susceptibility xHF in an effective magnetic field He,= 160 kOe parallel to the crystallographic [loo] axis vs. temperature T. Different symbols apply to increasing and decreasing field strength. Arrows indicate the temperatures above which hysteresis disappears(85MI, 86Ml].

Landoh-Bbmstein New Series 111132A

Ref. p. 1131

1.2.1 Alloys between Fe, Co or Ni

97

1.2.1.8 Magnetocrystalline anisotropy FeNi system Pressure dependence of the first order crystalline anisotropy constant K, of Fel,,-,Ni, Invar-type alloys, seeFig. 32. For x = 34.8 a pressurecoefficient (dK,ldp)/K, = - 8.4.10-’ bat’ was found [85Kl]. 1.00 *VI-3 J -3 0.50

0.25 t

0

G-1

-2 Fe,,,,,-xNix, Invar-type alloy. First-order magnetocrystalline anisotropy constant K, vs. applied pressurep on a (001) crystallographic plane at room temperature[85Kl]. Fig. 32.

-3 -L 0

1

3

2

4 kbor

5

P-

1.2.1.9 Magnetostriction Fe-Ni system Volume expansion and forced volume magnetostriction of Fe,OO-xNix Invar-type alloys seeFigs. 33 and 34, and forced linear magnetostriction seeFigs. 35 and 36. Co-Ni system Magnetostriction constants h,,, and h,,, seeFigs. 37-39.

Landolt-Bbmstein New Series 111132A

[Ref. p. I 13

1.2.1 Alloys between Fe, Co or Ni

98 200

50 .~~~‘o OC’ 0

I

-50 100

0 50

0

0

0 0 0 0 I 3 0 0

150 100

0 0

5

15

10

20

kOe 25

H-

Fig. 33. Fe,, 6Ni364. Annealed for IO h at 1000 “C. Volume expansion o vs. applied magnetic field H at various temperaturesT. Curie temperature Tc = 529 K [8511]. Fig. 34. Fe,,,O_,Ni,, disordered fee alloys. Forced volume magnetostriction adaH vs. temperature T, derived from data for H= 0...6 kOe and H= lo...20 kOe. Arrows indicate the Curie temperaturesTc [8511, seealso 84Yl].

0

coo

T-

600

lO...MkOe.

800

K 1000

Land&-Barnstein New Series W32A

Ref. p. 1131

1.2.1 Alloys between Fe, Co or Ni

99

1.6

I

120

=c ? 9 80 co

1.2

I d

0.8

40

0

0.4

4-I 30

40

50

60 x-

70

80

90

10: Ni

Fig. 35. FelOO-xNix,disordered fee alloys. Forced volume magnetostriction dol~H at various temperatures T vs. composition parameter x. The dashed curve represents the spontaneous volume magnetostriction mS[8X1, seealso 84Yl].

Land&-Bornstein New Series IIII3ZA

0 2.5 0

50

100

T-

150

200

250 K 300

Fig. 36. Fe,,,,Ni,,,, annealed at 950 ‘C and cooled to room temperature over a period of 6 h. Temperature dependence of the forced linear magnetostriction h = d(ANl)ld(u,H), where AN1is the relative change in length with respect to the length in zero field. TN is considered to be the NCel temperature of yFe clusters in the alloy [88Zl].

[Ref. p. 113

1.2.1 Alloys between Fe, Co or Ni 0 40-C

I

Co,OO-xNix

-ccH M0l

0 0 0 , n

-60

0

I 200

I 600

I 400

I 800

t

t

1000 K 1200

I-

Fig. 37. Co,OO-XNix,single crystal alloys. Linear

magnetostriction constant illoO vs. temperature T for various composition parameters x. Open circles [81KI]. solid circles [64Tl], solid triangles [80Ml], open triangles [77Fl].

-401 0

I 200

I 600

I 400

I 800

I 1000 K 1200

T-

Fig. 38. ColOO-xNix. single crystal alloys. Linear

magnetostriction constant ;I,, , vs. temperature T for various composition parameters x. Open circles [8lKl], solid circles [64Tl], solid triangles [80Ml], open triangles [77Fl].

Land&-Bernstein New Series II1132A

Ref. p. 1131

1.2.1 Alloys between Fe, Co or Ni

101

180 -KP

150

120l-

90 I 5 60 4 h B cz 30l-

0

-30l-

Fig. 39. Co,OO-xNix. Linear magnetostrictionconstants

40, and 41, vs. compositionparameterx at three temperaturesT [81Kl]. Crossesare from [59Yl] at -60 20

40

60 x-

80

100 Ni

293 K.

1.2.1.10 Density of states Fe-Co system The density of states obtained by self-consistent augmented spherical-wave calculations for various ordered Fe-Co alloys, have been calculated, seeFig. 40. For the De Haas-van Alphen frequencies of the fee alloy Co,,,Fe,,,,, measured and related to computed frequencies derived from self-consistent band-structure calculations, see [86Rl]. Fe-Ni system The density of states for Fe-Ni alloys have been calculated, Figs. 41-44. In many cases also the magnetic and crystallographic ground state properties were derived from these electronic structures [85Jl, 87J1,89M1, 89M2, 89P1,9OP1].

Land&-BBrnstein New Series IIV32A

Ref. p. 1131

1.2.1 Alloys between Fe, Co or Ni

101

180 -KP

150

120l-

90 I 5 60 4 h B cz 30l-

0

-30l-

Fig. 39. Co,OO-xNix. Linear magnetostrictionconstants

40, and 41, vs. compositionparameterx at three temperaturesT [81Kl]. Crossesare from [59Yl] at -60 20

40

60 x-

80

100 Ni

293 K.

1.2.1.10 Density of states Fe-Co system The density of states obtained by self-consistent augmented spherical-wave calculations for various ordered Fe-Co alloys, have been calculated, seeFig. 40. For the De Haas-van Alphen frequencies of the fee alloy Co,,,Fe,,,,, measured and related to computed frequencies derived from self-consistent band-structure calculations, see [86Rl]. Fe-Ni system The density of states for Fe-Ni alloys have been calculated, Figs. 41-44. In many cases also the magnetic and crystallographic ground state properties were derived from these electronic structures [85Jl, 87J1,89M1, 89M2, 89P1,9OP1].

Land&-BBrnstein New Series IIV32A

1.2.1 Alloys between Fe, Co or Ni

-8

-6

-4

-2

0 eV2 E-

-8

-6

-4

-2

[Ref. p, 113

0 eV2

Fig. 40. Fe-Co system. Spin-projected density of states.The energy is with respect

to Fermi energy Er. Calculations basedon local spin-density treatment of exchange and correlation. Augmented spherical-wave method used for the self-consistent energy-band calculation. The crystal-type structures are indicated [8482]. Arrows indicate the spin direction.

Landolt-Barnsrein New Series W32A

Ref. p. 1131

1.2.1 Alloys between Fe, Co or Ni

* Ry atom c

25

103

Fe,, ‘4 20 bee

20c

majority spin

-0.6

-0.5

n AA

r .J

majority spin

--.-total Ni ----Fe -0.4

-0.3

-0.2

-0.1

0

0.1 Ry 0.2

f-

-0.5

-0.4

-0.3

-0.2

-0.1

0

I I

0.1

0.2 Ry 0.3

f-

Fig. 41. Fe,,Ni,,, disordered fee alloy. Majority spin and minority spin total and component densities of statesn (I?) of the ferromagnetic alloy as a function of energy (relative to the Fermi level), basedon ab-initio calculations along the multiple-scattering coherentpotential approach (KKR-CPA) [85Jl].

Land&-B&mstein New Series IIII3ZA

Fig. 42. Fe,,Ni,,, disordered bee alloy. Majority spin and minority spin total and component densities of statesn (E) of the ferromagnetic alloy as a function of energy (relative to the Fermi level) [87Jl].

104

1.2.1 Alloys between Fe, Co or Ni

,t,,,:” “I

“‘-“’

FeIONieO )

[Ref. p. 113

Fe site

total

fCC

20 majority spin

1

10

I

$4

20 -0.6

-0.4

-0.2

0 Ry 0.2

Fig. 43. FezoNi,,. disordered fee alloy. Majority spin and minority spin total and component densities of

I

I

-0.6

-0.4

I

-0.2

I

I

0 Ry 0.2

statesn (E) of the ferromagnetic alloy as a function of energy (relative to the Fermi level) [89Al].

50 sta:es Ry atom 40

I

30

G c

20

10

0

a

0.2

0.4

0.6

0.8 Ry 1.0

Z-

’ Fig. 44. a Fe,Ni, ordered, and b Fe,,Ni,,, disordered fee Invar alloys. Total and partial DOS in the ferromagnetic state calculated using the linear muffin-

0

0.2

0.4

0.6

0.8

Ry

’

E-

tin orbital (LMTO) band method within the local spindensity approximation (LSDA) [92Ml].

Landolr-Bbmstein New Series 111132A

Ref. p. 1131

105

1.2.1 Alloys between Fe, Co or Ni

1.2.1.11 Elastic and magnetoelastic constants. Lattice dynamics Fe-Ni system Temperature dependence of the elasic constants see Figs. 45.. .48. Influence of applied magnetic fields on the Young’s and shear modulus of Fe,,Ni,, see Fig. 49. Phonon dispersion curves see Figs. 50 and 51.

Co-Ni system co ,,,,-,Ni,. The magnetoelastic coupling constants B, and B, are defined by the equations a IfJO= -+I

/cc,1 -c,2)

(54

RI,, = -pz

/CJ4

(5b)

and they are given for Col,,,,-xNix alloys in the Figs. 52 and 53. 55 I

GPi k,

I

140

I Fe 100-x Nix’

GPa

I

I

I

I Fe,,,

I

-xNix I I

130

120

I 110 I

2 u 100

90

25

80

701 70 -200

I 0

200

Fig. 46. Fe,,,-,Ni,,

400 T-

600

800

1000"C 1200

single crystals. Elastic shear constant cd4 as a function of temperature T, corresponding to a compression [89R3].

Fig. 45. Fel,,O-xNix, single crystals. Elastic shear constant c’= (cl, - cl,)/2 as a function of temperature T, determined by ultrasonic measurements. Curie temperaturesare marked by arrows [89R3].

Land&-BBmstein New Series IIV32A

106

1.2.1 Alloys between Fe, Co or Ni

GPoI

[Ref. p. 113

I

I

FL,

25

50

75

Ni

I

100

125

270 260 250

I G-

IG

240

230

,901 0

zoo-200 0

200 400

T-

150 K 175

800

1000“C1200 Fig. 48. Fe,,,O_XNi,, single crystals. Longitudinal elasticity modulus q in a [l lo] direction, measuredin an external field of 5 kOe in the low-temperature Fig. 47. Fe,W.XNiX, single crystals. Longitudinal range. The arrows indicate the onset of an anomalous elastic constant cL = (c,, + cl2 + 2cJ2 [89R3]. increasein cL [88S1,9lSl]. T-

600

Lmdolt-Barnstein New Series 1IVlZA

Ref. p. 1131

1.2.1 Alloys between Fe, Co or Ni

Fig. 49. Fe,,Ni,,, ordered single crystal. Influence of an externally applied magnetic field H on a the longitudinal elastic constant c, and b the transverse elastic constant c’= (cl1 -Q/2 at various temperatures T, as derived from ultrasonic pulse-echo experiments in the [I IO] crystallographic direction [9OSl]. For the vertical axis apply the following absolute values of the elastic constants at H = 5 kOe:

&OneV

35-

107

T

CL

C’

Kl

[lo2 GPa]

[lo* GPa]

4.2 77 200 300 400 500

23.25 21.87 21.54 21.67 22.20 23.30

1.57 1.58 1.84 2.13 2.39 2.57

Fe65Ni 35

30252015 VI-

Landolt-Bhrnstein New Series IW32A

Fig. 50. Fe,,Ni,,, Invar alloy. Room-temperature phonon dispersion along high-symmetry directions. Curves: fitted data on the basis of the Bohr-von Karmann model including 4 neighbour force constants [79El].

[Ref. p. 113

1.2.1 Alloys between Fe, Co or Ni

108

IL”

*III5 ‘0 80

I

40

3.0

ff 2.5 !it

L-I

-E 2.0 ro

I

0 1: 513K

0 t

-40 1 co’ -80

-120 0

0.025 0.050 0.075 0.100 0.125 0

Fig. 51. Fe,,Ni,,, Invar alloy. Phonon dispersion curves of the [@I] TA, mode in the small momentum region (relative phonon wavevector r) at several temperaturesT [79EI].

--

-ZOO] 0

200

400

600 T-

I 800

I 1000K 1 IO

Fig. 52. Co,OO-xNix,single crystals. Magnetoelastic coupling constant B, (see eq. 5) vs. temperature T for various values of the composition parameterx. Curves are the result of a model calculation. Curie point Tc [8lKl]. 2oc alO5 Pa

I %O-XNiX

16(

Fig. 53. Co,Oo-xNix, single crystals. Magnetoelastic coupling constant B, (see eq. 5) vs. temperature T for various values of the composition parameterx. Curves are the result of a model calculation. Tc: Curie point [8lKl].

400

600

800

1000 K 1:200

lLsndolt-Barnstein New Series lW32A

Ref. p. 1131

1.2.1 Alloys between Fe, Co or Ni

109

1.2.1.12 Thermal expansion, specific heat Fe-Co system For the specific heat of Fe&o,, see Fig. 54. At about 1230 K a bee-fee crystallographic first-order transition between two disordered phases takes place with a latent heat of transformation of 1.3 kcal mol-‘. In the vicinity of the Curie temperature of 995 K a second order transition occurs [7401]. Fe-Ni system Thermal expansion of polycrystalline Invar-type Fe,,,,Ni,,,, in the presence of an applied magnetic field see Fig. 55. Of technical importance is the coefficient of thermal expansion given in Fig. 56. Many theoretical approaches of the Invar problem, which plays a dominant role in the literature dealing with iron-rich Ni-Fe alloys, have been published in the last decade.For a general survey see [91Wl]. The Invar properties can be understood within a frame work of electronic band calculations based on various suppositions [92Ml, 92Pl]. The Invar effect is found close to the y-a stability limit, and it can also be understood starting from total energy calculations, [91M1,89M1, 89M2] and [91Fl] for ordered and disordered alloys, respectively. Fe-Co-Ni system Thermal expansion of super-Invar seeFigs. 56 and 57. 4 *lo-6 K-1

Fe65.5Ni34.5 H” 0 0

0 Ooo 0

sI 0

o-o

0 0 ,!i,,H=6T 000 ooo

0

0

i

0 0 0 o%o

00

000

41 o 0 00

000

2T 00

0

OO

I 8

0 0

1

0 0

I

1 a

0

0

0

CI-

0

-1l-

0.5~10‘~

0

0

0

0

0

0

O

0

00

0 00

o”

I

I

I

I

20

40

60

80

K

T-

Fig. 54. Fe,,,,Ni,,,S, annealed at 950 “C and cooled to room temperature over a period of 6 h. a The relative change in length All1 as a function of temperature T in the presenceof various magnetic fields H. b Tempera-

Landolt-Biimstein New Series IIU32A

-2,_

‘0

100

b

20

40

60

80

K 100

T-

ture dependence of the relative thermal expansion coefficient a= (dNdT)/Z in various magnetic fields H [88Zl].

110

1.2.1 Alloys between Fe, Co or Ni

[Ref. p. 113

0.6 I8 0.4

0.2 0

20

C.W.-

60

80 % 100

0 -0.2

Fig. 55. 64Fe36Ni (Invar); 63Fe4Co33Ni (superInvar), in wt%. Variation of the mean value of the expansion coefficient E per degree Celsius in the temperature range, O... 100 “C as a function of the degree of cold work (c.w.) for annealed and slowly cooled alloys [89H2].

-04

0

200

4ou

600

“C

a

I, -

Fig. 56. Super-Invar 62Fe4Co34Ni, in wt%. Mean thermal expansion coefficient a between 0 OC and 100 “C at different annealing temperatures T.. Full curves for various degrees of cold work. Dashed curve: 30 min at 950 OC,followed by furnace-cooling. Dot-dashed curve 30 min at 95O”C, followed by water-quenching [89H2].

0.50 fi gK 0.65 0.50 0.35 I 0.30 z 0.25 0.20 0.15

01

600

Fig. 57. Fe&o,,. Specific heat at constant pressure, C,,, vs. temperature T. The symbols correspond to three different runs [7401]. 700

800

900

1000

1100 1200K 1300

Landolt-IMrnstein New Series 111132A

Ref. p. 1131

1.2.1 Alloys between Fe, Co or Ni

111

1.2.1.13 Electrical resistivity and magnetoresistance Fe-Co system A detailed investigation on the effect of order on the electrical resistivity of Fe,,,,-$0, alloys at 4.2 K is given in [88Fl], see also Fig. 58. The anisotropic magnetoresistanceis defined as @PO = @,I - ~J(p11/3 + 2 ~1/3)0

(6)

where 4, and pL are the resistivities at magnetic saturation, when the magnetisation is parallel or perpendicular to the current, respectively. p,, is the resistivity in the demagnetised state. For data on Fe,,,O-xCox alloys see Figs. 59 and 60. For an analysis of the impurity scattering and phonon scattering effects, see [88Bl]. Fe-Ni system Influence of magnetic field on the electrical resistivity seeFigs. 6 1 and 62. 12 I PQcm FelooexCo,

a %

IO

E

8

4

t I 6 CT

I \G

4

$2

2

0

01 0

Fe

20

60

40 x-

80

100

co

-2 0

Fe

Fe,,,&o,. Zero magnetic field electrical resistivity pO at 4.2 K for (circles) ordered (furnaceFig. 58.

cooled) and (triangles) disordered (quenched) alloys [88Fl].

Landolt-Barnstein New Series IIU32A

20

40

x-

60

80

1

l

Fig. 59. Fe,O,,-xCox,furnace-cooled alloys. Relative anisotropic magnetoresistanceAplp, vs. composition parameterx for various temperaturesT[86Fl].

[Ref. p. 113

1.2.1 Alloys between Fe, Co or Ni

I 1=4.2K

30.8

13.2

I 30.0

39.2 I cb

Qr 51.6

38.4

50.8

37.6

4Fig. 60. Fe,, $kr,, 5 alloy, quenched from several temperatures To above and below the ordering Relative anisotropic temperature T,=736'C. magnetoresistance AplpO and zero-field electrical resistivity p0 at 4.2 K vs. To [86Fl].

5b.O

49.2 1 0

I 12

I

I 3

I 4

I 5

1 P 6 17

P,H Fig. 61. Fe,,O_xNi, alloys. Electrical resistivity p at 4.2 K as dependent on an externally applied magnetic field H parallel to the measuring current. Open circles: increasing H, solid circles: decreasingH [89M3].

Land&-Bbrnstein New Series lW32A

Referencesfor 1.2.1

113

2

% Fe65 Ni35

Fig. 62.

-0

1

2

&--

4

5

6T

7

Fe,,Ni,,. Relative variation of the longitudina’l magnetoresistivity (p(H) - p(O))/p(O) in an externally applied magnetic field H at various temperatures T. Open circles: increasing H, solid circles: decreasingH [89M3].

1.2.1.14 References for 1.2.1 59Al 59Yl

Arp, V., Edmonds, D., Petersen,R.: Phys. Rev. Lett. 3 (1959) 212 Yamamoto, M., Nakamichi, T.: Sci. Rep. Res. Inst. Tohoku Univ. Ser. A 11 (1959) 168

61Ml

Meyer, A.J.P., Asch, G.: J. Appl. Phys. 32 (1961) 330s

63Cl 6351

Crangle, J., Hallam, G.C.: Proc. R. Sot. London A 272 (1963) 119 Johnson, C.E., Ridout, M.S., Cranshaw, T.E.: Proc. Phys. Sot. (London) 81 (1963) 1079

64Bl 64Hl

Bando, Y.: J. Phys. Sot. Jpn. 19 (1964) 273 Hatherley, M., Hirakawa, K., Lowde, R.D., Mallett, J.F., Stringfellow, M.W., Torrie, B.H.: Proc. Phys. Sot. London 84 (1964) 55 Takahashi, M.: J. Jpn. Inst. Met. 28 (1964) 200

64Tl 68Ml

Menzinger, F., Caglioti, G., Shirane, G., Nathans, R., Pickart, S.J., Alperin, H.A.: J. Appl. Phys. 39 (1968) 455

69Al 69B1

Asano, H.: J. Phys. Sot. Jpn. 27 (1969) 542 Bardos, D.I.: J. Appl. Phys. 40 (1969) 1371

7OWl

Werner, S.A., Wiener, E., G&men, E., Arrott, A.: J. Appl. Phys. 41 (1970) 1363

71Sl 71Yl

Stauss,G.H.: Phys. Rev. B 4 (1971) 3106 Yurchikov, Y.Y.,‘Menshikov, A.Z.: Fiz. Met. Metalloved. 32 (1971) 168

Land&-BBmstein New Series 111/32A

Referencesfor 1.2.1

113

2

% Fe65 Ni35

Fig. 62.

-0

1

2

&--

4

5

6T

7

Fe,,Ni,,. Relative variation of the longitudina’l magnetoresistivity (p(H) - p(O))/p(O) in an externally applied magnetic field H at various temperatures T. Open circles: increasing H, solid circles: decreasingH [89M3].

1.2.1.14 References for 1.2.1 59Al 59Yl

Arp, V., Edmonds, D., Petersen,R.: Phys. Rev. Lett. 3 (1959) 212 Yamamoto, M., Nakamichi, T.: Sci. Rep. Res. Inst. Tohoku Univ. Ser. A 11 (1959) 168

61Ml

Meyer, A.J.P., Asch, G.: J. Appl. Phys. 32 (1961) 330s

63Cl 6351

Crangle, J., Hallam, G.C.: Proc. R. Sot. London A 272 (1963) 119 Johnson, C.E., Ridout, M.S., Cranshaw, T.E.: Proc. Phys. Sot. (London) 81 (1963) 1079

64Bl 64Hl

Bando, Y.: J. Phys. Sot. Jpn. 19 (1964) 273 Hatherley, M., Hirakawa, K., Lowde, R.D., Mallett, J.F., Stringfellow, M.W., Torrie, B.H.: Proc. Phys. Sot. London 84 (1964) 55 Takahashi, M.: J. Jpn. Inst. Met. 28 (1964) 200

64Tl 68Ml

Menzinger, F., Caglioti, G., Shirane, G., Nathans, R., Pickart, S.J., Alperin, H.A.: J. Appl. Phys. 39 (1968) 455

69Al 69B1

Asano, H.: J. Phys. Sot. Jpn. 27 (1969) 542 Bardos, D.I.: J. Appl. Phys. 40 (1969) 1371

7OWl

Werner, S.A., Wiener, E., G&men, E., Arrott, A.: J. Appl. Phys. 41 (1970) 1363

71Sl 71Yl

Stauss,G.H.: Phys. Rev. B 4 (1971) 3106 Yurchikov, Y.Y.,‘Menshikov, A.Z.: Fiz. Met. Metalloved. 32 (1971) 168

Land&-BBmstein New Series 111/32A

114

Referencesfor 1.2.1

72H 1

Hinoul, M., Witters, J.: Solid StateCommun. 10 (1972) 749

7401

Orehotsky, J., Schroder, K.: J. Phys. F 4 (1974) 196

75H1

Hennion, M., Hennion, B., Castets,A., Tocchetti, D.: Solid State Commun. 17 (1975) 899

76Ml 76M2 76M3

Mikke, K., Jankowska,J., Modrzejewski, A.: J. Phys. F 6 (1976) 63 1 Maeda, T., Yamau, H., Watanabe,H.: J. Phys. Sot. Jpn. 40 (1976) 1559 Muraoka, Y., Shiga, M., Yasuoka, H., Nakamura, Y.: J. Phys. Sot. Jpn. 40 (1976) 414

77D1 77D2 77El 77F1

Drijver, J.W., Woude, F. van der, Radelaar, S.: Phys. Rev. B 16 (1977) 985 Drijver, J.W., Woude, F. van der, Radelaar, S.: Phys. Rev. B 16 (1977) 993 Endoh, Y ., Noda, Y ., Ishikawa, Y .: Solid State Commun. 23 (1977) 95 1 Fujiwara, H., Tokunaga, T., Tange, H., Goto, M.: J. Phys. Sot. Jpn. 43 (1977) 1554

78Bl

Bendick, W., Ettwig, H.H., Pepperhoff, W.: J. Phys. F 8 (1978) 2525

79Cl 79El 79H1 7911

Chamberod, A., Laugier, J., Penisson,J.M.: J. Magn. Magn. Mater. 10 (1979) 139 Endoh, Y.: J. Magn. Magn. Mater. 10 (1979) 177 Hennion, B., Hennion, M.: J. Phys. F 9 (1979) 557 Ishikawa, Y., Onodera, S., Tajima, K.: J. Magn. Magn. Mater. 10 (1979) 183

80E1 80M 1

Everson, J.H., Chen, J.H., Clapp, P.C.: Phys. Status Solidi (a) 59 (1980) 795 Masumoto, H., Takahashi, M., Nakayama, T.: Trans. Jpn. Inst. Met. 21 (1980) 5 15

8lK1 81Ml

Kadowaki, S., Takahashi, M.: J. Phys. Sot. Jpn. 50 (1981) 1154 Meschter, P.J., Wright, J.W., Brooks, C.R.: J. Phys. Chem. Solids 42 (1981) 861

82T1

Tersoff, J., Falicov, L.M.: Phys. Rev. B 25 (1982) 4937

83Ml 83M2 83N1 83N2 83Pl 83P2

Mtiller, J.B., Hesse,J.: 2. Phys. B 54 (1983) 35 Mtlller, J.B., Hesse,J.: Z. Phys. B 54 (1983) 43 Nakai, I.: J. Phys. Sot. Jpn. 52 (1983) 1781 Nakai, I., Ono, F., Yamada, 0.: J. Phys. Sot. Jpn. 52 (1983) 1791 Pauthenet,R., Maruryama, H., Yamada, D.: J. Magn. Magn. Mater. 31-34 (1983) 835 Pierron-Bohnes, V., Cadeville, M.C., Gautier, F.: J. Phys. F 13 (1983) 1689

84Ml 84Sl 84S2 84Ul 84Vl 84Wl 84Yl

Morita, H., Chamberod, A., Steinemann,S.: J. Phys. F 14 (1984) 3053 Shiga, M., Nakamura, Y.: J. Magn. Magn. Mater. 40 (1984) 319 Schwarz, K., Mohn, P., Blaha, P., Kubler, J.: J. Phys. F 14 (1984) 2659 Ullrich, H., Hesse,J.: J. Magn. Magn. Mater. 45 (1984) 315 Victora, R.H., Falicov, L.M.: Phys. Rev. B 30 (1984) 259 Willgeroth, S., Ullrich, H., Hesse,J.: J. Phys. F 14 (1984) 387 Yamada, O., Tremolet de Lacheisserie, E.du: J. Phys. Sot. Jpn. 53 (1984) 729

85C1 85El 8511 8551 85K1 85L1

Comstock, R.J., Cohen, J.B., Harrison, H.R.: Acta Metall. 33 (1985) 423 Edwards, D.M., Muniz, R.B.: J. Phys. F 15 (1985) 2339 Ishio, S., Takahashi, M.: J. Magn. Magn. Mater. 50 (1985) 271 Johnson, D.D., Pinski, F.J., Stocks, G.M.: J. Appl. Phys. 57 (1985) 3018 Kagawa, H.: J. Phys. Sot. Jpn. 54 (1985) 873 Ledbetter, H.M.: J. Appl. Phys. 57 (1985) 5069

Land&-Barnstein New Series 111/32A

Referencesfor 1.2.1 85L2 85Ml 85M2 85M3 85M4 85P1 86F1 86Kl

115

Lukasiak, M., Zemcik, T., Suwalski, J., Piekoszewski, J.: Acta Phys. Pol. A 68 (1985) 79 Maruyama, H., Pauthenet, R., Picoche, J.-C., Yamada, 0.: C.R. Acad. Sci. Paris II 300 (1985) 595 Miyazaki, T., Ando, Y., Takahashi, M.: J. Appl. Phys. 57 (1985) 3456 Mitchell, P.W., Paul, D. Mck.: Phys. Rev. B 32 (1985) 3272 Martinez-Herrera, F.J., Mejia-Lira, F., Aguilera-Granja, F., Moran-Lopez, J.L.: Phys. Rev. B 31(1985) 1686 Pierron-Bohnes, V., Cadeville, MC., Parette, G.: J. Phys. F 15 (1985) 1441

86Rl

Freitas, P.P., Berger, L.: J. Magn. Magn. Mater. 54-57 (1986) 1515 Kellner, W.-U., Albrecht, T., Fahnle, M., Kronmtiller, H.: J. Magn. Magn. Mater. 62 (1986) 169 Maruyama, H., Pauthenet,R., Picoche, J.-C., Yamada, 0.: J. Phys. Sot. Jpn. 55 (1986) 3218 Miyazaki, T., Ando, Y., Takahashi, M.: J. Magn. Magn. Mater. 60 (1986) 219 Miyazaki, T., Ando, Y., Takahashi, M.: J. Magn. Magn. Mater. 60 (1986) 227 Pierron-Bohnes, V., Cadeville, M.C., Bieber, A., Gautier, F.: J. Magn. Magn. Mater. 54-57 (1986) 1027 Roeland, L.W., Tal, A., Wolfrat, J.C., Rabou, L.P.L.M.: J. Phys. F 16 (1986) 2045

87Cl 8751 87Rl 87Sl 87Tl

Cranshaw, T.E.: J. Phys. F 17 (1987) 967 Johnson, D.D., Pinski, F.J., Staunton, J.B.: J. Appl. Phys. 61 (1987) 3715 Rancourt, D.G., Smit, H.H.A., Thiel, R.C.: J. Magn. Magn. Mater. 66 (1987) 121 Staunton, J., Falicov, L.M.: J. Appl. Phys. 61 (1987) 3693 Tajima, K., B&i, P., Shirane, G., Ishikawa, Y., Kohgi, M.: Phys. Rev. B 35 (1987) 274

88Al 88Bl 88Fl 88Hl 88H2 88Ml

Abd-Elmeguid, M.M., Schleede,B., Micklitz, H.: J. Magn. Magn. Mater. 72 (1988) 253 Berger, L., Freitas, P.P., Warner, J.D., Schmidt, J.E.: J. Appl. Phys. 64 (1988) 5459 Freitas, P.P., Berger, L.: Phys. Rev. B 37 (1988) 6079 Hoshi, K., Oomi, G.: J. Phys. (Paris) Colloq. Suppl. 49 (1988) C8-305 Hawkins, R.J. Sanchez,J.M.: J. Phys. F 18 (1988) 767 Muniz, R.B., Albuquerque e Castro, Jd’, Edwards, D.M.: J. Phys. (Paris) Colloq. 49 (1988) C8-91 Menshikov, A.Z.: Physica B 149 (1988) 249 Shiga, M., Makita, K., Uematsu, K., Nakamura, Y.: J. Phys. (Paris) Colloq. Suppl. 49 (1988) C8-309 Zahres, H., Acet, M., Stamm, W., Wassermann,E.F.: J. Magn. Magn. Mater. 72 (1988) 80

86Ml 86M2 86M3 86Pl

88M2 88Sl 8821 89Al 89A2 89D1 89Hl 89H2 89M1 89M2 89M3 89M4 89Pl 89Rl 89R2 89R3

Akai, H.: J. Phys. Condens.Matter 1 (1989) 8045 Abd-Elmeguid, M.M., Micklitz, H.: Physica B 161 (1989) 17 Di Fabrizio, E., Mazzone, G., Petrillo, C., Sacchetti, F.: Phys. Rev. B 40 (1989) 9502 Hamdeh, H.H., Fultz, B., Pearson,D.H.: Phys. Rev. B 39 (1989) 11233 Hausch, G., Bather, R., Hartmann, J.: Physica B 161 (1989) 22 Moruzzi, V.L.: Physica B 161 (1989) 99 Moroni, E.G., Jarlborg, T.: Physica B 161 (1989) 115 Murayama, S., Ikeda, D., Miyako, Y., Nishiyama, K., Nagamine, K., Yamazaki, T., Dumpich, G., Wassermann,E.F.: Physica B 161 (1989)39 Menshikov, A.Z.: Physica B 161 (1989) 1 Podgomy, M.: Physica B 161(1989) 110 Rancourt, D.G., Chebab, S., Lamarche, G.: J. Magn. Magn. Mater. 78 (1989) 129 Rancourt, D.G.: J. Magn. Magn. Mater. 78 (1989) 153 Renaud, Ph., Steinemann, S.G.: Physica B 161 (1989) 75

Landolt-B6irnst.G New Series IIV32A

1.2.2 Binary alloys between Ti, V, Cr or Mn

116 90El 90Fl 90Hl 90Ml 90N 1 9001 9OPl 90Rl 9os1 90Tl 9ow1

91Fl 9lF2 9lMl 9lSl 9lS2 91Wl 92H1 92Ml 92N 1 92Pl 92Sl

[Ref. p. 218

Ebert, H., Winter, H., Johnson,D.D., Pinski, F.J.: J. Phys. Condens.Matter 2 (1990) 443 Fujita, M., Maruyama, H., Maeda, H., Koizumi, A., Yamazaki, H.: J. Magn. Magn. Mater. 90-91 (1990) 730 Hausch, G.: J. Magn. Magn. Mater. 92 (1990) 87 Moruzzi, V.L.: Phys. Rev. B 41 (1990) 6939 Nakai, 1.: J. Phys. Sot. Jpn. 59 (1990) 22 11 Ono, F., Asano, M., Tanaka, R., Endo, S.: J. Magn. Magn. Mater. 90-91 (1990) 737 Podgomy, M.: Acta Phys. Pol. A 78 (1990) 94 1 Rancourt, D.G., Hargraves, P., Lamarche, G., Dunlap, R.A.: J. Magn. Magn. Mater. 87 (1990) 71 Shiga, M., Makita, K., Uematsu, K., Muraoka, Y., Nakamura, Y.: J. Phys. Condens. Matter 2 (1990) 1239 Takzei, G.A., Grebenyuk, Y.P., Sych, 1.1.:Zh. Eksp. Teor. Fiz. 97 (1990)1022, Sov. Phys. JETP 70 (1990) 572 (Engl. Transl.) Wassermann, E.F.: Ferromagnetic Materials (Buschow, K.H.J., Wohlfarth, E.P, eds.), Amsterdam: Elsevier SciencePubl. 5 (1990) 237 Frtlchtl, H., Krey, U.: J. Magn. Magn. Mater. 94 (1991) L20 Fultz, B.: Phys. Rev. B 44 (1991) 9805 Mohn, P., Schwarz, K., Wagner, D.: Phys. Rev. B 43 (199 1) 33 18 Shiga, M., Makita, K., Uematsu, K., Muraoka, Y., Nakamura, Y.: J. Phys. Condens. Matter 3 (1991) 3577 Silin, V.P., Zverev, V.M., Thon, M., Wagner, D.: Phys. Lett. A 154 (1991) 45 Wassermann,E.F.: J. Magn. Magn. Mater. 100 (1991) 346 Heap, R.T., Mitchell, P.W., Needham,L.M.: J. Magn. Magn. Mater. 104-107 (1992) 715 Moroni, E.G., Jarlborg, T.: J. Magn. Magn. Mater. 104-107 (1992) 711 Nakai, I., Maruyama, H.: J. Magn. Magn. Mater. 104-107 (1992) 2053 Podgomy, M.: Phys. Rev. B 46 (1992) 6293 Siiderlind, P., Eriksson, O., Johansson,B., Albers, R.C., Boring, A.M.: Phys. Rev. B 45 (1992) 12911

1.2.2 Binary alloys between Ti, V, Cr or Mn Supplement to LB 111/19A,p. 282-3 10 1.2.2.1 V-Ti

SeeLB III/l 9A, p. 284-287

1.2.2.2 Cr-Ti

SeeLB 111/19A,p. 287,288

Land&-B6mstein New Series 111/32A

1.2.2 Binary alloys between Ti, V, Cr or Mn

116 90El 90Fl 90Hl 90Ml 90N 1 9001 9OPl 90Rl 9os1 90Tl 9ow1

91Fl 9lF2 9lMl 9lSl 9lS2 91Wl 92H1 92Ml 92N 1 92Pl 92Sl

[Ref. p. 218

Ebert, H., Winter, H., Johnson,D.D., Pinski, F.J.: J. Phys. Condens.Matter 2 (1990) 443 Fujita, M., Maruyama, H., Maeda, H., Koizumi, A., Yamazaki, H.: J. Magn. Magn. Mater. 90-91 (1990) 730 Hausch, G.: J. Magn. Magn. Mater. 92 (1990) 87 Moruzzi, V.L.: Phys. Rev. B 41 (1990) 6939 Nakai, 1.: J. Phys. Sot. Jpn. 59 (1990) 22 11 Ono, F., Asano, M., Tanaka, R., Endo, S.: J. Magn. Magn. Mater. 90-91 (1990) 737 Podgomy, M.: Acta Phys. Pol. A 78 (1990) 94 1 Rancourt, D.G., Hargraves, P., Lamarche, G., Dunlap, R.A.: J. Magn. Magn. Mater. 87 (1990) 71 Shiga, M., Makita, K., Uematsu, K., Muraoka, Y., Nakamura, Y.: J. Phys. Condens. Matter 2 (1990) 1239 Takzei, G.A., Grebenyuk, Y.P., Sych, 1.1.:Zh. Eksp. Teor. Fiz. 97 (1990)1022, Sov. Phys. JETP 70 (1990) 572 (Engl. Transl.) Wassermann, E.F.: Ferromagnetic Materials (Buschow, K.H.J., Wohlfarth, E.P, eds.), Amsterdam: Elsevier SciencePubl. 5 (1990) 237 Frtlchtl, H., Krey, U.: J. Magn. Magn. Mater. 94 (1991) L20 Fultz, B.: Phys. Rev. B 44 (1991) 9805 Mohn, P., Schwarz, K., Wagner, D.: Phys. Rev. B 43 (199 1) 33 18 Shiga, M., Makita, K., Uematsu, K., Muraoka, Y., Nakamura, Y.: J. Phys. Condens. Matter 3 (1991) 3577 Silin, V.P., Zverev, V.M., Thon, M., Wagner, D.: Phys. Lett. A 154 (1991) 45 Wassermann,E.F.: J. Magn. Magn. Mater. 100 (1991) 346 Heap, R.T., Mitchell, P.W., Needham,L.M.: J. Magn. Magn. Mater. 104-107 (1992) 715 Moroni, E.G., Jarlborg, T.: J. Magn. Magn. Mater. 104-107 (1992) 711 Nakai, I., Maruyama, H.: J. Magn. Magn. Mater. 104-107 (1992) 2053 Podgomy, M.: Phys. Rev. B 46 (1992) 6293 Siiderlind, P., Eriksson, O., Johansson,B., Albers, R.C., Boring, A.M.: Phys. Rev. B 45 (1992) 12911

1.2.2 Binary alloys between Ti, V, Cr or Mn Supplement to LB 111/19A,p. 282-3 10 1.2.2.1 V-Ti

SeeLB III/l 9A, p. 284-287

1.2.2.2 Cr-Ti

SeeLB 111/19A,p. 287,288

Land&-B6mstein New Series 111/32A

Ref. p. 2181

1.2.2 Binary alloys between Ti, V, Cr or Mn

117

1.2.2.3 Cr-V

Supplement to LB 111/19A,p. 289-295 Magnetic susceptibility Fig. 1. The curves obey a Curie-Weiss law above TN with an average magnetic moment per V atom of 1.45 f 0.11 pa and 1.02 f 0.19 pa for the alloys x = 0.26 and x = 0.51, respectively [94Hl]. Elastic constants at room temperature see Figs. 2 and 3a-c. See also subsect. 1.1.1.3, Fig. 3 1. Thermal expansion coefficient for alloys of Cr with up to 5 at% V see Figs. 25a and 26 in subsect. 1.l. 1.3. 1.75 *lCP *lo-4 @ mol 1.70

I

125 GPa

225 GPa

100

200

25

125

1.65

E x 1.60

V 1.50 250

275

300

325

350

375 K 400

T-

Fig. 1. Cr-x at% V, x = 0.26, 0.51. Molar magnetic susceptibility JJ,,vs. temperature 2’. T,: NCel temperature [94Hl].

Landolt-Bbmstein New Series IW32A

x-

Cr

Fig. 2. V-x at% Cr. Shear modulus G (open symbols) and bulk modulus B (solid symbols) vs. composition parameter x at room temperature. Circles: single crystal, triangles: polycrystalline [78Ll].

1.2.2 Binary alloys between Ti, V, Cr or Mn

118 390 GPO

[Ref. p. 218

105

I

Cr-xat%V

GPO

I

101

380

I\ u,.+\

360 _

'3

G

I

\

+'

L? 102

+'

pureCr‘-+ f \

350

101

:- I I II !I 3

360

103

100

). AA AA,

3301 50

I loo

I 150

I 200

I 250

1

I I

I

99 -50

300 K 350

b

I

’

100

150

200

250

300 K 350

I-

‘Y---t-l

I

125

‘u

140

135

.“”

50

100

0

150

200

250

300 K 350

Fig. 3. Cr-x at% V. Temperature dependence of the elastic constants a c,,. b c+, and c c’ = (c,, - c,,)12 [82Cl]. The data for pure Cr were takenfrom [71Pl] and for the upper curve in c from [79Kl].

T-

1.2.2.4 Mn-Ti

Supplement to LB III/l 9A, p. 295 For the variation of the Ntel temperature of antiferromagnetic alloys of orMn with concentrations of Ti seeFig. 4 and also Fig. 39 in subsect. 1.1.1. Resistivity Fig. 5.

small

Land&-B6mrtein New Series IW32A

1.2.2 Binary alloys between Ti, V, Cr or Mn

118 390 GPO

[Ref. p. 218

105

I

Cr-xat%V

GPO

I

101

380

I\ u,.+\

360 _

'3

G

I

\

+'

L? 102

+'

pureCr‘-+ f \

350

101

:- I I II !I 3

360

103

100

). AA AA,

3301 50

I loo

I 150

I 200

I 250

1

I I

I

99 -50

300 K 350

b

I

’

100

150

200

250

300 K 350

I-

‘Y---t-l

I

125

‘u

140

135

.“”

50

100

0

150

200

250

300 K 350

Fig. 3. Cr-x at% V. Temperature dependence of the elastic constants a c,,. b c+, and c c’ = (c,, - c,,)12 [82Cl]. The data for pure Cr were takenfrom [71Pl] and for the upper curve in c from [79Kl].

T-

1.2.2.4 Mn-Ti

Supplement to LB III/l 9A, p. 295 For the variation of the Ntel temperature of antiferromagnetic alloys of orMn with concentrations of Ti seeFig. 4 and also Fig. 39 in subsect. 1.1.1. Resistivity Fig. 5.

small

Land&-B6mrtein New Series IW32A

Ref. p. 2181 160

1.2.2 Binary alloys between Ti, V, Cr or Mn I

I

K

.

cxMn-xat%M I I

140 120 -

119

.

. ..

0 M-Cr 0 A Yi

I

Am .

? 100

-/+A-#+

I h’ 80

60 40 20

4.5

3.0

1.5

0

1.5

3.0

4.5

Fig. 4. aMn-x at% 3d element. NCel temperature TN vs. composition parameterx as derived from electrical resistivity measurements[76Wl].

ito

X

g 0.90 -

U

3U

IUU

KJU

LUU

L3U TAO

o.750

50

Land&-Bdmstein New Series 111132A

100

o II

50

I ’

100

o.g35 l---kPH

150

I 200

r-

I 250 K 300

T-

T-

lo

0.75 o 0

0

150

T-

I 200

I-

I 250 K 300

Fig. 5. aMn-x at% Ti. Electrical resistivity p relative to its value moo at 300 K as a function of temperature T [76Wl].

120

1.2.2 Binary alloys between Ti, V, Cr or Mn

[Ref. p. 2 18

1.2.2.5 Mn-V Supplement to LB III/l 9A, p. 295-299 Ntel temperaturesof AF alloys of ctMn with V, seeFig. 4 and also Fig. 39 in subsect. 1.1.1. 1.2.2.6 Mn-Cr Supplement to LB III/l 9A, p. 300-3 10 Cr-x at% Mn, x < 1 Neel temperature of AF alloys Fig. 4 and also 39 in subsect. 1.1.1. Magnetic phase diagram Fig. 9 in subsect. 1.1.1. Thermal expansion and bulk moduli Figs. 6, 7.

Crlaa-xMnr Lattice constants Fig. 8 and also Fig. 39 in subsect. 1.1.1. Low-field susceptibility Figs. 9, 10, magnetic phase diagram Fig. 11. Magnetic moments Figs. 12, 13. Thermal expansion Figs. 14, 15, electrical resistivity Fig. 16, specific heat Fig. 17. o phase CrMn, Low-field susceptibility Fig. 18, magnetisation Fig. 19. Curie temperature Tc = 86.2 f 0.3 K and spontaneous magnetisation at 4.2 K: o, = 0.26 G cm’ g-‘. This weak magnetisation suggests canted spins. High-field susceptibility 17.2.10” cm3g-’ [92Pl]. NMR spectra Fig. 20. Thermal expansion Fig. 21. ctMn with Cr dope For the occupation probability of substituted Cr atoms on the four crystallographically different sites of crMn as derived from neutron diffraction spectra, see [86Nl], and for the magnitude of the magnetic moments of substituted Cr on the four different crystallographic sites Fig. 61.

Land&-BOrnstein New Series IW3tA

Ref. p. 2181

.IO~/.Cr-xbt%Mn

1.2.2 Binary alloys between Ti, V, Cr or Mn

1

I

I

I

220

GPa

r?r?/

I

Cr-xat%Mn

200 180 160

140 120

1001, 100

I

I

I

240,

I

I

I

I

I

GPa I 200

I 0)

I

I

I ^ ^^

I X=U.LJ I

160 120

2::

GPa 200 160

80 0

100

200 T-

300

400

K 500

6

Fig. 7. Cr-x at%Mn, x= 0.09, 0.23 0.33. Bulk modulus B vs. temperature T. Trc: transition temperature between incommensurable and commensurable SDW phases. TN: Ntel temperature [87Al]. For x = 0.1 seealso [86Fl] for data up to 280 K.

2 0 0

100

200 T-

300

400 K 5

Fig. 6. Cr-x at%Mn, x = 0.09, 0.23 0.33. Linear thermal expansion coefficient LXvs. temperature T. Trc: transition temperature between incommensurable and commensurable SDW phases. T,: Neel temperature [87Al]. For x = 0.1 seealso [86Fl] for data up to 280 K.

Land&-Bbmstein New Series III/32A

1.2.2 Binary alloys between Ti, V, Cr or Mn

[Ref. p. 218

20

30 40-E cm3 9

15

20 15

25 2.880I car

I 10

I 20

I 30 x-

I 40

I 50

I 60

L” m

70

Fig. 8. Cr,,,O_xMn,.Lattice parameter a of bee alloys homogenised for 48 h at 1100 “C and quenched in ice water: Circles [86Sl], downward triangle [79Ml], triangle [58Pl].

t

I

I 15

25:

N”

20 25

.-

20

10

15 10

~0

30

60

90 T-

120 150 180K 210

Fig. 9. GCr,OO_,Mn,.Magnetic mass susceptibility x, vs. temperatureT. FC and ZFC indicate measurements in the field cooling and zero-field cooling mode, respectively [89Kl, seealso 86Sl].

LandolbB6malein New Series 111132A

Ref. p. 2181

1.2.2 Binary alloys between Ti, V, Cr or Mn 2*103 2.103,

123

I

1

I

I

I

I

60

80

K IO3

I

I

Y AF

:8 AF + spin gloss 3.5 300

Klo

500

700

600

600

K 900

20 Cr

Fig. 10. Cr-x at% Mn, polycrystalline. Low-field magnetic mass susceptibility x, vs. temperature T for various compositions x [85Al].

g

f II.

40

100

x-

Fig. 11. GCrn,O,Mn,. Magnetic phase diagram as derived from neutron diffraction and magnetic susceptibility data [89Kl]. P: paramagnetic, AF: antiferromagnetic.

I 5 CrlOO-xMnx

0.L “.“_

0

0.2

20 Fr

40

60

80

100

x-

Fig. 12. GCr,,,,,-xMnx.Average magnetic moment jj per formular unit as a function of Mn concentration x as derived from neutron diffraction data: Open circles [89Kl], solid triangles [58Kl], open triangles [64Hl], solid circles [79Ml].

Landolt-BOrnstein New Series W32A

0.1

0.2 T/T,

0.3

0.4

0.5

-

Fig. 13. Crso,sMn,s,s,Cr,,Mn,,. Normalised sublattice magnetisation vs. normalised temperature for two alloys of Fig. 12 [89Kl].

124

1.2.2 Binary alloys betweenTi, V, Cr or Mn

[Ref. p. 2 18

Fig. 14. Cr,OO-xMnx.Thermal expansion E vs. temperature. The linear strain E = All/,,,, where I,,, is the length at room temperature. Above a temperature T (indicated by the symbol triangle) the curves are linear. Transition points: Ntel points indicated by arrows, f: AF, + P; &:AF, + P. The arrows indicate the AF,, + AF, ICSDW transition. For x E 0.34 the up and down arrows coincide, corresponding to a triple point [89Bl].

Land&-Barnstein New Series 111/32A

1.2.2 Binary alloys between Ti, V, Cr or Mn

Ref. p. 2181

4 0 I 80 -4

,;o

0

200 300 400 500 600 700K 800 T-

-8

-121 0

I

I

I 40

I 20

Fig. 16. Cr-x at% Mn, polycrystalline. Electrical resistivity p vs. temperature T for various concentrations x [85Al].

I

80 K 100

60 T-

Fig. 15. Crl,,O-XMnX. Linear thermal expansion coefficient a vs. temperature T [89Wl, see also 86Sl]. For comparison are included the curves for Cu, Cr and ctMn [65Wl].

I

0.i

ri”

0.1

I

25

50

75

100

125 K 150

T-

0 tr

20

40

60

80

11

x-

Fig. 17. CrlOO-xMnx. Electronic specific heat coefficient y for various concentrations x. Solid circles [92W2], open circles [6OCl].

Land&-BOrnstein New Series IIU32A

Fig. 18. oCrMn,. Magnetic mass susceptibility ~a vs. temperature 7’, measured in a magnetic field of H= 500e [92Pl].

[Ref. p. 218

1.2.2 Binary alloys between Ti, V, Cr or Mn

126

0.8

I b

0.f

0.4

0.;

40 kOe 50

I

Fig. 19. oCrMn,. Mass magnetisation c vs. applied field Hat 4.2 K [92Pl].

20

30

40

50 Y-

60

70

80MHz 90

Fig. 20. bee Cr,,,O-XMn, alloys. Zero-field NMR spectra of “Mn at 1.4 K as measured by incoherent spin-echo spectrometry with a time separation of 30 ps of the two pulses [86Sl]. 15 40-6 K-1 10

I 5 I

-5

Fig. 21. oCrMn,. Linear thermal coefficient a vs. temperature7’ [92Pl]. 0

50

100

150

200

expansion

250 K 300

Lmdoh-Barnstein New Series lW3ZA

1.2.3 Binary alloys between Fe, Co or Ni and one of the elements Ti, V, Cr or Mn Supplement to LB 111/19A,p. 3 1I-430 Survey

For each of the binary alloys between Fe, Co or Ni and one of the elements Ti, V, Cr or Mn the numbers of figures and tables are given in which data on the properties specified are provided. Numbers in roman and italic refer to figures and tables, respectively. In some casesreferences are given to data mentioned in other subsections. Alloy

Phase diagram, Lattice constants

Magnetic Magnetic susceptibility, phase Paramagnetic diagram properties

Fe-Ti Fe-V Fe-Cr Fe-Mn Co-Ti co-v Co-Cr CoMn Ni-V Ni-Cr Ni-Mn

Magnetization, Average magnetic moment

Atomic NMR Spin waves, magnetic Mbssbauer Exchange moments, effect energy Spin structure 22 24, 2 36,39-42

25-281 51; 38*) 73,74 76 88,89

*) In subsect. 1.1.1

56-58

81, 82 90

34, 3537; 11*>, 12*) 52-55

59,60

7

7

79,80

83, 84 91

94,95 94,102, 103 104

61

Magnetic anisotropy, Magnetostriction

38, 3

62-65,4 75, 8 75, 77, 8,9 75, 78, 8 63, 75,8 109

96 105, 108

Specific heat, Electrical Thermal resistivity, Elastic expansion coefficients 23 33 4446

29-32 47-50

66

67-72,99

86,87 92,93 97, 100, 101

85 98,99

128

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

[Ref. p. 2 18

1.2.3.1 Fe-Ti Supplement to LB III/l 9A, p. 3 16-322 From low-temperature elastic and inelastic diffuse neutron scattering spectra of Fe with less than 3 at?/oTi is derived a magnetic moment of (- 0.50 rt 0.06) pg for the Ti atom. The minus sign indicates a moment antiparallel to the iron atomic moments. The mean-moment perturbation on the two first neighbour Fe shells is (- 0.07 f 0.02) pa [9lPl]. “Fe Mbssbauer data of Ti with x at??Fe in Fig. 22. The spectra display a quadrupole doublet corresponding to PTi (Fe) [85Gl]. For the low-temperature specific heat of antiferromagnetic TiFe, seeFig. 23, Debye temperature @r,= 490 K [9OWl]. 1.2.3.2 Fe-V Supplement to LB III/I 9A, p. 323-337 The influence of magnetic interactions on the atomic short-range order (SRO) of dilute FeV alloys is investigated by neutron scattering and NMR, Fig. 24. For the influence of heat treatment of the alloy on SRO see [82MI, 84P1, 86Pl]. The diffusivity D of V in Fe,-,V, is given by D = Do exp (- EIRT) with D, = 2.0 cm2s-’ and E = 229.8 +32.1x kJ mol-’ [7901]. For the magnetic moments of the individual atoms in the alloys see Fig. 25 and Table 1. For the critical exponent of Fe,,,,V,,, as derived from HhYpvalues is found p= 0.362 It 0.008 in the reduced temperature 1.54.10-’ < (I-TIT,) < 4.88.104 below Tc = 1111.2 K [88Cl]. “Fe Mossbauerdata Figs. 26,27 and Table 2. The hypertine coupling constants are (a) 1735 kOe/s-electron for itenerant s-like electrons, (b) 3240 and 3450 kOe/s-electron for the s-electrons localised in the first- and second-neighbor shell, respectively and (c) 3090 kOe/s-electron, the average value [83Dl]. “V and “Fe spin-echo spectra Fig. 28. Electrical resistivity and magnetoresistanceFigs. 29-32. Specific heat Fig. 33. Table 1. FeloomXVX. Magnetic moment distribution as derived from polarised neutron diffuse-scattering measurementsat 6 K. Aj: different e between averagemagnetic moments of V and Fe atoms i-it : average magnetic moment per atom hFc, jQ : averagemagnetic moment of Fe and V atoms,respectively. All moments in pB [87Ml]. Numbers in parenthesesgive the error in the last decimal.

0 1.1 2.0 2.7 5.8 10.1 14.7 20.6

-

3.109(25) 3.354(21) 3.269(28) 3.350(29) 3.303(3 1) 3.005(58) 2.894(25)

‘) As determined by [72A I]. b, As determined by [71Cl].

2.217 b, 2.187(5) 2.163(8) 2.140(15) 2.044(23) 1.899(25) 1.740(30) 1.540(36)

-

0.89(3) 1.13(3) 1.04(5) 1.1l(5) 1.07(6) 0.82(8) 0.76(6)

+2.22 l(6) +2.228(g) +2.229(16) +2.240(25) +2.232(28) +2.183(39) +2.135(41)

Ref. p. 2181

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

129

Ti -x at % Fe 57~e 1.00

------\

0.98 0.96 0.94 1.00 0.98 0

IO

30

20

40

K* 50

T2 -

0.96 0.94

Fig. 23. TiFe,, polycrystalline, annealed. Temperature dependenceof the molar specific heat CP, plotted as CJTvs. T* [9OWl].

0.96

-z 1.00 2 S 5 0.98 s 2'in 0.96 E 5 0.94 k

0.98

0.98

c

Fig. 22. f3Ti-x at% Fe, annealed for 2 h at 1000 OC,

0.98 -1.0

-0.5

0 Y-

Land&-Bbmstein New Series 111132A

0.5

1.0mm/s 1.5

water-quenched. “Fe Mijssbauer spectra at room temperature[85Gl].

130

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

[Ref. p. 218

Table 2. Feloo-xVxalloys. Mbssbauer data at room temperature as a function of the composition parameterx. H,,$O,O): magnetic hyperfine field on Fe atomsthat have no V atoms as near or nearestneighbour. Hhyp: average magnetic hyperfine field IS(O,O) : absolute isomer shift AK(O,O) : isomer shift relative to pure Fe [83Dl] Hyperfine fields in kOe , isomer shifts in mm s-’ X

%,

0 1.40 3.00 5.13 7.53 10.4 13.7 17.8

-

331.8 332.7 334.55 336.5 338.5 340.6 342.8 342.5

- 331.8 - 329.3 - 321.2 - 317.7 -311.65 - 303.5 - 293.9 - 278.2

-

0.098 0.095 0.096 0.092 0.089 0.0915 0.087

0.010 0.014 0.012 0.016 0.020 0.018 0.022

‘) The averagehypertine field shift is - 30.05 kOe and - 20.0 kOe for a V atom as the first- or second-nearest neighbour of a probe nucleus, respectively. b, The average change of the isomer shift is - 0.0191 mm s-’ and - 0.0106 mm s-’ for a V atom as the first- or second-nearestneighbour of a probe nucleus, respectively. O.jo-* l\,

I boo-x"x

-\ -0.2 'A

'\X=ZO

-04 neutron

-0.6 a

I

Fig. 24. Fe,OO-XV,alloys, annealed until equilibrium and quenched. Short-range order parameter (SRO) Et2 / x vs. relative reciprocal temperature T,IT, where Tc is the Curie temperature. El* = (8a, +6az) I14 with a, the SRO parameters in the Cowley sense. Measured either by a neutron diffuse scattering experiments or b NMR [86Pl].

Ref. p. 2181

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

131

2.2

2.1

I 2.0 I,I.9 IQ i IQ

I 1

1

Fig. 25. FeroO,V,, polycrystalline, quenched from the melt. Average magnetic moments of the Fe and V atoms, PFe and &, respectively, vs. composition parameter x measured at 6 K, derived from (solid circles) polarised neutron diffuse-scattering [87Ml], and from unpolarised neutron diffuse scattering (open circles) [82M2], (triangles) [77Yl]. Broken and full curves show CPA calculations of [78Hl] and [83Hl], respectively.

0

I 5

-2' -2 0 Fe

I 10

I 15

I 20

I 25

I 30

x-

335 kOe 325

0

Fe

3

6 x-

9

12

15

18

Fig. 26. Fe,,,O-xVxalloys. Magnetic hyperfine field Hhyp(O,O)on Fe atoms that have no near or nearest V neighbours, as derived from 57FeMijssbauer spectra of alloys with various composition parameters x at room temperature [83Dl]. Open circles represent data obtained for samplesdoped with Sn.

Landolt-Biirnstein New Series III/32A

215 0 Fe

3

6

9

12

15

18

x-

Fig. 27. Feu,O-xV, alloys. Average hyperfine field Hhyp at room temperature as a function of composition parameterx. The dashed curve applies to a simple dilution law [83Dl]. Open circles represent data obtained for samplesdoped with Sn.

132

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

Fe-xat%V

[Ref. p. 2 18

T= 4.2K

1=4.2K I

0.57

0.22

335

b

337

339

341

If-hyp

343

345 kOe 347

2.81 85

86

87

88

NhYP -

120

P--

--’

89

90

1 91 kOe

Fig. 28. Fe-x at% V. Spin-echo spectra of the main line at 4.2 K. a “V [82Ll], b “Fe [83Ll].

(F%,-A)83 47 T=SK

I

90

a”

60

Fig. 30. Fe,,,O-nVx,crystalline, annealed for 1 h at 900 “C; (Fe,o,-,V,h3B,7. amorphous, quenched. Residual electrical resistivity pO at 4 K vs. composition parameterx [93JI].

3c

0

4

8

x-

12

16

20

Landolt-BWnstein New Series llV32A

Ref. p. 2181

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

Fig. 29. Fe,OO-xVx. Parker plots: impurity contribution (Aplpo)i,, and electron phonon contribution (Aplp,),, to the change of the electrical resistivity between temperaturesof 273 K and 77 K. p,, is the resistivity at 4.2 K The square applies to pure Fe at room temperature. The dashed curve is theoretical [71S1, 88Bl].

80

I 60 \a 8 40

20

0

Fig. 31. Fe,oo-xVx,annealed polycrystalline samples. Longitudinal (II) and transverse (I) magnetoresistance Aplp vs. applied magnetic field Hat 4.2 K [71Sl].

-20 0

3

LandohB6rnstein New Series IW32A

6

9 H-

12

15

18 kOe Z

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

134

[Ref. p. 218

I

Fe,,:-XV,

T=213K

I

I

II, x =5.5 I-

11,10.8 c

0

3

6

9

12

15

18 kOe 21

c

12

8

16

20

x-

Fig. 33. FeloomxVx, crystalline, annealedfor 1 h at 900 ‘C; (Fe,00-xVx)83B,7,amorphous, quenched. Specificheat coefficienty vs. compositionparameter x [93Jl].

Fig. 32. Fe,,,O.xV,,annealedpolycrystalline samples. Longitudinal (II) andtransverse(I) magnetoresistance Ap!p vs. appliedmagneticfield Hat 273 K [71Sl].

1.2.3.3 Fe-Cr Supplement to LB III/I9A, p. 338-361 Magnetic phase diagram Fig. 34. The character of the phases present in nearly equiatomic Fe-Cr alloys as dependent on the heat treatment has been investigated by room-temperature Mlissbauereffect studies [93Dl]. The various stagesof phaseseparationprocessesin Fe-Cr alloys in relation with “spinodal” segregation has been examined by neutron small angle scattering techniques [86F2]. A change of sign in the SRO parametersin alloys Fe,,,JZr, near x = 10 indicates that the alloy exhibits short-range clustering at x > 10 and a tendency to form ordered compounds for x < 10 [84Ml]. For magnetic phase diagrams of Fe-0 alloys with small Fe content see Figs. 11 and 12 of subsect. 1.1.1 and Fig. 35. Mlissbauer spectra show an anomaly in the magnetic hyperfine field which is attributed to a transition from a ferromagnetic to a spin-glass state, [85D2] and Fig. 36. The reentrant spin-glass temperature Tr as a function of an applied magnetic field for the alloy Fe,,Cr,s is reproduced in Fig. 37. For a theoretical treatment see [93Al]. For spin-wave stiffness constants D see Fig. 38. Results of high-resolution inelastic neutron scattering seemto indicate that at low temperature spin waves can only be induced by the application of a magnetic field [88Ll, 89B2]. Landolt-B6mstein New Series llV3ZA

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

134

[Ref. p. 218

I

Fe,,:-XV,

T=213K

I

I

II, x =5.5 I-

11,10.8 c

0

3

6

9

12

15

18 kOe 21

c

12

8

16

20

x-

Fig. 33. FeloomxVx, crystalline, annealedfor 1 h at 900 ‘C; (Fe,00-xVx)83B,7,amorphous, quenched. Specificheat coefficienty vs. compositionparameter x [93Jl].

Fig. 32. Fe,,,O.xV,,annealedpolycrystalline samples. Longitudinal (II) andtransverse(I) magnetoresistance Ap!p vs. appliedmagneticfield Hat 273 K [71Sl].

1.2.3.3 Fe-Cr Supplement to LB III/I9A, p. 338-361 Magnetic phase diagram Fig. 34. The character of the phases present in nearly equiatomic Fe-Cr alloys as dependent on the heat treatment has been investigated by room-temperature Mlissbauereffect studies [93Dl]. The various stagesof phaseseparationprocessesin Fe-Cr alloys in relation with “spinodal” segregation has been examined by neutron small angle scattering techniques [86F2]. A change of sign in the SRO parametersin alloys Fe,,,JZr, near x = 10 indicates that the alloy exhibits short-range clustering at x > 10 and a tendency to form ordered compounds for x < 10 [84Ml]. For magnetic phase diagrams of Fe-0 alloys with small Fe content see Figs. 11 and 12 of subsect. 1.1.1 and Fig. 35. Mlissbauer spectra show an anomaly in the magnetic hyperfine field which is attributed to a transition from a ferromagnetic to a spin-glass state, [85D2] and Fig. 36. The reentrant spin-glass temperature Tr as a function of an applied magnetic field for the alloy Fe,,Cr,s is reproduced in Fig. 37. For a theoretical treatment see [93Al]. For spin-wave stiffness constants D see Fig. 38. Results of high-resolution inelastic neutron scattering seemto indicate that at low temperature spin waves can only be induced by the application of a magnetic field [88Ll, 89B2]. Landolt-B6mstein New Series llV3ZA

Ref. p. 2181

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

135

constants D see Fig. 38. Results of high-resolution inelastic neutron scattering seemto indicate that at low temperature spin waves can only be induced by the application of a magnetic field [88Ll, 89B2]. For an analysis of the magnetic phase diagram on the basis of Mijssbauer spectra in the compositional region where spin glass behavior is expected, see Figs. 39-42. For low concentrations of Fe in Cr the magnetisation distribution is given in Table 3. Spin-echo spectra in Fig. 43. Thermal expansion coefficients in Figs. 44,45. Specific heat Fig. 46, electrical resistivity and magnetoresistance Figs. 47, 48. Magnetoelastic properties Figs. 49, 50. Anomalies are found in the spin-glass phase, in the ferromagnetic region no anomalies are found [92A 11. Table 3. Cr,,,-,Fe,. Magnetic moment distribution as derived from the magnetic elastic diffuse scattering of polarised neutrons at low temperature T. The Fe moments pFe are oriented parallel to the SWD, the Cr moments per are not significantly disturbed by the Fe atoms [88Ml]. Numbers in parenthesesgive the error in the last decimal.

Alloy

PFe

Cr-2.8 at% Fe, single crystal Cr-4 at% Fe, polycrystalline

K I Fe100-xcrx 1100

I cL_-_ _^I

1 MJ'L 1 , IIn-q

bB1

kB1

4.2 11.5

2.13(5) 1.8(l)

0.72(2) 0.72(2)

I

2.75

1000

2.50

900

2.25

800

2.00

700

1.75

600

I 14 1.50

500

1.25

400)

I

I I

\ \

h

I

( 1.00

300

0.75

200

0.50

100

0.25

0 Fe

Land&-BBrnstein New Series IW32A

20

40 x-

60

Per

TKI

80 %7-

0 Cr

Fig. 34. Fe,oo-.$rX.Magneticphasediagram[9OW2]. Opencircles: magnetictransition temperaturesr,-, TN [83Bl]. Dashedcurve: averagemagneticmomentper atom, j?, [78Bl]. Triangles:T, [86F2]. Solid circles: j? [76Al]. RSG:reentrantspin glass;SG: spin glass. The spinoidal decompositionof the high temperature 0 phase occurs at 440(20)“C [80Rl] or 570 “C [86F2].

[Ref. p. 218

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

136 350

K 300 250 zoo 1 b-T 150 100 50

0

2.5

5.0

I.5 x-

10.0

12.5

15.0

17.5

Fig. 35. Fe,eoJr,. Ntel temperature as a function of composition as derived from measurementsof (open circles) longitudinal sound velocity and (triangles) thermal expansion coefficient [92Al]. Full curve and dashed curve: averages through experimental points obtained by other techniques [83Bl]. P: paramagnetic.

60

Llll ,0

I 10

I 30

I 20

I LO

K

I 50

T-

Fig. 36. Fe&r,,. Average magnetic hypertine field &,(H) vs. temperature T measured in various applied magnetic fields p,,H. Hty$ is the measured peak hyperfine field in the case pOH= I .05 T [85D2]. Solid symbols: increasing temperature,open symbols: decreasingtemperature.

I

25

c

Fig. 37. Fe,@,,. Reentrant spin-glass transition temperature Tr as a function of an applied magnetic field H, as derived from 57FeMbssbauer spectroscopy data. The types of symbols refer to three different kinds of interpretations of the measuring results [87Dl].

20

10: 0

5

10

15 H-

20

25 kOe 30

Ref. p. 2181

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

137

130 kOe 120

100

6

90 I a

I 5 a4

3

80 I

70

s Ix 60 50 0 0

30

60

90 T-

Fig. 38. Fe&r,,. Spin wave stiffness constant D vs. temperature T as derived from high-resolution inelastic neutron scattering measurements.Analysis on the basis of a double Lorentzian oscillator: circles [81Sl], downward triangle [SSLl], idem on the basis of a dampedharmonic oscillator: triangle [SSLl].

40

/

/

j

/

120

130

140

30 20

100

-Li

+

110

I-

150 K 160

I

IO

0

50

100

150 T-

200

250

300 K 350

Fig. 39. Fe&r,, doped with 0.6 at% “‘Sn. Sample homogenisedfor 24 h in vacuum at 1000 “C followed by quenching in oil. Temperature dependence of the average hyperfine field Htr,,r,obtained from 57Fe-site and ‘igSn-site Mijssbauer spectra. Insets: enlarged detail for the temperature region where magnetic order occurs. The linewidth of the single-line spectrum is r[84Dl].

Landolt-BOrnstein New Series IW32A

138

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

[Ref. p. 2 18

80 kOe 60

-60

-100 a

x-

Cr

Fe b

Fig. 40. bee FexCr,OO-X. Magnetic hyperfine fields HhYp vs. composition parameterx for a Fe and b Cr atoms. Theoretical curves: non-relativistic total and core

I

0

I

50

100

150 I-

n-b--

200

250

300 K 350

c”r

20

40

x-

60

80

hyperfine fields. Dot-dash curves: calculated total relativistic hyperfine fields [gOElI. Experimental: Fe [63JI], Cr [82LI, 83L.21.

Fig. 41. FeXCr,OO-xrx = 13.3, 25, doped with 0.7 at% ‘19Sn.Temperature dependenceof the average hyperfine field Ift,,n obtained from S7Fe-site and “‘Sn-site Mtissbauer spectra. For comparison the dashedcurves representthe curves of Fig. 39. Inset: a temperaturederivative of the 57Fe-sitecurve for Et,m, x = 13.3. b Probability P(N) for finding N Fe atoms as nearest neighbours around an 57Fe probe atom, as measured (full curve) and as expected from random Fe-Cr distribution (dashedcurve) [85Dl].

Landolt-Barnstein New Series lllll2A

Ref. p. 2181

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

300

139

93 .

250 + . 1 h"

200 .

19

22

25

Fig. 42. Fe.$rr,,,,-, for 20 I x I 35. Survey of the Curie temperature Tc as found in various investigations, showing the high sensitivity of the magnetic properties on the chemical order in the sample. The triangles l-3 apply to samples with increasingly homogeneous distribution of the atoms [84Dl]. 1 [75Hl], 2 [75Ll], 3 [77Al], 4 [77Nl], 5 [78Rl], 6 [81Sl], 7 [83Bl], 8 [84Dl]. 28

31

34

x-

Fe-xat%Cr

53Cr

7=4.2K

T=1.2K x=0.25

IIlLl

x=1.30

350

355

x=0.6

kOe

H hyp-

Fig. 43. Fe-x at% Cr. Spin-echo spectra of the mainline. a 57Feat 4.2 K [83Ll]; b 53Crat 1.2 K [82Ll]. f b Land&-Bbmstein New Series IIV32A

-.

63

-.

66

69 Hhyp-

72

kOe 75

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

50

100

150

200

250

300 K 350

a

50

100

150

100

150

b

[Ref. p. 218

200 T-

250

300 K 350

200

250

300 K 3 O

6

-4 0

T-

Fig. 44. 0-x at% Fe. Thermal expansion coefficient a vs. temperature T for various compositions x. The broken curves in a and b represent CI for the alloy

50

T-

Cr-5 at% V, which is paramagnetic at all temperatures. For x = 25 and x = 30 no anomalies were observed in the temperaturerange 77...450 K [92Al].

Landolt-B6rnrrein New Series 111132A

141

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

Ref. p. 2181

80 i&i 70

60

I 50 i: 40

30

I

500

650

800

950

1100 K 1250

T-

Fig. 46. Fe&r,, alloy. Molar specific heat C,, vs. temperature T. Measuring points: W.Pepperhoff. Full curve: calculated. Dashed curve: nonmagnetic contribution [8111].

100

200

300

400

K

!

TFig. 45. Cr,OO-XFeXalloys. Thermal expansion expressed as the linear strain E= Al/l,,,, where lzg3is the length at room temperature. Transition points: TN indicated by arrows and the AF,-AF, ICSDW phase transition temperature Tic by crosses[89Bl].

Land&-Bbmstein New Series 111132A

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

142

[Ref. p. 218

-1.2 I -1.4

-41 0

Fe

I 10

I 20 x-

I

I

I

30

40

50

Fig. 47. FerwxCrx, annealed at 840 “C slowly cooled. The samples x = 32.2 and 41.1 annealed at 1250 ‘C, quenched in oil. Parker plots: impurity contribution , (Ap/&m, and electron-phonon contribution, (A@&,hr to the change of the electrical resistivity p for temperatures of 299 K and 77 K. The square applies to Fe at room temperature. p0 is at 4.2 K [88BI].

\a -1.6 2 -1.8 -2.0

-6

-'Oo

10

20

30

40

50

60 kOe70

H-

Fig. 48. aFe25Cr,s,Fe,Ni,,_,Cr,,. Longitudinal (open circles) and transverse (solid circles) magnetoresistante Aplp at 4.2 K vs. applied magnetic field strenght H [93Bl]. Ap/p = (p(H) - p(O))/p(O).

Lmdolt-BBmstcin New Scrin 111132A

Ref. p. 2181

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

.,_I”

350 GPO

::“,L,: Gpo Cr - x at”/ Fe

320

II

290

G

260

a

:::l--mT-l 0 100

200

300

230 0

400 K 500

T-

100

200 T-

I 100

I 200

I 100

I 200 T-

b

300

400 K 500

300

400 K 500

I 300

I I 400 K 500

340 - .” GPO 335 II 330 uu325 320 3151 315’ 0

325 320

100

I 300

200

3151 0

I 400 K 500

d

T335 GPO

I 6

325 c; 320

315 0 330, 330 GPO

325 320

100

200 T-

300

400

315’ 0

K 500

f I

I

320

I

300 300’ 0 EC

Land&-Biirnstein New Series IIV32A

I

100

Iu,

200 T-

I x=20 I

300

400

K 500

Fig. 49. Cr-x at% Fe, homogenised for 72 h at 1000 “C. Samples x I 10 furnace-cooled, the other quenched. Elastic constant, cL = pvz, as a function of temperature r, where p is the density and vL the velocity of longitudinal sound waves of 10 MHz. No magnetic contribution is found in the case of shear waves [92Al].

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

60

90

13

I-

150

180

210 K 240

[Ref. p. 218

Fig. 50. Cr-1.5 at%Fe, sample as in Fig. 49a. MagneticcontributionAB to the bulk modulusB, as a function of temperatureT [92Al].

1.2.3.4 Fe-Mn Supplement to LB 111/19A,p. 362-373 A small amount of titanium (z 3.0 at%) allows the stabilisation of the bee phase of disordered Fe-Mn alloys up to 17.5 at% Mn [91P2]. For the lattice constants see Fig. 51 and also Fig. 39 in subsect. 1.1.1. There exists someambiguity about the short range order in annealedFe-Mn alloys with small concentrations of Mn [82Pl, 9lPl]. For the occupation probability of substituted Fe atoms on the four crystallographically different sites of cxMn as derived from neutron diffraction spectra see [86N I]. The uncertainty in the magnetic structure of y-type Fe-Mn alloys, see Fig. 52, is partially lifted by an analysis of Mossbauer transmission spectra at 4.2 K of a Fe,,,,Mn,, 2 single crystal. The results are not consistent with the [OOI] model (a) of a collinear antiferromagnet, but they seem to fit both the [ 1IO] and [1 1l] models (b) and (c), respectively [87Kl]. However, from a combination of spin-density measurements using elastic and inelastic neutron scattering on a single crystal of Fe,,Mn,, it is deduced that the magnetic structure should be collinear [87Bl]. Curie temperature of bee Fe-Mn alloys Fig. 53, fee Fe-Mn alloys Fig. 54, and aMn-type alloys Fig. 55. Influence of hydrostatic pressure on TN of fee Fe,,Mn,,,: dT,ldp = - 2.5 K bar-’ [78El]. Magnetic susceptibility of fee alloys Figs. 56a, b and for the influence of additions of C or Ge Figs. 57, 58. Magnetisation curves of bee Fe-Mn alloys Fig. 59, and the corresponding mean magnetic moment per atom, Fig. 60. For the magnetic moments of Fe atoms substituted at the four different sites of aMn, seeFig. 6 1. From low-temperature elastic and inelastic diffuse neutron scattering spectra of aFe with less than 3 at% Mn is derived a magnetic moment of pHn= 0.62 + 0.05 pB for the Mn atom, oriented parallel to the direction of the iron moments. The moment perturbation for the atoms in the two first-neighboring shells is - 0.07 f 0.02 pt, [91Pl], in good agreement with calculations [89Dl]. NMR spectra of bee Fe-Mn alloys in Fig. 62. Influence of pressure on NMR Fig. 63. Magnetic hyperfine field in /3Fe-Mn alloys Fig. 64. MSssbauer data for bee Fe-Mn alloys and for yFe-Mn sampleswith various concentrations of Ge seeFig. 65 and Table 4, respectively. Thermal expansion coefficient Fig. 66. For elastic and non-linear acoustic properties see Tables 5,6 and Figs. 67-69 and Fig. 99. Phonon dispersion curves for Fe,,Mn,, in Fig. 70. For electrical resistivity see Figs. 71, 72.

LandoIl-Bbmstein New Series 111/32A

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

60

90

13

I-

150

180

210 K 240

[Ref. p. 218

Fig. 50. Cr-1.5 at%Fe, sample as in Fig. 49a. MagneticcontributionAB to the bulk modulusB, as a function of temperatureT [92Al].

1.2.3.4 Fe-Mn Supplement to LB 111/19A,p. 362-373 A small amount of titanium (z 3.0 at%) allows the stabilisation of the bee phase of disordered Fe-Mn alloys up to 17.5 at% Mn [91P2]. For the lattice constants see Fig. 51 and also Fig. 39 in subsect. 1.1.1. There exists someambiguity about the short range order in annealedFe-Mn alloys with small concentrations of Mn [82Pl, 9lPl]. For the occupation probability of substituted Fe atoms on the four crystallographically different sites of cxMn as derived from neutron diffraction spectra see [86N I]. The uncertainty in the magnetic structure of y-type Fe-Mn alloys, see Fig. 52, is partially lifted by an analysis of Mossbauer transmission spectra at 4.2 K of a Fe,,,,Mn,, 2 single crystal. The results are not consistent with the [OOI] model (a) of a collinear antiferromagnet, but they seem to fit both the [ 1IO] and [1 1l] models (b) and (c), respectively [87Kl]. However, from a combination of spin-density measurements using elastic and inelastic neutron scattering on a single crystal of Fe,,Mn,, it is deduced that the magnetic structure should be collinear [87Bl]. Curie temperature of bee Fe-Mn alloys Fig. 53, fee Fe-Mn alloys Fig. 54, and aMn-type alloys Fig. 55. Influence of hydrostatic pressure on TN of fee Fe,,Mn,,,: dT,ldp = - 2.5 K bar-’ [78El]. Magnetic susceptibility of fee alloys Figs. 56a, b and for the influence of additions of C or Ge Figs. 57, 58. Magnetisation curves of bee Fe-Mn alloys Fig. 59, and the corresponding mean magnetic moment per atom, Fig. 60. For the magnetic moments of Fe atoms substituted at the four different sites of aMn, seeFig. 6 1. From low-temperature elastic and inelastic diffuse neutron scattering spectra of aFe with less than 3 at% Mn is derived a magnetic moment of pHn= 0.62 + 0.05 pB for the Mn atom, oriented parallel to the direction of the iron moments. The moment perturbation for the atoms in the two first-neighboring shells is - 0.07 f 0.02 pt, [91Pl], in good agreement with calculations [89Dl]. NMR spectra of bee Fe-Mn alloys in Fig. 62. Influence of pressure on NMR Fig. 63. Magnetic hyperfine field in /3Fe-Mn alloys Fig. 64. MSssbauer data for bee Fe-Mn alloys and for yFe-Mn sampleswith various concentrations of Ge seeFig. 65 and Table 4, respectively. Thermal expansion coefficient Fig. 66. For elastic and non-linear acoustic properties see Tables 5,6 and Figs. 67-69 and Fig. 99. Phonon dispersion curves for Fe,,Mn,, in Fig. 70. For electrical resistivity see Figs. 71, 72.

LandoIl-Bbmstein New Series 111/32A

Ref. p. 2181

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

145

Table 4. yFeMnGe alloys. 57FeMossbauer data at room temperature. IS: isomer shift relative to cxFe; Hhyp: average value of the hyperfine field. The quadrapole splitting is zero [9OY11. Mn

Ge

C

IS

[atO/,]

[atoh]

[at%]

[mm s-‘1

We1

31.52 30.02 29.87 29.49 28.1 la)

2.01 3.45 5.63 8.73

0.20 0.18 0.14 0.10 0.08

- 0.025 - 0.01 - 0.008 0.034 0.054

26.55 24.14 23.36 19.97 12.48

‘b,

“) y phasewith a traceof Ephase. Table 5. yFe,,Mn,,, single crystal. Elastic and nonlinear acoustic properties at room temperature as derived from ultrasonic wave velocities of 10 MHz pulses along the [ 1lo] crystallographic direction. d: density; cij: elastic constants; c’= (c,, - c,,)/2; B: bulk modulus; p: hydrostatic pressure. For comparison the properties of other Invar-type alloys (Fe,,Ni,, and Fe,,Pt,,) and of the elements Fe and Ni are also given [93Cl]. Numbers in parenthesesgive the error in the last decimal. Fe60Mn40 [93Cl] d

Cl1 c44

Cl2 c’ = (c,, - c,J2 B @Cl@P>p =0 @c ,2/3P)P)p =0 @44l3P)p=o

(ac ‘lap), =0 CaBlaP), =0

[kg mJ]

7820 170(l) 141(l) [GPa] . 98(2) [GPa] 36(l) 123(2) l?W 10.1 7.1 3.8 1.5 8.1

Wal Wal

Fe65Ni35 [92Ml] 8121 136(l) 98(l) 92(2)

Fe7& [92Ml] 11939 144(1) 80(l)

107(2)

22(l)

18(l)

107(2) 5.2 -2.1 5.7 3.6 0.3

120(2) - 19.2 -26 0.6 - 18 - 23.7

Ni [79Hl]

Fe [79Hl]

8900 247 122 153 47 184 6.0 4.7 2.4 0.6 5.3

7873 230 117 135 47 167 6.7 4.6 2.6 1.0 5.3

Table 6. yFe,,Mn,, single crystal. Temperature dependenceof the hydrostatic pressure derivatives of the various elasticity coefficients given in Table 5 [93Cl]. cL = (cl1 + c,~ + 2c,,)/2. Numbers in parenthesesgive the error in the last decimal.

T WI 293 313 333 353 373 393 413 428 453

Landolt-Bornstein New Series II1132A

(acLmp =o 12.45(20) 10.99(20) 8.69(20) 7.78(20) 7.96(20) 7.23(20) 7.46(20) 6.22(20) 6.99(20)

(ac44eop =o 3.84(6) 3.72(9) 2.72(5) 1.18(10) 2.68( 10)

(aBe-9,=o 1.46(5) 1.57(4) 0.53( 1) 0.41(l) 0.37( 1)

8.12(10) 6.75(10) 5.80(10) 6.47(10) 5.16(10)

[Ref. p. 218

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

146

y Fe-Mn

? lizLl3

2.86

0

0

x-

12

16

20

Fig. 51. bee Fe,OO..xMnx alloys. Lattice constant o at room temperature vs. composition parameter x. The alloys have been stabilised by addition of about 3 at% Ti to the melt [91P2].

Fig. 52. y-type Fe-Mn alloys. Energetically favoured magnetic structures [66Ul].

Fig. 53. bee Fe,,,-,Mn, alloys. Ferromagnetic Curie temperature rc vs. composition parameter x: Circles [69Al]; triangles [74Y 13; downward triangles: thermogravimetric determination, for x > 5 the structure has been stabilised by addition of about 3 at% Ti to the melt [91P2].

Landoh-Bbmsrein New Seriu 1W32A

Ref. p. 2181

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

147

600 K

I

500

500

400

400

300

I b.

200

300

200

100

a

U

x45C K

l

b I

I

I

425

4oc

1 375 l-z=

Fig. 54. fee Fe,,,O-xMnxalloys. a NCel temperature TN vs. composition parameterx. T, is considered to be a transition temperature to a spin-glass-like phase. b Influence of C additions on these transition temperatures [88Sl]. c Influence of Ge substitutions on TN as derived from magnetic susceptibility measurements[9OY13.

3%

325

300 c

K I

50

I

. M=Cr

-x Landolt-Biirnstein New Series 111/32A

cxMn-xat%M

I

Fig. 55. cxMn type alloys Fe,Mn,,,, and Cr,Mn,,,-,. NCel temperature TN vs. composition parameter x. Specific heat measurements: open circles [86Nl], electrical resistivity measurements: squares [86Nl], solid circles [76Wl].

M=Fe

x-

148

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

[Ref. p. 218

25

4 10 0 a

Fig. 56. a

1 yWb5

200

coo

600

T-

yFe&fn2S:

o.*/ 0

K

b

yFeo 7sMno2MX

y(Fe, 7shJno2F),00-nAIx.Magnetic volume susceptibility ~1. vs. temperature T measuredin a magnetic field H = 955 kA/m. T,: NCel temperature[86Zl].

150

I 300

450

6GU

K

i0

I-

b fee Fe,oo.xMnxalloys. Magnetic mass susceptibility x, vs. temperature T, measuredin a magnetic field of 50 Oe. Inset: influence of field cooling (FC) and zerofield cooling (ZFC) at low temperatures. T,: Ntel temperature. T, is considered to.be the temperature of a transition to a spin-glass-like phase. The arrows along the curves indicate the measuring sequences [88Sl].

Landolt-Bbrnstein New Series 111132A

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

Ref. p. 2181 1.6 *10-s cm3 75 1.4 1.3

t 25

1 1.2

4

s 1.1 IS 0.E

0.f

“0 150

300

T

450

Fig. 57. fee (Fe0,,Mn0,3)10r,-xCx. Influence of C additions on the magnetic susceptibilities as derived from the curves of Fig. 56 [88Sl].

4

6

8

kOe 10

300 T-

$00

500 K 600

Fig. 58. fee (Fe,,,Mn,,,),,,_,Ge,. Influence of Ge additions on the volume magnetic susceptibility xv [9OY 11.

0 2

200

100

600 K 750

Fe

2.5

5.0

7.5 x-

10.0

12.5

15.0

17.5

H-

Fig. 59. bee Fe,OO-xMn,alloys with 3 at% Ti added. Mass magnetisation 0 vs. applied magnetic field H at 10 K for various values of the composition parameter x [91P2].

Land&-BWnstein New Series lIV32A

Fig. 60. bee Fel,,,,-xMnx alloys with 3 at% Ti added. Mean magnetic moment per atom, &, vs. composition parameterx, as derived from the curves of Fig. 59 [91P2].

150

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

3.0.

h

I

Mn-xot%M

Fe97.L7 Mn 2.53

bee

-1 III

I 1.5 z 2 a”

1.0

0.5

[Ref. p. 218

f ri.

I

200

210

220

230

240 MHz 2

Y-

I

I

I

I

0.1 -x

0

0.1

0.2

0.3

OX

x-

Fig. 61. aMn with x at% substitutional Fe or Cr atoms. Iron and chromium magnetic moments, pFe, per, vs. concentration x for the atoms on each type of the four different crystallographic sites I-IV [86Nl].

Fig. 62. bee Fe,,,,,Mn,,,,. NMR spectra of “Mn nuclei at room temperature.Curve A before and curve B after annealing for one day at 820 “C. Inset: detail of spectrumB. S,, S, and S, resonancepeaks probably related to various short-range ordered atoms [82Pl].

Landok-Bdmsrein New Series III132A

Ref. p. 2181 241.5

151

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn I

I

MHz Fe- 0.5 at %Mn

ki;

T= 4.2K

p Mn lx ot%F/

241.0

$

25

240.5

T=1.4K

p

30

I 240.0 I

Al

0

A

v

IO

20

30

Sb 50

40

x-

“IT

0

2

Fig. 64. SMn alloys with x at% Fe, Co, Ni, Ir, Ru, In or Sb. 55Mn internal magnetic fields Hhyp at 1.4 K as 8 kbar 10 determined by NMR spin-echo technique [74Kl].

6

4

P-

Fig. 63. Fe-O.5 at% Mn; Co-O.5 at% Mn. “Mn NMR frequencies v vs. applied external hydrostatic pressure p at 4.2 K [86Kl]. 30

315

kOe

Y ho-,% .0x=39.7

Try

350

___ 2.5

5.0

Fe

7.5 x-

10.0

12.5

15.0

/d , ‘;r

17.5

Fig. 65. bee Fe,,,-,Mn,

alloys, with 3 at% Ti for stabilisation of the structure. Magnetic hyperfme field HhYpas derived from the various peaks in the “Fe Mossbauer spectra at room temperature. The various peaks are considered to be related to particular Fe-Mn configurations as indicated by the number of nearest neighbor (NN) Mn atoms in the vicinity to the Fe atoms [91P2]. Landolt-Btmstein New Series IIV32A

0

150

300

450

600

K

750

T-

Fig. 66. yFe,,,-,Mn,; (Fe, ,Mn,,,),,,&,. Linear thermal expansion coefficient cx vs. temperature T. The range of the NCel temperature values TN for both systemsis also indicated [88Sl, seealso 76R1, 78El].

152

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn 155 GPO-z+.. ‘2. \ 145-

[Ref. p. 2 18

\\ ‘\

135 s - 125. 125

-I 115 105 1 1050

a

b

SC GPO 45

150

I

3

T-

450

600

K 750

v I I I I 140 \

I

!

I

1001 0

' 150

I 300

I 450

4C I -cl 35

600

K 750 d

Fig. 67. yFe,,Mn,,. Temperature dependence of the elastic stiffness constants cL = (c,, + cl2 + 2c,,)/2, cq4 and c’ = (c,, - c,,)12 and the bulk modulus B. Dashed

T-

I 600

K :

curves represent theoretical extrapolations [93Cl]. For similar properties of yFe,,Mn,, see[81E1].

Landolt-Barnstein New Series 111/32A

153

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

Ref. p. 2181

10 a I 3 -10 s-2 \ s -20 -30 -4c

a

250

a

300 T-

350

400

I

250

300

350

400

450 K 500

T-

b

Fig. 68. yFe,,Mn,,. Temperature dependence of the hydrostatic pressure derivatives of the longitudinal elastic stiffness constant, (&,l@)l,=, and of the bulk 300 GPO

‘-200

450 K 500

modulus, (c%/@)~=~. For reference the curves for Fe,,N,, [88Rl] and Fe,,Pt,, [92Ml] are also given [93Cl].

I 1Fe7”Mn2”INS 1

34 30’ a

T

100

200

300

400

500

400

500

T-

b

3

600 K 700

150 GPO 140 130 I 120 27 110

160 a

a

100

200

300

400

500

600 K 700

r-

Fig. 69. Fe,&ho, Fe,,Mn,,, MnsI.sNiIs.s,Mn8,Ni15, single crystals. Elastic constants cc, c’ and cA4as a function of temperature 2’ as compiled by [9OW2]. Ultrasound measuring results: (triangles) Fe,,Mn,, Landolt-BOrnstein New Series IIll32A

90 a

c

100

200

300

600 K 700

T-

[88Rl], (circles) Fe,,,,Mn,,,, [81Ll], full curves Mn,,Ni,, [83H2], dashed curves Mn,,,,Ni,,,, [83H2]. Inelastic neutron scattering results (INS) [81El].

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

[Ref. p. 2 18

Fig. 70. yFe,,Mn,,. Phonon dispersion curves at room temperature[81El].

I

I

aMn-5.1ot%Fe

1

0.96

180 K 2w

160

e

0

il.00

do

0

0 ‘Ao

I

I aMn-9.6at%Fe

0 0 0d

0 0"0

0.98

0.960

f-

50

100

150

0 >o %-a 2000

00

E E 0.92 3

k 0.88 0.84 9”

250

K 300

0.80

0.930,pJ

160 K fI

50

100

150

200

180 I

250 K 300

I-

T-

Fig. 71. Mn-5 at% Fe, Mn-9.6 at% Fe. Both aMntype structure, annealed for 6 h at 620 “C. Electrical

resistivity p (normalised to the resistivity at 300 K) vs. temperatureT [76W 11.

Land&-Bbmrtcin New Series 11V32A

Ref. p. 2181

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

155

125 pQcm 120

110 105 100 95

A x = 6.18

I I

Irk-k I

I

P-

90 85 80 I QJ 15

Fig. 72. Fe-Mn-Al, Fe-Mn-Cr. Electrical resistivity p vs. Temperature T. NCel temperature TN from Fig. 56a [86Zl]. Compositions:

65

Alloy

60

4OL 75

150

225

300 T-

375

Mn [at%]

I

25.18

2 3 4 5 6 7 8

25.62 24.5 24.41 23.8 31.66 30.22 31

Al [at%]

Cr [at%]

Phase

y + traceE 1.16

y + trace E

4.45 6.18 9.78

Y Y Y

8.69 5.22

Y y

450 K 525

1.2.3.5 Co-Ti

Supplement to LB 111/19A,p. 374-379 Co-rich part of the Co-Ti phase diagram, Fig. 73. Co,Ti has the Ll, structure, which has also been found as the result of a linear muffin-tin orbitals total-energy calculation [89Pl]. Lattice parameter of Co-rich, Co,Ti compounds Fig. 74. Excess Co atoms substitute the Ti sites [85Tl]. Co,+,Ti,, intermetallic compounds are a single phase in the range of 0 I x I 0.180 [83Ul]; for the influence on the magnetic properties of strain induced by cold-rolling see Table 7. NMR spectra of annealed and plastically deformed Co,,Ti,, reveal Co atoms with different magnetic characters [86S3]. Spin-echo spectra Fig. 75 and Table 8.

Landolt-BOrnstein New Series 111132A

Ref. p. 2181

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

155

125 pQcm 120

110 105 100 95

A x = 6.18

I I

Irk-k I

I

P-

90 85 80 I QJ 15

Fig. 72. Fe-Mn-Al, Fe-Mn-Cr. Electrical resistivity p vs. Temperature T. NCel temperature TN from Fig. 56a [86Zl]. Compositions:

65

Alloy

60

4OL 75

150

225

300 T-

375

Mn [at%]

I

25.18

2 3 4 5 6 7 8

25.62 24.5 24.41 23.8 31.66 30.22 31

Al [at%]

Cr [at%]

Phase

y + traceE 1.16

y + trace E

4.45 6.18 9.78

Y Y Y

8.69 5.22

Y y

450 K 525

1.2.3.5 Co-Ti

Supplement to LB 111/19A,p. 374-379 Co-rich part of the Co-Ti phase diagram, Fig. 73. Co,Ti has the Ll, structure, which has also been found as the result of a linear muffin-tin orbitals total-energy calculation [89Pl]. Lattice parameter of Co-rich, Co,Ti compounds Fig. 74. Excess Co atoms substitute the Ti sites [85Tl]. Co,+,Ti,, intermetallic compounds are a single phase in the range of 0 I x I 0.180 [83Ul]; for the influence on the magnetic properties of strain induced by cold-rolling see Table 7. NMR spectra of annealed and plastically deformed Co,,Ti,, reveal Co atoms with different magnetic characters [86S3]. Spin-echo spectra Fig. 75 and Table 8.

Landolt-BOrnstein New Series 111132A

156

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

Table 7. Co,Ti, Co-rich (22 at% Ti). Spontaneous mass magnetisation at 4.2 K and Curie temperature T, versus strain E induced by coldrolling [86S2]. &

TC

a,

WI

WI

[G cm3g-‘1

0 “) Acb) IO 25 50 71 H7

49 49 47 73 282 420 > 420

8.94 7.84 12.1 IO.5 14.2 26.0 43.2

‘) Annealedfor 15h at 1123K. b, As-sliced

specimen with slight internal

‘) Thin shavings

strains.

from the buttons with large undefined

internal

strains.

Table 8. hcp Co-O.5 at % Ti, V, Cr or Mn. Spin-echo “Co NMR data at 4.2 K. t: resonance frequency of the domain satellites; Avo: quadrupole splittings of the domain satellites. The main line domain resonance frequency is 220 MHz [76Kl]. Frequencies in MHz. Numbers in parenthesesgive the error in the last decimal.

Nearest-neighbor satellites

Second-neighborsatellites

V

4

V

A%

Ti

184.0 206.0

0.098(11) 0.286( 12)

210

0.171(5)

V

181.8 203.5

0.214(4) 0.154(5)

212

0.188(4)

Cr

178.2 197.0

0.400(34) 0.100(20)

214

0.226(5)

Mn

166.6 187.5

0.533(26) 0.270(20)

214

0.157(4)

Impurity

[Ref. p. 218

Ref. p. 2181

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

157

3.616 A 3.612

I 3.608 0

I

3.604

I \I

.

1250 3.600 18

1200

21

22

23

24

25

I 26

Fig. 74. Co,Ti with excess Co atoms. Lattice parametera at room temperature according to various sources (2)-(d) mentioned in [85Tl]. Symbol (I) applies to experimental work of [85Tl].

1100 1050

co

20

x-

1150

1000 0

19

5

10

15

x-

20

25

30

35

Fig. 73. Co-Ti alloys. Co-rich part of the phase diagram. Curves are calculated, various types of points according to experimental results: solid triangle downward [83Ul]. For the other symbols see the referencesin [83Ul].

Landolt-Bbmstein New Series 111/32A

158

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

[Ref. p. 218

Co- 0.5at % Ti hcp I=hK

Co- 0.5 at % Cr

160 c

170

180

Co- 0.5at %Mn

190 200 2' -

210

220 MHz230

Fig. 75. hcp Co-O.5 at% Ti, V, Cr or Mn. “Co spinecho spectra at 4 K. See also Table 8. Open circles:

d

160

170

180

190

Y-

200

210

220MHz230

domain resonances. closed circles: wall resonances [76Kl]. For spectraat room temperaturesee [71D1].

1.2.3.6 Co-V

Supplement to LB III/l9A, p. 380-383 The phasediagram of the Co-rich Co-V system has been reexamined, Fig. 76. “Fe Mijssbauer data in Fig. 77 and Table 8. One V atom residing in the first-neighbor shell reduces the “Fe-site hyperfine field by AHr,,.r= 38.4 kOe and the isomer shift by A.S= 0.0020 mms-’ [88Dl]. Spin-echo spectra Fig. 75 and Table 9.

Landolt-Bbmstein New Series llI/l2A

158

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

[Ref. p. 218

Co- 0.5at % Ti hcp I=hK

Co- 0.5 at % Cr

160 c

170

180

Co- 0.5at %Mn

190 200 2' -

210

220 MHz230

Fig. 75. hcp Co-O.5 at% Ti, V, Cr or Mn. “Co spinecho spectra at 4 K. See also Table 8. Open circles:

d

160

170

180

190

Y-

200

210

220MHz230

domain resonances. closed circles: wall resonances [76Kl]. For spectraat room temperaturesee [71D1].

1.2.3.6 Co-V

Supplement to LB III/l9A, p. 380-383 The phasediagram of the Co-rich Co-V system has been reexamined, Fig. 76. “Fe Mijssbauer data in Fig. 77 and Table 8. One V atom residing in the first-neighbor shell reduces the “Fe-site hyperfine field by AHr,,.r= 38.4 kOe and the isomer shift by A.S= 0.0020 mms-’ [88Dl]. Spin-echo spectra Fig. 75 and Table 9.

Landolt-Bbmstein New Series llI/l2A

Ref. p. 2181

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

159

Table 9. CO,,,~-~V~ alloys. 57FeMiissbauer data at room temperature as a function of composition parameterx. For definition of the symbols see Table 2. Hyperfine fields in kOe, isomer shifts in mm s-’ [88Dl].

0

321.9 321.0 319.9 317.9 316.5 310.8 308.3 303.7 295.3

1.1

1.9 3.6 4.9 7.5 8.5 10.0 12.5

321.9 316.3 310.0 300.3 292.9 273.4 264.6 254.7 229.0

0.011

0.008 0.007 0.005 0.006 0.015 0.014 0.025 0.024

“) The averagehyperfine field shift is - 38.4 kOe and - 11.6 kOe for a V atom as the first- or second-nearest neighbor of a probe nucleus, respectively.

600 I /

500 8

c

m a-4

I I

I m am-d

m

I I I

a1 12

16

0 CO

20

phases: o CG,, , e ccI, : G,+?L b aH+aI , a aI+%

24

28

,

Fig. 76. ColOO-xVxsystems.Part of the phase diagram obtained from correlating the results of X-ray and electrical resistivity measurements,the latter indicated by a cross [79Al].

Land&-Bbmstein New Series IIIl32A

2

4

6

8

10

12

14

x-

Fig. 77. CO,,,~-~V~alloys. Average hyperfine field HI,~ at room temperature as derived from 57Fe Mossbauer spectra [88Dl].

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

[Ref. p. 218

1.2.3.7 Co-Cr

Supplement to LB III/I9A, p. 384-391 “Co NMR spectra of hcp Co,,,_,Cr, alloys Figs. 75, 78 and Table 8. The incremental frequency shift of “Co NMR due to substitution of a Cr atom in the nearest-neighbor shell is - 32 k 2 MHz at 4.2 K [93Ml].

. .

l

. .

50

150

100

200

*

MHz

1

Fig. 78. CO,~,,-~C~~ hcp alloys. sgCoNMR spectraat 4.2

K [93Ml].

250

Y-

Landolt-Barnstein New Series 111/32A

Ref. p. 2181

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

161

1.2.3.8 Co-Mn

Supplement to LB 111/19A,p. 391-400 The magnetic phase diagram is shown in Figs. 79, 80. A new state of superantiferromagnetism (SAF) is found for Co,OO-xMnx alloys with a composition between the ferromagnetic regions (0 < x < 25) and the antiferromagnetic region (42 <x < 52). The SAF state is believed to be a mixed state of antiferromagnetic clusters of finite size (= 10 nm) in a paramagnet[84M2, 85Ml]. Atomic disorder for alloys within the SAF composition region have been investigated by polarised neutron scattering [92Wl]. Neutron diffuse scattering experiments in BMn-Co alloys give an indication of long period magnetic modulations [84Fl]. Magnetic susceptibilities of alloys in the SP and SAF composition ranges Figs. 81, 82 and magnetisation curves Figs. 83,84. Spin-echo spectra Fig. 75 and Table 8. Pressuredependenceof 55MnNMR frequency in cobalt Fig. 63. Electrical resistivity Fig. 85. Thermal expansion Fig. 86. Specific heat Fig. 87.

Vi00s; K l1200 IIOOC

I8OC I

F Ih 6OC

ICI

20

30

ft0

50

60

Fig. 79. Co,OO-xMnx. Magneticphasediagramof the Co-rich side based on magnetisation measurements and on neutron diffraction properties. Dashed curves represent second-order and solid lines first-order phase transitions, respectively. The Ta curves represent temperatures where some kind of blocking, i.e. “freezing in” of the ferro- and antiferromagnetic clusters, occurs. SP: superparamagnetism, SAF: superantiferromagnetism [85Ml]. The symbols are according to different sources.

Land&-BBmstein New Series IIV32A

co

x-

Fig. 80. CoIoo-xMn,. Revised structural phase diagram, see also Fig. 79, based on electrical resistivity (open circles) and thermal expansion (solid circles) measurements. Martensitic transformation fee + hcp (ye E) [9OJl, 91Al].

162

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

[Ref. p. 2 I8

4( 3!

-

800 I 5 -2 600 L ?? 400 10 5

0

50

100

150

200

250 K 300

7-

a

Fig. 81. Corn--xMnx7 (25 < x < 32). Magnetic susceptibility vs. temperature T. a ac susceptibility xac, b dc susceptibility xdc in a magnetic field of

0

50

100 I-

0

b

150

200

230 K 300

20

40

60 T-

80

K 100

726 Am-‘, zero-field cooled (solid circles) and cooled in the magnetic measuring field (open circles) [85Ml].

Fig. 82. CoS6Mr+,.Inverse magnetic masssusceptibility xi’ vs. temperatureT. Transition to the superantiferromagnetic state at TsAF[85Ml].

Landoh-Barnrtein New Series 11lL2A

Ref. p. 2181

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

163

18

bU

8 50

t

40

12 I b

30

9

b

6.0

I 6 b

I b

-105A/m9

H-

Fig. 83. Con,aVxMnx.Magnetic mass magnetisation rs vs. applied field H at T= 300 K (solid lines) and

200 K (dashed lines) for various compositions x [85Ml].

i20 _.

“0

150

300 T-

450

600 K 750

Fig. 84. Co,OO-xMnx.Mass magnetisation u measured in a magnetic field of 7.96.10’ Am-’ for various compositions x, measured for increasing and decreasingtemperature [85Ml].

Land&-Bbmstein New Series 111132A

100

I

I

0

200

400

...**

600 T-

I _...W

800

1000 K 1200

Fig. 85. Co,,,,,-xMnxalloys. Electrical resistivity p vs. temperature T for various compositions x. The arrows indicate the direction of the temperature change, the hysteresis corresponds to the E f) y transformation [91Al].

164

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

[Ref. p. 218

35 10-6 K-’ 30

25 I 20

8 ‘5

10 5

0 a

200

400

600

800

1000K 1200

7-

Fig. 86. Co,,Mn,. Co,,Mn,,. Thermal expansion coefficient a vs. temperature 7’. Arrows indicate the direction of the temperature change. Below and above

0 b

200

400 400

600

800

1000 K 1200

I-

300K different measuring techniques were used [9OJl].

Landolt-Bbrnstein New Series 111132A

Ref. p. 2181

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

35 J

mol K

30

molK

35

255 J

molK 40

35

I

i: 30

52: J

-mol K

50

25 20 200

400

600

T-

800

1.2.3.9 Ni-Ti See LB 111/19A, p. 401404

Land&-Barnstein New Series W32A

1000

Fig. 87. Co,OO-xMnx.Specific heat C, vs. temperature T [79Bl]. 1200K lit00

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

166

[Ref. p. 218

1.2.3.10 Ni-V Supplement to LB III/l 9A, p. 405-407 Proposed phase diagram Fig. 88, lattice parameters Fig. 89. Magnetic susceptibility Fig. 90. Arrott plots Fig. 91. Ordered N&V has the DO,, structure, which has also been found as the result of a linear muffin-tin orbitals total-energy calculation [89Pl, see also 87X1]. Specific heat and electronic contribution to the specific heat Figs. 92,93.

l-

1400 1

1200

1000

800

600

Fig. 88. V-N system. ProNV

posed phasediagram [7OSl]. V

lo

20

30

40

50 Ni -

60

80

90 at% Ni

Landolt-Barnstein New Series 11U32A

Ref. p. 2181

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

5

IO

15

20

25

30

167

Fig. 89. V,,,-xNi,. Lattice parameter a vs. Ni content for alloys quenched from 1200 “C [7OSl].

x-

180 I 160 6 140 120

100

100

140

180 T-

Landolt-Bbmstein New Series 111/32A

220

260

K 300

Fig. 90. N&V. Molar magnetic susceptibility x,,, vs. temperature T for (1) fee disordered state, and (2) Pt,Mo-OS type [85T3].

1.6

8

I --E

[Ref. p. 218

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

168

I

n//r/ /PI/

I/

0

I: I

6

b

0

100

a

2w

300

400

SW

mol/cm’700

H/rm -

b

0

300 400 H/flm -

500 mol/cmJ700

0.20 NE

b

0.15

0 c

250

1000 H/Vm -

mol/cm3

Fig. 91. Ni,,,-,V, alloys. Arrott plots dm vs. H/a, at various temperatures for three different alloys. The curves representmodel calculation results [79A2].

Ref. p. 2181 5.4 -!!!L mol K*

I

0

Ni,V

0

I

5.0

169

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn IO mJ mol K2

8

i T2-

Fig. 92. N&V. Variation of the molar specific heat C, with temperature T, expressed as C,lT vs. T2 [85T3]. Open circles: fee disordered state, solid circles: ordered state.

20

40

x-

60

80

100 Ni

Fig. 93. Ni,V,,,,. Electronic specific heat coefficient y vs. composition parameter x; x = 25 taken from [71S2]. Downward triangles: ordered state, triangles: disordered state, circle: pure metal [81Tl].

1.2.3.11 Ni-Cr

Supplement to LB III/l 9A, p. 408-4 13 The room temperature lattice parameter of Ni,,,,Cr,,,, is a= 3.54 A [81Ll]. Influence of external hydrostatic pressure on the Curie temperature for Ni-Cr alloys Figs. 94, 95: Volume magnetostriction Fig. 96. Thermal expansion Fig. 97. Elastic moduli Figs. 98, 99. Specific heat Figs. 100, 101.

-121 0

I 100

Landolt-Biirnstein New Series IIV32A

I 200

I

I

I

300

400

500

I I 600 K 700

Fig. 94. Ni-Cr, Ni-Mn, Ni-Cu alloys. Influence of pressure p on the Curie temperature T,. Open symbols: direct measurement;solid symbols: derived from the measurement of forced magnetostriction dw/dH [81T3].

Ref. p. 2181 5.4 -!!!L mol K*

I

0

Ni,V

0

I

5.0

169

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn IO mJ mol K2

8

i T2-

Fig. 92. N&V. Variation of the molar specific heat C, with temperature T, expressed as C,lT vs. T2 [85T3]. Open circles: fee disordered state, solid circles: ordered state.

20

40

x-

60

80

100 Ni

Fig. 93. Ni,V,,,,. Electronic specific heat coefficient y vs. composition parameter x; x = 25 taken from [71S2]. Downward triangles: ordered state, triangles: disordered state, circle: pure metal [81Tl].

1.2.3.11 Ni-Cr

Supplement to LB III/l 9A, p. 408-4 13 The room temperature lattice parameter of Ni,,,,Cr,,,, is a= 3.54 A [81Ll]. Influence of external hydrostatic pressure on the Curie temperature for Ni-Cr alloys Figs. 94, 95: Volume magnetostriction Fig. 96. Thermal expansion Fig. 97. Elastic moduli Figs. 98, 99. Specific heat Figs. 100, 101.

-121 0

I 100

Landolt-Biirnstein New Series IIV32A

I 200

I

I

I

300

400

500

I I 600 K 700

Fig. 94. Ni-Cr, Ni-Mn, Ni-Cu alloys. Influence of pressure p on the Curie temperature T,. Open symbols: direct measurement;solid symbols: derived from the measurement of forced magnetostriction dw/dH [81T3].

170

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

lo3 ’ P

(,

0

Nil00 -xcrx v, II 4

10’

P

L

0, Ii

I

L-Lhi

I

I

K

0

2

4

[Ref. p. 218

6 x-

8

P 0 d, P

10

I

12

14

Fig. 95. Nin,&rx alloys. Curie temperature Tc vs. composition parameterx: open symbols and triangles [82Sl], downward triangles [72Bl], solid circles [81T3].

0.8 I.

k * 0.6

-6 -1 -8

0

4’

-0

0.2

0.4

0.6

0.8

1.0

1.2

T/T, Fig. 96. Nir,,&r,. Forced volume magnetostriction dcddH vs. relative temperature T/T,, where T, is the Curie temperature [81T3]. X

0

1.9

Tc[K]

633

550

3.9 451

5.9 337

50

100

150 200 T2 -

250

300 K 350

Fig. 97. Ni,,&r, alloys. Thermal expansion coefficient a vs. temperature T plotted as cdT vs. T *. Solid symbols for paramagnetic (P) alloys, open symbols for ferromagnetic (F) alloys [82Sl, 89K2J.

7.9 214

Land&-Barnstein New Series 111/32A

Ref. p. 2181

171

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

I

170

160 t

130

150

120

140

110 300

350

400

450

500

130 550 K 600

I-

alloy. Elastic moduli, cL, c’ Fig. 98. fee Ni8,,,4Cr19.6 and cA4vs. temperature T [81Ll]. c~=(c,,+c,,+2c&& c'=(c~~-c,,)/2.

Land&-Bbmstein New Series 111/32A

Fig. 99.

%&r19.&

F%&fn3&

Fe68,SN4.&r~4.~

MO2.5 fee alloys. Bulk modulus B vs. temperature T [81Ll].

[Ref. p. 2 18

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

172

14.0 mJ

18 J

molK2 13.5

IldK 16

1371 97 99

101

103 105

107 KlW

II

f

I ’ 6’ ’ 8

II

K 10

12.5 I ? 12.0 3

14.0 mJ molK* 13.5

10 9 8

11.5

6

0

20

40

60

80

100

K 120

I-

Fig. 100. Ni,,Cr, alloy. Specific heat C,, vs. temperature T. Upper inset: CIJT on an expanded T scale in the T, region Lower inset: low-field ac magnetic susceptibility vs. Ton an arbitrary scale for definition of T, [82Sl].

10.0 0

2

4

6

8

10

K

Fig. 101. Niloo_,Cr, alloys. Low-temperature specific heat vs. temperatureT for various compositions of the alloy. Curves: data published by Moody [70Ml]. Insert: low-field ac magnetic susceptibility for the alloy x = I I [82SI].

1.2.3.12 Ni-Mn Supplement to LB III/19A, p. 414-430 Disordered Ni,,,O.xMnx alloys with x = 25 show interesting magnetic properties. The disordered atomic state can be obtained by rapidly quenching into water of samples (encapsulated in a quartz tube in an argon atmosphere) that were annealed for days at 900 C. For the kinetics of the order-disorder transition in Ni,Mn see [86Wl]. Atomic short range order has been investigated in disordered fee NiMn alloys by polarisation analysis of neutron diffuse scattering at 4.2 K. Ni atoms prefer a Mn

nearest-neighbor environment [84M3]. Magnetic phase diagram Figs. 102, 103 and 94. The reentrant spin glass (SG) ordering is accompanied by a net ferromagnetic moment of the F state, this phase is called a mixed ferro-spin-glass (FSG) state [87A2]. For a theoretical discussion of two distinct magnetic states of the same atomic species see [93Al]. The low amplitude ac susceptibility of disordered Ni-Mn in the magnetic transition states is rather complex, showing relaxation effects, [88Al, 9001, 91K1, 92Rl]. Influence of magnetic field cooling on the hysteris curves Fig. 104. Evidence for the existence of magnetic domains in the reentrant spin glass is found by neutron

[Ref. p. 2 18

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

172

14.0 mJ

18 J

molK2 13.5

IldK 16

1371 97 99

101

103 105

107 KlW

II

f

I ’ 6’ ’ 8

II

K 10

12.5 I ? 12.0 3

14.0 mJ molK* 13.5

10 9 8

11.5

6

0

20

40

60

80

100

K 120

I-

Fig. 100. Ni,,Cr, alloy. Specific heat C,, vs. temperature T. Upper inset: CIJT on an expanded T scale in the T, region Lower inset: low-field ac magnetic susceptibility vs. Ton an arbitrary scale for definition of T, [82Sl].

10.0 0

2

4

6

8

10

K

Fig. 101. Niloo_,Cr, alloys. Low-temperature specific heat vs. temperatureT for various compositions of the alloy. Curves: data published by Moody [70Ml]. Insert: low-field ac magnetic susceptibility for the alloy x = I I [82SI].

1.2.3.12 Ni-Mn Supplement to LB III/19A, p. 414-430 Disordered Ni,,,O.xMnx alloys with x = 25 show interesting magnetic properties. The disordered atomic state can be obtained by rapidly quenching into water of samples (encapsulated in a quartz tube in an argon atmosphere) that were annealed for days at 900 C. For the kinetics of the order-disorder transition in Ni,Mn see [86Wl]. Atomic short range order has been investigated in disordered fee NiMn alloys by polarisation analysis of neutron diffuse scattering at 4.2 K. Ni atoms prefer a Mn

nearest-neighbor environment [84M3]. Magnetic phase diagram Figs. 102, 103 and 94. The reentrant spin glass (SG) ordering is accompanied by a net ferromagnetic moment of the F state, this phase is called a mixed ferro-spin-glass (FSG) state [87A2]. For a theoretical discussion of two distinct magnetic states of the same atomic species see [93Al]. The low amplitude ac susceptibility of disordered Ni-Mn in the magnetic transition states is rather complex, showing relaxation effects, [88Al, 9001, 91K1, 92Rl]. Influence of magnetic field cooling on the hysteris curves Fig. 104. Evidence for the existence of magnetic domains in the reentrant spin glass is found by neutron

173

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

Ref. p. 2181

depolarisation effects. The size of the magnetic domains decreaseswith increasing x from lo...50 pm for x =23 to several thousands of Angstroms at x= 25 [90M1,91M1,92Sl]. Spontaneous magnetisation Figs. 105-107. Magnetic anistropy fields Figs. 105, 108, for surface anistropies see [93A2]. Spin wave stiffness constant Fig. 109. Magnetic moment analysis of the constituting atoms by polarised neutron scattering in [91P3, 92P2]. 7210

IV.2

K

4,

K

GPa -1 15

160

-1 IO 120

5 0 I 3 \ L-" 5-o

I 100 h

00

__' 10

60

t-1 I5 01 ii -22

23

24

25

26

21

20

Fig. 102. Ni,O,,-xMnx, x = 25, disordered alloys. Magnetic phase diagram as derived from magnetisation data. Multicritical point x = 23.9, T= 102 K [87A2].

Land&-Biirnstein New Series IIV32A

5

IO x-

15

20

20 25-'

Fig. 103. Ni-x at% Mn, ordered (I) and disordered (2) alloys. Open symbols: Curie temperature rc, and solid symbols: influence of externally applied pressurep on rc for various compositions x [80Al]. (3): data from [78Tl].

174

I

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

[Ref. p. 218

5 0

b -5

“I {/ I

-

-1.0

-0.5

.

0

0.5

1.0

1.5

2.0

2.5kOe3.0

H

Fig. 104. Nil,,O_xMnx, x = 25, disordered alloys.

Magnetic hysteresis curves after cooling of the samples to 4.2 K in different applied magnetic fields

HaPP,parallel to the measuring field H [84Al, 87K2, seealso 93Sl].

Land&-Bornstein New Series 111132A

Ref. p. 2181

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

30 Gcm3 9 20

175

Gem” g 25

I b IO

20

I 15

b

0 23.0

23.5

24.0

x-

24.5

25.0

25.5

26.0 0

40

80

120

160 K

200

T-

Fig. 105. Niu,,,+Mnx, x e 25, disordered alloys. Spontaneous magnetisation 0 and unidirectional magnetic anisotropy field HA at 4.2 K, as induced by field cooling, vs. composition parameterx [87Kl]

Fig. 106. Ni,,Mn,,, disordered alloy. Magnetisation d measured as a function of temperature T in various magnetic fields H after cooling in the applied field (FC) and in absence of the magnetic field (ZFC) [84Al, 93Sl].

4.8 kG 4.E 1.4 Li I 5 L( * 3.t 3.f

e

100

3.’

r

50

ZFC

3’.d

25

50

75 T-

100

125

150 K 175

Fig. 107. N&Mn,,, disordered alloy. Temperature dependence of the saturation magnetisation A4, as derived from ferromagnetic resonancespectra [8801].

Landolt-Biirnstein New Series IIU32A

0

25

50

75 T----,

100

125 K 150

Fig. 108. Ni,,Mn,,, disordered alloy. Temperature dependence of the magnetic anisotropy field HA in both the ZFC and FC state, as derived from ferromagnetic resonancespectra [8801].

176

1.2.3 Binary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

[Ref. p. 218

Ni,, ,Mn,, 6, disordered alloy. Spin wave stiffness constant D vs. temperature T as derived from inelastic neutron-scattering experiments using a double Lorentzian model (DL) or a damped harmonic oscillator model (DHO) [84Hl]. Fig. 109.

0

50

100

150

200

250 K 300

I-

Landoll-Bbrnrtein New Series 111132A

1.2.4 Ternary

alloys between Fe, Co, or Ni and one or more of the Ti, V, Cr or Mn elements

Supplement to LB 111/19A,p. 43 l-490 Survey

For each of the ternary alloys between Fe, Co or Ni and one or more of the elements Ti, V, Cr or Mn, the numbers of the figures and tables are given in which data on the properties specified are provided. Numbers in roman and italic refer to figures and tables, respectively. Alloy

Phase diagram Lattice constants

Fe-Cr-Mn

Magnetic Magnetic susceptibility phase Paramagnetic diagram properties

Magnetization Average magnetic moment

NMR Mbssbauer effect

56

118, 122

123, 124

110,111

Spin waves Exchange energy

Magnetic anisotropy Magnetostriction

Specific heat Electrical Thermal resistivity expansion Elastic coefficients

112

113-116 \

Fe-Co-Ti Fe-Co-Cr

127

Fe-Ni-Mn

41 129-133

125, 126

127

Fe-Co-Mn Fe-Ni-Cr

117, 119-121

134-136, 139

10

129-133,

156-158, 164

151-155, 159

137, 138 155, 160

61, 162, 165-168

163

140

128

169-171

142, 143, 145-147

144, 148-150

172, 177, 178

173-176

178

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

[Ref. p. 218

1.2.4.1 Fe-Cr-Mn

Supplement to LB III/I9A, p. 436 Magnetic susceptibility of fee alloys Fig. 56a. The magnetic phase diagram for bee alloys with about 75 at% Cr, Fig. 110 and for Cr-Mn alloys with small concentrations of Fe, Fig. 111,magnetostriction Fig. 112, thermal expansion Figs. 113-I 16 and resistivity Fig. 117. An atomically disordered alloy with about equal concentrations of Fe and Cr obtained by annealing at high temperature (e.g. 1300 K) disorders by annealing at a low temperature, where AF and FM “segregates”can be identified [91Sl]. For its influence on magnetic properties and resistivity see Figs. I 18, 119. Electrical resistivity and magnetic transition points of bee Fe-Cr-Mn alloys Figs. 120, 121. Alloys Cr,,(Fe,Mn,-,),, quenched from a temperature above the miscibility gap exhibit segregation [92X1]. For the magnetisation of these alloys seeFig. 122. Magnetic hyperfine fields Figs. 123, 124.

Fig. 110. beeCr,5Fe,Mn25..,. Magneticphasediagram derived From electrical resistivity data: 1 [89Al], 2 [68Pl]; magnetisationmeasurements:3 [89Al]; neutron scattering, magnetisation: 4 [83Bl]; MBssbauerdata: 5 [85D2]. F: ferromagnetic,AF: antiferromagnetic, P: paramagnetic.

Land&-Barnstein New Series 111132A

Ref. p. 2181

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

100

0

a

0.4

0.2

x-

0.8

0.6

1.2

1.0

Fig. 111. (Cr~~.~Fel,~LMn,~ (Cr~&%.A#n,. Magnetic phase diagrams. NCel temperature TN, upper and lower transition temperatures, T,, and T;,,

0

b

0.2

0.4

x-

0.6

0.6

1.0

1.2

between transverse and longitudinal incommensurate SDW phases, respectively. Derived from thermal expansion data [92Fl]. .-

Cr,,Fk, Mn25-x '

"$

I

1

I

I

6 I 4 c1 2

-2’ 0 0

1

2

3

4

5

T

100

150 T-

200

250 K 300

6

P’oH--Fig. 112. bee Cr,,Fe,,,,Mn,,,,. Linear magnetostriction ,I. vs applied magnetic field Hat various temperatures T. T, = 25 K, TN = 442 K [89Al].

Land&-Biirnstein New Series IW32A

50

Fig. 113. bee CrrsFe,Mnz5,. Thermal expansion coefficient czvs. temperature T for various compositions x [89Al].

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

180 25 *lo-6 K-’ 20

.,;-; K-’ 20

15

I

15

1, 10

8

10

I

5

5

0 25,

0

[Ref. p. 2 18

100

200

300 T-

400

500

600 K 700

0

100

200

300

400

500

600 K 700

0

100

200

300 I-

400

500

600 K 700

I I I I I b-4

100

200

300

400

500

600 K 700

Fig. 114. fee Fe,,_,Cr,Mn,,C,. Linear thermal expansion coefficient czvs. temperature T. 0: volume magnetostriction as derived from the area between the

experimental (solid) curve and the hypothetical extrapolation of the paramagnetic part of this curve, as representedby the dotted curve[76Rl].

Landoh-Bbrnstein New Series liV32A

Ref. p. 2181

181

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn 3: .10-l 30 25 I 20 w 15 IO

5 0

150 200 250 300 350 400 450 500K 550 T-

Fig. 115. bee Crss,5,Mn,Fe0,5. Thermal expansion expressed as the linear strain E= Al/l,,,, where lzg3is the length at room temperature. Above a temperature T (indicated by a triangle) the curves are linear. Transition points: ? NCel point, & AF, t) P, open circle AF, + AF,, the ICSDW transition. For x = 0.16 the up and down arrows coincide, corresponding to a triple point [89Bl].

Landolt-BOrnstein New Series III132A

I

150

I

I

I

250

350 T-

450

I 550 K 650

Fig. 116. (Cr,,,,Fe,,,),,,_,Mn,. Linear thermal expansion coefficient expressed as the linear strain E= Al/l,,, vs. temperature T. ? NCel temperature TN; upper and lower transition temperaturesbetween AF, and AF, phases are indicated by circle and double arrow, respectively [89Bl].

30

I

[Ref. p. 218

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

182

I

Cr,,Mn 25-A

o"

20

g 10 (1 54 2 ;= F 0

25I b 20-

r $2 cb -10

-20

-7n -50

0 300 200

350 l-

500

650 K 800

Fig. 117. bee Cr,sMn2s.,Fe,. Electrical resistivity expressedas [p(300 K) - p(T)]/p(300 K) vs. temperature T [89Al].

0.1,

-0.81 0

, I I I-- I-- LAL’L6.3’“L3.5”“’ 10.2

50

100

150 l-

I

1Z,=270K

400

500

T-

600

700

800 K 900

Fig. 118. Cr,, ,Fe,, ,Mn,, ?. Magnetisation IY vs. temperature 7’ for the segregated (I) state and the disordered (2) state. Tc = 460 K: Curie temperature of the dominating FM composition of the segregates; T, : average Curie point; T,: annealing temperature. Dashed curve: expected behavior in the absenceof AF segregates[9 I SI].

I

Fig. 119. Cr,, 3Fe,, SMn,, *. Electrical resistivity expressedas Lp(T) - p(300 K)]/p(300 K) vs. temperature T for various degreesof AF and FM segregations. The lowest curve is for a not annealed sample in the disordered state, kept for 30 min at 1300 K. The other curves are obtained after annealing sequentially at various temperaturesT, for 20 d. The sample “680 K” was kept at this temperaturefor 40 days [9l SI] 200

250

300 K 350

Landoh-Barnstein New Series llV32A

Ref. p. 2181

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn 1.2,

183

I

I

1.1

1.0 t

I

0.9I

!n-“AA?;S-I

E K2 ” 0.8 ? ic G 0.7

,o

3.6

0

50

a

100

150

200

0.4I=-0

250 K 300

T-

n

’ 50

I

I 100

I 150

I 200

I

I I 250 K 3W

T-

b

Fig. 120. a bee CraO-xMnxFeZO, b bee CrT5-,Mn,Fez5. Relative electrical resistivity @(7’)/p(273 K) vs. temperature T for various composition parametersx.

I

Arrows indicate the estimated NCel temperatures TN [93Tl].

45 Gcm3 T40

a

Cr,,(Fe, Mn,-x)25 I I

D

. I .

25 -

20;

x-

20

30

Fig. 121. Cr80-xMnxFe20,CrT5-,Mn,Fez5. Estimated NCel temperatures TN as derived from Fig. 120. Broken curves: extrapolations. Full circle: Tc for and full triangle: I”, for Cr,,Fe,,, from Q&20 [83Bl] and [93Tl], respectively.

Land&-Bornstein New Series 111/32A

0 x = 0.804 . 0.720 0 0.640

0.2

P

I0.4 0.6 T/TC -

0.8

1.0

Fig. 122. Cr75(Fe,Mn1-.J25, annealed for 1 h at 1lOO”C, water-quenched.Mass magnetisation crmeasured in a magnetic field of 60 kOe vs. temperature T. The values of cr are scaled with the composition parameter x and the temperature T with the Curie temperaturesI”, of the various alloys. cr and rc values are derived from Arrott plots. The samples show segregation, the remaining magnetisation at rc is relatively large, approximately 60 % of the value at 0 K [92X1].

184

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

[Ref. p. 2 18

\ \ \

t

\7=50K

0

50

I,

100

150 HhYP -

a Fig. 123. Magnetic

Cr,,(Fe,Mn,-,),,, hyperfine field

I

sof

I

I/

” I

200

-

250 kOe 300

alloys of Fig. 122. distribution P(H,,,,) at

0

I

I v l”.im t . 1

I

I

I

I

50

100

various temperatures [92X1].

150 Hhyp -

200

250kOe300

T, a x = 0.804, b x = 0.640

Fig. 124. Cr,,(Fe,Mn,_,),,, alloys of Fig. 122. Mean

*‘[I/ 0

0 b

50

magnetic hyperfine field vs. temperature T for various compositions x [92X1]. 100

150 I-

200

250’ K 300

Landoh-B6rnrtein New Series llV32A

Ref. p. 2181

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

185

1.2.4.2 Fe-Co-Ti

Supplement to LB 111/19A,p. 439-445 The compound (Fe,,Co,,)Ti shows weak itinerant ferromagnetism [79B2]. Specific heat Fig. 125, resistivity Fig. 126. 50

1 pSh

iii-t

40

6

4 ! 0

30

I

a I h

L.? 20

2

Qr lo-

IO

IO

20

30

10 KZ 50

e 6

0

50

150

200

250 K 300

T-

Fig. 125. (Fe,,,Co,,,)Ti. Specific heat CP vs. temperature T. Inset: CP/T vs. T2 at low temperatures[79B2].

Landolt-BOrnstein New Series IW32A

4.10. 5

6

7

89

2

3

KC0

T-

Fig. 126. (Fe,,,Co,,,)Ti. Electrical resistivity differencep(r) -p(O) vs. temperature T [79B2].

186

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

[Ref. p. 218

1.2.4.3 Fe-Co-Cr Supplement to LB III/19A, p. 447-450 Structural and magnetic phase diagram Fig. 127.

Cr

Fe - Co - Cr

co

10

20

30 Fe-

40

50 of% 60‘

Fig. 127. Fe-Co-Cr. Room-temperaturestructural and magnetic phase diagram of Co-rich side as compiled by [9OW2]. Ferromagnetic region F [34Ml]. Structural data [59Kl]. Crosses at y-a phase-transition line: “Stainless-lnvar” and “CoElinvar”. The inset representsthe structural composition at 1200 OC[SIR]].

Landolr-Barnsrein New Series W32A

Ref. p. 2181

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

187

1.2.4.4 Fe-Co-Mn Supplement to LB 111/19A,p. 451-457 Thermal expansion coefficient Fig. 128. 33 *lo-6 K-1 31-

’ F%lo‘““o.094coo.802 2 hl77 b.163 %.660 29 - 3 Fe0.246 M”o.230 coo.524 4 FeD.274M”o.260 27 -

5

%.309Mn

6

Feo.3~1 Mb.309

h66

o.d%.394 Coo.360

25 - 7 FeomMnomCoo.329 8 Feo.406 Mno.400 Coo.194

Fig. 128. Fe-Mn-Co.

7N 5 0

oL 200

400

I 600

T-

-0

I 800

XI 1000 K 1200

Linear thermal expansion coefficient cr vs. temperature T. Inset: Curie temperature Tc and NCel temperature T, vs. composition parameterx for (Fe&o,,,),-,Mn,[77Bl].

1.2.4.5 Fe-Ni-V Supplement to LB 111/19A,p. 458 From 6’Ni Mijssbauer effect measurementson (Fe0,406Ni0,594)0,841V0.159 at 4.2 K is derived an average magnetic hyperfine field EhYP=74.6f3.4 kOe, with a second moment fi = 16.1 +3.1 kOe [87Sl]. Neutron diffraction does not give pertinent information on the magnetic moment of the Ni atom in this kind of ternary alloys [83Cl, 85Ll].

Landolt-Bbmstein New Series 111/32A

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

188

[Ref. p. 218

1.2.4.6 Fe-Ni-Cr

Supplement to LB III/19A, p. 459-463. Structual and magnetic phase diagram Figs. 129-133 and Table 10. For static magnetic susceptibility Figs. 134-136 and for magnetisation curves Figs. 137, 138. Complex magnetic susceptibility Figs. 139, magnetostriction Fig. 140. Fig. 141 shows the “Fe isomer shift for Fe,,Ni,,Cr,, with TN= 17 + 1 K. For the influence of Cr substitutions on long-range and short-range atomic order in Ni,Fe see [87M2, 88C2]. Linear thermal expansion coefficient Figs. 142, 143, Young modulus Fig. 144. Specific heat Figs. 145-147, resistivity and magne’toresistanceFigs. 148-150. Table 10. Fe,,_,Ni,Cr,,. Transition temperaturesT, (Curie point), TN

(NCel point) and TSG(spin-glass transition point); spontaneousvolume magnetisation 4xM, [84M4]. X

30 26 23 21 19 17 14 10

Ni

TC

TSG

TN

4nM,

Kl

Kl

WI

WI

144 56 35

> 300 (CXphase)

3.8 1.92 0.69

7 20 10 12 13 26 40 (Y phase)

50 Fe -

fiphase)

60

70

80

90 of%

Fe

Fig. 129. Fe-Ni-Cr. y range of the low temperature dotted. The AF region is questionable.m, dashed

structuralandmagneticphasediagramascompiledby curves:martensitictransformations[76W2]. Crosses: [9OW2] from data of [78Ml, 82M3, 84M4]. Full commerciallnvar and Elinvar compositions[75Il, curves representrc of the F phase.Reentrantspin- 76W2,81T2]. glass (RSG) phaseshatched.pure spin-glassphases Landolt-Barnstein New Series 111132A

Ref. p. 2181 160

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn I

K

I

.Fe80-xNix Cr,,

1

1

600 I I K Fe, Nigo-,Crlo

40

45

50

55

60

65

70

x-

10

15

20

25

30

35

x-

Fig. 130. Fe,,-,Ni,Cr,,. Magnetic phase diagram as derived from magnetic measurements and neutron diffraction spectra. (I) rc for long-range ferromagnetism F; (2) transition to field-induced ferromagnetism FIFM; (3) transition to spin-glass phase SG; (4) Lr, for long-range AF [84M4, seealso 87A33. 500. K.

I

I Fe,,

Ni,,-,

Fig. 131. Fe,Ni,,Jk,,, annealed at 1000 “C for 6 h. Magnetic phase diagram. AS: asperomagnetism, r,: spin-glass freezing temperature. (I) derived from x(r, H) curves, (2) from magnetostriction measurements, (3) from Young’s moduli measurements

Cr,

400

Fig. 132. Fe,,Ni,,,Cr,. Magnetic phase diagram as derived from magnetisation measurements[84D3]. 0

Land&-Bbmstein New Series 111132A

4

8

x-

12

16

20

[Ref. p. 218

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

190

30 Oe 25

20

15

IO

5

8

10

12

1Z K 16

0

‘,2

K

30

0

10

20

30 K 40

T-

l-

Fig. 133. Fe,?%,,-,Crz,, disordered fee alloys. Magnetic phase diagram showing the various transition

>

20

IO

I-

temperatures as a function of an externally applied

magnetic field Hap,,,[86Tl, 87Ti].

I FesgNi2,Cr2b

Fig. 134. Fe,,Ni,,Cr,,, fee alloys. Reciprocal magnetic mass susceptibility x,-l vs. temperature T in various measuring fields H [84M4]. 0

30

60

90

120

150 K 180

T-

Land&-Bbmrlein New Series 111132A

Ref. p. 2181

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn I

4i 13

4c

ml

,f+

-4

191 I

Fe~6 Nil,CrZO

.Y -4 I\ \

1

I

I

45

60

75

70

3:

25

I

3c

60

25

50

x" 20

40

I x"

I x"

20

15

30 20

.-

U

15

--

30

K 90

T-

Fig. 135. FeB,--XNiXCrl,,,fee alloys. Static magnetic mass susceptibility xs vs. temperature T, measuredin external fields Harp,in the zero-field-cooled state. For the transition temperatures rc, TSGsee Table 10. The dashed curves for x = 23 apply to field cooling in the measuring field [84M4]. 35 Gem' 9 30

FeQn-,NiwCr,, I

I

I

Fig. 136. Fe,,Ni,,Cr,,, fee alloys. Magnetic mass susceptibility x, vs. temperature T in various magnetic measuring fields H [84M4].

T=5K

25

20 I

35 I

b 15

30 b

10

25

Fig. 137. fee Fe,,-XNi,Cr,,. Mass magnetisation cr vs. applied magnetic field H at low temperature T (zerofield cooling) [84M4].

5

0, 0

IO

20

30 H-

Land&-Bbrnstein New Series 111/32A

$0

50

kOe 60

192

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

Fe6, Nil9 cr20

I

’

I

[Ref. p. 218

I

3.c I 2.E b

2s lC.w 1.C

0.5

0

15

30

45

I-

60

75 K 90

Fig. 138. Fe,,Ni,,Cr,,. Mass magnetisation u vs. temperature T for various applied magnetic fields H. Dashed curve: sample cooled in a magnetic field of 1 kOe [84M4].

Ref. p. 2181

193

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

Fe57 Ni2, Cr20

H,,,= 0.4 Oe

.

0 Hbios= 0 100Oe H,,=O.4 Oe

Ho,=4 Oe

l

:

0 a

0

’

IOOOe

0

100 01

200 500

vA

200 500

Hbias=

.

him

P

I

I

I

I

20

40

60

80

200 500

. 0

K

I :x

I 0

100

T-

I

I

I

I

20

40

60

80

K

II

I

T-

b

Ho,= 4 Oe ' Hbios' 0 0 100 Oe 0 200

.

Fig. 139. Fe,,Ni,,Cr,,, annealed for several days at 1200 K. a Real part, and b and c imaginary part of the magnetic susceptibility, x’ and x”, respectively, vs. temperature T for two values of the measuring field Ha, of frequency f = 130 Hz. Various externally biasing fields, Hbiasr were applied [89Ll, see also 85T2, 86Tl].

I

2.1Vcm3/g

I U c

Landolt-BBrnstein New Series IW32A

500

I

^^ LU

I

I -60

._ 4u T-

I

80

K

100

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

194

- 0.07

14 10-6

I

[Ref. p. 218

I

y Fe,,Ni,,Cr,, -0.08 57Fe - 0.09

Fe!

*7 E

I

-0.10

!: .te

,

:T:’

.-

.l .r

l *p’ 3 I’

q - 0.11 - 0.12@#u”

0

Fig. 140. Fe,,_,Ni,Cr,,, annealed at 1000 OCfor 6 h. Linear saturation magnetostriction A, in a strong magnetic field as a function of temperatureT [85D3].

I”

150

300

450 I-

600

750 900 K 1050

Fig. 141. Fe,,Ni,,Crz,. “Fe Mossbauer isomer shift IS with respectto aFe at room temperature,vs. temperature T [84Wl].

I

*‘$ I Fe,, Ni,, 13~~ ’

I

IL+” I

I

I I NE-’

I

-1

4-

I -2 i -3

2-

-4 0

10

20

30

40 K 50

Fig. 142. Fe,,Ni,,Cr,,, annealed at 900 “C for 15 min. Linear thermal expansion coefficient CTvs. temperature T. a,,,(T) calculated on the basis of the specific heat. Inset: a,,,=a(Q--q,,(T), the spin glass contribution [87A3, seealso 88A2, 76RI].

Landolt-Barnstein New Series 111132A

Ref. p. 2181

I

-0

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

n+I’cI

50

a

100

I

I

150

200

0491

250 K 300

T-

Fig. 143. Fe,O-XNi,Crzo, annealed at 900 T for 15 min. a linear thermal expansion coefficient a and b spin glass contribution a;, vs. temperature T. Arrows

Land&-Bdmstein New Series 111132A

195

b

-0

50

100

150

T-

200

250 K 300

with symbols indicate the respective Curie temperatures [87A3, seealso 85D3].

[Ref. p. 218

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

196 23Q-

32

I

J

GPOFe,,-,Ni, Cr,o

mol K

28

3i

2E

24 3;

I 21 a 2r 3: 1601

50

I

I

I

I

200

350

500

650 K

I-

Fig. 144. Fe,,_,Ni,Cr,,, annealed

21 at 1000 “C for 6 h.

Young’s modulus E vs. temperature T for various concentrations x. Dashed curve: data in the presence of a magnetic

21 3:

field of 8.104 A/m [85D3].

h559ho4

Ni0.337

IO

600

2

2

450

750

900

1050 K 1200

T-

Fig. 145. Fe-Cr-Ni alloys. Specific heat C,, in the paramagnetic region vs. temperature T. Dashed curves are calculated [81BI].

Land&-Bamalein New Series W32A

Ref. p. 2181

0

20

Land&-BOrnstein New Series 111/32A

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

40

60

T-

80

100 K

197

Fig. 146. Fe,,Ni,,Cr,,. Specific heat C, vs. temperature T. Inset: CP/T vs. T* [88L2, seealso 83D2].

198

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

0.e

[Ref. p. 2 18

35 mT molK* 30

J ml”, I

I

25

0.5

h 20

0.2

15

0.3

10 25

b

30

35

40

x-

45

50

55

60

0.2 0.1 0 0.3 I 3

0.2 0.1 0 0.2 0.i 0 0.3 0.2 0.1

nl -0

a

r 4

I 8

I 12

I 16

I K 20

Fig. 147. Fe,,_,Ni,Cr,,, annealed at 1000 “C for 6 h. a Specific heat C,, vs. temperature T for various concentrations x. b Electronic specific he-* coefficient y[85D3].

I-

Land&-Barnstein New Series 111132A

199

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

Ref. p. 2181

26 I 92.20-

I !

...i. .. 92.15 -

'x,

I I

92.10 I 92.05

v

72.6072.55

. ... .‘.>&. .T.

‘“. -h

72.50

20 l

‘%

72.45

-Sk

I I 72.401 64.30 “...,. . . ‘..‘.‘.“.,.. ( 64.25 ‘Q).-.:. ‘45. A‘... -9. 64.20 %.

64.15 -0.5

0

0.5

I 17] /

17 5 x 5 30, fee alloys, homogenised at 1050 T for 100 h. Electrical resistivity p vs. logarithm of temperature Tin [K], for various concentrations x [92Bl].

Fig. 148. Fe,,-,Ni,Cr,,,

1.0

1.5

log T -

Land&-Bdmstein New Series III132A

.

200

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

-0.2

-0.6

0 %

-0.8

[Ref. p. 218

-0.2 I F -0.4 2

I

'kl

7n I

0 % -0.2

-8 -12 0

10

20

30 H-

40

50

60 kOe70

Fig. 149. Fe,,_,Ni,Cr,,. Longitudinal (open circles) and transverse (solid circles) magnetoresistance expressed as Aplp at 4.2 K vs. applied magnetic field strength H [93Bl]. The curves have been shifted for clarity, Ap/p = 0 for H = 0.

Fig. 150. Fe,,Ni,,Cr,,, homogenised at 1050 “C for 30 h. Longitudinal magnetoresistance (A@p)tt vs. applied magnetic field H at various temperatures T [gINI].

Landolr-Barnstein New Series IlV32A

Ref. p. 2181

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

201

1.2.4.7 Fe-Ni-Mn

Supplement to LB 111/19A,p. 464-476 The magnetic properties of compounds of the ternary ordered fee Fe-Ni-Mn system have been calculated on the basis of spin-polarised self-consistent linear-muffin-tin-orbital band-structure theory. A statistical theory is applied for disordered compounds [9OJ2,90Hl].For the magnetic phase diagram of the Fe-Ni-Mn system see Fig. 151,and for the reentrant spin-glass system (Fe,,,,Ni,,,,),,,_,Mn, the Figs. 152, 153. Influence of externally applied magnetic fields on the magnetic transition temperatures, Fig. 154, 155. Low-field magnetic susceptibility Fig. 156-158. An example of the influence of temperature on the ac susceptibility is given in Fig. 159. The peaks in the x’(T) and ~“(7’) curves are related to magnetic transitions. Besides the T, peak, additional peaks (T, and T,) are found near the reentrant ferromagnet to spin-glass transition. The influence of the amplitude or frequency of the measuring field, the presence of a bias field and the field-cooling condition on these peaks is described in [85Sl, 88H1, 88L3, 90T1,92El] for these alloys with competing exchange interactions. An example of magnetisation versus temperature curves is given in Fig. 155 for different values of the externally applied magnetic field strength. An “experimental” susceptibility curve x&T) is derived as indicated in the caption of the figure. Magnetisation curves Fig. 160. For a more complete survey of magnetisation curves for alloys both in ZFC and FC state, see [85Sl, 91Bl]. Neutron inelastic scattering spectra Figs. 161, 162 and spin-wave stiffness constants Fig. 163. The 57Fe Mijssbauer spectra have been measuredat low temperature for two series of alloys represented in the phase diagram of Fig. 164. For examples of the spectra see Figs. 165, 166, and for the magnetic hyperfine fields Figs. 167, 168. Linear and volume magnetostriction Figs. 169-171, linear thermal expansion Fig. 172. Elastic constants Figs. 173a-d, electrical resistivity Figs. 174, 175 and magnetoresistanceFig. 176. Specific heat Figs. 177, 178. Mn A

Fe-Ni-Mn

Fig. 151. Fe-Ni-Mn system. Magnetic phase diagram in the fee y phase. Compiled by E.F. Wassermann from [67Sl, 76M1, 74E1, SlMl, 87A3, 88821. Contour lines r, in the AF phase and T, in the F phase. Dotted region: pure spin-glass phase; hatched region: area of a reentrant spin-glass phase below ferromagnetic ordering. Crosses: commercial Invar and Elinvar compositions [89W2]. Fe

IO

Landolt-Bornstein New Series 111132A

20

30 .’ 40

50 Ni -

60

70

80 at% 90

Ni

202

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

200

500.

K

I

[Ref. p. 2 18

I

K ‘\(Fe0.6SNi0.35)100 -x M”x I 450- b I

160

120

80-

40 0’ 00

0

5.

10

x-

15

20

25

30

Fig. 152. (Fe, 6,Ni, 35),c,0-xMnx. Magnetic phase diagram derived from various types of magnetisation measurements.Downward triangles: Curie temperature; triangles: transition temperature into the spinglass state. Circles representthe temperaturefor maximum spontaneous magnetisation for each alloy [92W3, seealso 90Tl].

0

5

10

15

20

25

Fig. 153. (Fe,,SNi, 35),00-xMnx. Magnetic phase diagram obtained from an evaluation of the mean magnetic hyperfine field derived from Mossbauer spectra[87Hl, 89Hl].

Landolt-B6mstcin New Serk 111132A

Ref. p. 2181

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

200 K (k0.65

I Ni0.35)100-x

Mn

x= 12.65 X

0

b 0

1

2

a

203

3

4

1

2

3

4

kOe 5

kOe 5

HK

x =15.95

120

80

c

0

Landolt-Biirnstein New Series II1132A

1

2

3

:

H-

4

kOe 5

Fig. 154. (Feo,65Ni0,,5),oo_xMnx, annealed at 1300 K for 120 h. Influence of externally applied magnetic field H on the characteristic temperatures. Tc: Curie temperature,T,,,: maximum of spontaneousmagnetisation and q,,,, transition to a complete disordered spinglass state (for definition see Figs. 155, 159) [91Bl, seealso 88H1, 90Kl].

204

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

45 tcm3 9

I

b

I

135

I

I

( Fe0.65Ni0.35)85.77 Mn 14.23

40 1

$ 120

35

105

30

90

25

75

20

I 60 2

IiT

[Ref. p. 2 18

15

j\\qob

U

50

100

150

Fig. 155. (Fe,,bSNiO &a5 ,,Mn,, *,, zero-field cooled (ZFC). Example for definition of the transition temperatures T,-, T,, and Ti, of Fig. 154a-c. The experimental susceptibility xLahE AM/AH,,,,, is calculated as the difference between “neighboured” M vs. T curves, the result being divided by the difference of the applied external field strengths HappI [91Bl].

H=l.5kOe

200

250 K 300

l-

300 -10-5 & 9

30If*IO-5 giy 9 25

I

I

Fe65(Ni0 . 7Mn03'35 .

20l-

15 I x"

IC E,-

0 a

40

80

120

160

K

t

2

T-

Fig. 156. a Fe,,(Ni,,Mn, J3.( and b Fe,,(Ni, ,Mn, &. Magnetic mass susceptibility ~a in various magnetic

b

40

80

120

160 K

200

l-

fields Has a function of temperatureT [85Sl, see also 90Kl].

Landolt-Barnstein New Series IIII32A

Ref. p. 2181

.10-2 cm3 -ii-

I

4 x"

205

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn 10 .10-j d 9 8

H=lCOe

Ni&%.I3413; P I Fe65(

I!

100

t

75

6

x"4

50

0

200

100

K

300

400

T-

Fig. 157.

0

200

100

300

K

1

T-

Fe,,(Ni,,,,,Mn,,,,),,,

Fe,,(Ni,.,,Mn,,,,),,,

disordered fee crystals. Magnetic mass susceptibility xs, measuredwith a field strength of 10 Oe. Solid and open symbols correspond to zero-field cooling (ZFC) and field cooling (FC), respectively [93M2].

Fig. 158. Fe,,(Ni,,,,,Mn o.134)35,bd?%8Mno,22h~ disordered fee crystals. Magnetic mass susceptibility xs, measuredwith a field strength of 10 kOe. Difference between ZFC and FC is less than indicated by the size of the symbols [93M2].

-., .'"-3

(Fe65Ni135)0.8864 ~no*l136

I

I

Fig. 159. (Fe,,Ni,,),,,,,,Mn, ,,s6 in FC and ZFC state. Example of characteristic temperatures r, (low), rn (high) and Tc in the curves for the real (x7 and imaginary (x”) part of the magnetic susceptibility (given in arbitrary units). Amplitude and frequency of the measuring field 10 mT and 470 Hz, respectively [92El]. 0

40

80

120 T-

Landolt-Bbmstein New Series 111132A

160

K

200

206

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

60

l

I

b

a

b

40

0

10

20

H-

30

40 kOe 50 b

Fig. 160. a b led% s&h 134)35 and disordered fee crystals. Mass %A% #no d3+ magnetisation ~vs. applied magnetic field at various

counts f Fe&Ni, I.*ss~no.,34)3~ 10 min I

I

b

0

[Ref. p. 218

’ T:260K

I

I

I

I

2

3

4 meV 5

I

10

20

30

40 kOe 50

H-

temperaturesT. ZFC samplesmeasuredfor increasing field strengths [93M2].

l Fig. 161b

1

E-

0

Fig. 161s +

Fig. 161. Fe,,(Ni, 866Mn0,&, ordered fee crystal. Inelastic neutron scattering spectra at a 8 K (spinglass phase) and 200 K (ferromagnetic phase) and b 260 K (ferromagnetic phase) for various scattering wave vectors q. The increase of the scattering at the high energy side is due to the tail of the phonon signal [93M2].

Ref. p. 2181

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

207

450 counts

300

20min

Klmin

400

250

350

250

50 125

250

a

25 00

Landolt-BOrnstein New Series III/32A

0.5 0.5

1.0 1.0

E-

1.5

2.0 meV 2.5

50 0

0.5

1.0

1.5 E-

2.0 meV 2.5

[Ref. p. 218

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

208 500

I

I

I

9 =0.1838-l

Fe,,(Ni,,, MnO&

300 counts M P 250 4 200150100-

0.7

1.0

1.3

1.6

1.9

2.1 meV2.5

500.7

1.0

1.3

1.6

1.9

2.2 meV2.5

E-

aoc

600 60[ counts 20min

counts M

I

q=0.2131-’ I

1 1=30K

T=30K

601 4OC 3oc 300 401 2OC 200 201 0.7

1.0

1.3

1.6

1.9

2.2 md 2.5

100 IOC 0.7

1.0

1.3

E-

1.6

1.9

2.2 meV 2.5

E-

600 counts 10

q=o.239 x-’ T= 1OOK

400

.--

0.7

I J 1.0

1.3

1.6

1.9

2.2 meV 2.5

0.7

1.0

1.3

1.6

1.9

2.2 meV 2.5

E-

Fig. 162.

Fe,&& ,,Mn,&,. Inelastic neutron scattering spectra at 8 K. 30 K and 100 K. This alloy

has not a ferromagnetic phase, but a P-SG transition at about 50 K [93M2].

Landolt-BBmrrcin New Series 111132A

Ref. p. 2181

0

50

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

100

150 T-

Fig. 163. Fe,,(Ni,,,,Mn,,,,,),,,

200

250

209

300 K 350

ordered fee crystal. a Spin-wave stiffness constant D and b spin-wave

b

T-

energy gap A vs. temperature T [93M2].

Fig. 164. Fe&i,-,Mn,),, and (Fe65Ni3s),-xMnx,alloy series representedin the phase diagram by a range of circles and by a dashedcurve, respectively. Mn -

Landolt-Bornstein New Series llV32A

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

210

.

1=4.2K

F~,,(NI,-, Mn, lj5

.

. -10

I

I

I

I

I

I

I

I

-8

-6

-4

-2

0

2

4

6 mm/s 10

Y-

[Ref. p. 218

I

Fig. 165. Fe,,(Ni,-,Mn,),,, see Fig. 164, alloys annealed at I100 “C for 100 h. “Fe MBssbauer spectra at 4.2 K. The solid curves have been calculated on the basis of the magnetic hyperfine field distribution histograms of Fig. 167 [84Sl].

Landolt-B6mstein New Series IIIWZA

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

Ref. p. 2181

57Fe T= 5K

J0.084 ‘% A

L

+

r

0

I

100

I

200 Hhyp -

300

kOe

400

(Fe6SNi3s)1-xMnx, see Fig. 164, alloys annealed at 1300 K for 120 h. “Fe Mdssbauer spectra at 5 K (right-hand side) and the corresponding Fig. 166.

Landolt-Bbmstein New Series IW32A

-8

-4

0

4

mm/s

V-

magnetic hyperfine field distributions (left-hand side) [89Hl].

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

0 HhyP -

[Ref. p. 218

Fig. 167. Fe65(Ni,-,Mn,)3salloys, see Fig. 164. Magnetic hyperfine field distribution curves and histograms derived from the spectra of Fig. 165 [84Sl].

Ll

Landolt-BOrnstein New Series lW32A

Ref. p. 2181

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

320

I

kOe

213

I

(Fe, fi5Ni, d,-, Mn,

200

I 160 E 1s' 120

0

20

40

60

b 80

I

a

0

I

b

50

100

I

150

200

\I

I

250 K 300

80

100 K 120

T-

Fig. 168. (Fe,,,,Ni,,,,),,Mn, alloys, see Fig. 164. Mean magnetic hyperfine field HhYPvs. temperature T as derived from spectra of and similar to those of Fig. 166. a distorted ferromagnetic and reentrant-spinglass alloys, b pure spin glass and distorted antiferromagnetic alloys. As an example of an Fe-rich alloy the curve for Fe,,Ni,, is also given [89Hl].

T-

8 -10-6

I

I

x = 26.5; T, =I60 K

0.8

0

a

10

20

H-

30

40

50 kOe 60

Fig. 169. Fes,,Ni,MnsO, alloys. Linear magnetostriction ;1 vs. applied magnetic field H at various tem-

Landolt-B6rnstein New Series IIV32A

0 b

IO

20

30

40

50 kOe60

H'-

peratures T. a x = 34.8, b x = 26.5. Inset in a: magnetic phasediagram [88A3].

[Ref. p. 2 18

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

214

.*

Fe,, (Ni,-, Mn, )35 l= 4.2K .

Fig. 170. Fe,, ,Ni,, sMn,, z and Fe,, sNi,,,,Mn2, .,. Linear magnetostriction 1 vs. temperature T in constant externally applied magnetic fields H. Arrows indicate the Neel temperatureTN[88A3].

I 10

I 20

.

I

I

30

40

/X-=0.25

kOe !

H-

Fig. 171. Fe,,(Ni,-,Mn,),,, see Fig. 164. Volume magnetostriction CLIvs. applied magnetic field H at 4.2 K [85Wl].

-

BOO K

I /

600

J

100 200

I

I

I

Fe,oMn,,;AF.+,

I I 3

400

600

Fe50Ni,Mn50-x I 800

I 1000K 1200

Fig. 172. Fe,,Ni,Mn,,_,. Linear thermal expansion coefficient a vs. temperature T. Compiled in [89W2] from data of [77Bl] and [88A2]. Inset: Magnetic phasediagram.

TLandolt-Bbmrlein New Series 111/32A

Ref. p. 2181

215

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

>I”

GPO 130 125

200’ 0

I 200

I 400

7-

I 600

K

I 800

0 b

400

200

600

K

800

T260 GPO 250 220

I

210

c; 210 200 220 210

400

200

600

K

800

T-

Fig. 173. Fe65(Ni,-XMn.J35,see Fig. 164, single crystals. Elastic constants vs. temperature T as derived from ultrasonic pulse-echo technique experiments in an applied magnetic field H parallel to the [l lo] direction and perpendicular to the direction of the

Land&-Biirnstein New Series 111132A

d

200 200’ 0

I 25

I 75

I 50

I 100

I I 125 K 150

T-

wave propagation vector. The data are extrapolations to H=O. Curie temperaturesTc determined from Arrott plots. a longitudinal modulus c,=(c,,+c,,+~c,,)/~; b shear modulus c,,; c shear modulus c’=(c,,-c,,)/2; d cL in the low-temperature range [9OS1, 91S2].

216

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

[Ref. p. 218

140 pi2cm

;:41* iY476 +

1x

1.53-

t Qr lot

9(

-

1200K 1400 a

/-

Fig. 174. Fe5,(Ni,Mn,-,)5,. fee alloys. Electrical resistivity p vs. temperature T for various alloys with a antiferromagnetic ground state and b ferromagnetic ground state. The arrows indicate Ntel and Curie

8(

II

b

200

400

600

800

1000 1200K 1400

T-

temperatures,respectively. For each alloy the number of conduction electrons per atom, e/a, is shown. In a the the constant c is added in order to separate the curves [78B2].

Landolr-Barnstein New Series 111132A

Ref. p. 2181

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn 11.25 w5

I

I

I

Bcm (Fe0.65Ni035)916Mn81 . . 11.00

11.50

217

.

I 11.25 Ql 11.00

Qr

10.25 10.75

10.501J/i 1o.5o 0

10.00

50

100

a

200

150

250 K 300

b

T10.6 .10-5 Rem 10.4

9.75 0

50

100

150

200

250 K 300

T-

0.65Ni0.35 $2.3 Mn 7.7 I

I

I

9.8 9.8 0

9.6 0

50

100

150

10

20 I-

200

30

40 K 50

250 K 300

Fig. 175. (Fe,,,,Ni,,,,),,,_,Mn, alloys annealed at 1300 K for 120 h. The electrical resistivity p vs. temperature T [89B3].

T-

c

Fig. 176. (Fe,,,,Ni,,,,),,,,Mn,, x = 11.36, annealed at 1300 K for 120 h. Magnetoresistance Aplp, in a pulsed magnetic field of 1.6 Oe, vs. temperature T as measuredin the vicinity of the Curie temperature with and without an applied magnetic field H. p. is the resistivity without applied magnetic fields [92B2]. T-

Landolt-Bornstein New Series IIV32A

218

[Ref. p. 218

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

30 Kh 25

20 1 15 e 10

5

0

0

100

50

150

200

250 K 300

T-

a

Fig. 177. Fe,,Ni,,Mn,,. a Total specific heat C,, vs. temperature T. Inset: CIJT vs. 7” for the low temperature range. b Electronic and magnetic specific heat

O

25

50

b

15

100

125 K 150

T-

C,, obtained after substracting the lattice contribution calculated for a Debye temperature 0, = 420 K from

the dataof a [89L2].

100 InJ molK 80

I

L?

60

40

Fig. 178. Fe,,Ni,,Mn,,. Low-temperature specific heat C, as measured in various applied magnetic fields H [88L4, seealso88L.31. 0

2

1

3

K

I-

1.2.4.8 References for 1.2.2,1.2.3 and 1.2.4 34M1

Masumoto, H.: Sci. Rep. Tohoku Imp. Univ. Ser. I, 23 (1934) 265

51Rl

Rideout, S., Manley, W.D., Kamen, E.L., Lement, B.S., Beck, P.A.: Trans. Am. Inst. Min. Metall. Pet. Eng. 191 (1951) 872

58Kl

Kasper, J.S., Waterstrat, R.M.: Phys. Rev. 109 (1958) 1551

Landoll-B6rnstein New Series W32A

218

[Ref. p. 218

1.2.4 Ternary alloys between Fe, Co or Ni and Ti, V, Cr or Mn

30 Kh 25

20 1 15 e 10

5

0

0

100

50

150

200

250 K 300

T-

a

Fig. 177. Fe,,Ni,,Mn,,. a Total specific heat C,, vs. temperature T. Inset: CIJT vs. 7” for the low temperature range. b Electronic and magnetic specific heat

O

25

50

b

15

100

125 K 150

T-

C,, obtained after substracting the lattice contribution calculated for a Debye temperature 0, = 420 K from

the dataof a [89L2].

100 InJ molK 80

I

L?

60

40

Fig. 178. Fe,,Ni,,Mn,,. Low-temperature specific heat C, as measured in various applied magnetic fields H [88L4, seealso88L.31. 0

2

1

3

K

I-

1.2.4.8 References for 1.2.2,1.2.3 and 1.2.4 34M1

Masumoto, H.: Sci. Rep. Tohoku Imp. Univ. Ser. I, 23 (1934) 265

51Rl

Rideout, S., Manley, W.D., Kamen, E.L., Lement, B.S., Beck, P.A.: Trans. Am. Inst. Min. Metall. Pet. Eng. 191 (1951) 872

58Kl

Kasper, J.S., Waterstrat, R.M.: Phys. Rev. 109 (1958) 1551

Landoll-B6rnstein New Series W32A

Referencesfor 1.2.2-l .2.4

219

58Pl

Pearson, W.B.: A Handbook of Lattice Spacings and Structures of Metals and Alloys, London: PergamonPress(1958) p. 539

59Kl

Kiister, W., Hofmann, G.: Arch. Eisenhtittenwes. 30 (1959) 249

6OC1

Cheng, C.H., Wei, C.T., Beck, P.A.: Phys. Rev. 120 (1960) 426

63Jl

Johnson, C.E., Ridout, M.S., Cranshaw, T.E.: Proc. Phys. Sot. 81 (1963) 1079

64Hl

Hamaguchi, Y., Kunitomi, N.: J. Phys. Sot. Jpn. 19 (1964) 1849

65Wl

White, G.K.: Proc. Phys. Sot. 86 (1965) 159

66Ul

Umebayashi, H., Ishikawa, Y.: J. Phys. Sot. Jpn. 21 (1966) 1281

6711 6701 67S1

Ishikawa, Y., Endoh, Y.: J. Phys. Sot. Jpn. 23 (1967) 205 Okamoto, T., Fujii, H., Tsurui, T., Fujiwara, H., Tatsumoto, E.: J. Phys. Sot. Jpn. 22 (1967) 337 Shiga, M.: J. Phys. Sot. Jpn. 22 (1967) 539

68Pl

Pepperhoff, W., Ettwig, H.H.: Z. Angew. Phys. 24 (1968) 88

69Al

Arajs, S.: Phys. Status Solidi 31 (1969) 217

70Ml 7OSl

Moody, D.E., Staveley, M.G., Kuentzler, R.: Phys. Lett. A 33 (1970) 244 Stevens,E.R., Carlson, O.N.: Metall. Trans. 1 (1970) 1267

71Cl 71Dl 71Pl 71Sl 71S2

Crangle, J., Goodman, G.M.: Proc. R. Sot. London A 321(1971) 477 Durand, J.: J. Phys. (Paris) 32 (1971) 823 Palmer, S.B., Lee, E.W.: Philos. Mag. 24 (1971) 311 Sueda,N., Fujiwara, H.: J. Sci. Hiroshima Univ. Ser. A 35 (1971) 59 Spitzli, P.: Phys. Kondens. Mater. 13 (1971) 22

72Al 72Bl

Aldred, A.T.: Int. J. Magn. 2 (1972) 223 Besnus, M.J., Gottehrer, Y., Munschy, G.: Phys. Status Solidi (b) 49 (1972) 597

74E1 74Kl 74Yl

Ettwig, H.H., Pepperhoff, W.: Phys. Status Solidi (a) 23 (1974) 105 Kohara, T., Asayama, K.: J. Phys. Sot. Jpn. 37 (1974) 401 Yamauchi, H., Watanabe,H., Suzuki, Y., Saito, H.: J. Phys. Sot. Jpn. 36 (1974) 971

75Hl 7511 75Ll

Hesse,J., Rtibartsch, A.: Physica B 80 (1975) 33 Ishikawa, Y., Kohgi, M., Noda, Y.: J. Phys. Sot. Jpn. 39 (1975) 675 Loegel, B., Friedt, J.M., Poinsot, R.: J. Phys. F 5 (1975) L54

76Al 76Kl 76Ml

Aldred, A.T.: Phys. Rev. B 14 (1976) 219 Kawakami, M.: J. Phys. Sot. Jpn. 40 (1976) 56 Men’shikov, A.Z., Kazantsev, V.A., Kuzmin, N.N.: Pis’ma Zh. Eksp. Teor. Fiz. 23 (1976) 6; Sov. Phys. JETP Lett. 23 (1976) 4 (Engl. Transl.) Richter, F., Pepperhoff, W.: Arch. Eisenhtittenwes. 47 (1976) 45 Williams jr., W., Stanford, J.L.: J. Magn. Magn. Mater. 1 (1976) 271 Warnes, L.A.A., King, H.W.: Cryogenics 16 (1976) 659

76Rl 76Wl 76W2

Landolt-BBrnstein New Series lW32A

220 77Al 77Bl 77Ml 77N 1 77Y 1

78Bl 78B2 78El 78Hl 78Ll 78Ml 78Rl 78Tl 79Al 79A2 79Bl 79B2 79Hl 79Kl 79Ml 7901 79Yl

Referencesfor 1.2.2-I .2.4 Aldred, A.T., Kouvel, J.S.: Physica B 86-88 (1977) 329 Bendick, W., Ettwig, H.H., Richter, F., Pepperhoff, W.: Z. Metallkd. 68 (1977) 103 Mokhov, B.N., Goman’kov, V.I., Makarov, V.A., Sakharova, T.V., Nogin, N.I.: Zh. Eksp. Teor. Fiz. 72 (1977) 1833; Sov. Phys. JETP 45 (1977) 962 (Eng!. Transl.) Nemanich, R., Kimball, C.W., Dunlap, B.D., Aldred, A.T.: Phys. Rev. B 16 (1977) 124 Yamashita, O., Yamagushi, Y., Watanabe,H.: Annu. Prog. Rep. on Neutron Scattering in JAERI 61 (1979) report M Burke, S.K., Rainford, B.D.: J. Phys. F 8 (1978) L239 Bendick, W., Pepperhoff, W.: J. Phys. F 8 (1978) 2535 Endoh, Y.: J. Magn. Magn. Mater. 10 (1978) 177 Hamada,N., Miwa, H.: Prog. Theor. Phys. 59 (1978) 1045 Lenkkeri, J.T., Lahteenkorva, E.E.: J. Phys. F 8 (1978) 1643 Menshikov, A.Z., Sidorov, S.K., Teplykh, A.Y.: Fiz. Met. Metalloved 45 (1978) 949; Phys. Met. Metallogr. 45 Nr. 5 (1978) 42 (Engl. Transl.) Rode, V.E., Finkelberg, S.A., Skurikhin, A.V.: Phys. Met. Metallogr. 45 (1978) 433 (Engl. Transl.) Tange, H., Tokunaga, T., Goto, M.: J. Phys. Sot. Jpn. 45 (1978) 105 Aoki, Y., Obi, Y., Komatsu, H.: Z. Metallkd. 70 (1979) 436 Acker, F., Huguenin, R.: J. Magn. Magn. Mater. 12 (1979) 58 Bendick, W., Pepperhoff, W.: J. Phys. F 9 (1979) 2185 Beille, J., Towfiq, F., Voiron, J., Senateur,J.P.: J. Magn. Magn. Mater. 11 (1979) 193 Hearmon, R.F.S.: Landolt-B&stein, New Series, Vol. III/l 1 (Hellwege, K.-H., ed.), Berlin, Heidelberg, New York: Springer (1979) 11 Katahara, K.W., Nimalendran, M., Manghnani, M.H., Fisher, E.S.: J. Phys. F 9 (1979) 2167 Maki,S.,Adachi,K.: J.Phys. Sot. Jpn.46(1979) 1131 Obrtlik, K., Kucera, J.: Phys. Status Solidi (a) 53 (1979) 589 Yamamoto, Y., Nakagiri, N., Nomura, M., Tange, H., Fujiwara, H.: Jpn. J. Appl. Phys. 18 (1979) 2139

80Al 80Rl 80Tl

Arnold, Z., Kamarad, J.: J. Magn. Magn. Mater. 15-18 (1980) 1167 Rivlin, V.G., Raynor, G.V.: Int. Met. Rev. 1 (1980) 21 Tange, H., Goto, M.: J. Phys. Sot. Jpn. 49 (1980) 957

81Bl 81El 8111 81Ll 81Ml

8lT3

Bendick, W., Pepperhoff, W.: J. Phys. F 11 (1981) 57 Endoh, Y., Noda, Y., Iizumi, M.: J. Phys. Sot. Jpn. 50 (1981) 469 Inden, G.: Physica B 103 (1981) 82 Lenkkeri, J.T.: J. Phys. F 11 (1981) 1991 Men’shikov, A.Z., Burlet, P., Chamberod, A., Tholence, J.L.: Solid State Commun. 39 (1981) 1093 Shapiro, S.M., Fincher, C.R., Palumbo, A.C., Parks, R.D.: Phys. Rev. B 11 (1981) 6661 Turek, P., Kuentzler, R.: Physica B 107 (198 1) 257 Takzey, G.A., Sych, I.I., Men’shikov, A.Z., Teplykh, A.Y.: Fiz. Met. Metalloved 52 Nr. 6 (198 1) 1657; Phys. Met. Metallogr. 52 No 6 (198 1) 27 (Engl. Transl.) Tange, H., Yonei, T., Goto, M.: J. Phys. Sot. Jpn. 50 (1981) 454

82Ll 82Ml 82M2

Ltltgemeier, H., Dubiel, S.M.: J. Magn. Magn. Mater. 28 (1982) 277 Mirebeau, I., Cadeville, M.C., Parette,G., Campbell, I.A.: J. Phys. F 12 (1982) 25 Mirebeau, I., Parette,G.: J. Appl. Phys. 53 (1982) 1960

81Sl 81Tl 8lT2

Landolt-Barnstein New Series IIWZA

Referencesfor 1.2.2-I .2.4 82M3 82Pl 82Sl 83B1 83Cl 83Dl 83D2 83H1 83H2 83Ll 83Ul 84Al 84Dl 84D2 84D3 84Fl 84Hl 84Ml 84M2 84M3 84M4 84P1 84s 1 84W1 85Al 85D1 85D2 85D3

221

Men’shikov, A. Z., Takzey, G.A., Teplykh, A.Y.: Fiz. Met. Metalloved 54 Nr. 3 (1982) 465; Phys. Met. Metallogr. 54 Nr. 3 (1982) 41 (Engl. Transl.) Pierron, V., Cadeville, M.C.: J. Phys. F 12 (1982) 549 Simpson, M.A., Smith, T.F.: Aust. J. Phys. 35 (1982) 307 Burke, S.K., Cywinski, R., Davis, J.R., Rainford, B.D.: J. Phys. F 13 (1983) 45 1 Cable, J.W., Thompson, J.R., Sekula, S.T.: J. Magn. Magn. Mater. 40 (1983) 147 Dubiel, S.M., Zinn, W.: J. Magn. Magn. Mater. 37 (1983) 237 Deryabin, A.V., Rimlyand, V.I., Larionov, A.P.: Fiz. Tverd. Tela (Leningrad) 25 (1983) 1921; Sov. Phys. Solid State25 (1983) 1109 (Engl. Transl.) Hennion, M.: J. Phys. F 13 (1983) 2351 Hausch, G., Schmolz, A., T&ok, E., Warlimont, H.: J. Phys. (Paris) Colloq. 12 (1983) C9471 Ltitgemeier, H., Bohn, H.G., Dubiel, S.M.: J. Magn. Magn. Mater. 31-34 (1983) 547 Uhrenius, B., For&n, K.: Z. Metallkd. 74 (1983) 610 Abdul-Razzaq, W., Kouvel, J.S.: J. Appl. Phys. 55 (1984) 1623 Dubiel, S.M., Sauer, Ch., Zinn, W.: Phys. Rev. B 30 (1984) 6285 Dubiel, S.M., Zinn, W.: Phys. Rev. B 29 (1984) 2279 Deryabin, A.V., Chirkov, Y.A., T’kov, A.V.: Zh. Eksp. Teor. Fiz. 86 (1984) 609; Sov. Phys. JETP 59 (1984) 355 (Engl. Transl.) Funahashi, S., Kohara, T.: J. Appl. Phys. 55 (1984) 2048 Hennion, B., Hennion, M., Hippert, F., Murani, A.P.: J. Appl. Phys. 55 (1984) 1694 Mirebeau, I., Hennion, M., Parette,G.: Phys. Rev. Lett. 53 (1984) 687 Men’shikov, A.Z., Dorofeev, Y.A.: Pis’ma Zh. Eksp. Teor. Fiz. 40 (1984) 59; JETP Lett. 40 (1984) 791 (Engl. Transl.) Moze, O., Hicks, T.J.: J. Phys. F: Met. Phys. 14 (1984) 2 11 Majumdar, A.K., Blanckenhagen, P.von: Phys. Rev. B 29 (1984) 4079 Pierron-Bohnes, V., Mirebeau, I., Balanzat, E., Cadeville, M.C.: J. Phys. F 14 (1984) 197 Shiga, M., Nakamura, Y.: J. Magn. Magn. Mater. 40 (1984) 319 Willgeroth, S., Ulrich, H., Hesse,J.: J. Phys. F 14 (1984) 387

85T3 85Wl

Aidun, R., Arajs, S., Moyer, C.A.: Phys. Status Solidi (b) 128 (1985) 133 Dubiel, S.M., Sauer, Ch., Zinn, W.: Phys. Rev. B 32 (1985) 2745 Dubiel, S.M., Sauer, Ch., Zinn, W.: Phys. Rev. B 31 (1985) 1643 Deryabin, A.V., T’kov, A.V., Shvetsov, B.N., Larionov, A.P., Zakharov, I.V.: Fiz. Tverd. Tela 27 (1985) 834; Sov. Phys. Solid State27 (1985) 511 (Engl. Transl.) Galvlo da Silva, E., Preston, R.S., Gonser, U.: J. Appl. Phys. 57 (1985) 1063 Laar, B. van, Maniawski, F., Kaprzyk, S.: J. Phys. F 15 (1985) 675 Men’shikov, A.Z., Takzei, G.A., Dorofeev, Y.A., Kazantsev, V.A., Kostyshin, A.K., Sych, 1.1.:Zh. Eksp. Teor. Fiz. 89 (1985) 1269; Sov. Phys. JETP 62 (1985) 734 (Engl. Transl.) Shiga, M., Satake,T., Wada, Y., Nakamura, Y.: J. Magn. Magn. Mater. 51 (1985) 123 Takasugi, T., Izumi, 0.: Acta Metall. 33 (1985) 33 Takzei, G.A., Kostyshin, A.M., Grabenyuk, Y.P., Sych, 1.1.:Zh. Eksp. Teor. Fiz. 89 (1985) 2181;Sov. Phys. JETP 62 (1985) 1259 (Engl. Transl.) Turek, P., Kuentzler, R., Bieber, A., Jesser,R.: Solid StateCommun.53 (1985) 979 Wada, H., Muraoka, Y., Shiga, M., Nakamura, Y.: J. Phys. Sot. Jpn. 54 (1985) 4761

86Fl 86F2

Fawcett, E., Roberts, R.B., Day, R., White, G.K.: Europhys. Lett. 1 (1986) 473 Furusaka, M., Ishikawa, Y., Yamaguchi, S., Fujino, Y.: J. Phys. Sot. Jpn. 55 (1986) 2253

85Gl 85Ll 85Ml 85Sl 85Tl 85T2

Land&-Bbmstein New Series 111/32A

222 86KI 86N 1 86P1 86Sl 8632 86S3 86TI 86Wl 8621 87Al 87A2 87A3 87Bl 87Dl 87H1 87Kl 87K2 87M 1 87M2 87Sl 87Tl 87X1 88Al 88A2 88A3 88Bl 88Cl 88C2 88Dl 88HI 88Ll 88L2 88L3 88L4 88Ml 8801 88Rl -88Sl 8832

Referencesfor 1.2.2-l .2.4 Kasamatsu, Y., Hihara, T., Kojima, K., Kamigaichi, T.: J. Magn. Magn. Mater. 54-57 (1986) 1107 Nakai, Y., Yamamoto, N., Kunitomi, N., Achiwa, N.: J. Phys. Sot. Jpn. 55 (1986) 1188 Pierron-Bohnes, V., Cadeville, M.C., Bieber, A., Gautier, F.: J. Magn. Magn. Mater. 54-57 (1986) 1027 Shiga, M., Miyake, M., Nakamura, Y.: J. Phys. Sot. Jpn. 55 (1986) 2290 Shinohara, T., Takasugi, T., Yamauchi, H., Kamiyama, T., Yamamoto, H.Izumi, 0.: J. Phys. F 16 (1986) 1845 Shinohara, T., Shinogi, A., Endo, K., Takasugi, T., Izumi, 0.: J. Phys. F 16 (1986) L89 Takzei, G.A., Kostyshin, A.M., Grebenyuk, Y.P., Sych, 1.1.:Zh. Eksp. Teor. Fiz. 90 (1986) 1843; Sov. Phys. JETP 63 (1986) 1081 (Engl. Transl.) Wakabayashi,N.: Phys. Rev. B 33 (1986) 644 1 Zhang, Y.: Acta Metall. Sin. A 22 (1986) 470 Alberts, H.L., Lourens, J.A.J.: J. Phys. F 17 (1987) 727 Abdul-Razzaq, W., Kouvel, J.S.: Phys. Rev. B 35 (1987) 1764 Acet, M., Stamm,W., Zlhres, H., Wassermann,E, F.: J. Magn. Magn. Mater. 68 (1987) 233 Bisanti, P., Mazzone, G., Sacchetti, F.: J. Phys. F 17 (1987) 1425 Dubiel, S.M., Fischer, K.H., Sauer,Ch., Zinn, W.: Phys. Rev. B 36 (1987) 360 Huck, B., Hesse,J.: J. Magn. Magn. Mater. 70 (1987) 425 Kennedy, S.J., Hicks, T.J.: J. Phys. F 17 (1987) 1599 Kouvel, J.S., Abdul-Razzaq, W., Ziq, Kh.: Phys. Rev. B 35 (1987) 1768 Mirebeau, I., Parette,G., Cable, J.W.: J. Phys. F 17 (1987) 191 Marwick, A.D., Piller, R.C., Cranshaw, T.E.: J. Phys. F 17 (1987) 37 Stadnik, Z.M., Griesbach, P., Dehe, G., Gtltlich, P., Maniawski, F.: J. Magn. Magn. Mater. 70 (1987) 436 Takzei, G.A., Kostyshin, A.M., Sych, 1.1.:Fiz. Tverd. Tela 29 (1987) 2434; Sov. Phys. Solid State 29 (1987) 1401 (Engl. Transl.) Xu, J.-H., Oguchi, T., Freeman,A.J.: Phys. Rev. B 35 (1987) 6940 Aitken, R.G., Daneshvar, K.: J. Appl. Phys. 63 (1988) 4096 Acet, M., Zahres, H., Stamm,W., Wassermann,E.F.: J. Appl. Phys. 63 (1988) 3921 Acet, M., Zahres, H., Stamm, W., Wassermann,E.F.: J. Phys. (Paris) Colloq. 49 (1988) C8121 Berger, L., Freitas, P.P., Warner, J.D., Schmidt, J.E.: J. Appl. Phys. 64 (1988) 5459 Chang, X.S., Hohenemser,C.: Phys. Rev. B 37 (1988) 261 Cranshaw, T.E.: J. Phys. F 18 (1988) 43 Dubiel, S.M.: Phys. Rev. B 37 (1988) 7284 Huck, B., Landes, J., Stasch, R., Hesse, J.: J. Phys. (Paris) Colloq. Suppl. 49 (1988) C81141 Lequien, S., Hennion, B., Shapiro, S.M.: Phys. Rev. B 38 (1988) 2669 Lecomte, G.V., Schubert, N.: Phys. Lett. A 131 (1988) 64 Lecomte, G.V., Schubert, N., Wassermann,E.F.: J. Magn. Magn. Mater. 71 (1988) 3 18 Lecomte, G.V., Schubert, N., Opheys, M.F., Wassermann,E.F.: J Phys. (Paris) Colloq. Suppl. 49 (1988) C8-3 11 Moze, O., Mitchell, P.W., Burkes, S.K., Davis, J.R., Booth, J.G.: J. Phys. F 18 (1988) 527 Gner, Y., Aktas, B., Apaydin, F., Harris, E.A.: Phys. Rev. B 37 (1988) 5866 Renaud, Ph.: Ph. D. Thesis, Universite de Lausanne,Switzerland (1988) Stamm, W., Zahres, H., Acet, M., Schletz, K., Wassermann,E.F.: J. Phys. (Paris) Colloq. 49 (1988) C8-315 Stamm, W.: Ph. D. Thesis, Physics Departement.,University of Duisburg, Germany (1988)

Landoh-Barnstein New Series 111132A

Referencesfor 1.2.2-1.2.4 89Al 89Bl 89B2 89B3 89D1 89Hl 89Kl 89K2 89Ll 89L2 89P1 89Wl 89W2 90El 90H1 9OJl 9052 90Kl 90Ml 9001 9os1 90Tl 9OWl 9OW2 9OYl 91Al 91Bl 91Kl 91Ml 91Nl 91Pl 91P2 91P3 91Sl 91S2

223

Acet, M., Schneider, T., Zahres, H., Stamm, W., Wassermann, E.F., Pepperhoff, W.: Physica B 161 (1989) 63 Butylenko, A.K.: Fiz. Met. Metalloved 68 (1989) 873; Phys. Met. Metall. 68 (1989) 37 (En& Transl.) Bbni, P., Shapiro, S.M.: J. Phys.: Condens.Matter 1 (1989) 6123 Bottger, Ch., Hesse,J.: Z. Phys. B 75 (1989) 485 Drittler, B., Stefanou, N., B&gel, S., Zeller, R., Dederichs, P.H.: Phys. Rev. B 40 (1989) 8203 Huck, B., Hesse,J.: J. Magn. Magn. Mater. 78 (1989) 247 Kawarazaki, S., Yasuda, K.: J. Phys. Sot. Jpn. 58 (1989) 4200 Kaiser, A.B., Smith, T.F.: Physica B 160 (1989) 33 Lecomte, G.V., Rellinghaus, B., Wassermann,E.F.: Physica B 161 (1989) 49 Lecomte, G.V., Schubert, N., Wassermann,E.F.: Physica B 161 (1989) 46 Pei, S., Massalski, T.B., Temmerman, W.M., Sterne, P.A., Stocks, G.M.: Phys. Rev. B 39 (1989) 5767 White, G.K., Nakamura, Y., Shiga, M., Kaiser, A.B.: J. Phys. Sot. Jpn. 58 (1989) 3485 Wassermann,E.F.: Physica Scripta T 25 (1989) 209 Ebert, H., Winter, H., Johson, D.D., Pinski, F.J.: J. Phys. Condens.Matter. 2 (1990) 443 Herman, F., Jepsen,0.: Phys. Rev. B 41 (1990) 6811 John, C., Ztihres, H., Acet, M., Stamm, W., Wassermann,E.F., Pepperhoff, W.: J. Appl. Phys. 67 (1990) 5268 Jepsen,O., Herman, F.: Phys. Rev. B 41 (1990) 6801 Kyprianidis, I.M., Melidis, K.G., Tsoukalas, LA.: Solid StateCommun. 76 (1990) 943 Mirebeau, I., Itoh, S., Mitsuda, S., Watanabe,F., Endoh, Y., Hennion, M., Calmettes, P.: J. Appl. Phys. 67 (1990) 5232 Oner, Y., Aktas, B.: Phys. Rev. B 42 (1990) 2425 Shiga, M., Makita, K., Uematsu, K., Muraoka, Y., Nakamura, Y.: J. Phys.: Condens. Matter 2 (1990) 1239 Takzel, G.A., Grebenyuk, Y.P., Sych, 1.1.:Zh. Eksp. Teor. Fiz. 97 (1990) 1022; Sov. Phys. JETP 70 (1990) 572 (Engl. Transl.) Wada, H., Hada, M., Shiga, M., Nakamura, Y.: J. Phys. Sot. Jpn. 59 (1990) 701 Wassermann, E.F.: Invar: Moment-volume Instabilities in Transition Metals and Alloys (Buschow, K. H. J., Wohlfarth, E. P., eds.), Amsterdam: North-Holland Publ. Co. 5 (1990) 237 Yansheng, Zhang, Hongbin, Zeng, : J. Phys.: Condens.Matter 2 (1990) 2015 Acet, M., John, C., Wassermann,E.F.: J. Appl. Phys. 70 (1991) 6556 Bbttger, Ch., Stasch,R., Wulfes, A., Hesse,J.: J. Magn. Magn. Mater. 99 (1991) 280 Kunkel, H., Roshko, R.M., Ruan, W., Williams, G.: J. Appl. Phys. 69 (1991) 5060 Mirebeau, I., Itoh, S., Mitsuda, S., Watanabe, T., Endoh, Y., Hennion, M., Calmettes, P.: Phys. Rev. B 44 (1991) 5120 Nath, T.K., Majumdar, A.K.: J. Appl. Phys. 70 (1991) 5828 Parette, G.: J. Appl. Phys. 69 (1991) 6135 Paduani, C., GalvBo da Silva, E., Perez-Alcazar, G.A., McElfresh, M.: J. Appl. Phys. 70 (1991) 7524 Petrillo, C., Sacchetti, F., Scafi, M.: Phys. Rev. B 44 (1991) 9418 Schneider, T., Acet, M., Wassermann,E.F., Pepperhoff, W.: J. Appl. Phys. 70 (1991) 6559 Shiga, M., Makita, K., Uematsu, K., Muraoka, Y., Nakamura, Y.: J. Phys. Condens. Matter 3 (1991) 3577

Land&-Bbmstein New Series III/32A

224 92Al 92Bl 92B2 92El 92F 1 92M 1 92Pl 92132 92Rl 92Sl 92Wl 92W2 92W3 92X 1

93Al 93A2 93Bl 93Cl 93Dl 9351 93Ml 93M2 93Sl 93Tl 94Hl

Referencesfor 1.2.2-I .2.4 Alberts, H.L., Lourens, J.A.J.: J. Phys.: Condens.Matter 4 (1992) 3835 Banerjee, S., Raychaudhuri, A.K.: Solid StateCommun. 83 (1992) 1047 Barnard, R.D., Biittger, Ch., Thamm, S., Hesse,J.: J. Phys.: Condens.Matter 4 (1992) 7219 Eckelt, T., Bottger, Ch., Hesse,J.: J. Magn. Magn. Mater. 104-107 (1992) 1665 Fawcett, E., Galkin, V.Yu.: J. Magn. Magn. Mater. 109 (1992) L139 MaRosa, L., Saunders, G.A., Rahdi, H., Kawald, U., Pelzl, J., Bach, H.: Phys. Rev. B 45 (1992) 2224 Pavlovic, A.S.: J. Magn. Magn. Mater. 104-107 (1992) 2035 Petrillo, C., Sacchetti, F., Scafi, M.: J. Magn. Magn. Mater. 104-107 (1992) 2015 Roshko, R.M., Ruan, W.: J. Phys.: Condens.Matter 4 (1992) 6451 Sato, T., Ando, T., Watanabe,T., Ito, S., Endoh, Y.: J. Magn. Magn. Mater. 104-107 (1992) 1625 Wildes, A.R., Kennedy, S.J., Cussen,L.D., Hicks, T.J.: J. Phys.: Condens. Matter 4 (1992) 8961 Wada, H., Inoue, T., Shiga, M.: J. Magn. Magn. Mater. 104-107 (1992) 693 Wulfes, A., Bbttger, Ch., Hesse,J., Sievert, J., Ahlers, H.: J. Magn. Magn. Mater. 104-107 (1992) 2069 Xu, W.M., Steiner, W., Reissner, M., Posinger, A., Acet, M., Pepperhoff, W.: J. Magn. Magn.Mater. 104-107(1992)2023 Akai, H., Dederichs, P.H.: Phys. Rev. B 47 (1993) 8739 Aktas, B., Oner, Y.: J. Phys.: Condens.Matter 5 (1993) 5443 Banerjee, S., Raychaudhuri, A.K.: J. Phys.: Condens.Matter 5 (1993) L295 Cankurtaran, M., Saunders,G.A., Ray, P., Wang, Q., Kawald, U., Pelzl, J., Bach, H.: Phys. Rev. B 47 (1993) 3161 Dubiel, S.M., Costa, B.F.O.: Phys. Rev. B 47 (1993) 12257 Jen, S.U., Chang, S.A.: Phys. Rev. B 47 (1993) 5822 M&y, C., Jedryka, E., Panissod,P.: J. Phys.: Condens.Matter 5 (1993) 1547 Motoya, K., Muraoka, Y.: J. Phys. Sot. Jpn. 62 (1993) 28 19 Sato, T., Ando, T., Watanabe,T., Itoh, S., Endoh, Y., Furusaka, M.: Phys. Rev. B 48 (1993) 6074 Tsuchiya, Y., Takita, H., Murayama, S., Hamaguchi, Y.: J. Phys. Sot. Jpn. 62 (1993) 3764 Hill, P., Naushad, A., Oliveira, A.J.A. de, Ortiz, W.A., Camargo, P. C. de, Fawcett, E.: J. Phys.: Condens.Matter 6 (1994) 1761

Landolr-Barnstein New Series 11113tA

Ref. p. 2821

1.3 4d, 5d elements, alloys, and compounds with main group elements

225

1.3 4d and 5d elements, alloys and compounds between themselves or with main group elements 1.3.1 General remarks This section treats magnetic properties of 4d and 5d transition elements, and their alloys and compounds with themselves and with group l-6 elementsof the periodic table. Papers or references which have been surveyed for compilation in this section are mainly those published from 1980 to 1995; some earlier papers are considered as well becauseof comparison and reference. Figures and tables are classified and arranged in the order of increasing atomic number of the 4d and 5d transition elements, i.e., in the order Zr, Nb, MO, Tc, Ru, Rh, Pd and Hf, Ta, W, Re, OS, Ir, Pt; for each of these transition elements tables and figures are further classified according to the increasing atomic number of the elementswith which the transition element under consideration forms alloys or compounds; ZrZn, , however, is put at the end of the Zr section. Physical properties and effects which are listed are magnetic susceptibility, magnetization (magnetostriction), magnetic resonance, dHvA effect etc. (NMR, Knight shift, muon-Knight shift, EPR, dHvA effect, Mijssbauer effect, UPS, XPS), transport properties (magnetoresistance, Hall effect, electrical resistivity, thermoelectric power) and thermal properties (specific heat, DOS, lattice constant, superconducting transition temperature, hydrogen absorption isotherm). For explanations and theoretical descriptions on the temperature dependence of the magnetic susceptibility, high-field magnetization, Knight shift, magnetostriction, magnetoresistance,Hall effect, etc., seesect. 1.3, in LB 111/19A. Survey Substancesare arranged (i) in the order of increasing atomic number of the transition elements and (ii), for each transition element, they are classified to the increasing atomic number of elements with which the transition element forms alloys or compounds. Numbers in roman and italic refer to figures and tables, respectively. Magnetic susceptibility

Magnetization

ZrH, 132 Zr,PD,-, I Zr0.70Be0.30 7, 9, 10 Zr,Cul-x @-xCuI-x)o998Gd0.002 ZrZn, 24-26, 35, 36, 23,27-34, 4-7 37-40,42-44, 4-7 36 Zr,,Hf,Zn, 14, 77,8 13, 3, 8 Zr,Ru,-, 15, 3, 8 ZrRu, 16 Zro.74fio26 Zr,Rh 17-19,l

Landolt-Biirnstein New Series 111/32A

Magnetic resonance, dHvA, etc.

Transport properties

Thermal properties

3-5 6 1 2

8,9,2

11,12 45-49

2

50

41,51, 7

3 3 2 1

226

1.3 4d, 5d elements,alloys, and compounds with main group elements Magnetic susceptibility

Zr,Rh,, Zr,RhH, Zr?RhH, ZrzPd Zr,PdH, ZrHfi ZrOsz Zrlr, Zr, J% 22 NW Nb,AI WCW3A~,-,M, (M = Ga, Ge) WJ%, Nb,Ru-, NbPd, Nb, d’do 725 Nb,Ta,_,H, Nb,.,Ta,C, Nb,Pt, ,Au,, Nb,SnH,

9 19,20

Transport properties

Thermal properties

20

9 20

2

2 51 3

15,3 15 16

2

52-54,64 59 60

2

52,55-58,65 61

54 76 62 63 64 67,68

65,66 68,69

68

70 71 72 72 54 73

Tc TcH,

74 75

Ru,-TM, 3, 8 (M = Zr, Al, Ga) RUM 78, 8 (M = Hf, Ti, Al, Ga) Ru_,M, (x I 0.0064) 76 (M = V, Nb, Ta) RulZr I5

PdH,

Magnetic resonance, dHvA, etc.

22 18 22

Mo,Si Mo,Ge Mo,Nb,-, Ru,MoO,

Rh,Cu,_, Rh,Zr, Rh,Zr,H, Hf2Rh Rh,Hf,,, Rh Jra Rh-Pd

Magnetization

[Ref. p. 282

72 72

74 77,8 8

79-82 16-18,9 19 83 9 84-86 87,105

21

20

88,89 Landolt-Barnstein New Series 111132A

Ref. p. 2821

1.3 4d, 5d elements, alloys, and compoundswith main group elements Magnetic susceptibility

I’d,-,Cu, Pd,-,M, (x 50.4) (M = Pt, Cu, Ti) PLMxH, (M = Cu, Au) Pd,-,Se, (x 50.015) Pd,Se, PdZr, PdZr,H, Pd-Ag Pd,-,Nb,H, (x I 0.1) Pd,-,Mo,H, (x < 0.1) Pd,-,Ru,H, (x I 0.1) Pd-Rh WJW$ Pd,-,M, (x 50.015) (M = W Ad Pd,-&&x ~LKH, Pd,-,M,H, (x 20.32) (M = Pt, Ti)

Magnetization

90 92

Thermal properties

91

94 95 18 22 87 97 99, 100 102 87

96 98 101 IO

103,105 104,105 106 107

35 78, 8 83, 9 3 3

TaH,

53,64, 110

108 51 8 9 3 3 55, 56, 65, 66, 109 109

TaDo o8

TaC, Ta,-,Nb,H, ‘&JLC, ‘NxWx

67,68 64 67,68 110

w, WC

111 110

Re,Si ReSi, ReJL (M = Nb, MO, V)

115 117 118

Os,Zr Os-Hf Os-Ir

15 3 87

Landolt-Bbmstein New Series 111132A

Transport properties

93

HtZn, Hf,Zr,-,Zn, HfRu HfnWn Hf,,Os, HfOs,

WJa,,

Magnetic resonance, dHvA, etc.

227

68 65,66

112

113,114 116 118

3

1.3 4d, 5d elements, alloys, and compounds with main group elements

228

Magnetic susceptibility

Magnetization

Magnetic resonance,

Transport properties

[Ref. p. 282 Thermal properties

dHvA, etc.

BaJaIrO, Ir,Zr WW, Ir-0s Ir-Pt

119 15 84-86 87 87

Pt CaPtSi PLxCu, PtGa, Pto

22Zro

Pt,

,Nb,Au,

Pt,Pd,-, Pt-Au

120,lI

113, 114,121 122 123 124 16

78

124 70

7

92 87

1.3.2 Zr alloys and compounds 1.3.2.1 Alloys and compounds except ZrZn,

Fig. 1. ZrH, 70. Temperature dependence of the magnetic susceptibility for two different samples (1 and 2) annealed at 798 K for three different periods; sample I: 8 and 14 days, respectively, and sample 2: 21 days [85Bl].

1.3 4d, 5d elements, alloys, and compounds with main group elements

228

Magnetic susceptibility

Magnetization

Magnetic resonance,

Transport properties

[Ref. p. 282 Thermal properties

dHvA, etc.

BaJaIrO, Ir,Zr WW, Ir-0s Ir-Pt

119 15 84-86 87 87

Pt CaPtSi PLxCu, PtGa, Pto

22Zro

Pt,

,Nb,Au,

Pt,Pd,-, Pt-Au

120,lI

113, 114,121 122 123 124 16

78

124 70

7

92 87

1.3.2 Zr alloys and compounds 1.3.2.1 Alloys and compounds except ZrZn,

Fig. 1. ZrH, 70. Temperature dependence of the magnetic susceptibility for two different samples (1 and 2) annealed at 798 K for three different periods; sample I: 8 and 14 days, respectively, and sample 2: 21 days [85Bl].

1.3 4d, 5d elements, alloys, and compoundswith main group elements

Ref. p. 2821

229

Fig. 2. ZrH,. Composition dependence of the magnetic susceptibility at 300 K and its extrapolated value at 0 K for unannealed samples (open symbols) and samples annealed at 798 K for 21 days (solid symbols). At x = 1.70 measurementswere made for two different samples(1 and 2) annealed at 798 K for three different periods; sample 1: 8 and 14 days, respectively, and sample 2: 21 days [85Bl]. 1.5

“o-3 (SK)-” 55

1.6

Zr H,;70

1.7

x-

I

1.8

1.9

I

I

200

240

I

2.0

I

50 I Y -7 5 45 40

-SO

‘20

‘60

280 K 320

T-

Fig. 3. ZrH,,,,. Temperature dependenceof the proton (T,T)-“* values for unannealed samples (open symbols) and annealed samples (solid symbols), where T, is the spin-lattice relaxation time and T is the temperature. Annealing periods are 14 days for sample 1 and 21 days for sample 2, both at 798 K [85Bl].

Landolt-B6rnstein New Series IW32A

-1.5

1.6

1.7

x-

1.8

1.9

2.0

Fig. 4. ZrH,. Composition dependence of the proton values at about 300 K for unannealed (T,T)-“* samples (open symbols) and annealed samples (solid symbols), where T, is the spin-lattice relaxation time and T is the temperature. Triangles [83Kl], circles [85Bl]. Solid circles: samples annealed at 798 K for 21 days. At x = 1.70, sample 1 was annealed for 14 days and sample 2 for 2 1 days.

230

1.3 4d, 5d elements, alloys, and compounds with main group elements

[Ref. p. 282

68 .lV (sK)-“~ 64

60

IO.‘11 2.5

0.26’44 1.7

1.8

1.9

2.0

3.0

3.5

4.0 l/T -

4.5

5.0-10-3K-‘5.5

Fig. 6. Zr,PD,-,. Spin-lattice relaxation rate 6-l plotted against inverse temperature[91B2].

Fig. 5. ZrH,. Composition dependence of the “Zr Knight shift K and proton (TIT)-“* value for E phase ZrH,. where T, is the spin-lattice relaxation time and T is the temperature. I: [83Kl], 2: [85Bl], 3: [91H2], 4: [93Nl].

Table 1. Zr, ,,Rh, z5,Zr, ,,Be, 30.Magnetic susceptibility x, and electronic specific heat coefficient yof amorphous and metastable crystalline Zr-based alloys. The susceptibilities do not depend on temperature for the range from the superconducting transition temperature 2.. .4 K to 300 K. Ax/x and by/y denote the relative changes of x and y between amorphous samples and metastable crystalline ones [82Pl, 83Pl]. State

Zro &ho 2s

amorphous

Axfx X8 [ 1O-‘cm’g-‘1 [Oh]

Y [mJ mol-‘K-*1

1.18

5.1 12

Zro ,,Beo3.

metastable crystalline

1.05

amorphous

1.71 1.62

Ref.

[O/o]

28

82P1

36

83Pl

4.0 4.44 6

metastable crystalline

AY~Y

3.26

1.3 4d, 5d elements, alloys, and compoundswith main group elements

Ref. p. 2821

231

100

I

15

?5

50 25

CU

I

I

I

I

I

0.2

0.4

0.6

0.6

2r

x-

Zro!iC”o5 . .

3.2

Land&-Biirnstein New Series 111132A

1

3.3

3.4

3.5

Fig. 7. Zr,Cu,-x. Magnetic susceptibility of amorphous and crystalline alloys at room temperature is plotted against composition, where the contribution to the susceptibility due to core diamagnetism is removed. Open circles: amorphous alloys, solid circles: crystalline alloys [81A2].

1

1=4K v=39.97MHz

I 3.6

I T 3.7

Fig. 8. Zr, &u,,~. Spin-echo spectrum of 63Cu and %I in amorphousalloy at 4 K [82El].

1.3 4d, 5d elements,alloys, and compoundswith main group elements

232

[Ref. p. 282

1 %. 6

I ‘2 EN F

0.2 a

0.4 x-

0.6

0.8

lr

5

b

cu

0.4

0.2

0.6

x-

0.8

14 40-s (31113 mol 12

I

10

Fig. 9. Zr,Cu,_,,

$

Zr,Cu.

Composition

dependence

of a

the ‘%I (6sCu) Knight shift, b 9’Zr Knight shift, K, and c the magnetic susceptibility after subtracting the

8

diamagnetic alloys circle) 0.2

0.5

0.6

0.6

(open [82El].

contribution, circles)

xm, for amorphous and

crystalline

Zr,Cu

Zr,Cu,_, (solid

lr

x-

C

Fig. 10. Zr,Cu,-x. electron magnetic [84El]. 0.4

x-

0.6

0.8

Composition susceptibility

dependence of the dof amorphous alloys

Zr

Land&-Barnstein New Series 111132A

Ref. p. 2821

1.3 4d, 5d elements, alloys, and compounds with main group elements

0.14

I

0.12

I

I

40 oe

I

I (Zrx C"l-x )o.w Gd0.002I

I= 4.2... 40K

I T

233

I

K

-

30

Y

E

P i

I

L T 20 s a ‘;;

P

IO

a

0.061 cu

0.2

0.4 x-

0.6

0.8

Zr

Gd,,,,,. Composition dependFig- 11. (ZrxCuI-xh998 ence of a the g-shift, Ag, relative to g = 1.992 and b the Korringa rate, d(AH)ldT, for amorphous alioys,

0 b

cu

0.2

0.4

0.6

0.8

;r

X-

where AH is the linewidth of the EPR spectra and 2’ is the temperature [84El].

Table 2. Zr,M,-,, M = Cu, Ni, Pd, Pt, Co, Rh. Korringa rate d(AH)/dT, residual linewidth AH,, g-

factor, g-shift Ag and Korringa ratio R = (gl.@kJ d(AH)ldT (Ag)’ for Zr-based amorphous alloys doped with 0.2 % Gd. In the last but one column, n,(E,) is the d-electron density of statesat the Fermi energy calculated from ni(Er) e g(0.2~kgpn)-1J~2d(AH)/ dT, Jfd being the exchange interaction between the Gd 4f-electron and the conduction d-electron; in the last column, n(E,) is the density of states derived from the electronic specific heat coefficient. nd and n are measured in units of eV-’ per atom per spin [84El]. Alloy

d(AH)ldT

AH,

[Oe K-‘1

WI

Zro.72Cuo.28 36.2 f 2.5 Zro.67Nio.33 Zro.67P4.33 Zro.78Pto.22 Zro.67Coo.33 Zro.74fio.26

Landolt-Bbmstein New Series III/32A

39.1 f 1.0 30.1 f 2.0 37.2 f 4.0 30.0 f 5.0 35.4 -+4.1

610 f 20 610% 11 614*20 1060*70 920 f 80 690 f 50

2.095 f 0.014 2.106 f 0.017 2.104~0.010 2.111ztO.040 2.113 f 0.026 2.128 f 0.020

0.103 f 0.014 0.114 f 0.017 0.112&0.010 0.119&0.040 0.121 f 0.026 0.136 f 0.020

0.15 0.14 0.11 0.12 0.09 0.09

0.90 0.94 0.82 0.92 0.82 0.90

0.93 1.07

234

0.1

1.3 4d, 5d elements, alloys, and compounds with main group elements

0.2

0.3 PoH -

0.4

1

0.5

Fig. 12. (Zr, IsCu, &, 998Gd0 c,02.EPR spectrum of an amorphous alloy at 4.2 K and 9.258 GHz. The solid line representsa fit to the data by a Lorentzian curve [84El].

O

50

100

150

200

T-

[Ref. p. 282

250 K 300

Fig. 13. Zr,Ru,.+. Temperature dependence of the inverse magnetic susceptibility [73Tl].

0

50

150

100

200

250 K 300

T-

H-

Fig. 15. ZrM,, M = Ir, OS, Ru. Temperature dependence of the magnetic susceptibility [85Sl].

Fig. 14. Zr, 5 Ru, s. Magnetic field dependenceof the magnetization at various temperatures[73Tl].

Land&-Barnstein New Series 111132A

Ref. p. 2821

1.3 4d, 5d elements, alloys, and compoundswith main group elements

235

Table 3. (Zr,Hf),(Ru,Os),. Basic data on magnetic and thermal properties [86K2]. x(300 K): magnetic susceptibility at 300 K, y : electronic specific heat coefficient, @: Debye temperature, T,: superconducting transition temperature, R: electron-phonon interaction constant, F: Landau enhancement factor. The Landau enhancement factor has been described on p. 491 in LB 111/19A.According to the Landau theory, the spin paramagnetic susceptibility of the itinerant electron system is exactly given by

at absolute zero, where 1’(&) is the density of states at the Fermi energy which correctly includes the effect of the electron-electron interaction, and the Landau enhancementfactor F = (1 + ly,)-’ denotes the enhancementof the spin susceptibility due to the electron correlation. If 1 + Y0< 0, the system becomes ferromagnetic at absolute zero. The electronic specific heat coefficient y is enhanced by the electron-phonon interaction through an approximate relation 2

y=~k;v&)(l+l) . Thus F can be calculated in terms of the observedvalues Xspin,y and il as F = a2ki (l+‘)Xspin

3u;

= 7.292 (l+$

r”

Y

where 2 and y are xspinand y measuredin units of 10m4 cm3mol-I and mJ mall’ K-‘, respectively. X(300K)

ZrRu HfOs Hfo.,&.z ZrRu, ZrOs, HfOs,

Landolt-BOrnstein New Series 111/32A

r,

[ 1OW4 cm3g-atom-‘]

0, Y [mJ g-atom-’ K-*1 [K]

WI

0.446 0.245 0.823 1.16 0.876 0.719

1.oo 0.66 3.60 4.72 3.70 2.84

1.92 2.90 1.85

404 348 225 361 308 330

a

F

0.49 0.55 0.49

2.67 2.68 2.75

1.3 4d, 5d elements,alloys, and compoundswith main group elements

236

[Ref. p. 282

4.0 -10-r & 9 3.2

I

2.4

r:

I

1.3

1.2

’ 1.6 1.1 I 1.01 0

“0

50

I I 100 l-

80

160 T-

I I 150

I

I 200

I

I

I

I

250 K 300

240 K 320

Fig. 16. Zr,M,_,, M=Rh. Ni, Pt. Temperature dependence of the magnetic susceptibility of Zr-based amorphous alloys [84EI].

1.8 *10-r . @ !J

I

I

Fig. 17. Zr,Rh. Temperature dependence of the magnetic susceptibility for amorphous alloys. In the upper three curves samples are melt-spun alloys, whereas in the lowest curve the sample is an anvilpiston-quenched alloy [88Bl].

I

Zr;Pd,Zr3Rh

1.4 I

1.2

N” 1.0 0.E 0.6 0.4

0

50

100

150

200

250 K 300

lFig. 18.Zr,Pd, Zr,Rh. Temperature dependenceof the magnetic susceptibility for amorphous(open symbols) and crystalline (solid symbols) alloys. Circles: Zr,Pd, triangles: Zr,Rh [85VI].

0

50

100

150

200

250 K 300

TFig. 19. Zr,RhH,. Temperature dependence of the magnetic susceptibility of amorphous hydrides [85Vl].

Landolt-Bbmrwin New Series 111132A

237

1.3 4d, 5d elements, alloys, and compounds with main group elements

Ref. p. 2821

2.5 1 eV*atom 2.0

I

z ;

-.

a

0

1

2

3

4

5

6

x-

--

c

1

0

0.2

gF

2

x-

3

4

5

6

0.1 ii.1 co

om-+i-o.l 0

-0.1

-0.1

-0.2

I -0.2 b -0.3

b

0

1

2

x-

3

4

5

6

Fig. 20. Zr,RhH,. Composition dependence of a the magnetic susceptibility estimated at 0 K, x0, b the density of states deduced from the electronic specific heat coefficient, L(Er), and c the spin-lattice relaxation time T, expressedin the form (T,T)-I’*, for amorphous hydrides. Open symbols: melt-spun samples, solid symbols: anvil-piston-quenched samples [88Bl].

II

-0.3 I

I

0.91 0.9

II

I

.I

0.8 0.8

N” 0.7

b

-0.4 ,

-0.5

-0.4

0.6

-0.5

0.5 . t

-0.6

0.41 0.4 0

0 mooa mooch 5

IO T-

. 50

100

150

200

250 K 300

T15

-0.7 20 K 25

Fig. 21. Zr,RhH,. Temperature dependence of the magnetization in a magnetic field of 1 kOe for x = 0 and 4.25 [94Rl].

Land&-Biirnstein New Series 111/32A

1.0

0.1 m x=4.25 !y 9 0

l

Zr,RhH,

-0.6 0

1.5

Fig. 22. Zr,PdH,. Temperature dependence of the magnetic susceptibility of amorphous hydrides [85Vl].

1.3 4d, 5d elements, alloys, and compoundswith main group elements

238

[Ref. p. 282

1.3.2.2 ZrZn,

While ZrZn, is composed of two elements of nonmagnetic metals, it exhibits weak itinerant ferromagnetism at low temperatures; its saturation magnetic moment is 0.11...0.13 pB per formula unit. Weak ferromagnetism of ZrZn, is peculiar in several respects. Its magnetization relation can be described basically in the Stoner model or molecular field theory; within the band model, this weak ferromagnetism may be attributed to a high narrow peak in the density of states curve at the Fermi energy. If one assumesthat the free energy of the systemcan be expanded in even powers of magnetization M and temperature T,

F= F,-3T2 +&. +a,T2)M2 +lbM4) 2

2

4

(1)

one obtains, in the presenceof a magnetic field I-I, the magnetization relation H=(q) +c7,T2)M+bM3 ,

(2)

where F,, yO,a,, Q, and b are functions of pressure. This can be rewritten in the form, first given by Wohlfarth [68Wl], (3)

where MOand x0 are the magnetization and susceptibility at T = H = 0, and T, is the Curie temperature. In the absenceof a magnetic field, eq. (3) becomes (4)

The differential susceptibility at zero field can be obtained also from eq. (3);

xo[‘-(T’Tc)2]-1

,TTc.

It is known that relations (3) and (4) are well satisfied in ZrZn,; for T < T, the Stoner model gives a thorough description for this weak ferromagnetism. Above T,, however, the Stoner model gives x 0~[(T/T,-)‘- l]-‘, whereas the observed susceptibility seems to follow a Curie-Weiss law; x cc [T/O- 11-l. The Curie-Weiss law was predicted by spin fluctuation theories [72Ml, 73Ml] or the Fermi liquid model [9lMl]. Now here rises a puzzle. If the effect of electron correlation is really important as the Curie-Weiss behaviour suggests, it should influence the properties for T < T,. According to the Fermi liquid model, the free energy contains logarithmic terms with respect to M and T, and the expansion (1) in powers of M2 cannot be permitted at low temperatures; the logarithmic dependecehas been observed in Y(Co, Al), [95Ml] and Lu(Co, Ga), [94Ml]. Why does not the effect of electron correlation appear in ZrZn, ? There is another puzzle in the critical exponents or critical amplitudes of ZrZn,. According to the theory of critical phenomena,near the Curie temperature, the temperature and field dependenceof M and x is defined as

Land&-Bmwein NW Series 111/32A

Ref. p. 2821

1.3 4d, 5d elements,alloys, and compoundswith main group elements

MS = bo(-ty

) t I 0,

x-I = h, tY

,tro,

239

b0

p,H=d,M”

,t=O.

Here t = (T- Tc)/Tc; b,, ho/b, and d,, are critical amplitudes and fl, y and Srepresent critical exponents. The critical exponents and amplitudes derived from different theoretical models are listed in Table 4. Seeger et al. [95Sl] performed experimental study on the critical behaviour of ZrZn,. They measured the M-H curve (Figs. 24,32), X-T curve (Fig. 25) and M-T relation (Fig. 28). From these, they analysed the data via various plots to obtain the critical exponents and amplitudes (Tables 5, 6); modified Arrott plot (Fig. 33) Kouvel-Fisher plot (Figs. 26, 30) scaling plot (Figs. 27,31, 35) and In M vs. In poH plot (Fig. 34). The final results are listed in Table 6. If one compares these with Table 4, it is concluded that ZrZn, obeys rather accurately the mean field theoy (or molecular field theory). It is astonishing to seethat an ideal ferromagnet within the mean field theory exists in nature; ZrZn, seemsto be only one example. To answer the question why ZrZn, follows the mean field theroy is an unsolved problem. It is known that the free energy of the form (1) gives the critical exponents in agreement with the mean field theory. In this sense,the fact that the magnetization curve obeys the Stoner model is consistent with the critical exponents following the mean field theory, since (T/T,)* - 1 u 2[(T/T,) - l] for T = Tc. Although the effect of spin fluctuations is believed to be crucial in the critical region or in weak ferromagnets, it does not appear at all in ZrZn,. Why? According to the Fermi liquid model, the Stoner theory is exact only when the quasiparticle interaction function is constant and does not depend on the energies of two quasiparticles. It is not clear, however, why the interaction does not vary with the quasiparticle energy in ZrZn,; is this related to a special feature of the density of states in ZrZn,? More theoretical studies are neededfor the final answer.

Land&-Bbmstein New Series 111/32A

1.3 4d, 5d elements,alloys, and compounds with main group elements

240

mrl Zr’Zn7 I I

I

I

I

I

1.x

-10

0

10

20

[Ref. p. 282

1

20

x -2

-6 -8 -50

-40

-30

-20

30

40 ml 50

10 5 1 0 x -5

-10

-15

b

-‘i&o -4ao -3000 -2000 -1000 0 PI+ -

1000 2000 3000

ml 5000

Fig. 23. ZrZn,. Hysteresis loops measured at 5 K, a in the low-field range and b in the high-field range [95Sl].

Landolt-BBmrtein New Series 111132A

Ref. p. 2821

1.3 4d, 5d elements, alloys, and compounds with main group elements 15.0

K

26

29

32

35

38

41

K U

241

I

Zr Zn,

26

29

T-

32

35

38

41 K 44

T-

Fig. 24. ZrZn,. Temperature dependence of the inverse magnetic susceptibility (in SI-unit) [95Sl].

Fig. 25. ZrZn,. Determination of the critical exponent y through Kouvel-Fisher plot; [d(ln X’)/d7’-’ vs. T [95Sl]. 2.0

ml 1.6

26.0

26.5

27.0

27.5

28.0

28.5 K 29.0

T-

Fig. 26. ZrZn,. Inverse magnetic susceptibility X1 (in SI-unit) is plotted to fit the (h,lb,)tY dependence, where t = (T - Tc)/Tc, through which the critical amplitude &lb, is determined [95Sl].

Landolt-Bbrnstein New Series 111/32A

0

IO

20

30

40

K E

T-

Fig. 27. ZrZn,. Temperature dependence of the magnetization at y,H = 1.5 mT [95S11.

1.3 4d, 5d elements, alloys, and compounds with main group elements

242

[Ref. p. 282

8 ml I 6 5 I 4 J 3 2

1 0 10

12

14

16

16

20

22

24 K 25

- 17.0

18.5

20.0

21.5

23.0

24.5 K 26.0

l-

l-

Fig. 28. ZrZn,. Temperature dependenceof the spontaneous magnetization [95SI 1.

Fig. 29. ZrZn,. Determination of the critical index p through Kouvel-Fisher plot; [d(ln M,)ldT]-’ vs. 7’ [95Sl].

-23.5

24.0

24.5

25.0

25.5

26.0 K 26.5

I-

Fig. 30. ZrZn,. Spontaneousmagnetization M, is plotted to fit the bo(-tf dependence,where f=(7’-Tc)ITc, through which the critical amplitude b, is determined [95S1].

0

0.2

0.4 0.6 PO/ -

0.e

1 1.0

Fig. 31. ZrZn,. Magnetization curves, M vs. pc,H, at various temperaturesnear the critical point [95SI].

Landoh-Barnstein New Series lW32A

Ref. p. 2821

1.3 4d, 5d elements, alloys, and compounds with main group elements

243

- 5.2

-5.6 I -5.8 29.50K I,/

R c -6.0 - 6.2 - 6.1

-7.0 -4.0 -3.5 -3.0

0

30

60 90 (poH/M)“Y -

120

150

180

Fig. 32. ZrZn,. Modified Arrott plot; &I@ plotted against (p0H/A4)“y at various temperatures near the critical point, where fl= 0.50 and y= 1.02 [95Sl].

-4.15 1.5

-2.5 -2.0 In (poH) -

-1.5 -1.0 -0.5

0

Fig. 33. ZrZn,. In A4 plotted against In ().@I) at various temperatures near the critical point, through which the critical exponent 6 and the critical amplitude d, are determined. M and nOH in tesla [95Sl].

Fig. 34. ZrZn,. Scaling plot; In (Ml]@) vs. In (poH/ltjfi&3, where t = (T- Tc)/Tc, p= 0.490 and y= 1.000 for T < Tc and 1.020 for Z’> r,-, to confirm the correctness of ,0, y and t values. Temperature range; 26.200 k 2.620 K. Mand p&in tesla [95Sl]. 2.5

Landolt-Bbmstein New Series 111132A

3.5 In(,uJ//I t I’p’7’l -

6.5

1.5

244

1.3 4d, 5d elements,alloys, and compoundswith main group elements

[Ref. p. 282

4. Critical exponents and reduced critical amplitudes derived from different theoretical models. MFT: mean field theory; M,(O): saturation magnetization; PI:saturation magnetic moment. Table

Exponent

MFT ‘)

Heisenbergmodel ‘)

king model *)

P

112 1 3

0.365 1.387 4.803

0.325 1.240 4.816

Heisenbergmodel fee, s= l/24)

Ising model fee, s= l/23)

1.69 1.58 1.55

1.49 1.52 1.81

Y 6 Reduced amplitude

MFT s=

l/23)

1.73 1.73 1.0 ‘) [SOGI]. 2) [77Gl]. ‘) [81Kl]. 4, [85K2].

Table 5. ZrZn,. Critical exponents derived from different methods. Error is + 10 % in S, and f 5 % elsewhere [95Sl].

Method:

Modified Arrott plot

Kouvel-Fisher plot

Scaling plot

0.50 1.02 1.02

0.487 1.046

0.49 1.02 1.oo

In M vs. In (p,H) plot

Exponent P Y(T> Tc) Y’ U< Tc> 6

3.11

Table 6. ZrZn,. Saturation values, critical amplitudes and reduced critical amplitudes [95Sl].

Saturation values

M,(O) P

0.0145 T 0.083 pB

Critical amplitudes

6, hdbo 4

0.0110 T 575 8.54.106T’-”

Reduced critical amplitudes

0.76 4.49.10-3 1.09

Lend&Barnstein New Series 111132A

Ref. p. 2821

245

1.3 4d, 5d elements, alloys, and compounds with main group elements

1.0

I

0.8 m

2 0.6 0.4

n Fig. 35. Zr,-,Hf,Zn,. Temperature dependenceof the inverse magnetic susceptibility for the weak itinerant electron ferromagnet ZrZn,, exchange enhanced paramagnetHfZn, and their solid solutions [8301].

Lll

All

fin

K

inn

Fig. 36. ZrZn,,,. ‘l’emperature oepenoence or me mverse magnetic susceptibility at 0 kbar and 19.3 kbar [75Hl]. 2.0

3.0 Gcm3 9

9

2.5

Zr Zn,., 1.6

I

d'

2.0

I

I 1.5 b

b

0.8

1.0

0

12

3

4

5

6

7 kOe8

0

2

6

4

8

10 kOe 12

H-

H-

Fig. 37. ZrZqg. Magnetization curves, 0 vs. H, at various temperatures,at 7.5 kbar [75Hl].

Fig. 38. ZrZn,,,. Magnetization curves, cs vs. H, various temperatures,at 19.3 kbar [75Hl].

Land&-Bhrnstein New Series 111132A

al t

I .3 4d, 5d elements,alloys, and compoundswith main group elements

246

4.5

4.5 Gcmy 9 4.0

[Ref. p. 282

I

ZrZn2

2.5 b 2.0

0

2

4

6

I 10 kOe 12

8

0

4

8

12

16

20

K 24

I-

H-

Fig. 39. ZrZn,.,. Magnetization curves, various pressures,at 4.5 K [75HI].

CT vs.

H, at

Fig. 40. ZrZn,. Temperature dependenceof the spontaneous taneous magnetization magnetization for four different samples [75CI].

2z AmolK2

I

l

ZrZn2

16

? c: 12

Fig. 41. ZrZn,. Magnetic heat capacity C,,,divided by temperature7’ is plotted against 7’ for the four samples in Fig. 40, where C,,, is determined by subtracting from the measuredheat capacity the nonmagnetic heat capacity of the form, yT + pr3 +..., which was fitted to the data far below rc and above Tc. Numbers inside

8

the curves denote the magnetic entropy j:(C,,, / 7’)dT in units of mJ mol-‘K-’ [75Cl]. 0

5

10

15

20

25

K

30

Landolr-Bmntein New Series 111132A

Ref. p. 2821

1.3 4d, 5d elements, alloys, and compounds with main group elements

247

Table 7. ZrZn,. Magnetic and thermal properties of the four samples in Figs. 40 and 41. T,: Curie temperature determined by four different methods, u(O,O):spontaneousmagnetic moment at 0 K, x0: differential magnetic susceptibility at zero field and at 0 K, ACrc. heat capacity jump at T,, calculated on the basis of the mean field theory through AC,c = o(O,O)z/x,Tc with x,, from the Arrott plot, and measured [75Cl]. Sample No.

TcWI Specific Arrott heat plot

1 2 3 4

7 12 19 22

8.6 12.8 21.4 20.8

a(W)

AC Hysteresis suscep- curve tibility 9 14 22.5 22.2

31 24 35 24

AC,c [mJ mol-’ K-l]

x0

[G cm’ g-‘1 [IO-“ cm3g-‘1 Calculated Measured

2.60 2.85 3.00 4.05

1.58 1.06 3.63 0.60

106 129 25 280

24 77 238 420

5 Am2’ (mol 1 4

b

a

b

0

5

10 &H/o.

15

20 Tmol/AmL25

-

Fig. 42. ZrZn,. a Magnetizationrelation, UVS.H, andb Arrott plot, d vs. H/o, at varioustemperatures[86Dl].

Land&-Biirnstein New Series III/32A

1.3 4d, 5d elements, alloys, and compounds with main group elements

248

[Ref. p. 282

3 2 2 1

1

0

0

Fig. 43. ZrZn,, Zr, ,,Zn, 66.Magnetization curves, the CTvs. H relation, for Laves phase compound ZrZn, and amorphousalloy Zr, ,,Zn, 66[87Y I].

H-

12.5 10.0 I Q 1.5

I

8

0

5

10

P-

15

20

0

K’ 25

Fig. 44. ZrZn,. a Magnetic moment per Zr atom is plotted against T’ at various magnetic fields, b temperature coefficient of the average magnetic

b

2

4

6

8

1

10

POHmoment p,(H), is plotted against H, where p,(H) is defined byp(T,H)=p(O,H)-p,(H)T2 [gOHI].

Landolr-Bbrnslein New Series lW32A

Ref. p. 2821

1.3 4d, 5d elements,alloys, and compoundswith main group elements

I

249

I

majority spin

I 0.9

* F

0.8 0.7

minority spin -

0.6 0

IO

250

15 20 /Joi -

25

30 1 35

Fig. 45. ZrZn,. Magnetic field dependence of the effective mass m*, in units of the bare electron mass, for the majority and minority spin measured by the dHvA effect [82Rl].

I

T ZrZn2 T =1.3K 230

800

!

210

I 600

a

190

27 400

200

:::’ 0 a

5

IO

15

20

25

PO/ -

Fig. 46. ZrZn,. Difference of the up-spin and downspin dHvA frequencies, AA as a function of magnetic

Land&-Bbmstein New Series 111132A

YI 0

30 1 35

b

I 2

I 6 lp~H)~'~-

I 8

I IO T"j 12

field H, a Af vs. H, b H’13Af vs. H213. Solid circle [81Ml], open circles [82Rl].

1.3 4d, 5d elements, alloys, and compounds with main group elements

0.09

-3

I 0.10

I 0.11

I I 0.12 0.13 (/lo HP -

I 0.14

I

I

u.15 -.-

U.lb ^‘-

I-*’

[Ref. p. 282

Fig. 47. ZrZn,. Line profiles of the dHvA oscillations at 1.56 K in the field range 6 to 1I T at pressures up to 4.3 kbar [89Ml].

Fig. 48. ZrZn,. Pressure derivative of the dHvA frequency, d/ldp, for the majority and minority spin Fermi surfaces plotted against magnetic field H at 1.56 K [89Ml].

Lmdolt-Bihr~ein New Series W32A

Ref. p. 2821 1.2

1.3 4d, 5d elements, alloys, and compounds with main group elements

251

I

me Zr Zn, 1.1

0 -

majority spin -B

1.0

I

-.++-,

*E 0.9,,1-,

O.8..-----=-Y:-0 (,

T

Y

)

-Pry 0.7 0

1

Fig. 49. ZrZn,. Pressure dependenceof the effective mass m* of electrons, in units of the bare electron mass, on the majority and minority spin Fermi surfacesmeasuredby the dHvA effect [89Ml].

minority spin r 3 c kbor 5

2 P-

2 I 0.8 z3 $ 0.6 f 1, Qr 0.41 0

b

10 a

20

30

40

K

8

12

16

T

I 20

POH -

I

50

T-

Fig. 50. ZrZn,. a Temperature dependence of the magnetoresistanceAp/&O) at various magnetic fields, where p(H) is the electrical resistivity at applied field H and Ap= p(H) -p(O), b the coefficient of the T2

Landolt-Bbrnstein New Series W32A

4

term in p(H) below the Curie temperature, p,(H)/p,(O), is plotted against H, where p,(H) is defined by p(H) = p,,(H) + p,(17)~~. Solid lines are drawn smoothly through the data points [SODl].

252

mJ

1.3 4d, 5d elements,alloys, and compoundswith main group elements 15.0

15.0 L

g-ofwnK2

g- otomK2 12.5

12.5

I

[Ref. p. 282

10.0

10.0

1.5

I 1.5

s

s 5.0

5.0 0 H=D . 60kOe

b A

oa Fig. 51. coefficient

10

20 I’

1OOkOe150 kOe

I 30

K’

-

ZrZn,, HfZnz. Electronic specific (specific heat divided by temperature

40

0

I

I 20 12 -

10

b heat C/7)

is plotted againstT* ZrZn,

and b HfZn,

at various

I 30

magnetic

fields

K’

I 40

for a

[9OI I].

Landolt-Btirnstein New Series 111132A

Ref. p. 2821

1.3 4d, 5d elements, alloys, and compoundswith main group elements

253

1.3.3 Nb alloys and compounds -44.0 rm 9.36

-44.2 -

NbH0.10

NbH 0.76

-44.4

-44.6 -

- 49.00

NbH om

I F

4.

0

I 2

IbHO.60 0

7.67

NbHO.78

-49.25 0

+

-49.50

o

~~ -39.35

-39.45

340

:

a

420

T-

K 460

5.36 380

420 K 460

T-

Fig. 52. NbH,. Temperature dependence of a the magnetic volume susceptibility (in cgs-unit) and b the

Land&-Bdmstein New Series 111/32A

r -39.55 340

b

380

T-

420

K 460

-55.81 380

420

K 460

T-

proton Knight shift KH for (a,a’) phase NbH, at various hydrogen concentrations [84Bl].

254

1.3 4d, 5d elements,alloys, and compoundswith main group elements

/

RT 1

5.0

I 0

0.2

OX x-

0.6

0.8

[Ref. p. 282

1.0

Fig. 53. VH,, NbH,, TaH,. Composition dependence of the magnetic volume susceptibility (in cgs-unit) of hydrides determined by proton NMR (solid symbols) and ordinary susceptibility measurements (open symbols). I: [62Zl], 2: [70Al], 3: [70Dl], all solid symbols: [77Kl].

5.2

5.4

5.6

“” -

5.8

6.0

6.2

Fig. 54. NbH,, Nb,-,Mo,. Comparison of the magnetic susceptibility of NbH, at room temperature with that of Nb,-,Mo, plotted against the number of valence electrons, n, (or against x or y). I: [62Tl], 2: [74Hl], 3: [82B2], 4: [77Kl], 5: [88Rl].

LandoltJMrnstein New Series llV32A

Ref. p. 2821

1.3 4d, 5d elements, alloys, and compounds with main group elements

I KH. 21 H-

I 13

255

I 0 wm

K,=66 H-

64~~

1=17O"C,ct-phase

K, = Glppm H-

Landolt-Bornstein New Series 111132A

Fig. 55. NbH,,,,, TaH,,,,, VH,,,,,. Proton NMR line profiles at various temperatures. The shift KH was measuredwith respectto water [77Kl].

256

1.3 4d, 5d elements, alloys, and compounds with main group elements

[Ref. p. 282

0 wm -20

-40 I k= -60

-0

*c-16.05

0.2

0.4 x-

I

0.6

0.8

1.0

Fig. 56. VH,, NbH,, TaH,. Composition dependence of the proton Knight shift for a-phase transition-metal hydrides. The shift is given relative to bare protons [77Kl].

I/ I 130.0 130.5 131.0 Xm -

67.0 Xm

-

Fig. 57. NbH,. Proton Knight shift KH (in parts per million) is plotted against the magnetic susceptibility

Xm -

67.1

61.8

68.2

68.6

Xm-

x,, (in units of 10e6cm3 mol-‘) for (a,a’) phaseNbH, with temperatureas an implicit parameter[84Bl].

Landolt-Barnsrein New Series W32A

-14 ,

I

Ppm1 NbHx 1

-16

II

II

I -18 ! y* -20

I

257

1.3 4d, 5d elements, alloys, and compounds with main group elements

Ref. p. 2821

!.

l

I

I I

I RT

I I

I p I

=

I

I I

I

-47

c -49

6.8

-51

200 -55

0

0.2

0.4

x-

0.9

0.6

1.0

250

1.2

Fig. 58. NbH,. Composition dependenceof the proton Knight shift KH in the a phase (solid circles) and l!I phase (open circles) niobium hydrides at room temperature. KH is given relative to bare protons. Dashed lines denote boundaries of regions, where the regions I, II, III and IV represent the a, a + l3, p and l3 + y phases,respectively [93Ul].

'2

K

Fig. 59. Nb,AI. Temperature dependence of the magnetic susceptibility from the superconducting transition temperature up to room temperature. Open circles: quenched sample, solid circles: annealed sample. The susceptibility of the annealed sample at 293 K is 6.90~10-4cm3mol-’[84Jl].

(Nb,-, Zr, I3 AL,-,M,

4zTqq

x”

l

l

4’ . .

.I,

l

(

5,

1.6

::I: I.‘

0

50

” . I, . 1 I

6.10-2 0

0.5

1.0

1.5

2.0

2.5.10% 3.0

t-

100

150

200

250 K 300

TFig. 60. (Nb,,Zr,),Al,-,My, M = Ga, Ge. Temperature dependence of the magnetic susceptibility for alloys based on Nb,Al. I: Nb,Al, 2: Nb,AI,,,,G%,,,, 3: Nb,Al,,,,Ge,,,,, 4: 0% 99Zro,oI)3AL 5: (Nb9~%03)#J

Land&-Biirnstein New Series 111132A

E 10-l 8

P4Sll.

Fig. 61. (Nb,-,Zr,),Al,-,M,, M = Ga, Sn. Nuclear magnetization M(t) for alloys based on Nb,Al, in the form [M(W) - M(t)]/M(oo), plotted against time t in a semi-log scale; this graph shows recovery of the magnetization to the equilibrium value M(w). I: Nb,Al, 2: Nb,AI,,,Ga,,, 3: (Nb,,,,Zr,,,,),Al, 4: Nb,Al,,,Sn,,, [80Ml].

I .3 4d, 5d elements, alloys, and compounds with main group elements

0.14 I 100

140

180

220

[Ref. p. 282

260

K

3

J-

0

50

100

150

l-

200

250

K 300

Fig. 63. Nb, 27SPd0 725.Temperaturedependenceof the magnetic susceptibility in various magnetic fields [86Kl].

Fig. 62. NbPd,. VPd,. Temperature dependenceof the magnetic susceptibility [82B3].

I= 433K

16

61 I

Fig. 64. Nb,Ta,_,H,. Magnetic volume susceptibility

I al

(in cgs-unit) of metal hydrides at composition x as a function of the hydrogen concentration y measuredby proton NMR at 433 K. I: [77KI], 2: [82Bl], 3: [82B2J, other symbols: [88Rl].

I

1.0

Landoh-Bbmslein New Series 111132A

Ref. p. 2821 IO wm

1.3 4d, 5d elements, alloys, and compoundswith main group elements

259

I

Nb, To,-,H,

T=433K

0

-60L 0

0.4

0.2

0.6

0.8

1.0

Fig. 65. Nb,Ta,,H,. Proton Knight shift relative to a bare proton for alloys of various compositions x at 433 K plotted against hydrogen concentration y. 1: [77Kl], 2: [82Bl], 3: [82B2], other symbols: [88Rl].

Y-

0 pm

16 .10-6 & 9

I

T=433K

-10 12 -20

I s

IO 8

-30 x”

6 -40 4 I

I/I

I 2

y;;im

0 80

100

120

140

1160

!20

Xm -

Fig. 66. Nb,Ta,,H,. Proton Knight shift is plotted against the magnetic susceptibility at 433 K for various compositions x with hydrogen concentration y as an implicit parameter. I: [77Kl], 2: [82B2], other symbols: [88Rl].

Landolt-Bbmstein New Series IIV32A

200

400

600

800

1000 1200 K 1400

T-

Fig. 67. Nb,,Ta$,. Temperaturedependenceof the magnetic susceptibility for solid solutions at various compositions [82Dl]. Curves: 1: NbC,.,,, 2: Nbo.,,QmC,.oo~ 3: Nbo.mTa.,oC1.oo, 4: Nbo.,o’b.,oC,.oo,5: Nbo.,oTa.&o 96, 6: Nbo.25Ta.75Cl.04~ 7: Nbo.loTa.goCI.oo~ 8: Ta%gg.

160

-2.0

16 *lo-6 g$ mol 14

pRcm

-1.6

120

1

[Ref. p. 282

1.3 4d, 5d elements, alloys, and compounds with main group elements

260

80

16 K

-1.2 4: 12

aI

?5

I 40

-0.8

0

‘S C -0.4

Nbt

0.2

0.4 x-

0.6

0.8

10

8 NbC

MC

Fig. 68. Nb,_,Ta$. Composition dependence of the magnetic susceptibility x, electrical resistivity A Hall

0.2

OX

x-

0.6

0.8

1

coefficient R and superconducting transition temperature r, for solid solutions [82Dl].

140 @cm 130

80

120

160

200

240

280 K 320

l-

b

60

80

a

120

160

200

210

280

K 320

l-

Fig. 69. Nb,-,Ta.$,. Temperaturedependenceof a the electrical resistivity and b Hall coefficient for solid solutions at various compositions [82Dl]. Curves:

I: Nbo zsTa dG

0412: Nbo soTao 2oC1 oo>

3: Nbo94Ta,o&

oo3 4: Nbo40T~060C096~

5: Nb,

,,Ta 4oCIoo76: Nbo loTao goCl o.

Land&-Barnsrein New Series 11113?A

Ref. p. 2821

261

1.3 4d, 5d elements, alloys, and compoundswith main group elements

OX % 0.79

*lo-6 gy mol

0.78

800

1 0.77 k

750

0.76

I 700 g

t4

0.75 U.d

530

5.2

I

I

I

5.4

5.6

5.8 -

x9

I

I

1

300

6.0 .10“cm3/mol6.4

510 I

Fig. 70. Nb,Pt,,,Au,,,. Nb Knight shift plotted against the magnetic susceptibility with temperature as an implicit parameter[70Bl].

200I 0

I 50

150

100

Nb,SnH, - ,.”n I 200 250 K 300

T-

Fig. 71. Nb,SnH,. Temperature dependence of the magnetic susceptibility for various compositions [84Sl].

1.3.4 MO alloys and compounds 3s *IO cm

0.20

I

(SKI-’

Mo,Si

mol 2s

0.16

2.i

I 0.12 -7 ;z

I

E * 1.t

"' 0.08

0

0

a

100

T-

200 K 3000

100

l-

200 K 300

Fig. 72. MosSi, Mo,Ge. Temperature dependenceof a the magnetic susceptibility, and b nuclear spin lattice relaxation rate of “MO, (rrq-‘, for neutron irradiated and unirradiated samples. Mo,Si; curve 1: unirradiLandolt-Biirnstein _. ^ ---..-.

0

b

100

T-

200 K 300O

100

200 K 300

T-

ated sample, 2: irradiated sample with fluence @ = l.3.10zo cm-*. Mo,Ge; Curve 1: unirradiated sample, 2: irradiated sample with fluence @= 2.1020cm-2 [86Al].

Ref. p. 2821

261

1.3 4d, 5d elements, alloys, and compoundswith main group elements

OX % 0.79

*lo-6 gy mol

0.78

800

1 0.77 k

750

0.76

I 700 g

t4

0.75 U.d

530

5.2

I

I

I

5.4

5.6

5.8 -

x9

I

I

1

300

6.0 .10“cm3/mol6.4

510 I

Fig. 70. Nb,Pt,,,Au,,,. Nb Knight shift plotted against the magnetic susceptibility with temperature as an implicit parameter[70Bl].

200I 0

I 50

150

100

Nb,SnH, - ,.”n I 200 250 K 300

T-

Fig. 71. Nb,SnH,. Temperature dependence of the magnetic susceptibility for various compositions [84Sl].

1.3.4 MO alloys and compounds 3s *IO cm

0.20

I

(SKI-’

Mo,Si

mol 2s

0.16

2.i

I 0.12 -7 ;z

I

E * 1.t

"' 0.08

0

0

a

100

T-

200 K 3000

100

l-

200 K 300

Fig. 72. MosSi, Mo,Ge. Temperature dependenceof a the magnetic susceptibility, and b nuclear spin lattice relaxation rate of “MO, (rrq-‘, for neutron irradiated and unirradiated samples. Mo,Si; curve 1: unirradiLandolt-Biirnstein _. ^ ---..-.

0

b

100

T-

200 K 300O

100

200 K 300

T-

ated sample, 2: irradiated sample with fluence @ = l.3.10zo cm-*. Mo,Ge; Curve 1: unirradiated sample, 2: irradiated sample with fluence @= 2.1020cm-2 [86Al].

262

1.3 4d, 5d elements,alloys, and compounds with main group elements

[Ref. p. 282

0.16

.lO‘~ & mol

O.lE

200

250 K

3

Fig. 73. Ru,MoO,. Temperature dependence of the molar magnetic susceptibility [94Sl].

1.3.5 Tc alloys and compounds

40-51

'

'

Fig. 74. Tc. Temperature dependenceof the magnetic susceptibility x,, electrical resistivity A and thermoelectric power Q [75Sl].

Landott-Barnstein New Series 111132A

262

1.3 4d, 5d elements,alloys, and compounds with main group elements

[Ref. p. 282

0.16

.lO‘~ & mol

O.lE

200

250 K

3

Fig. 73. Ru,MoO,. Temperature dependence of the molar magnetic susceptibility [94Sl].

1.3.5 Tc alloys and compounds

40-51

'

'

Fig. 74. Tc. Temperature dependenceof the magnetic susceptibility x,, electrical resistivity A and thermoelectric power Q [75Sl].

Landott-Barnstein New Series 111132A

0

263

1.3 4d, 5d elements, alloys, and compounds with main group elements

Ref. p. 2821

0.3

0.6

1.2

0.9

1.5

Fig. 75. TcH,. Temperature dependence of the magnetic susceptibility, in relative units, for various

0.3

0

K 1.8

0.9

0.6

1.2

1.5 K

1.8

hydrogen concentrations [89Al].

1.3.6 Ru alloys and compounds 2.251

I

I

I ,i

I

I

I

I i=77K

1.250

I

I I I I I I

I

Y 1.125

I

0.625 b 0.500

0.254 0.50

0.250 0.52

0.54

0.56 x-

0.58

0.60

0.62

0.64 0.125

M = V, Nb, Ta. Magnetic Ru,,M,, susceptibility at 77 K plotted against composition x. Open and solid symbols refer to the tetragonal and cubic phase,respectively [88Tl].

Fig. 76.

r

0

50

I

I

100

150 T-

I

200

250

300 K 350

Fig. 77. RI.I-~M~, M = Zr, Al, Ga. Magnetic field

dependenceof the magnetization at 1.2 K and at 4.2 K [73Tl].

Landolt-Bbmstein New Series 111132A

0

263

1.3 4d, 5d elements, alloys, and compounds with main group elements

Ref. p. 2821

0.3

0.6

1.2

0.9

1.5

Fig. 75. TcH,. Temperature dependence of the magnetic susceptibility, in relative units, for various

0.3

0

K 1.8

0.9

0.6

1.2

1.5 K

1.8

hydrogen concentrations [89Al].

1.3.6 Ru alloys and compounds 2.251

I

I

I ,i

I

I

I

I i=77K

1.250

I

I I I I I I

I

Y 1.125

I

0.625 b 0.500

0.254 0.50

0.250 0.52

0.54

0.56 x-

0.58

0.60

0.62

0.64 0.125

M = V, Nb, Ta. Magnetic Ru,,M,, susceptibility at 77 K plotted against composition x. Open and solid symbols refer to the tetragonal and cubic phase,respectively [88Tl].

Fig. 76.

r

0

50

I

I

100

150 T-

I

200

250

300 K 350

Fig. 77. RI.I-~M~, M = Zr, Al, Ga. Magnetic field

dependenceof the magnetization at 1.2 K and at 4.2 K [73Tl].

Landolt-Bbmstein New Series 111132A

264

1.3 4d, 5d elements,alloys, and compoundswith main group elements

0

50

100

150

200

250 K 300

T-

[Ref. p. 282

Fig. 78. RUM, M = Hf, Ti, Al, Ga. Temperature dependenceof the inverse magnetic susceptibility [73Tl].

Table 8. Ru,_,M,, M = Zr, SC,Ti, Hf, Al, Ga. Basic constants appearing in the modified Curie-Weiss

law of the magnetic susceptibility, x= x0 + C/(T- O), and in the magnetization relation at high magnetic fields, c= a, + xsH, deduced from the least mean square fit to the data in Figs. 13 and 79 for x and Figs. 14 and 78 for a[73Tl].

Rue49Zro5I Rue5oZro5. Rue5IZro49 Rue55Zro45 Ru,Zr RuSc RuTi RuHf Rue5&o 48 RuGa

X0

c

0

a,

XS

[10V6cm3g-‘1

[10s6Gcm3K g-l]

[K]

[Gcm’g-‘1

[ 1Od cm3g-‘1

0.42 0.43 0.47 f 0.03 0.66 lk 0.03 1.05 1.10 0.90 f 0.10 0.17 0.71 zk0.03 0.68 + 0.06

0.7 27 47 f 3 60 f 3 0 0 12* 1 0.9 77 f 4 88* 5

0 0.4 1.0 f 0.5 0.7 f 0.6 0 0 1.0*0.3 0 4.8 f 1 2.2 f 0.8

0.20 0.33

0.45 0.50

0.55 0.71

0.6 1.18

Landolt-BBmstein New Series W32A

Ref. p. 2821

265

1.3 4d, 5d elements, alloys, and compounds with main group elements

1.3.7- Rh alloys and compounds Table 9. Ti-Rb, Zr-Rb, Hf-Rb. Electronic specific heat coefficient, 3: and magnetic susceptibility at room temperature, x,,,, for ordered alloys [SSKl]. Y

xm

[mJ g-atom K-*1

[ 1Om5 cm3 g-atom-‘]

Ti Ti,Rh TiRb TiRb,

3.34 1.58 2.46 2.85

6.61 7.58 6.61

Zr Zr,Rb ZrRb ZrRb,

2.80 2.56 1.20 2.75

13.7 15.1 5.65 5.07

Hf Hf,Rb ‘) Hf,fi *) HfRb

2.15 2.72 2.79 1.25 2.54 4.7

6.75 6.48 4.00 4.04 5.54

HfRh3

Rh

I) As cast. *) Annealed for 2 h at 1300°C. 0.150 (SKI-’ 0.125 0.4

0.100 1

2 0.6

I ml75 ;g

I 0.8

c, c-’ 0.050

1.0 1.0

% % 1.2I 1.2 CU CU

n

0.2

0.4

0.6

0.8

I

0.025

Rh

Fig. 79. Rh,Cu,,. Composition dependence of the ‘03RhKnight shift I&, at 4.2 K [SlAl].

0 c:u

0.2

0.4

x-

0.6

0.8

Rh

Fig. 80. Rh,Cu,-,. Composition dependence of the nuclear spin lattice relaxation rate of ‘03Rh, (T,T)-’ [87El].

Landolt-Bijmstein New Series III132A

266

““Cu

1.3 4d, 5d elements,alloys, and compoundswith main group elements

0.2

0.4

X-

0.6

0.8

[Ref. p. 282

Rh

Fig. 81. Rh,Cu,_,. Composition dependence of the %u Knight shift FL-,at 4.2 K [81Al].

cu

0.2

0.4

x-

0.6

0.8

Rh

Fig. 82. Rh,Cu,_,. Composition dependence of the nuclear spin lattice relaxation rate of %I, (T,T)-’ [87El]. OAR 40-E & 9 0.U OR I 0.44 ?T 0.4: O.Si 0.41

0.U

ml

zul

I-

300

400

500 K 6 0

Fig. 83. Hf,Rh. Temperature dependence of the magnetic susceptibility for the “as cast” sample [88Kl].

Landolt-Barnstein New Series 111132A

Ref. p. 2821

1.3 4d, 5d elements, alloys, and compoundswith main group elements

267

1.8 .10-1 gg mol 1.5

0.9 I G 0.6

Rh

0.2

0.4

x-

0.6

0.8

Ir

Fig. 85. Rh,&,. Composition dependence of the magnetic susceptibility at temperatures of every 200 K from 0 to 1800 K. Open circles: [69Wl], solid circles: [68Al].

0

300

600

1200

900

1500 K 1800

Fig. 84. Rh,,Ir,. Temperature dependence of the magnetic susceptibility at various compositions [69Wl].

OL

I

I

I

I

Rh

0.2

0.4

0.6

0.8

Land&-Bbmstein New Series 111132A

Fig. 86. Rh,,Ir,. Composition dependence of the molar magnetic susceptibility at 273 K [91Tl]. Ir

[Ref. p. 282

1.3 4d, 5d elements,alloys, and compoundswith main group elements

268

1.3.8 Pd alloys and compounds 401 40

I

pm pm

I

I

I

1

PdH: PdH,

/

/

I/

30

I

20 t

/’ lo-

o s * Kli

0

0.2

f IL

1’ 0.1

0.6

0.8

1.0

x-

Fig. 88. PdH,. Muon (p’) and proton Knight shifts. K,, and K,,. as a function

of the hydrogen

concentration

x

[84Gi].

nr.d Fig. 87. Rh-Pd, Pd-Ag. OS-Ir. Ir-Pt, Pt-Au. Magnetic susceptibility of platinum group metals and their alloys at low temperatures plotted against the number of open-shell

30-

s and d electrons.

nrcd. [69W I].

30,

I

iv

ppm PdHo.~o

I

I

iI

I

I

I

I

Pd H 0.75 I

I

I 7-T-l

I

200

1

1T 1

/

Ti PI

!- 1 1 t t Ti 111 1 tli 0

I

0

0 1 ’ ’ ‘lTlQ ‘, ’ 1’ ’

YIIT

I

tI’\

1 T

iTi 1 fib\1 1 - IL f r1u 200

-20 250

Fig. 89. PdM,, x = 0.70, 0.75. Temperature

300 K 350 dependence

0

0

1 I

50

100

of the muon (p’) Knight

150

200

250

300 K 350

Ishift K, [8402].

Landoh-BBrnrtein New Series 111132A

Ref. p. 2821

1.3 4d, 5d elements, alloys, and compounds with main group elements

269

;:r,i 1Pd,-,Cu,

600 T-

BOO

1000 K 1200

Fig. 90. Pd,-,Cu,. Heating curves of the magnetic susceptibility for deformed and annealed samples. Curves 1, 3: x = 0.54. Curves 2, 4 : x = 0.55. Solid circles: samples deformed by cold drawing, open circles: samples annealed at 670 K for 4 h. Crystal structures of deformed and annealed samples are Al (disordered state) and B2 (ordered state), respectively [91S2].

300

500

700

900

K

ii0

T-

Fig. 91. Pd,,Cu,. Temperature dependence of the electrical resistivity of deformed alloys during heating (solid circles) and cooling (open circles). Curve 1: x = 0.60, 2: x = 0.55 [91S2].

.,o-66 cm3

-5 4 In 3 3 I, m * 2

X2

1

0 Pd

1

0.05

0.10

0.15

x-

0.20

0.25

0.30

0.35

Fig. 92. Pd,,M,, M=Pt, Ti. Composition dependence of the magnetic susceptibility at 293 K [89Vl].

0 -1

0

0.1

0.2

0.3 0.4 x+y -

0.5

0.6

0.7

Fig. 93. Pd,-,M,Hy, M=Cu, Au. Magnetic susceptibility as a function of the number of valence electrons, x + y [86Gl]. Land&-Bbmstein New Series IIV32A

270

1.3 4d, 5d elements, alloys, and compounds with main group elements Fl

1.0 Pd, Se, 40-7 .... . .. .. .....*.-.-c!!PL *...... . . . .. * . . . .. . . . . 9

‘$ Pd,-,ie, 0 -ir Ii ,:****-- * . \i......... - * 1 6 :.... ...**-. . . . *a. .0.005 . ;. ) 5 +.-.,....... .**.

w”

[Ref. p. 282

0

I x"

x :0.015

-‘. - ’

-0.5 -1.0

-1.5 I ::

0

50

100

l-

150

200

250 K 300

Fig. 94. Pd,_,Se,. Temperature dependence of the magnetic susceptibility of pure Pd and Pd(Se) solid solutions [88Tl]. 4*10’T=373K

PO Pd,-, NbxH, 1

I

-2.011 0

I

I

50

100

I-

I

I

150

200

250 K 300

Fig. 95. Pd,Se,. Temperature dependence of the magnetic susceptibility for various compounds [87T13. LO,

*10-g m3

1

I

P$,-, Nb, H,

I

1

,

I

ll=373KI

n 6 L 1

10’ 0

0.15

0.30

0.45

0.60

0.75

Y-

Fig. 97. Pd,_,Nb,H,. Hydrogen concentration dependence of the magnetic susceptibility at 373 K [89Wl].

Fig. 96. Pd,-,Nb,H,.. Absorption and desorption isotherms of the equilibrium pressure p plotted as a function of the hydrogen concentration y at 373 K [89Wl].

LandoIl-Birrnrtein New Series 111132A

Ref. p. 2821 4.107

1.3 4d, 5d elements, alloys, and compoundswith main group elements

271

I

p0 Pd,-,Mo,H,

T=373K

T =373K

2 . IO' 8 6

41

iI

I I

L

/ I

I. I 4

” 54

i-l

r

1 II I I P I P

I

$

I

t I i

I 2.5

t

1

s 1.5

2 IO5 8 6 4 2

Fig. 99. Pd,-,Mo,H,. Hydrogen concentration dependence of the magnetic susceptibility at 373 K [89Wl]. Fig. 98. Pd,.+Mo,H,. Absorption and desorption isotherms of the equilibrium pressurep plotted as a function of the hydrogen concentration y at 373 K [89Wl].

Fig. 100. Pd,-,Mo,H,. Composition dependence of the magnetic susceptibility at 293 K. Curve I: x = 0, 2: y = 0, 3: x = 0.01, 4: x = 0.05 [91Vl]. 0.1

Landolt-BOrnstein New Series IW32A

0.2 x+y -

0.3

0.4

0.5

272

1.3 4d, 5d elements, alloys, and compounds with main group elements

If

2

I/

I

lo5 8 6 4 2.1q

I 0.2

I-

0.4

I 0.6

[Ref. p. 282

I 0.8

Fig. 101. Pd,_,Ru,H,. Absorption and desorption isotherms of the equilibrium pressurep plotted as a function of the hydrogen concentration y at 373 K [89Wl].

Y-

7 -10-q

m3 ii%

40-9 .I?.

mol 5 4

I G3 2 1

0

0.45

0.60

Y-

Fig. 102. Pd,_,Ru,H,. Hydrogen concentration dependence of the magnetic susceptibility at various temperatures[SSWI].

Land&-Barnsrein New Series 111132A

Ref. p. 2821

1.3 4d, 5d elements, alloys, and compoundswith main group elements

.wl c&,

0.03

y-2,

273

Rh, A!,

mol

7.5 1 E 7.0 x 6.5 0.3at %ig 6.0

6.5 6.0

“‘“II

9 Pd,-.Rh,

5.01

”

5.01 0

50

100 T-

150

200

250 K 300

Fig. 103. Pd,-,Rh,, Pd,,Ag,. Temperature dependence of the magnetic susceptibility for Pd and various alloys. The Curie-type behavior of the susceptibility arising from magnetic impurities has been subtracted so that the resulting susceptibility behaves like x(O) + AT2 for a temperature range between 15 and 30 K [69Hl].

0.1000.075 0.050 0.025 -x

Land&-Bbmstein New Series 111/32A

0

1 50

100

150

200

\I

250 K 300

IFig. 104. Pd,-,,Rh,Ag,. Temperature dependence of the magnetic susceptibility for Pd and various alloys. The Curie-type behavior of the susceptibility arising from magnetic impurities has been subtracted so that the resulting susceptibility behaves like x(O) + AT2 for a temperaturerange between 15 and 30 K [69Hl].

Fig. 105. Pd,,Ag,, Pd,,Rh,, Pd,-,,Rh,Ag,. Composition dependence of the magnetic susceptibility, extrapolated values at 0 K, for alloys. I: [53Hl], 2: [63Ml], 3: [69Hl]. 0

0.025 0.050 0.075 o.loo x-

274

1.3 4d, 5d elements,alloys, and compoundswith main group elements

[Ref. p. 282

Table 10. Pd,_,.Rh,.,Pd,$h,H,. Magnetostriction data of Pd-Rh alloys. 4: longitudinal strain, Q: transverse strain, Sr: volume magnetostriction, S,: shape magnetostriction. SF = (SV/v)/B* = (E;,+ 2q)/B’, S, = (q - &J/B* [84Pl].

Pd PdHo0145 Pdo&ho 01 PdowRhoorHo010s

q/B?

EJB’

SV

sr

[ 1O-“T-*1

[ 1o-‘@I?]

[ 1o-‘O-J?]

[ 1o-‘ol-*]

-2O~k4 -24

65k I 73

110*5 122

-85 f 5 -97

11 f 1 6

112rt3 107

235 f 6 220

-101 f 3 -101

Pdo&ho 03 Pdo&ho o,Ho0075

112*5 102

206 f 1 193

524 f 5 488

-94 f 5 -91

Pdo&ho os Pdo&ho osHo0073

147&5 134

2195 1 207

585 rt 5 548

-72 f 5 -73

4.0 *lo+ & 9

3.0 2.5 I 2.0 x” 1.5 1.0 0.5

Fig. 106. Pd,-,W,H,. Hydrogen concentration dependenceof the magnetic susceptibility at room tem-

perature.Curves: I: x = 0, 2: x = 0.01,3: x = 0.05,4: x = 0.07, 5: x = 0.08 [84Bl].

0

0.05 010

0.5 Y-

0.20 0.25 0.30 0.35

Fig. 107. Pd,-,M,H,, M = Pt, Ti. Hydrogen concentration dependence of the magnetic susceptibility at 293 K. Curves: I: M = Pt, x = 0.1, 2: M = Pt, x = 0.22, 3: M = Pt, x = 0.32, 4: M = Ti, x = 0.02, 5: M = Ti, x = 0.05, 6: M = Ti, x = 0.09 [89Vl].

Landolt-B6rnrtein New Series IlV32A

Ref. p. 2821

1.3 4d, 5d elements, alloys, and compoundswith main group elements

275

25

,Or 0

1

1

1

1

1

1

0.'

0.2

0.3

0.4

0.5

0.6

x+y -

Fig. 108. Pd,-,M,H,, M = Pt, Ti. Electrical resistivity at 293 K plotted as a function of x + y. Curves: I: Pd,,Pt, 2: Pd,-,Ti,. 3: Pd,,,,Ti,,,,Hy, I: Pd,,,,Ti,,,,H,, 5: Pd,,,,Ti,,,,HY [89Vl].

1.3.9 Hf alloys and compounds SeeFigs. 35, 51,78, 83 and Tables 3, 8,9

1.3.10 Ta alloys and compounds -T

-T .-IO00 K

20

A

800

500

600

I

I

I

1.2

1.4

1.6

1000 K 1 I s-1 8 Tao0.08

500

400 I

I

I

I/

2.5

3.0

300 l/1 P I I

2513

I

I 5 ‘09 ; I

5

'09 ; 6 5 4

3 1.0

a

l/T-

Fig. 109. TaH,, TaD,,,s. a Proton spin-lattice relaxation rate q-’ in TaH, plotted against inverse temperature at various compositions. 1: x = 0.04, 2: x = 0.04

Land&-B6mstein New Series IW32A

IO1-l 1.0

l.810-3 K-' 2.0

b

1.5

2.0

3.5.10-3K-'4.0

VT -

after 6 h at 990 K, 3: x = 0.11 [91Hl], 4: x = 0.2 [89Hl]. b Deuteron spin-lattice relaxation rate q-’ in TaD,,,, plotted against inverse temperature [91Hl].

Ref. p. 2821

1.3 4d, 5d elements, alloys, and compoundswith main group elements

275

25

,Or 0

1

1

1

1

1

1

0.'

0.2

0.3

0.4

0.5

0.6

x+y -

Fig. 108. Pd,-,M,H,, M = Pt, Ti. Electrical resistivity at 293 K plotted as a function of x + y. Curves: I: Pd,,Pt, 2: Pd,-,Ti,. 3: Pd,,,,Ti,,,,Hy, I: Pd,,,,Ti,,,,H,, 5: Pd,,,,Ti,,,,HY [89Vl].

1.3.9 Hf alloys and compounds SeeFigs. 35, 51,78, 83 and Tables 3, 8,9

1.3.10 Ta alloys and compounds -T

-T .-IO00 K

20

A

800

500

600

I

I

I

1.2

1.4

1.6

1000 K 1 I s-1 8 Tao0.08

500

400 I

I

I

I/

2.5

3.0

300 l/1 P I I

2513

I

I 5 ‘09 ; I

5

'09 ; 6 5 4

3 1.0

a

l/T-

Fig. 109. TaH,, TaD,,,s. a Proton spin-lattice relaxation rate q-’ in TaH, plotted against inverse temperature at various compositions. 1: x = 0.04, 2: x = 0.04

Land&-B6mstein New Series IW32A

IO1-l 1.0

l.810-3 K-' 2.0

b

1.5

2.0

3.5.10-3K-'4.0

VT -

after 6 h at 990 K, 3: x = 0.11 [91Hl], 4: x = 0.2 [89Hl]. b Deuteron spin-lattice relaxation rate q-’ in TaD,,,, plotted against inverse temperature [91Hl].

1.3 4d, 5d elements, alloys, and compounds with main group elements

216

[Ref. p. 282

X,Y -

0.2

0.4

0.6

0.E

’

Fig. 110. TaH,, Ta,_,W,. Comparison of the magnetic susceptibility of TaH, at room temperature with that of Ta,_,W, plotted against the number of valence electrons, nV(or against x or y). Solid circles: [62Tl], squares: [78KI J, half-tilled circle: ]82B2], open circles: [88Rl]. 5.0

5.4 “v -

5.2

5.6

5.8

6.0

1.3.11 W alloys and compounds

2.5 2.0 9

I

b

1.5

0

10

20

30

40

50 kOe 60

H-

00-1°

250 K 300 I-

Fig. 111. W, WC. Temperature dependence of the magnetic susceptibility of W and WC, and inverse magnetic susceptibility of WC [86Ll].

Fig. 112. WC. Magnetic field dependenceof the magnetization at various temperatures below 300 K [86Ll].

1.3 4d, 5d elements, alloys, and compounds with main group elements

216

[Ref. p. 282

X,Y -

0.2

0.4

0.6

0.E

’

Fig. 110. TaH,, Ta,_,W,. Comparison of the magnetic susceptibility of TaH, at room temperature with that of Ta,_,W, plotted against the number of valence electrons, nV(or against x or y). Solid circles: [62Tl], squares: [78KI J, half-tilled circle: ]82B2], open circles: [88Rl]. 5.0

5.4 “v -

5.2

5.6

5.8

6.0

1.3.11 W alloys and compounds

2.5 2.0 9

I

b

1.5

0

10

20

30

40

50 kOe 60

H-

00-1°

250 K 300 I-

Fig. 111. W, WC. Temperature dependence of the magnetic susceptibility of W and WC, and inverse magnetic susceptibility of WC [86Ll].

Fig. 112. WC. Magnetic field dependenceof the magnetization at various temperatures below 300 K [86Ll].

Ref. p. 2821

1.3 4d, 5d elements, alloys, and compounds with main group elements

I 2

I 0

I 4 ‘b

I 6

277

Fig. 113. Pt, W, WC. Line shapesof the UPS spectra plotted against the binding energy of electrons, Eb = EF-E [86Ll].

I I 8 eV 10

-

w

0

I 2

I 4

I 6

I 8

I

10

I

12 eV

[b -

Fig. 114. Pt, W, WC. Line shapesof the XPS spectra plotted against the binding energy of electrons, E,,=E,-E[86Ll].

Landolt-Biirnstein New Series IW32A

0

5

15

IO [b -

20

25 eV 2

1.3 4d, 5d elements, alloys, and compounds with main group elements

278

[Ref. p. 282

1.3.12 Re alloys and compounds 1.25 -10-C

blcm

I

Re2Si

1.00

” o” O

0

74

00 ,,O

0.7E

0 0

I 0

Qr 6,

0.5c moo0

0.25 0

50

150

100

200

250 K 300

l-

Fig. 115. Re,Si. Temperature dependenceof the magnetic susceptibility measured in a magnetic field of 10 kOe [91Sl].

-6s,

,

~$1 ReSi, /

I

/

I

I

1

1

I H=SkOe

t

50

100

150

250 K 300

Fig. 116. Re,Si. Temperature dependenceof the electrical resistivity [91Sl].

I

-68 -70

s

-72 -71 -76’ 0

I 200

I 400 r-

I 600

I 800 K

I 1000

Fig. 117. ReSi,. Temperature dependenceof the magnetic susceptibility measured in a magnetic field of 4 kOe [85Sl].

Landoh-BBrnstein New Series 111132A

Ref. p. 2821

1.3 4d, 5d elements, alloys, and compounds with main group elements

279

I 20 ; 15 10 5 0 a

0.10

0.15

I

I

I

I

I

I

x-

0.34, nm

I

0.33

0.20 0.25

I

I I

I

H-s

t I I 0.31

0.05

C

0.10

0.15

0.20

0.25

x-

1.3.13 OS alloys and compounds See Figs. 15, 87 and Table 3

Landolt-Biirnstein New Series 111132A

0.30

0.35

I

I

I

I

I

b

0

0.05

0.10 0.15 0.20 x-

I

0.25

I

0.30 0 5

I I

I 0.32 D

0.30 0

I

I

0.05

Fig. 118. RexM,+ M = Nb, MO, V. Composition dependenceof a the magnetic susceptibility x,,,, b superconducting transition temperature T, and c lattice con0.30 0.35 stant a [87Sl].

Ref. p. 2821

1.3 4d, 5d elements, alloys, and compounds with main group elements

279

I 20 ; 15 10 5 0 a

0.10

0.15

I

I

I

I

I

I

x-

0.34, nm

I

0.33

0.20 0.25

I

I I

I

H-s

t I I 0.31

0.05

C

0.10

0.15

0.20

0.25

x-

1.3.13 OS alloys and compounds See Figs. 15, 87 and Table 3

Landolt-Biirnstein New Series 111132A

0.30

0.35

I

I

I

I

I

b

0

0.05

0.10 0.15 0.20 x-

I

0.25

I

0.30 0 5

I I

I 0.32 D

0.30 0

I

I

0.05

Fig. 118. RexM,+ M = Nb, MO, V. Composition dependenceof a the magnetic susceptibility x,,,, b superconducting transition temperature T, and c lattice con0.30 0.35 stant a [87Sl].

[Ref. p. 282

1.3 4d, 5d elements,alloys, and compoundswith main group elements

280

1.3.14 Ir alloys and compounds

Fig. 119. Ba,CaIrO,. Temperature dependenceof the inverse magnetic susceptibility [93Dl].

200

0

600

LOO

K

800

T-

1.000

I 0.995

I 0.995 c .s

E 'cl 'C 0.990

.E r E 0.990

E 0.985

0.985 0.980

0.960 1 -20

I I -15 -10

I

I

I

I

-5

0

5

10

. -5 -4

0.9751 ’ -5 -4 b

I Ir

0951

I

15mmMO

Y-

a

c

I

’ -3

’

’

’

-2

-1

0

V-

I

’

’

1

2

’ 3

’ mm/s5

T-4.lK

Fig. 120. Ba,CaIrO,, Ir. 19% MBssbauer spectra of Ba,CaIr06 at a 4.2 K, and b 65 K. c shows the spectrum of Ir metal at 4.2 K for the isomer shift reference [93Dl]. -3 -2

-1

Y-

0

1

2

3

mm/s

Land&-Bbrnsrein New Series 111/32A

Ref. p. 2821

1.3 4d, 5d elements, alloys, and compoundswith main group elements

281

Table 11. Ba,CaIrO,. Hyperfine interaction parametersfor ‘931rat 65 K and 4.2 K, derived from the spectra in Fig. 121. Hi:;’ : hyperfine field calculated from the splitting of the excited l/2-state with g,/, = 1.007, g&g,,,: g-factor ratio, e2qQ: quadrupole interaction, W: linewidth of the Lorentzian lines, IS: isomer shift relative to Ir metal [93Dl]. T

(14

We1

Kl Ba,CaIrO,

g,,*k3,*

Hbp

65 4.2

1497 f 8

9.003 f 0.030

e%Q

W

IS

[mm s-‘1

[mm s-‘1

[mm s-l]

0.53 f 0.04 0.93 f 0.04

0.80 f 0.05 0.85 f 0.02

1.38 f 0.02 1.36 f 0.02

1.3.15 Pt alloys and compounds 100 wm

-150 0

0.2

0.4

0.6

0.8

40%m3/gl.Z

Fig. 121. Pt. Muon (p’) Knight shift K,, plotted as a function of the magnetic susceptibility [84Gl]. Fig. 122. CaPtSi. Magnetic susceptibility for three different crystal structures plotted as a function of the inverse field. Curve I: cubic, 2: monoclinic, 3: orthorhombic [93El].

Landolt-BWnstein New Series IW32A

Ref. p. 2821

1.3 4d, 5d elements, alloys, and compoundswith main group elements

281

Table 11. Ba,CaIrO,. Hyperfine interaction parametersfor ‘931rat 65 K and 4.2 K, derived from the spectra in Fig. 121. Hi:;’ : hyperfine field calculated from the splitting of the excited l/2-state with g,/, = 1.007, g&g,,,: g-factor ratio, e2qQ: quadrupole interaction, W: linewidth of the Lorentzian lines, IS: isomer shift relative to Ir metal [93Dl]. T

(14

We1

Kl Ba,CaIrO,

g,,*k3,*

Hbp

65 4.2

1497 f 8

9.003 f 0.030

e%Q

W

IS

[mm s-‘1

[mm s-‘1

[mm s-l]

0.53 f 0.04 0.93 f 0.04

0.80 f 0.05 0.85 f 0.02

1.38 f 0.02 1.36 f 0.02

1.3.15 Pt alloys and compounds 100 wm

-150 0

0.2

0.4

0.6

0.8

40%m3/gl.Z

Fig. 121. Pt. Muon (p’) Knight shift K,, plotted as a function of the magnetic susceptibility [84Gl]. Fig. 122. CaPtSi. Magnetic susceptibility for three different crystal structures plotted as a function of the inverse field. Curve I: cubic, 2: monoclinic, 3: orthorhombic [93El].

Landolt-BWnstein New Series IW32A

282

Referencesfor 1.3

0

0.2

0.4

x-

0 *10-a & mol

0.6

0.6

1.0

Fig. 123. Pt,J.Zu,. Composition dependence of the “‘Pt T,T values, where T, is the spin-lattice relaxation time and T is the temperature.The experimental point marked Ll , is for the ordered state, and others are for the disordered state. Dashed line shows general tendency: 1: [6411], 2: pure Pt [77Cl], 3: [91Bl].

Ptta, . . . . . . ...”

. . . . . .

b. . . . . . l * 1

-20

I -40 ,:

-60

50 50 8

100 100

150 150

I 200 200

I

I

250 K 300

T-

Fig. 124. PtGa,, AuGa,. a Temperaturedependenceof the magnetic susceptibility of PtGa, [93Hl]; for reference, the data for AuGa, arc also plotted [68Jl].

b b Temperature dependence of the thermoelectric power Q of PtGa, [93Hl]; the data for Au and AuGa, are taken from [52Hl] and [63Jl], respectively.

1.3.16 References for 1.3 50Gl

Ginzburg, V.L., Landau, L.D.: Zh. Eksp. Teor. Fiz. 20 (1950) 1064

52Hl

Hoare, F.E., Matthews, J.C.: Proc. R. Sot. London A 212 (1952) 137

53H1

Hoare, F.E., Matthews, J.C., Walling, J.C.: Proc. R. Sot. London A 216 (1953) 502

62T1 6221

Taniguchi, S., Tebble, R.S., Williams, D.E.G.: Proc. R. Sot. London A 265 (1962) 502 Zanowick, R.L., Wallace, W.E.: J. Chem. Phys. 36 (1962) 2059 Landoh-Barnstein New Series 111132A

282

Referencesfor 1.3

0

0.2

0.4

x-

0 *10-a & mol

0.6

0.6

1.0

Fig. 123. Pt,J.Zu,. Composition dependence of the “‘Pt T,T values, where T, is the spin-lattice relaxation time and T is the temperature.The experimental point marked Ll , is for the ordered state, and others are for the disordered state. Dashed line shows general tendency: 1: [6411], 2: pure Pt [77Cl], 3: [91Bl].

Ptta, . . . . . . ...”

. . . . . .

b. . . . . . l * 1

-20

I -40 ,:

-60

50 50 8

100 100

150 150

I 200 200

I

I

250 K 300

T-

Fig. 124. PtGa,, AuGa,. a Temperaturedependenceof the magnetic susceptibility of PtGa, [93Hl]; for reference, the data for AuGa, arc also plotted [68Jl].

b b Temperature dependence of the thermoelectric power Q of PtGa, [93Hl]; the data for Au and AuGa, are taken from [52Hl] and [63Jl], respectively.

1.3.16 References for 1.3 50Gl

Ginzburg, V.L., Landau, L.D.: Zh. Eksp. Teor. Fiz. 20 (1950) 1064

52Hl

Hoare, F.E., Matthews, J.C.: Proc. R. Sot. London A 212 (1952) 137

53H1

Hoare, F.E., Matthews, J.C., Walling, J.C.: Proc. R. Sot. London A 216 (1953) 502

62T1 6221

Taniguchi, S., Tebble, R.S., Williams, D.E.G.: Proc. R. Sot. London A 265 (1962) 502 Zanowick, R.L., Wallace, W.E.: J. Chem. Phys. 36 (1962) 2059 Landoh-Barnstein New Series 111132A

Referencesfor 1.3

283

6351 63Ml

Jan, J.P., Pearson,W.B.: Philos. Mag. 8 (1963) 279 Manuel, A.J., St.Quinton, J.M.P.: Proc. R. Sot. London A 273 (1963) 412

6411

Itoh, J., Asayama, K., Kobayashi, S.: Proc. Colloq. AMPERE 13 (1964) 162

68Al 68Jl 68Wl

Andres, K., Jensen,M.A.: Phys. Rev. 165 (1968) 533 Jaccarino, V., Weger, M., Wernick, J.H., Menth, A.: Phys. Rev. Lett. 21 (1968) 1811 Wohlfarth, E.P.: J. Appl. Phys. 39 (1968) 1061

69Hl 69Wl

Hahn, A., Treutmann, W.: Z. Angew. Phys. 26 (1969) 129 Weiss, W.D.: Z. Angew. Phys. 26 (1969) 124

70A1 70Bl 70Dl

Aronson, S., Reilly, J.J., Wiswall, R.H., Jr.: J. Less-CommonMet. 21 (1970) 439 Bernasson, M., Descouts, P., Fltikiger, R., Treyvaud, A.: Solid State Commun. 8 (1970) 837 Ducastelle, F., Caudron, R., Costa, P.: J. Phys. Chem. Solids 31 (1970) 1247

72M1

Murata, K.K., Doniach, S.: Phys. Rev. Lett. 29 (1972) 285

73M1 73Tl

Moriya, T., Kawabata, A.: J. Phys. Sot. Jpn. 34 (1973) 639 Tamminga, Y., Barkman, B., de Boer, F.R.: Solid State Commun. 12 (1973) 731

74Hl

Hechttischer, D.: Thesis, Berlin 1974

75Cl 75Hl 75Sl

Clinton, J.R., Viswanathan, R.: J. Magn. Magn. Mater. 1 (1975) 73 Huber, J.G., Maple, M.B., Wohlleben, D., Knapp, G.S.: Solid State Commun. 16 (1975) 2 11 Spitsyn, V.I., Zinov’ev, V.E., Gel’d, P.V., Balakhovskii, O.A.: Dokl. Akad. Nauk SSSR221 (1975) No.1, 145

77Cl 77G1 77K1

Carter, C.C., Bennett, L.H., Kahan, D.J.: Metallic Shifts in NMR, Oxford: Pergamon, 1977, Vol. 1 LeGuillou, J.C., Zinn-Justin, J.: Phys. Rev. Lett. 39 (1977) 95 Kazama, S., Fukai, Y.: J. Less-CommonMet. 53 (1977) 25

78KI

Kobler, U., Schober, T.: J. Less-CommonMet. 60 (1978) 101

80D1 8OMl

Dublon, G., Habbal, F., Bevk, J.: Solid State Commun. 36 (1980) 623 Matukhin, V.L., Satin, I.A., Shamray,V.F.: Phys. Met. Metallogr. USSR (Engl. Transl.) 50 (1980)No. 3,63

81Al 81A2 81Kl 81Ml

Abart, J., Voitlander, J.: Solid State Commun. 40 (1981) 277 Altounian, Z., Tu, G.-H., Strom-Olsen, J.O.: Solid State Commun. 40 (1981) 221 Kaul, S.N.: Phys. Rev. B 24 (1981) 6550 Mattocks, P.G., Dixon, A.E.: J. Phys. F 11 (1981) L147

82Bl 82B2 82B3 82Dl 82El 82Pl

Baden, W., Schmidt, P.C., Weiss, A.: J. Less-CommonMet. 88 (1982) 171 Baden, W.: Thesis, Darmstadt 1982 Burmester, W.L., Sellmyer, D.J.: J. Appl. Phys. 53 (1982) 2024 Dubrovskaya, L.B., Nazarova, S.Z., Prekul, A.F.: Phys. Status Solidi (a) 69 (1982) 167 Eifert, H.-J., Elschner, B., Buschow, K.H.J.: Phys. Rev. B 25 (1982) 744 1 Panova, G.Kh., Chernoplekov, N.A., Shikov, A.A., Savel’ev, B.I.: Zh. Eksp. Teor. Fiz. 82 (1982) 548; Sov. Phys. JETP (Engl. Transl.) 55 (1982) 319

Landoli-Biirnstein New Series 111132A

284

Referencesfor 1.3

82Rl

van Ruitenbeek, J.M., Verhoef, W.A., Mattocks, P.G., Dixon, A.E., van Deursen, A.P.J., de Vroomen, A.R.: J. Phys. F 12 (1982) 2919

83Kl 8301 83Pl

Korn, C.: Phys. Rev. B 28 (1983) 95 Ogawa, S.: J. Magn. Magn. Mater. 31-34 (1983) 269 Panova, G.Kh., Savel’ev, B.I., Khlopkin, M.N., Chernoplekov, N.A., Shikov, A.A.: Zh. Eksp. Teor. Fiz. 85 (1983) 1308; Sov. Phys. JETP (Engl. Transl.) 58 (1983) 759 Siegrist, T., Hulliger, F., Travaglini, G.: J. Less-CommonMet. 92 (1983) 119

83Sl 84BI

845I 84Pl 84Sl

Berseneva,F.N., Volkenshteyn, N.V., Galoshina, E.V., Gromov, V.I., Timofeyev, N.I., Shubina, T.S.: Phys. Met. Metallogr. USSR (Engl. Transl.) 57 (1984) No. 2, 65 Baden, W., Schmidt, P.C., Weiss, A.: J. Less-CommonMet. 104 (1984) 99 Eifert, H.-J., Elschner, B., Buschow, K.H.J.: Phys. Rev. B 29 (1984) 2905 Gygax, F.N., Hintermann, A., Rtiegg, W., Schenck, A, Studer, W., van der Wal, A.J.: J. Less-CommonMet. 101 (1984) 97 Gygax, F.N., Hintermann, A., Rtiegg, W., Schenck, A., Studer, W., van der Wal, A.J.: Hyperfine Interact. 17-19 (1984) 377 Junod, A., Jorda, J.-L., Pelizzone, M., Muller, J.: Phys. Rev. B 29 (1984) 1189 Pluzhnikov, V., Maszkiewicz, M., Fawcett, E.: J. Phys. F 14 (1984) 2411 Shamrai, V.: J. Low Temp. Phys. 56 (1984) 51

85Bl 85Kl 85K2 85Sl 85Vl

Bowman, R.C., Jr., Craft, B.D., Cantrell, J.S., Venturini, E.L.: Phys. Rev. B 31 (1985) 5604 Kuentzler, R., Waterstrat,R.M.: Solid StateCommun. 54 (1985) 5 17 Kaul, S.N.: J. Magn. Magn. Mater. 53 (1985) 5 Slebarski, A., Wohlleben, D., Weidner, P.: Z. Phys. B 61 (1985) 177 Venturini, E.L., Bowmam, R.C., Jr., Cantrell, J.S.: J. Appl. Phys. 57 (1985) 3542

86Al

Aleksashin, B.A., Verkhovskiy, S.V., Mikhalyov, K.N., Stepanov,A.P., Arkhipov, Y.Ye., Goshchitskiy, B.N.: Phys. Met. Metallogr. USSR (Engl. Transl.) 62 (1986) No. 2,67 van Deursen A.P.J., Schreurs,L.W.M., Admiraal, C.B., de Boer, F.R., de Vroomen, A.R.: J. Magn. Magn. Mater. 54-57 (1986) 1113 Galoshina, E.V., Timofeyev, N.I., Zhakarov, A.B., Shubina, T.S., Berseneva,F.N.: Phys. Met. Metallogr. USSR (Engl. Transl.) 61 (1986) No. 5, 65 Kuentzler, R., Water&at, R.M.: J. Less-CommonMet. 120 (1986) 3 17 Kuentzler, R., Waterstrat, R.M.: J. Less-CommonMet. 125 (1986) 261 Lin, Z.-D., Wang, C.-H., Shen, D.-H.: Acta Phys. Sin. 35 (1986) 98 Mohn, P., Schwarz, K.: Solid State Commun. 57 (1986) 103

84B2 84El 84Gl 8462

86Dl 86Gl 86Kl 86K2 86Ll 86MI 87El 87SI 87Tl 87Yl 88Bl 88Kl 88Rl 88Tl 88T2

Ebert, H., Winter, H., Abart, J., Voitlander, J.: J. Phys. F 17 (1987) 1457 Smol’yaninova, E.A., Stribuk, Ye.K., Tyavlovskiy, V.I.: Phys. Met. Metallogr. USSR (Engl. Transl.) 63 (1987) No. 3,95 Takabatake,T., Ishikawa, M., Jorda, J.L.: J. Less-CommonMet. 134 (1987) 79 Yasuda, H., Sumiyama, K., Nakamura, Y.: Trans. Jpn. Inst. Met. 9 (1987) 692 Bowman, R.C., Jr., Cantrell, J.S., Samwer,K., Tebbe, J., Venturini, E.L., Rush, J.J.: Phys. Rev. B 37 (1988) 8575 Kuentzler, R., Waterstrat, R.M.: Solid StateCommun. 68 (1988) 85 Richter, K.-H., Weiss, A.: J. Less-CommonMet. 142 (1988) 301 Takabatake,T., Ishikawa, M., Junod, A.: J. Phys. Sot. Jpn. 57 (1988) 2763 Tsukamoto, T., Koyama, K., Oota, A., Noguchi, S.: Cryogenics 28 (1988) 580

Land&-Btmrtein New Series lW32A

Referencesfor 1.3 89A1

285

89Wl

Antonov, V.Ye., Belash, I.T., Bukov, K.G., Zharikov, O.V., Pal’nickenko, A.V., Teplinskiy, V.M.: Phys. Met. Metallogr. USSR (Engl. Transl.) 68 (1989) No. 6, 153 Han, J.-W., Lichty, L.R., Torgeson, D.R., Seymour, E.F.W., Barnes, R.G., Billeter, J.L., Cotts, R.M.: Phys. Rev. B 40 (1989) 9025 Mazumdar, I.Lo.S., Mattocks, P.G.: Phys. Rev. Lett. 62 (1989) 2555 Volkenshteyn, N.V., Galoshina, E.V., Zhakarov, A.B., Timofeyev, N.I., Shubina, T.S., Berseneva, F.N.: Phys. Met. Metallogr. USSR (Engl. Transl.) 67 (1989) No. 6, 58 Wicke, E., Frolich, K.: Z. Phys. Chem., N. F. 163 (1989) 35

90H1 9011

Hayden, S.M., Paulsen,CC.: Physica B 165+166 (1990) 201 Ikeda, K., Yoshizawa, M., Kai, K., Nomoto, T.: Physica B 165+166 (1990) 203

91Bl

Banhart, J., Kuentzler, R., Pfeiler, W., Christ, T., Weinberger, P., Voitlander, J.: Phys. Rev. B 44 (1991) 11624 Buszko, M., Tegenfeldt, J., Ahlzen, P.-J., Andersson, Y.: J. Less-CommonMet. 172-174

89H1 89Ml 89Vl

91B2

(1991) 618

91Hl 91H2 91Ml 91Sl 91S2 91Tl 91Vl 93D1 93El 93Hl 93Nl 93Ul

Hampele, M., Majer, G., Messer, R., Seeger,A.: J. Less-CommonMet. 172-174 (1991) 631 Han, J.W., Torgeson, D.R., Barnes, R.G., Peterson,D.T.: Phys. Rev. B 44 (1991) 12353 Misawa, S., Tanaka, T., Tsuru, K.: Europhys. Lett. 14 (1991) 377 Siegrist, T., Greendan, J.E., Garrett, J.D., GongWenhe, Stager, C.V.: J. Less-Common Met. 171(1991) 171 Senchenko,A.A., Piratinskaya, I.I., Zelenin, L.P., Vereshchagin, YuA.: Phys. Met. Metallogr. USSR (Engl. Transl.) 72 (1991) No. 2, 105 Tripathi, S.N., Bharadwaj, S.R., Chandrasekharaiah,M.S.: J. PhaseEquilibria 12 (1991) 606 Volkenshteyn, N.V., Galoshina, E.V., Shubina, T.S., Berseneva,F.N., Zakharov, A.B., Timofeyev, N.I.: Phys. Met. Metallogr. USSR (Engl. Transl.) 71 (1991) No. 6, 123 Demazeau,G., Jung, D.-Y., Sanchez,J.-P., Colineau, E., Blaise, A., Fournes, L.: Solid State Commun. 85 (1993) 479 Evers, J., Oehlinger, G., Polborn, K., Sendlinger, B.: J. Solid State Chem. 103 (1993) 45 HSU,L.-S., Zhou, L.-W., Williams, R.S.: J. Phys. Chem. Solids 54 (1993) 913 Niedzwiedz, K., Nowak, B., Zogat , O.J.: J. Alloys Comp. 194 (1993) 47 Ueda, T., Hayashi, S., Hayamizu, K.: Solid State Commun. 87 (1993) 429

94Sl

Murata, K.: Thesis, Tohoku University, 1994 Raj, P., Suryanarayana,P., Sathyamoorthy, A., Shashikala,K., Iyer, R.M., Dhar, S.K., Gupta, L.C., Sahni, V.C., Begum, R.J.: J. Alloys Comp. 206 (1994) 47. Stedman,N.J., Cheetham,A.K., Battle, P.D.: J. Mater. Chem. 4 (1994) 64 1

95Ml 95Sl

Misawa, S.: Physica B 211 (1995) 158 Seeger,M., Kronmtiller, H., Blythe, H.J.: J. Magn. Magn. Mater. 139 (1995) 312

94Ml 94Rl

Landolt-Biirnstein New Series 111/32A

286

1.4.1 3d elementswith Zr, Nb, MO or Hf, Ta, W, Re

[Ref. p. 330

1.4 Alloys and compounds of 3d elements with 4d or 5d elements 1.4.1 3d elements with Zr, Nb, MO or Hf, Ta, W, Re 1.4.1.1 Introduction Magnetic properties of alloys and compounds of 3d elements and 4d or 5d elements, mainly reported in the last decade, are presented. Most of studies are concentrated on the inter-metallic compounds. Among them, the Laves phase compound, AB,, and their pseudo-binary systems have been extensively investigated. Laves phases are classified into three structure types: (i) Cl5 (cubic, MgCu,-type), (ii) Cl4 (hexagonal, MgZn,-type) and (iii) C36 (hexagonal, MgNi,-type). Crystal structure and magnetic properties of the Laves phase compounds of 3d and 4d or 5d elements are summarized in Table 1. Details of the magnetic properties have been described in the last edition of this series (LB III/19A, subsect. 1.4.1). During the last decade, considerable progress has been made in computational physics. The band calculations have been performed for a lot of intermetallic compounds and their magnetism is discussed on the basis of the electronic structure. In the present edition, the density of states (DOS) and the total energy of the Laves phasecompounds are compiled. Another recent progress in the present field is the application of various new experimental techniques to the intermetallic compounds, such as perturbed angular correlation technique (PAC) and muon spin relaxation (pSR). These data are also collected in this section. Table 1. Crystal structure [90Ml] and magnetism of the Laves phase AB, compounds. S: superconductivity; F: ferromagnetism; AF: antiferromagnetism; P: paramagnetism. A/I3

V

Cr

Mn

Fe

co

Zr

Cl5 S Cl5 S

Cl4 P Cl4

Nb

c15, Cl4 P c15, Cl4 P c15, Cl4

Ta

c15, Cl4

Cl5 F c15, Cl4 F Cl4 P, AF Cl4 P Cl4 Cl4

Cl5 P Cl5 P Cl5 P Cl5 P

Hf

MO W

Cl4 Cl4 P

1.4.1.2 Ti and V alloys and compounds No data of Ti alloys and compounds have been reported after the publication of the last edition (LB 111/19A)of this series. The compounds V,Zr and V,Hf show superconductivity below 8 K. These compounds also undergo a structural transformation at around 100 K. The magnetic properties of V,Zr and V,Hf have been reported in a normal state as well as in a superconducting state.

Land&-Bmntein New Series 111132A

Ref. p. 3301

1.4.1 3d elementswith Zr, Nb, MO or Hf, Ta, W, Re

287

Survey

V,Zr

V,Hf V2Zro.5Hfo.5

Properties

Fig.

X&T) Xnl(T)>cpm Y Mm 3: @D 49 n(E) Avon Y>@n

1 293 4 5 6 4 7

XdT)

Table

Ref. 84Sl 84Kl 85S1 8OJl 83K1 85S1 89D1

2 2 3 2

Table 2. Superconducting transition temperature T,, electronic specific heat coefficient y and the Debye temperature Bn, of various V,Zr samplesand a V,Hf [84Kl], [85Sl]. The samples Sl-S4 were prepared in a levitation crusible, followed by annealing at 1200 “C for 120 h. Sl, S2 and S4 were taken from different sites of the same ingot, S3 from a different ingot [84Kl]. The samples Al-A4 were prepared by argon arc-melting. Al and A2 were as-castsamples,while A3 and A4 were annealed at 1000 “C for 15 h [85Sl]. For Sl-S4, T, of the rhombohedral phaseis listed.

Sample

T, WI

y [mJ K-*mol-‘1

0, Kl

Ref.

V,Zr V,Zr V,Zr V,Zr V,Zr V,Zr V,Zr V,Hf

8.0 8.0 7.7 8.0 7.81 7.82 7.00 8.23

56.7 53.4 48.6 51.0 42.0 40.5 39.0 60.6

189 195 203 195 257 279 279 214

84K1 84Kl 84Kl 84Kl 85Sl 85Sl 85S1 85S1

(Sl) (S2) (S3) (S4) (Al) (A2) (A3) (A4)

Table 3. Fermi energy EF (Ry), DOS, both total, n,,, and, decomposed by site c1 and angular

momentum I, n; (states/unit cell Ry) of the Laves phase compounds containing Zr. The calculation was performed by using the APW method [83Kl]. a ntot

Zr V,Zr

0.6010 V Zr

Fe,Zr

0.6281 0.6577 co

Land&-Bbmstein New Series 111132A

14.75

.29.62

1.022

46.13

2.219 0.9411

18.40 1.487

111.8 25.03

1.057 0.4799

133.5 27.94

0.1551 1.282

8.939 0.7235

265.5 7.822

0.8295 0.3343

275.4 10.16

0.4979

4.580

57.39

0.1647

62.63

321.2

Fe Zr Co,Zr

0.7403 222.1

78.99

[Ref. p. 330

1.4.1 3d elementswith Zr, Nb, MO or Hf, Ta, W, Re

288

.f$ q! 5.50 5.25

5.00 s 4.15

4.50 4.25

Lrn ..--

0

200

400

600 I-

800 1000 1200K 1400

Fig. 1. Temperature dependence of the magnetic susceptibility of V,Zr up to 1300 K [84SI].

225 $l

lan

0

50

100

150

200

259 K 300

Fig. 2. Temperature dependence of the magnetic susceptibility of V,Zr for various kinds of samples labelled as Sl to S3 [84KI]. Detailed explanations on samplesare given in Table 2.

/ V2Zr !

Fig. 3. Low-temperature specific heat of several V,Zr samplesplotted as C,,lT vs. T* [84Kl]. Details of the samplesare described in Table 2. For all the samples, two distinct superconducting transitions are observed. The higher transition temperature originates in the cubic (ClS) phase, while the lower one in the rhombohedral phase. Solid lines are tits of the normal-state data by the following equation, C,, = yT + /?T’ + aTS, and dashed lines are guides to the eye.

Landolr-Barnstein New Series 1IV32A

Lef. p. 3301

1.4.1 3d elements with Zr, Nb, MO or Hf, Ta, W, Re

289

Fig. 4. Magnetic hysteresis curves of spherical V,Zr (a) and V,Hf (b) samples at 4.2 K. (1) As-cast V,Zr, 50 kOe 60 HWI -

Landolt-Biirnstein New Series 111132A

(2) V,Zr annealed at 1000 “C for 4 h, (3) as-cast V,Hf, (4) V,Hf annealed at 1000 “C for 15 h [85Sl].

1.4.1 3d elementswith Zr, Nb, MO or Hf, Ta, W, Re

states iiiimmy

[Ref. p. 330

V,Zr

350'

300

250

I 200 G c 150

100

50

0

Fig. 5. Total DOS of V,Zr calculated by using the LMTO method [8OJl].

Land&Barnstein New Series lW32A

Ref. p. 3301

1.4.1 3d elementswith Zr, Nb, MO or Hf, Ta, W, Re

I

2000 20Id-

VP

Oj

I 5 e

_ '0 VS 0 100-

,

Fig. 6. Total and partial DOS of V,Zr calculated by using the APW method [83Kl].

Landolt-B6rnstein New Series IW32A

291

292

1.4.1 3d elementswith Zr, Nb, MO or Hf, Ta, W, Re

0

50

loo

150

200

3 250 K 301

[Ref. p. 330

Fig. 7. Temperature dependenceof the magnetic susceptibility of V,Zr, 5Hf05 [89Dl].

1.4.1.3 Cr alloys and compounds The magnetic properties of Cr alloys have been investigated from the viewpoint of itinerant electron antiferromagnetism. The coexistence of an SDW state with a superconducting state was found in the Cr-Re system. The band calculations were performed for the intermetallic compounds Cr,Zr and Cr,Hf, Survey

Cr,Zr Cr,Nb (Cr,-,ALJJr (Cr,_,Al,)zHf Cr,-,Mo, Cr,-JeX

Table

Ref.

Composition

Properties

Fig.

x I 0.6 x IO.6 OIx10.174 x 5 0.005

total energy total energy x,(x) x*(x) a(T), B(T), q(0) CLvl3,c,,m

8 8 9 9 10, 11, 12 13

88A1 88A1 8482 8432 86Vl 93Bl

14 15 16, I7 18

85Nl 83Nl 84Tl 84Kl

c44

0 I x IO.4 x = 0.3 0.26 I x 5 0.3 0.06 IX IO.3 x = 0.26

(T),

cdlr)

TEWYTN(X) X&T) CpVl ‘*‘Re and ‘*‘Re NMR T,(T)

19

4

85Nl

Land&-Bdmrtein New Series 11113tA

292

1.4.1 3d elementswith Zr, Nb, MO or Hf, Ta, W, Re

0

50

loo

150

200

3 250 K 301

[Ref. p. 330

Fig. 7. Temperature dependenceof the magnetic susceptibility of V,Zr, 5Hf05 [89Dl].

1.4.1.3 Cr alloys and compounds The magnetic properties of Cr alloys have been investigated from the viewpoint of itinerant electron antiferromagnetism. The coexistence of an SDW state with a superconducting state was found in the Cr-Re system. The band calculations were performed for the intermetallic compounds Cr,Zr and Cr,Hf, Survey

Cr,Zr Cr,Nb (Cr,-,ALJJr (Cr,_,Al,)zHf Cr,-,Mo, Cr,-JeX

Table

Ref.

Composition

Properties

Fig.

x I 0.6 x IO.6 OIx10.174 x 5 0.005

total energy total energy x,(x) x*(x) a(T), B(T), q(0) CLvl3,c,,m

8 8 9 9 10, 11, 12 13

88A1 88A1 8482 8432 86Vl 93Bl

14 15 16, I7 18

85Nl 83Nl 84Tl 84Kl

c44

0 I x IO.4 x = 0.3 0.26 I x 5 0.3 0.06 IX IO.3 x = 0.26

(T),

cdlr)

TEWYTN(X) X&T) CpVl ‘*‘Re and ‘*‘Re NMR T,(T)

19

4

85Nl

Land&-Bdmrtein New Series 11113tA

Ref. p. 3301

1.4.1 3d elementswith Zr, Nb, MO or Hf, Ta, W, Re

293

Table 4. Thermodynamical properties of superconducting Crr-,Re, alloys [84Tl]. y: electronic specific heat coefficient, @,: Debye temperature, H,(O): critical magnetic field at 0 K, T,: superconducting transition temperature, d(O)lk,T,: gap parameterat 0 K. H,(O)

X

0.26 0.30

[rnJ K-2mol-‘]

z]

Pel

21

5.50 5.68

469 448

526 729

2.40 3.35

40)/k, T, 1.81 1.71

Cr, Zr

Cr, Nb

I

I

I

I

I

6.8

6.9

7.0

7.1

7.2

A 7

a-

Fig. 8. Total energy of Cr,Zr and Cr,Nb as functions of lattice constant for the nonmagnetic (P) and antiferromagnetic (AF) states in the Cl5 and Cl4 struc-

I

I

I

I

7.0

7.1

7.2

7.3

a-

I

7.4 A

i

tures [SSAl]. The LMTO method was used for the calculations. The vertical lines represent the experimental values of the lattice constant.

Fig. 9. Composition dependence of the magnetic susceptibility of (Cr,-,Al,),Zr and (Cr,,Al,),Hf with the Cl4 structure [8482]. For both series, the susceptibility is independent of temperature between 4.2 K and 300 K. k,M

0.1

Landolt-Blirnstein New Series IW32A

0.2

0.3 x-

0.4

0.5

0.6

0.7

[Ref. p. 330

1.4.1 3d elementswith Zr, Nb, MO or Hf, Ta, W, Re

294

10.0 *lo-6

K-1 I 7.5

~ 5.0 2.5

2.5

0

100

MO

300

l-

400 K 500

0

100

200

300

400 K 500

300

400

T-

2.5 1

0

I

100

I

I

200

I

300

t-

-

1

400 K

500

10.0 40-6

0

100

200 T-

K 500

.@ K-1 6

K-’

7.5

/

x =0.1740

t 5.0 I 2.5

0

50

100

150

200

250 K 300

l-

Fig. 10. Temperature dependence of the thermal expansion coefficient a of Cr,_,Mo, alloys [86Vl].

0

50

100 l-

150

200 K 250

The arrows indicate the NCel temperature TN. The dashedline representsa of paramagneticCr+Sat%V.

Land&-BBrnrtein New Series W32A

Ref. p. 3301

1.4.1 3d elements with Zr, Nb, MO or Hf, Ta, W, Re

295

234 GPa

194 0

100

200 T-

300

400

K 500

226 GPa

0

100

200

300

400

K 500

T-

2251 GPa

221 I *

216 211 206 0

213

100

200 T-

300

400

K 500

209 0

100

200

300

400 K

500

100

200

300

400 K

500

219 GPa 217 t 209 Q

215

206

213

--”

0

100

200

300

400 K 500

T-

Fig. 11. Temperature variation of the bulk modulus B of Cr,,Mo, alloys [86Vl]. The chain line represents

Land&-Bbmstein New Series III132A

211 0

T-

the paramagneticbehavior. The arrows indicate r,.

1.4.1 3d elementswith Zr, Nb, MO or Hf, Ta, W, Re

296

0Cr

0.05

010

0.15

0.20

0.25

[Ref. p. 330

Fig. 12. Composition dependenceof the spontaneous volume magnetostriction at 0 K, w, (0), of Cr,-,Mo, alloys [86VI].

x-

csow-p TIC

IUJ .

l%& 0:.z \ ‘\ \ 1d’p*. 102. .\

.. pN%

330 LISOW

mow

r,,

I 3

TN

‘%.

l

\ ;.

101

LISOW

l

*;a\,

:r.

Tsf

‘\.

TISOW f

‘,

l

_

‘. -9 . 300

. . 0. a,

8

270. 0

100

200 T-

300

400 K 500

991 0

I 100

I 200

b

I 300

I

I

400 K 500

I155

360

GPa

GPa LISOW

TISOW

a

csow

P

330

1 u’

--TIC

. . .

I’--

xn 0 0

100

200

300

400

P

1351

III

T-

Fig. 13. Temperature dependenceof elastic constants, cl,, cL. c44and (c,, - c,J2 of Cro,&eooa5P3Bll. In

0

d

I 100

'\ 200

300

500 K 500

T-

this concentration range, three magnetically ordered phasesappearwith increasing temperature, i.e., longi-

Land&-Barnstein New Series IW32A

Ref. p. 3301

1.4.1 3d elements with Zr, Nb, MO or Hf, Ta, W, Re

tudinal incommensurate SDW (LISDW), transverse incommensurate SDW (TISDW), commensurateSDW (CSDW). T,, is the transition temperature from LISDW to TISDW, Tic from TISDW to CSDW and

297

TNthe NCel temperature. The dashed curves represent the corresponding elasitc constants of the paramagnetic Cr,,,,V,,,, alloy.

2.32 -10-S @ 9

400 1.88 40-E gly 9

I 300 b-z=

I

2.26 x" 2.24

200 1.84

2.22

x" 100

olo Cr

1.82 l.BO 0.1

x-

0.2

0.3

0

0.4

Fig. 14. Composition dependence of the superconducting transition temperature r, and the Ntel temperature TNof Cr,,Re, alloys [85Nl].

50

100

150 T-

200

250

300 K 350

Fig. 15. Temperature dependence of the magnetic

susceptibility of Cr,,,,Re,,,,. Curve I: as-cast sample; 2: annealed at 1000 “C for one week [83Nl]. The sampleswere prepared in argon arc-melting.

14 mJ molK2 KZ 12 2

IO I ? e

1 8 6

a

I

I

6 4

0 x =0.26 H=5kOe

2

A x =0.30 H=lO kfle

00

5

IO

15

20

K* 25

T2-

Fig. 16. Low-temperature specific heat of Cr,,,,Re,,,, alloys in various magnetic fields and Cro.70Reo.30 plotted as Cp/T vs. T* [84Tl]. Straight lines are fits of the data by C, = yT + /3T3.

Land&-Biirnstein New Series IW32A

1.0

1.5

2.0

2.5 3.0 7,/T -

3.5

4.0

4.5

Fig. 17. Electronic specific heat C,, of Cr,,,,Re,,, in the superconducting state plotted against T,/T [84Tl]. The solid line is the fit of the data by the equation expectedfrom the BCS theory, C,,IyT, = 8.5 exp[-0.818 d(O)lkJ’j, where d(0) is the energy gap at 0 K.

298

1.4.1 3d elementswith Zr, Nb, MO or Hf, Ta, W, Re

1 =1.3 K

Cr0.74Rell.26

0

ooooo

00°

0

0

0

0

M0

$a

(m:fPI 100

0

0

I xi .s 4 c ’

H=3kUe

, co

I 50

80 0

0

I 60

I, 70

MHz

Y-

I 60. b-r : 40

0

T-

o”O”

0

2.5

b

[Ref. p. 330

5.0

7.5

10.0

3

4

K

12.5kOe15.0

H-

Fig. 18. a Spin echo NMR spectrum of lssRe and ‘*‘Re in Cr, ,,Re, 26at 1.3 K in the external magnetic field of 3 kOe [84Kl]. b Magnetic field dependence of the signal intensity at 40 MHz of Cr,,,Re,,,, at 1.3 K [84Kl]. A solid curve shows the field dependence of the electrical resistivity p [85Nl].

Fig. 19. Temperature dependenceof the nuclear spinlattice relaxation rate, l/T,, of ‘*‘Re and ‘*‘Re of Cr, ,,Re,,, [85Nl, 84Kl]. Open circles: measured in H = 2 kOe; closed circles: in H = 7 kOe. The arrow indicates the superconducting transition temperature r,. The solid line is the Korringa relation, T,T= const. The dashedcurve is the fit of the data by the equation

expectedfrom the BCStheory, l/T, = 459.exp[- 1.76TJT] (ms)-‘.

1.4.1.4 Mn alloys and compounds A few studies on the magnetic properties of Mn,Zr and related compounds have been reported. Survey

Mn,Zr Mn, ,,CoZr Mn2ZrodfO o2 Mn,Nb

Properties

Fig.

Ref.

n(E) total energy X,(T) PAC total energy

20 21 22

8511 88A1 74F1 90Fl 88Al

21

Landoh-Barnstein New Series lW32A

298

1.4.1 3d elementswith Zr, Nb, MO or Hf, Ta, W, Re

1 =1.3 K

Cr0.74Rell.26

0

ooooo

00°

0

0

0

0

M0

$a

(m:fPI 100

0

0

I xi .s 4 c ’

H=3kUe

, co

I 50

80 0

0

I 60

I, 70

MHz

Y-

I 60. b-r : 40

0

T-

o”O”

0

2.5

b

[Ref. p. 330

5.0

7.5

10.0

3

4

K

12.5kOe15.0

H-

Fig. 18. a Spin echo NMR spectrum of lssRe and ‘*‘Re in Cr, ,,Re, 26at 1.3 K in the external magnetic field of 3 kOe [84Kl]. b Magnetic field dependence of the signal intensity at 40 MHz of Cr,,,Re,,,, at 1.3 K [84Kl]. A solid curve shows the field dependence of the electrical resistivity p [85Nl].

Fig. 19. Temperature dependenceof the nuclear spinlattice relaxation rate, l/T,, of ‘*‘Re and ‘*‘Re of Cr, ,,Re,,, [85Nl, 84Kl]. Open circles: measured in H = 2 kOe; closed circles: in H = 7 kOe. The arrow indicates the superconducting transition temperature r,. The solid line is the Korringa relation, T,T= const. The dashedcurve is the fit of the data by the equation

expectedfrom the BCStheory, l/T, = 459.exp[- 1.76TJT] (ms)-‘.

1.4.1.4 Mn alloys and compounds A few studies on the magnetic properties of Mn,Zr and related compounds have been reported. Survey

Mn,Zr Mn, ,,CoZr Mn2ZrodfO o2 Mn,Nb

Properties

Fig.

Ref.

n(E) total energy X,(T) PAC total energy

20 21 22

8511 88A1 74F1 90Fl 88Al

21

Landoh-Barnstein New Series lW32A

Ref. p. 3301

I states

1.4.1 3d elementswith Zr, Nb, MO or Hf, Ta, W, Re

299

Mn,Zr

unity

600

500

400 1 4, 300 G

--------

d Mn(2a) d Mn(6h)

200

100

0 0.1

0.2

0.3

0.4

0.5

0.6 0.7 E-

0.8

0.9

1.0

1.1 1.2Ry 1.3

Fig. 20. Density of statesof Mn,Zr calculated by using the KKR method [8511]

Mn,Nb

7.2

a

7.5

[I-

Fig. 21. Total energy of Mn,Zr and Mn,Nb as functions of lattice constant for the nonmagnetic (P), ferromagnetic (F) and antiferromagnetic (AF) statesin the Cl5 and Cl4 structures [88Al]. The LMTO

Landolt-Btirnstein New Series 111/32A

6.7

6.8

6.9

7.0

a i

U-

method was used for the calculations. The vertical lines represent the experimental values of the lattice constant.

300

1.4.1 3d elementswith Zr, Nb, MO or Hf, Ta, W, Re

Fig. 22. Temperature dependence of the inverse magnetic susceptibility of Mn, ,,CoZr [74FI]. This compound forms the Cl 5 structure with a = 7.05 A. The inverse susceptibility obeys the Curie-Weiss law above 50 K with pefr= 3.2 pa1f.u. and O= -95 K.

3.

.*.=* 1 ,.a.*

/* -100

-50

I 0

I 50

I 100

r-

I 150

I

I

[Ref. p. 330

I

200 250 K 300

1.4.1.5 Fe alloys and compounds The Laves phase Fe compounds show a variety of magentism depending upon the species of the partner element. Fe,Zr and Fe,Hf are ferromagnetic. Antiferromagntism is observed in their pseudobinary systems. Temperature-induced magnetic transition between ferro- and antiferromagnetism states was found in Fe,Hf,..,Ta, and Fe,Zr,_,Nb,. Fe,Nb and Fe,Ta are considered as enhanced Pauli paramagnets.Recent NMR results suggestthat Fe,Nb is weakly antiferromagnetic. Off-stoichiometric Fez,xNb,_,is ferromagnetic for both x > 0 and x < 0. Survey

Composition Fe,Zr

Properties

Fig.

magnetization density 49 n(E) spin density total energy

23 24 25 26 27

b+Jb,-,

impurities PAC n(E) total energy -0.04 I x IO.04 a(T), o(H) x=0 ggghG&(H) -0.008 I x I 0.002 -0.04 Ix IO.04 T,(x), TN(X) x=0 WJ, T,(T) -0.02 I x IO qm,l Y x=0 4% total energy x=0

Ref. 92Wl

3

5 6

Pm Pzr Kyp of

Fe,Hf

Table

7

83Kl 85Ml 85Ml 88Al 92Wl 86Bl

28 27 29,30, 3 1 32,33 34

91Pl 8512 88Al 87Sl 9OYl 88Yl

35 36,37 38 39 27

88Yl 9OYl 9OWI 8511 88Al

8

Landolt-Barnstein New Series 111132A

300

1.4.1 3d elementswith Zr, Nb, MO or Hf, Ta, W, Re

Fig. 22. Temperature dependence of the inverse magnetic susceptibility of Mn, ,,CoZr [74FI]. This compound forms the Cl 5 structure with a = 7.05 A. The inverse susceptibility obeys the Curie-Weiss law above 50 K with pefr= 3.2 pa1f.u. and O= -95 K.

3.

.*.=* 1 ,.a.*

/* -100

-50

I 0

I 50

I 100

r-

I 150

I

I

[Ref. p. 330

I

200 250 K 300

1.4.1.5 Fe alloys and compounds The Laves phase Fe compounds show a variety of magentism depending upon the species of the partner element. Fe,Zr and Fe,Hf are ferromagnetic. Antiferromagntism is observed in their pseudobinary systems. Temperature-induced magnetic transition between ferro- and antiferromagnetism states was found in Fe,Hf,..,Ta, and Fe,Zr,_,Nb,. Fe,Nb and Fe,Ta are considered as enhanced Pauli paramagnets.Recent NMR results suggestthat Fe,Nb is weakly antiferromagnetic. Off-stoichiometric Fez,xNb,_,is ferromagnetic for both x > 0 and x < 0. Survey

Composition Fe,Zr

Properties

Fig.

magnetization density 49 n(E) spin density total energy

23 24 25 26 27

b+Jb,-,

impurities PAC n(E) total energy -0.04 I x IO.04 a(T), o(H) x=0 ggghG&(H) -0.008 I x I 0.002 -0.04 Ix IO.04 T,(x), TN(X) x=0 WJ, T,(T) -0.02 I x IO qm,l Y x=0 4% total energy x=0

Ref. 92Wl

3

5 6

Pm Pzr Kyp of

Fe,Hf

Table

7

83Kl 85Ml 85Ml 88Al 92Wl 86Bl

28 27 29,30, 3 1 32,33 34

91Pl 8512 88Al 87Sl 9OYl 88Yl

35 36,37 38 39 27

88Yl 9OYl 9OWI 8511 88Al

8

Landolt-Barnstein New Series 111132A

Ref. p. ]

1.4.1 3d elementswith Zr, Nb, MO or Hf, Ta, W, Re Composition

Table

Ref.

8

46

9OWl 8512 93Jl 8512 93Jl 8512 9121 90Dl 92Sl 9121 93Nl 79Ll 81A1 82Al

47 48,49

84Y1 84Yl

0 5 x 2 0.5

fix), @D,A(x) +U$ TN(X),

50 41,42 42 51 52 53 54 55 56 57,58

94Cl 9121 9121 86Kl 85Hl ’ 85Wl 93Wl 93Wl 93Wl 93Yl

x=0.1 0 2 x IO.4

&I a(T), x,(T)

59 60

Fe,Ta Fer-,Mo, Fe,Mo Fe,-,K Fe,W (Fe,-,Si,),Zr

Fe,Nb,,Mo, Fe,Ta,-,Ti,

Fig.

Y n(E)

0 Ix IO.08

Fatw n(E) 0 I x 5 0.04 Patw 4-Q 0 I x IO.2 4x), dx) O<xIO.17 Hhyp,Is, e*qQ O<xIO.17 f&v IS 0 5 x 5 0.2 4x), 44 57FeME 0 I x IO.825 0.01 I: x I 0.25 PAC x=0.1 PAC x = 0.5 PAC, Olxll

(Fe,-,Si,),Hf (FeI-,A1J2Hf Fe,Hf,,Ta,

Property

301

x = 0.85, x = 0.95 x = 0.9 OIx10.13 01x10.17 x = 0.2 x=0.1 x = 0.2 x = 0.2 0.1 1x50.7 Olxll

Hh,,U4 vs. P T,(X)? TN(X) PFe

(0,

Tl(T)

PSR 4x>, 4x) a,(x) ANI T,(P) Too3Lr,(P) C*(T) p(r)

40 40 41,42 43 44 41,42 45

7 7

85Yl 88Wl

Table 5. Magnetic moments in pB of individual atoms in Fe,Zr estimated either from experiments or calculations. The experimental values were obtained by polarized neutron diffraction measurements [92Wl]. The calculations were performed by ASW [85Ml], LMTO [88Al] and the tight-binding approximation (TBA) [86Yl]. Atom

Experiments

ASW

TBA

LMTO

Fe Zr

2.1 l(3) - 0.32(5)

1.90 - 0.56

1.87 - 0.53

1.81

Ref.

[92Wl]

[85Ml]

[86Yl]

[88Al]

Land&-Bornstein New Series III/32A

302

1.4.1 3d elementswith Zr, Nb, MO or Hf, Ta, W, Re

[Ref. p. 330

Table 6. Hyperfine fields at impurity ions in Fe,Zr estimated by nuclear orientation experiments

[86Bl]. Impurity

Hbyp We1

SC

53 25 215 215 126

v Cr Mn co

Table 7. Hyperfine field at ‘*‘Ta of various compounds measured by y-y time differential perturbed angular correlations (PAC).

Fe,Hf Fe2Zrodfo ol Fe2Zro8fo l Fe2ZroW. 5 Fe0 &o. J2Hf (Fe, aCooJ2Hf

Ref.

TKI

IHb,,(Wl WeI

300 293 300 78 300 300 300

144 63, 92”) 63.8 61.2 65 74, 23b) 16

91P1 79L1 81Al 81Al 82Al 91P1 9lPl

‘) Two kinds of Hhypwere observed.The lower Hhypis dominant. b, Two kinds of Hhypwere observed.The higher Hhypis dominant. Table 8. Electronic specific heat coefficient of Fe,+,Nb,+ and Fe,Ta. yo: experimental value [9OWl];

y-,: estimated from DOS [85Il, 85121;a: enhancementfactor defined as ~~;xl~~‘ca,.

Fe2 ooNb, o.

Fe, J% o1 Fe, 98NbI.02 Fe,Ta

a

Y

YCd

[EJ K-‘mol-‘1

[mJ K-*mole’1

43 46 48 48

9.1

4.7

9.1

5.3

Land&-Barnstein New Series 111fl2A

1.4.1 3d elements with Zr, Nb, MO or Hf, Ta, W, Ke

Ref. p. 3301

Fe2Zr :

‘---sy;,) \(’ t / -’ \ \f\ ,-J \, /‘\J l-1 I I-d ‘1 -0 \’ t0 . ..\-----d/. *. . .

‘I . 0.

:

‘\\

‘\\//

/

f

.. :*. ..... ,...*

*. :’

(110) 1 / I/ -1

)

.

*...

jUj

\

. .

Fig. 23. Magnetization density in the (1 IO) plane of Fe,Zr determined by polarized neutron diffraction measurementsfor a single crystal [92Wl]. Solid lines: positive contours at 0.5 pB A-’ intervals; dashed lines: negative contours at 0.02 pa Am3intervals; the zero contour is dotted.

Landott-B6mstein New Series II1/32A

1.4.1 3d elements with Zr, Nb, MO or Hf, Ta, W, Re

[Ref. p. 330

50 -

10 Zr P 0.

I

10 zr s 0

0.1

--

:

I

0.2

0.3

0.4 E-

n

1

I

0.5

0.6

0.7 Ry 0.6

Fig. 24. Total and partial DOS of paramagneticFe,Zr calculated by using the APW method [83Kl].

Landolt-Bbmsrein New Series 111132A

Ref. p. 3301

305

1.4.1 3d elements with Zr, Nb, MO or Hf, Ta, W, Re

, 2001

-I

sties unit cell Ry spin

FezZr

175-

150-

125-

100-

Fe d

75 -

50-

I

25 -

G; -4 loo-

0 Fe

----

[85Ml].

2r d 50-

25 -

-0.4 9

-0.2Ir t-tF

0I -

0.2 I

I 0.4 R:Y (

Fig. 25. d-electron DOS for spin-up (t) and spindown (1) electrons of ferromagnetic Fe,Zr calculated by using the ASW method [85Ml].

Landolt-BWnstein New Series IIV32A

1.5 1.0 Fe-B distance -

2.0

A 2.5 Zr

Fig. 26. Spherical averageof the spin density of Fe,Zr

75 -

-00.8 I -0.6I

0.5

306

1.4.1 3d elementswith Zr, Nb, MO or Hf, Ta, W, Re

, Fe,Zr

[Ref. p. 330

Fe,Nb

I

I

I

I

6.8

6.9

7.0

7.1

I

7.2 A 7.3

6.5

I

I

I

I

6.6

6.7

6.8

6.9

I

7.0 A :

Cl-

'\.-.,a' ClSF I

I

I

I

Ej.8

6.9

7.0

7.1

0-

I

7.2 %

Fig. 27. Total energy of Fe,Zr, Fe,Nb and Fe,Hf as functions of lattice constant for the nonmagnetic (P), ferromagnetic (F) and antiferromagnetic (AF) states in the Cl5 and Cl4 structures [88Al]. The LMTO method was used for the calculations. The vertical lines represent the experimental values of the lattice constant.

Landolt-Barnsrein New Series 111132A

307

1.4.1 3d elements with Zr, Nb, MO or Hf, Ta, W, Re

Ref. p. 3301 700, states

iiiimny

FezHf

600~

500-

400 -

I G; 300-

- tot01

I.

c

---

d Fe(6h) d FelZa)

------

200 -

100 -

0, 0.1

05

0.7

0.6

0.8

0.9

1.1

1.0

1.2 Ry 1.3

E-

Fig. 28. Density of states of paramagnetic Fe,Hf calculated by using the KKR method [8512]. 2.0 Y 1.6

I 1.2

b 0.8

0

I

I IO

30

20

40

50

T-

Fig. 29. Temperature dependence of the magnetization of stoichiometric Fe,Nb [87SI].

Land&-BWnstein New Series IIV32A

10.0

K 60 HOPPl

12.5 kOe 15.0

-

Fig. 30. Magnetization curves of stoichiometric Fe,Nb at various temperatures[87S I].

308

I

“b

1.4.1 3d elements with Zr, Nb, MO or Hf, Ta, W, Re

[Ref. p. 330

16

I “b

12

a

0

2.5

5.0

7.5

10.0

12.5 403 g/d

$ cm3

I

I Fe,Nb

3

2

1

b

Fig. 31. b vs. H/a plots of Fe2+xNb,-x at 4.2 K [87Sl]. a x= 0 and -0.04, b x=0.04. The results indicate that stoichometric Fe,Nb has no spontaneous 10

0

17.5

H/o- -

a

MO3 g/cm3 5

H/u -

magnetization, while the off-stoichiometric compounds in both Fe-rich (x > 0) and Nb-rich (x < 0) regions are ferromagnetic.

I

Hopp,= 9.7kOe

o~oooooo

B

10

15

HOPPl 0

100

200

300

400

500

600 K 700

l-

20

(kOe)* 30

-

Fig. 33. Magnetic field dependenceof the temperature Tmax of the magnetic susceptibility maximum of Fe,Nb [9OYI].

Fig. 32. Temperature dependence of the inverse magnetic

susceptibility

of Fe,Nb at 9.7 kOe [9OY I].

Land&-Bcmstein New Series 111132A

1.4.1 3d elementswith Zr, Nb, MO or Hf, Ta, W, Re

Ref. p. 3301

3” I KI Fe,+,Nb,-, I I

nn v=lOMHz 1=4.2K

Fez+, Nbl-,

K=O

$

309 I

I

/I

60

--k

I 45 k 30

oJn \

-1.045 -0.030 -0.015

Fe?Nb 0.015

0.030 0.045

xFig. 35. Proposed magnetic phase diagram of Fe,,Nb,,. Open circles: r, [87Sl]; closed circles: TN [88Yl].

-0.006 . =-e-r’

-0.008 8

9

I 10 11 HOPPl -

12 kOe

Fig. 34. g3NbNMR spin-echo spectra of Fe,+,Nb,-, at

4.2 K [88Yl]. The arrows indicate the position for Knight shift K = 0.

Land&-BBmstein New Series III132A

1.4.1 3d elementswith Zr, Nb, MO or Hf, Ta, W, Re

310

[Ref. p. 330

-6 Fig. 36. Knight shift K of 93Nbvs. magnetic susceptibility x,,, plots of Fe,Nb [9OYI].

-7 Xm

-

10.0 l/SK

7.5 > :

5.0 2.5

0

10

20

30

K

10

I15.0 l/sK 25

12.5

0

0

10 T-

20

30

K

Co

10

r-

20

30

K

CO

Fig. 37. Temperature dependenceof the nuclear spinlattice relaxation rate, l/T,, of 93Nb of Fe,Nb with various resonance frequencies [9OYl]. T,r and r,s indicate the longest and shortest components of T,, respectively. Both r,, and T,, show a peak at around 15 K, when the frequency is fixed at 3 and 4 MHz, while no peak is observed at 10 MHz. These results suggest the phase transition takes place under low magnetic fields (3...4 kOe) and is suppressedby high magnetic fields (= 10 kOe).

Ref. p. 3301

1.4.1 3d elements with Zr, Nb, MO or Hf, Ta, W, Re

46

Fig. 38. Low-temperature specific heat of Fe2+,Nbl-, plotted as CJTvs. T* [9OWl].

tot01 ............ d Nb

l 1

c

--------

d Fe(20) d Fe(6h)

100

200_: 0

7 0.1

Land&-BWnstein New Series 111132A

0.2

‘6.3

d 7

0.8

0.9

1.0

1.1Ry 1.2

Fig. 39. Density of statesof Fe,Nb calculated by using the KKR method [8511].

312

1.4.1 3d elementswith Zr, Nb, MO or Hf, Ta, W, Re

I

T=5K

[Ref. p. 330

I

2.15

I 1:

2.10 2.05

O 7.06

2.00

7.04 -415

1.95,

te

0.02

0.04 x-

0.06

0.08

0.10

7.02 7.000

Fig. 40. Composition dependence of the average atomic moment of Fe-MO and Fe-W alloys at 5 K [93Jl].

0

0.04

0.08

x-

phose

mixed phases 0.04

0.08

x-

OS2

0.16

0.20

Fig. 41. Composition dependence of the lattice parameter a of (Fe,-,Si,),Zr, (Fe,-,Al,),Zr and (Fe,-,Si,),Hf systems with the Cl5 structure [9lZl]. For (Fe,-,Si,),Hf, mixed phaseswith the Cl4 and Cl5 structures were obtained for 0 I x IO.03.

Fig. 42. Composition dependence of the saturation magnetization, q, of (Fe,-,Si,),Zr, (Fe,-,Al,),Zr, (Fe,-,Si,),Hf and (Fe,-,Al,),Hf systems at room temperature[9 IZ I]. al2

066

0.20

Landolt-B6rnstein New Series lW32A

1.4.1 3d elementswith Zr, Nb, MO or Hf, Ta, W, Re

Ref. p. 3301 240~

I

I

koe 1Fe,-,Si,);, Zr 220”

I IA

I A

313

I

T=4.2 K I

v

140 a

0.1 mm -i0

-0.2 FezZr 0.025 0.050 0.075 0.100 0.125 0.150 0175 x-

Lmdolt-BBmstein New Series 111132A

Fig. 43. Composition dependenceof 57FeMijssbauer parametersof (Fe,,Si,),Zr with the Cl5 structure at 4.2 K [90Dl]. a Hypertine field HhYPat Fe nuclei. b Electric quadrupole splitting, e*qQ/2. c Isomer shift, 18, relative to aFe. Mossbauer spectra were analyzed by assuming three Fe sites. Site I: Fe surrounded by only Fe atoms with B= 0’; site II: Fe surrounded by only Fe atoms with B= 70.3’; site III: Fe with at least one Si atom in the nearest neighbor. Here, B is an angle between the hyperfine field and [ 11l] direction.

94 r

I

I

kOe _

Fe,Zr,-, Hf,

92 ::

1=293K

0

66 -2 + 61

zoo

--ia 2

kOe 175

62

L 150 P

60

t

[Ref. p. 330

1.4.1 3d elements with Zr, Nb, MO or Hf, Ta, W, Re

314

125

0.05

010

0.15

0.20

0.25

0.30

x-

1OU

Fe,Zr 0.025 0.050 0.015 0.100 0.125 0.150 0.175

x-

Fig. 44. Composition dependenceof “Fe M&batter parametersof (Fe,-,Si,),Zr with the Cl5 structure at room temperature [92Sl]: Isomer shift IS, relative to aFe, and average hyperfine field H,,Yp,at Fe nuclei. Mossbauer spectra were analyzed by assuming six Fe sites with different local environments.

Fig. 45. Composition dependenceof hyperfine fields at ‘*‘Ta of Fe,Zr,..,Hf, measured by y-y time differential perturbed angular correlations (PAC) at 293 K [79Ll]. Two kinds of hypertine tields were found for each compound. The lower field (H,)is due to the Hf sites without Hf atoms in the nearest neighbor (nn), while the higher one (I&) to the Hf sites with one Hf atom in nn.

90 kOe

65 60 0

20

40

60

80 kbor 100

P-

Fig. 46. Pressuredependenceof the hyperfine field at “‘Ta of Fe,Zr, sHfo5measuredby y-y time differential perturbed angular correlations (PAC) at 300 K [82Al].

Fi,Zr

0.2

0.4 x-

0.6

0.8

Fe,Nb

Fig. 47. Magnetic phase diagram of Fe,Zr,-,Nb, [84Yl]. Closed circles: Tc; open circles: TN.

Land&-Barnstein New Series IlV32A

Ref. p. 3301

.

1.4.1 3d elementswith Zr, Nb, MO or Hf, Ta, W, Re

,)

0

. .

‘0

. .

.

0 l .I .

0

20

x = 0.95 0.85

0

l %..

40

60

c

80

-

l&L0

100 K 120

T-

Fig. 48. Temperature dependence of the magnetization per Fe atom of Fe,Zr,+Nb, estimated from the g3NbNMR studies [84Y I].

Landolt-BSmstein New Series IW32A

40

80

T-

120

160

200 K 240

Fig. 49. Temperature dependenceof the nuclear spinlattice relaxation rate l/T, of g3Nb of Fe,Zr,,,,Nb,,,, measuredat 10 MHz [84Y 11.The solid line represents the calculated results based on the self-consistent renormalization theory of spin fluctuations.

[Ref. p. 330

1.4.1 3d elements with Zr, Nb, MO or Hf, Ta, W, Re

316 0.25

1=90K 0.20

0.20

I 0.15 r E

1 0.15 i? ?i E

;O.lC ZL

E 0.10 3.

0.05

[

2.5

7.5

5.0

1

12.5ps 15.0

0

i

5uS

1

0.25

0.25

0.2[

t F0.15 3O.U a a 0.05

[

2.5

5.0

I-

7.5

10.0

12.5JIS 1

Fig. 50. pSR spectra of Fe,Zr, ,Nb,, at various temoeratures in zero field Ilower curve) and in the

0

2.5

5.0

t-

7.5

10.0

125 ps 1

longitudinal field of 100 Oe (upper curve) [94Cl]. Solid curves representthe calculated results.

Landolt-Bbmstcin New Series W32A

1.4.1 3d elements with Zr, Nb, MO or Hf, Ta, W, Re

Ref. p. 3301

317

5 ~1cr3 4

3 I s Q2 100

I

I

I

1

0

100

50

150

200

250

300 kOe350

I

I

I

I

I

0

5

10

15

20

n-

Hoppl-

Fig. 51. Longitudinal magnetostriction at various temperatures for Fe,Hf,,,T%,, [86Kl].

-

I

I

25 kbor 30

Fig. 52. Magnetic phase diagram (T-p diagram) of

Fe2Hfo.9Ta.l WHll.

0

100

200

300

K

1

T-

O

5

IO

15

20

25 kbar 30

P-

Fig. 53. Pressure dependence of the magnetic transition temperatures of Fe,Hf,,,Ta,,, [85Wl]. &: NCel temperature; TO: ferromagnetic to antiferromagnetic transition temperature.

Landolt-BOrnstein New Series II1/32A

Fig. 54. Specific heat curve of Fe,Hf,,,Ta,,, [93Wl]. The solid curve representsthe paramagneticpart of C, with y= 24 mJ K-* mol-’ and @n= 355 K.

1.4.1 3d elementswith Zr, Nb, MO or Hf, Ta, W, Re

a

0

50

100

T-

150

200

250 K 300

0

50

100

150

b

Fig. 55. Temperature dependenceof the electrical resistivity of Fe,Hf,-,Ta, [93Wl]. a x= 0.1, 0.3, 0.5

[Ref. p. 330

200

250 K 300

T-

and 0.7; b x = 0.2, normalized by the electrical resistivity at 295 K.

400 K 20

1 360

.

.

.

@ 30'

, 320

.

.

l .

20 .

280 b Fe,HF

.

0.2

0.4 x-

0.6

0.8

FeJo

0.8

Ferlo

lOa*

oea

Fe,Hf

0.2

0.k x-

0.6

0.8

Fe,10

1

T

.

I

.

.

1 t- OILY. b2H1

Fig. 56. Composition dependence of the thermal and transport properties of Fe,Hf,-,Ta, [93Wl]. a Electronic specific heat coefficient z b Debyetem-

__ 0.2

-

Il.4

x-

0.6

perature 0,; c coefficient of the T*-term of the electrical resistivity A.

Land&-B6mstein New Seriu 111132A

Ref. p. 3301

1.4.1 3d elements with Zr, Nb, MO or Hf, Ta, W, Re

319

35 w3 & mol

0

50

100

a

150

200

250 K 300

T-

0

50

b

Fig. 57. Temperature dependence of the magnetic susceptibility a and the inverse susceptibility b of

100

150 T-

200

250 K 300

(Fe,,AI,),Nb [93Yl]. The arrows indicate the NCel temperaturer,.

;; (Fe,:,d~x)2N6~

-1.2 1 0

I 40

I 80

I 120

160 K

1 200

TFe;Nb

0.1

0.2 x-

0.3

0.4

0.5

Fig. 58. Magnetic phase diagram of (Fe,,Al,),Nb [93Y 11.Closed circles: Tc; open circles: r,.

Land&-Bbmstein New Series 111132A

Fig. 59. Temperature dependenceof the Knight shift of g3Nb,K, of Fe,Nb,,,Mo,,, [85Yl].

320

1.4.1 3d elementswith Zr, Nb, MO or Hf, Ta, W, Re

[Ref. p. 330

5 n3 -

Fe,Ta,-,li, 1

I

I b

Fig. 60. Temperaturedependence of the magnetization and the inverse magnetic susceptibility of Fe,Ta,-,Ti, at Harp, = 13kOe [88Wl].

1.4.1.6 Co alloys and compounds In Co-Zr and Co-Hf systems, several Co-rich compounds were found to be ferromagnets with high Curie temperatures. The (Co,Fe,J,Hf compounds with 0.65 < x 5 0.75 show itinerant electron metamagnetismat high fields. Survey Composition

Properties

Co,Zr

P(T),w-k

WJr2

40 total energy a, b, c, Tc, 0

Co,,-,M,Zr (M = Fe, Ni) Co, ,-,Fe,Zr Co,Hf Co,Hf (CoxFeI-x)2Hf

Co,Nb

Y

Fig.

Table

Ref.

61,62 63 64

9 3

9382 83Kl 88Al 9OCl 93Pl

10

0 I y 14.2

T(Y)> a,(Y)

65

0 I y IO.9

P,(H), P,(T) Pm, WI, Y a, b, c, Tc, 0

66,67 61362

PFc-Co

68,

0 5 x I 0.8 Olxll 0 Ix 5 0.4

tx),

a(H)

9 10

69

T,(x), p(Tj,s(T) 70, 71, 72 PAC total energy 64

7

91Bl 93B2 9OCl 88Sl 92Gl 91Pl 88Al

Land&-Bbrnstein New Series IIKZA

320

1.4.1 3d elementswith Zr, Nb, MO or Hf, Ta, W, Re

[Ref. p. 330

5 n3 -

Fe,Ta,-,li, 1

I

I b

Fig. 60. Temperaturedependence of the magnetization and the inverse magnetic susceptibility of Fe,Ta,-,Ti, at Harp, = 13kOe [88Wl].

1.4.1.6 Co alloys and compounds In Co-Zr and Co-Hf systems, several Co-rich compounds were found to be ferromagnets with high Curie temperatures. The (Co,Fe,J,Hf compounds with 0.65 < x 5 0.75 show itinerant electron metamagnetismat high fields. Survey Composition

Properties

Co,Zr

P(T),w-k

WJr2

40 total energy a, b, c, Tc, 0

Co,,-,M,Zr (M = Fe, Ni) Co, ,-,Fe,Zr Co,Hf Co,Hf (CoxFeI-x)2Hf

Co,Nb

Y

Fig.

Table

Ref.

61,62 63 64

9 3

9382 83Kl 88Al 9OCl 93Pl

10

0 I y 14.2

T(Y)> a,(Y)

65

0 I y IO.9

P,(H), P,(T) Pm, WI, Y a, b, c, Tc, 0

66,67 61362

PFc-Co

68,

0 5 x I 0.8 Olxll 0 Ix 5 0.4

tx),

a(H)

9 10

69

T,(x), p(Tj,s(T) 70, 71, 72 PAC total energy 64

7

91Bl 93B2 9OCl 88Sl 92Gl 91Pl 88Al

Land&-Bbrnstein New Series IIKZA

Ref. p. 3301

1.4.1 3d elementswith Zr, Nb, MO or Hf, Ta, W, Re

321

Table 9. Thermal and transport properties of Co,Zr and Co,Hf. y : electronic specific heat coefficient; A: coefficient of the F-term in the electrical resistivity at low temperatures. A [n!A cm K-‘1

;rnJ K-‘mol-‘1 Co,Zr

23a) [79Ml] 29 [92Gl]

Co,Hf

0.9 [93B2] ;9;B2]

“) Data shown in Fig. 97 in LB 111/19A,subsect. 1.4.1 (p. 556).

Table 10. Magnetic and related properties of Co,,Zr, and Co,Hf [9OCl]. Co,,Zr, was obtained by quenching Co,,,Zr from 1000 “C and Co,Hf was obtained by quenching Co,,,Hf from 1130 “C. a, b, c: lattice parameters, Z’c: Curie temperature. The magnetization c was measured at 16 kOe at room temperature. Structure (Spacegroup)

a,6 c

bml

21

b cm’ g-l]

CollZr2

orthorhombic (Pcna)

758

71.9

Co,Hf

orthorhombic (Pcna)

a = 0.48 b = 0.82 c=3.6 a = 0.47 b = 0.83 c = 3.8

768

57.9

-6

0

200

100

600

-14 800 K 1000

0

100

200

300

400

500

600 K 700

T-

Fig. 61. Temperature dependence of the electrical resistivity p of Co,Zr and Co,Hf [93B2]. The residual resistivity p,, was subtracted. Land&-Bbmstein New Series 111/32A

Fig. 62. Temperature dependenceof the thermopower S of Co,Zr and Co,Hf [93B2].

1.4.1 3d elementswith Zr, Nb, MO or Hf, Ta, W, Re

322

300Cod

102r s 0-f 0.1

02

I 0.3

0.4 E-

0.5

I 0.6

I

0.7 Ry 0.6

Fig. 63. Total and partial DOS of Co,Zr calculated by using the APW method [83Kl].

[Ref. p. 330

1.4.1 3d elementswith Zr, Nb, MO or Hf, Ta, W, Re

Ref. p. 3301

Co2!r

323

CozNb

,C14P

\ \

I 6.7

I 6.6

I

I 6.6

I 6.9

A

U-

%O

structures [88Al]. The LMTO method was used for the calculations. The vertical lines represent the experimental values of the lattice constant.

Fig. 64. Total energy of Co,Zr and Co,Nb as functions of lattice constant for the nonmagnetic (P) and ferromagnetic (F) states in the Cl 5 and Cl4

110 $j@

Tz7gK M=Fe

I

h"

lo5*I 1001

I

l

I-

b"

Ni 700

650

a

SOOL Eo,,Zr

1

3

2

4

!5

Y-

Fig. 65. Composition dependenceof Tc (a) and oSat 78 K (b) of Co,,-,M,Zr with M = Fe (closed circles) and Ni (open circles) [93Pl].

Landolt-Btirnstein New Series 111132A

b

801

I

I

Co,,Zr

1

2

I 3

Y-

324

1.4.1 3d elements with Zr, Nb, MO or Hf, Ta, W, Re

[Ref. p. 330

6.0

I

1.5

T=S.ZK o-

10

20

30

40

50

200

60 kOe70

Fig. 66. Magnetic field dependenceof the magnetization of Co, ,-,Fe,Zr [9lBl].

(co, Fe,-, I2 Hf

T=UK

400

600

K

T-

HOPPf -

Fig. 67. Temperature dependenceof the spontaneous magnetization of Co,,,_,Fe,,Zr[91BI].

$$

( Co, Felmx12 Hf

f+-J7j3

I

3.675

15

b

10

0 Fe,Hf

0.2

0.4

0.6

0.8

Co,Hf

xFig. 68. Composition dependence of the average magnetic moment. pFe.co,of (Co,Fe,&Hf at 4.2 K [88Sl]. Open circles: measured at HBDpl = 10 kOe; closed circles: at Harp,= 380 kOe.

0

100

200 HOPPl

300

kOe 400

-

Fig. 69. Magnetization curves of (Co,Fe,_,),Hf at 4.2 K [88’S]]. The compounds with 0.65 Ix IO.75 show metamagneticbehavior at high fields.

Land&-BOrnstein New Series 111/32A

1.4.1 3d elements with Zr, Nb, MO or Hf, Ta, W, Re

Ref. p. 3301

325

50 1 25 Qr 0

Fig. 70. Dependence of Tc on the composition of (Co,Fe,,),Hf [92Gl].

Fig. 71. Temperature dependenceof the electrical resistivity p of (Co,Fe,,),Hf [92Gl].

Pi T

Co,Fe,-,I2 Hf

I

0 - 2.5

I

-5.0

w

-7.5

fb

-12.5 w

Fig. 72. Temperature dependenceof the thermopower -15.0I 0

Land&-Bijmstein New Series 111132A

200

400 T-

I 600

I 800

I S of (Co,Fe,-,),Hf [92Gl]. K 1000

326

1.4.1 3d elementswith Zr, Nb, MO or Hf, Ta, W, Re

[Ref. p. 330

1.4.1.7 Ni alloys and compounds Intermetallic compound Ni,Nb is paramagnetic down to 1.5 K. The Ni,.Co,,_,Zr,, alloys show a martensitic transformation in the concentration range of 10 I y _ K @o xm(300 K)> 3: % x,(300 K), 3: @o X&7 C/T x,(300 K), 3: @o xm(300 K), 3: @o

vpt,

6.500 6X75

6.450

6.425

e/a -

Land&-B6rnstein New Series IIV32A

6.400

Table

3 1 1 1 1 3 1 1

Ref. 8501 8501 8501 8501 8501 85Tl 85Tl 85Tl 85Tl 85Tl 85Tl 85Tl 85Tl 85Tl 85Tl

Fig. 1. Magnetic susceptibility of CsCl type V os+xRuo.s-xat 300 K and 77 K plotted against the 6.375 6.350 electron/atom ratio e/a and x [8501].

1.4.2 3d elements with Ru, Rh, Pd or OS, Ir, Pt

334 ‘0.06 o

_ , 0

0

“O.SlR~ 0.49

t

[Ref. p. 382

3

’ 0.04 ‘; eCI G 0.02

O8

120

p&m

60 40-b

cm3 T 2.50

I 2.25 ?Y

I

a

I

Fig. 2. a Tetragonal distortion, E= c/u - I, b electrical resistivity, p and c magnetic susceptibility x, of Va 5&J, 49 as a function of temperature. For comparison, Xg Of v. S4Ru0 46, which undergoes no structural transformation upon cooling to 4 K, is shown in c by closed circles [8501]. TL: structural transition temperature.

J

100

150

200 l-

250

300 K 350

100

140 140

180

220

260

K 300

l-

Fig. 3. Temperature dependence of the magnetic susceptibility of a VPd and b VPt,. Open symbols: fee

b

100

140

180

220

260 K 300

T-

disordered state; full symbols: ordered state (see Table I) [UTI].

Land&-Barnstein New Series lW32A

Ref. p. 3821

1.4.2 3d elementswith Ru, Rh, Pd or OS,Ir, Pt

335

Table 1. Low-temperature specific heat coefficiient y, Debye temperature @,, and magnetic susceptibility at room temperature for VT, VT, and VT, alloys (T = Pd and Pt) in the ordered (0) and disordered (D) state [85Tl]. Alloy

VPd VPd, VPd, VPt vpt, VP&

Structure type

Unknown Pt,Mo Al,Ti(DO,,) AuCd(B 19) AuCuI(L I,,) Pt,Mo Cu,Au(L 12)

y [mJ g-atom-‘K-*1

@IWI

0

D

0

D

0

D

4.99 3.59 3.97 3.38 2.99 2.00 3.00

5.75 5.39 5.15

366 388 427 355 340 314 296

320 311 357

156 97 107 148

177 147 136

280 255

81 Ferro

118 111

3.02 2.10

xm [ 1Odcm3g-atom-‘]

1.4.2.3 Cr alloys Survey X

Cr,,Ru,

CrI-xOs,

x < 0.25 x < 0.25 x = 0.25 y = 0.1,0.15,0.22 x50.1 / y = 0.1, x = 0.03 y = 0.22, x = 0.06 xco.15 x = 0.025, 0.04

&Pd, CrPt, O<x 0.25, it is basically fee. However, the alloys undergo substantial tetragonal distortion in 0.28 <x < 0.34 [SSKl]. In the equiatomic region, tetragonal CuAuI type ordered structure is formed and in the Pd-rich region, the Cu,Au-type structure appears. Therefore, magnetic and other properties depend on heat treatments. Magnetic anisotropy constants and magnetostriction constants have been measured for ferromagnetic Fe,-,Pd, alloys.

1.6 t IA?1.4 Fig. 71. Composition dependence of the Curie tem1.2

igii:

* Fe

Land&-Bbmstein New Series IW32A

perature Tc and the saturation magnetic moment per atom at 4.2 K for quenched Fe,,Pd, alloys: in the case of the magnetic moment, open, closed and halfopen circles are data on the fee, bee and fct phases, respectively [SSKl]. 0.2

0.4

0.6

0.8

Pd

1.4.2 3d elements with Ru, Rb, Pd or OS, Ir, Pt

Ref. p. 3821

ieRh,-, it,

bet

i/ I ’ j AF ; IAF’:AF 1 I\ I+! 200 I I , 11 ;AF’I

'

Fig. 70. Magnetic phase diagram of FeRh,,Pt, alloys: AF, antiferromagnetic phase; AF’, martensitic antiferromagnetic phase; F, ferromagnetic phase; P, paramagnetic phase. Broken and solid lines indicate the first-order and second-order phase transition, respectively. Solid circles: Curie temperature; open circles: paramagnetic Curie temperature. Solid triangles represent the first-order phase transition temperature between antiferromagnetic and paramagnetic phases; open triangles that between AF and F phases[94Y 11.

300

FeRh

0.2

AF

Ip

\ \

0.6

0.4

371

0.8

FePt

x-

1.4.2.5.2 Fe-Pd based alloys The crystal structure of iron-rich Fe,-,Pd, alloys is bee for x < 0.25. For x > 0.25, it is basically fee. However, the alloys undergo substantial tetragonal distortion in 0.28 <x < 0.34 [SSKl]. In the equiatomic region, tetragonal CuAuI type ordered structure is formed and in the Pd-rich region, the Cu,Au-type structure appears. Therefore, magnetic and other properties depend on heat treatments. Magnetic anisotropy constants and magnetostriction constants have been measured for ferromagnetic Fe,-,Pd, alloys.

1.6 t IA?1.4 Fig. 71. Composition dependence of the Curie tem1.2

igii:

* Fe

Land&-Bbmstein New Series IW32A

perature Tc and the saturation magnetic moment per atom at 4.2 K for quenched Fe,,Pd, alloys: in the case of the magnetic moment, open, closed and halfopen circles are data on the fee, bee and fct phases, respectively [SSKl]. 0.2

0.4

0.6

0.8

Pd

[Ref. p. 382

1.4.2 3d elements with Ru, Rh, Pd or OS, Ir, Pt

372

1.6 I 1.2 Id

0.4 x-

0.6

Fig. 72. Composition dependence of the mean magnetic moment for Fe,_,Pd,, (Fe, sNi, s),-,Pd,, and Ni,_,Pd, alloys, obtained by extrapolating to zero field and zero temperature [86A I].

0 .mI”

I

r-

I I 200 300 l-

I I 400 500

-10 ez

-

erg cm3

I

Fe,-, Pd,

cmI-J

1

h

1.2

1

I

0.8

.

‘I-

I

G0.4 - 1.0&+?

0

. .

.

l

0 b

.

150

300

r-

450

x =0.338 0.357 0.406

600

K 750

Fig. 74. Temperature dependence of the cubic magnetic anisotropy constant, K, for fee Fe,_,Pd, alloys. Samples are single crystals quenched from 1100 ‘C [86h41].

I : :

J,

0

I I 600 K 7000

Fig. 73. Temperaturedependenceof the uniaxial magnetic anisotropy constants, KU, and Ku2 for the fct Feo.ad% 30~alloy: I”, and rc indicate the fee-fct transition point and the Curie temperature, respectively. The sample is a single crystal quenched from 1100 “C [86Ml].

OO@b

.. .

I 100

01 0

Pd

0.8

I

0.26 x=o.33

- -\la\ . II ed

0 - 0.4 0

4

I 50

150

100

200

I

I

250 K 300

7Fig. 75. Temperature dependenceof the cubic anisotropy constant K, of Fe, 67Pd033and Fe, 74Pd026alloys for both quenched (open symbols) and annealed (solid symbols) samples[86M2].

Land&-Barnstein New Series llKl?A

Ref. p. 3821

1.4.2 3d elementswith Ru, Rh, Pd or OS,Ir, Pt

373

80

60 I c-2

a

-20’ 0.3

I 0.4

I 0.5

I 0.6 x-

I 0.7

I 0.8

I 0.9

I Pd

40

0.3 b

0.4

0.5

0.6

0.7

0.8

0.9

P

x-

100 -10-6

80 60

I I 4

40

20 0

c

-20 -20: 0.3

0.4

Land&-BBmstein New Series 111132A

0.5

0.6 x-

0.7

0.8

0.9

Pd

Fig. 76. Composition dependenceof the magnetostriction constants il,OO,A,,, and /2, for Fe,-,Pd, at a 0 K (extrapolated), b 77 K and c 300 K: symbols 1 are after [86M3]); symbols 2 correspond to those obtained by [83M2], symbol 3 is A$after [84Sl].

[Ref. p. 382

1.4.2 3d elements with Ru, Rh, Pd or OS, Ir, Pt

374 400

kOe

I

I bee

300 meVA’

I

Fe,-, Pd,

I fee I

380

250

I 360 200

e = 340 I cl

320 300 0.1

150

100 0.2

0.3

0.4

0.5

x-

0.6

0.7

0.8 50

Fig. 77. Composition dependenceof the mean hyperfine field HhYpfor “Fe in disordered Fe-Pd alloys: extrapolated to 0 K after [75TI]; at 20 K after [UKI].

fct * fee 0 0.2

0.3

0.4

x-

0.5

0.6

0.7

I 0.8

Fig. 78. Composition dependence of the spin wave stiffness constant D for Fe,_,Pd, alloys: open circles, from the specific heat for disordered alloys; solid circles, from the specific heat for ordered FePd and FePd,; triangle, from thermomagnetic curves for disordered alloys; squares for x = 0.28 and x = 0.36, from neutron scattering at room temperature [88Kl].

0.6

0 0

25

50

75

100

125kOe150

Fig. 79. Magnetization curves of Fe(Pd,Pt,_,), alloys at 4.2 K: curve 1, x = I; 2, 0.67; 3, 0.6; 4, 0.53; 5, 0.49; 6, 0.47; 7, 0.33; 8, 0.2; 9, 0.07; 10, 0 [85K2].

HLand&-Barnstein New Series 111/32A

1.4.2 3d elementswith Ru, Rh, Pd or OS,Ir, Pt

Ref. p. 3821

0.6

Ps

0.25

0.1 01 0

0 FePt, I 50

I 100

I

I

150

200

250 K 300

Fig. 80. Temperature dependenceof magnetization for Fe(Pd,Pt,,), alloys at H= 100 kOe: curve 1, x = 1; 2, 0.67; 3, 0.6; 4, 0.53; 5, 0.49; 6, 0.47; 7, 0.33; 8, 0.2; 9, 0.07; IO, 0 [85K2].

0.2

0.4

0.6

0.8

FePd,

Fig. 81. Composition dependence of the volume susceptibility and the spontaneous magnetization for Fe(Pd,Pt,,), alloys: at 4.2 K and 300 K [85K2]. The cross for x = 1 is taken from [77K2].

Pd

Fe- Ni- Pd

Fig. 82. Projection of the magnetic phase diagram of Fe,(Ni,-,Pd,),-, ternary alloys. Contours indicate the Curie temperaturesin K. The dashed line in the lower right corner indicates the phase boundary of cxFe [84Zl]. Ni

40

60 Fe-

Landolt-BOrnstein New Series IIV32A

80 at%

Fe

1.4.2 3d elements with Ru, Rh, Pd or OS,Ir, Pt

376

[Ref. p. 382

Fig. 83. Temperature dependence of the thermal 0

2cQ

400

600

800 K 1000

expansion coefficient of Fe,,,,(Ni,_,Pd,), 35 alloys. Arrows indicate the Curie temperature[9OZl].

T-

1.4.2.5.3 Fe-h based alloys The crystal structure is fee except for the iron rich region. FCCFe-4 alloys are magnetically weak, probably weakly antiferromagnetic. Magnetic properties of Fe,,(Ir,_,Pt,),, alloys have been investigated [7282].

Landolt-B8rnstein New Series 111132A

1.4.2 3d elements with Ru, Rh, Pd or OS,Ir, Pt

376

[Ref. p. 382

Fig. 83. Temperature dependence of the thermal 0

2cQ

400

600

800 K 1000

expansion coefficient of Fe,,,,(Ni,_,Pd,), 35 alloys. Arrows indicate the Curie temperature[9OZl].

T-

1.4.2.5.3 Fe-h based alloys The crystal structure is fee except for the iron rich region. FCCFe-4 alloys are magnetically weak, probably weakly antiferromagnetic. Magnetic properties of Fe,,(Ir,_,Pt,),, alloys have been investigated [7282].

Landolt-B8rnstein New Series 111132A

Ref. p. 3821

1.4.2 3d elements with Ru, Rh, Pd or OS,Ir, Pt

377

4.0 .10-c

’ ’

-cm3 9

._ln H= 9.5kOe

Fe0,65(1rl-~Pt~ IO.35

3.5I-

3.0l-

I

80

2.1i-

60

2sI-

J

b

I x” IL..,-

1.0I< I

0

100

I

I

200

300

I

400

I

0.:I-

500 K 600

0.25). Cu,Au-type Fe,Pt, CuAuI-type FePt and Cu,Au-type FePt, order structures are formed. Iron-rich fee Fe-Pt alloys exhibit remarkable Invar-type behaviour for both ordered and disordered states.Neutron scattering for both ferromagnetic [8011] and paramagnetic region [86Bl], and Miissbauer effect under high pressure [89Al] have been measured.

a

I -10

I

I= 4.2K disordered

FeO.72 Pt 0.28

I -5

I 0

I

5 mm/s

I 10

Y-

b

7.4.2K

I I

I

I

I

-10

-5

0

5 mm/s

I 10

V-

Fig. 87. 57FeMBssbauerspectraof Fe, 72Pt028at 4.2 K and various pressures:a disordered phase, b ordered phase [89Al].

Landoh-BBrnrtein New Series 111132A

Ref. p. 3821

1.4.2 3d elements with Ru, Rh, Pd or OS, Ir, Pt

379

1.0

0.8

I s 0.6 P-Y \ $0.4

0.2

-I

0

a

2

4

6

8

GPO IO

P-

0

2

4

b

Fig. 88. a Pressure dependenceof the average effec-

tive hyperfine field for 57Feat 4.2 K and b the Curie temperature for disordered and ordered phase of Fe,,r,Pt,,,,. Tc at ambient pressure,Tc (0), are 510 and

WI

U--

60

0.4 I

0.5 f 20.0 THz

-- 15.0

l-f.4

LA‘:

q[A-‘1

-

Fig. 89. Magnon dispersions at 11 K of Fe,Pt (Fe,,7,Pt,,,,) alloys along the three principal axes. LA and TA are the longitudinal and transverse acoustic phonon dispersions, respectively [8011]. The solid lines are guides to the eyes. Vertical dashedlines indicate the Brillouin zone boundary.

Landolt-BOrnstein New Series IW32A

GPO IO

380 K for the ordered and the disordered phase, respectively [89Al] The data points at 1.8 GPa (crosses) are taken from [8 1H2].

I 17.5

-~

8

P-

-!l0.1 0.2 0.3 I I I ++

6

380

1.4.2 3d elementswith Ru, Rh, Pd or OS,Ir, Pt

[Ref. p. 382

1.4.2.6 Co and Ni alloys Co and Ni form solid solutions with Pd and Pt over the full composition range. Magnetic properties of these alloys are sensitive to heat treatment. This is due to formation of ordered structures in the Co-Pt and Ni-Pt systems. It is suggested that the formation of a short-range ordered structure affects magnetic properties such as crystalline anisotropy of Co-Pd alloys [86Ml]. Survey

Co,-,Pd, C%xP4 Ni,_,Pt,

X

Properties

Fig.

Ref.

0.24 I x IO.73 0.2 < x < 0.9 0 <x -=c0.6

K,(T) T,(x) P,, (xl 3T,(x)

90 91 92,93

86M4 86Cl 86Cl

.105O erg cm3

.1050 !!Y cm3

K=0.73

-5.0 ! -1.5 *-lo.0 -12.5

-12.5

-15.0 -17.5 50

1Ml

150

200

250

-17.5 50

: I K 350

100

150

T-

200

250

300 K : I

200

250

300 K 350

l-

0O

.lOP erg zi3

*lo5 erg cm3

I

- 5.0 I

-5.0

G -7.5

?.5 5.5

-10.0

-10.0 -12.51 -12.51 50

100

150

I 250

200

300 K 350

T-

Fig. 90. Temperature anisotropy

constant

dependence

-12.5 50

100

150

Tof the cubic crystal

K, for Co,_,Pd,

alloys.

I, 2, 3

correspond to three different heat treatments ing, annealing and as-grown,respectively)[86M4].

(quench-

Landolt-BWnstein New Series 111/32A

0.7 .PB

K co,-x Pi,

\ 1200

381

1.4.2 3d elementswith Ru, Rh, Pd or OS,Ir, Pt

Ref. p. 3821

I

I

Nil-, Pt,

T=4.2K

0.6

A*

0.5 1000 *

(

I 0.4

/(j

(

II

800 I L’2

400

200 0.1

‘\

Iii1

600

1

,iIl

0.2

0.3

L $.

112

II

\

jI I

i 1 1I

0.2

t

0.1 c Ni

0.4 x-

0.5

0.6

0.7

0.8

Fig. 91. Magnetic and chemical phase diagram for Co,-,Pt, alloys. Solid circles, Curie temperature for annealed samples; open circles for quenched samples [86Cl]. 1000

I2 0.3

0.1

0.2

0.3

0.4

0.5

0.b

x-

Fig. 92. Saturation magnetization of Ni,,Pt, alloys at 4.2 K in annealed (solid circles) and quenched (open circles) samples[86Cl].

I

K Ni,-,Pt, I 900-

Fig. 93. Magnetic and chemical phase diagram for Ni,,Pt, alloys. Solid circles, Curie temperature for annealed samples; open circles for samples quenched from 1150 K [86Cl].

lo:=] Ni

0.1

Land&-Bdrnstein New Series IIU32A

0.2

0.3

x-

0.4

0.5-

0.6

I

382

Referencesfor 1.4.2

1.4.2.7 References for 1.4.2

72S1 7282

Sumiyama, K., Shiga, M., Nakamura, Y.: Phys. Status Solidi (a) 13 (1972) K75 Shiga, M. Kosaka, M., Nakamura, Y.: Phys. Status Solidi (b) 50 (1972) 35 1

75c1

Coles, B.R., Jamieson,H., Taylor, R.H., Tari, A.: J. Phys. F 5 (1975) 565

75Tl

Tsurin, V.A., Yurchikov, E.E., Menshikov, A.Z.: Fiz. Tverd. Tela 17 (1995) 2915; Sov. Phys. Solid State (Engl. Transl.) 17 (1975) 1942

77Kl 77K2 79M1

Kanashiro, M., Kunitomi, N.: J. Phys. Sot. Jpn. 43 (1977) 1559 Kelarev, V.V., Vokhmyanin, A.P., Pirogov, A.N., Siderov, S.K.: Neutron diffraction of metals, alloys and compounds (in Russian), Sverdlovsk, UNTs, AN SSSR,34 (1977) Mydosh, J.A., Nieuwenhuys, G.J., Verbeek, B.H.: Phys. Rev. B 20 (1979) 1282

8011

Ishikawa, Y., Tajima, K., Noda, Y.: J. Phys. Sot. Jpn. 48 (1980) 1097

81H1 81H2 81Kl

Ho, S.C., Maartense,I., Williams, G.: Phys. Rev. B 24 (1981) 5174 Hayashi, K., Mori, N.: Solid StateCommun. 38 (1981) 1057 Karpov, Yu.G., Vereshchagin, Yu.A., Sidorenko, F.A., Kuranov, A.A.: Physical Properties of Metals and Alloys. Works of Urals Polytechnical Institute (in Russian) Sverdlovsk (1981) p. 139

83C1

Cherkashin, B.V., Vereshchagin, Yu.A., Kuranov, A.A., Gel’d, P.V.: Fiz. Met. Metalloved. 55 (1983) 1133; Phys. Met. Metallogr. (Engl. Transl.) 55 (1983) No. 6 82 Cherkashin, B.V., Vereshchagin, Yu.A., Sidorenko, F.A., Kuranov, A.A.: Fiz. Met.. Metalloved. 55 (1983) 820; Phys. Met. Metallogr. (Engl. Transl.) 55 (1983) No. 4 184 Lecomte, G.V., v. Lohneysen, H., Wassermann,E.F.: Z. Phys. B 50 (1983) 239 Menshikov, A.Z., Gasnikova, G.P., Dorofeev, Yu.A., Sodorov, S.K.: Physica B 123 (1983) 96 Matsui, M., Adachi, K.: J. Magn. Magn. Mater. 31-34 (1983) 115

83C2 83L1 83Ml 83M2 84Pl 84Rl 84Sl 8421 85Kl 85K2 8501 85Pl 85Sl 8532 85Tl 86Al

Podgomykh, S.M., Kourov, N.I., Tsiovkin, Yu.N., Volkenshteyn, N.V.: Fiz. Met.. Metalloved. 58 (1984) 265; Phys. Met. Metallogr. (Engl. Transl.) 58 (1984) No. 2 47 Rashid, M.H., Sellmyer, D.J.: J. Appl. Phys. 55 (1984) 1735 Schmidt, J.E., Berger, L.: J. Appl. Phys. 55 (1984) 1073 Zatoplyayev, A.K., Menshikov, A.Z., Kazantsev, V.A.: Fiz. Met. Metalloved. 58 (1984) 694; Phys. Met. Metallogr. (Engl. Transl.) 58[4] (1984) 59 Klimars, S., Hesse,J., Huck, B: J. Magn. Magn. Mater. 51 (1985) 183 Kourov, N.I., Tsiovkin, Yu.N., Volkenshteyn, N.V., Mydlarz, T.: Fiz. Met. Metalloved. 59 (1985) 307; Phys. Met. Metallogr. (Engl. Transl.) 59 (1985) No. 2 85 Oota, A., Kusunoki, H., Tsuchiya, M., Takei, H., Noguchi, S.: J. Phys. F 15 (1985) 1103 Petrisor, T., Giurgiu, A., Pop, I., Dadarlat, N.: J. Magn. Magn. Mater. 53 (1985) 185 Sato, T., Nishioka, T., Miyako, Y., Takeda, Y., Morimoto, S, Ito, A.: J. Phys. Sot. Jpn. 54 (1985) 1989 Schreiner, W.H., Stamm, W., Wassermann,E.F.: J. Phys. F 15 (1985) 2009 Turek, P, Kuentzler, R., Biebel, A., Jesser,R.: Solid StateCommun. 53 (1985) 979 Antropov, V.P., Zatoplyayev, A.K., Menshikov, A.Z.: Fiz. Met. Metalloved. 62 (1986) 621; Phys. Met. Metallogr. (Engl. Transl.) 62 (1986) No. 3 193

Landolr-Bbrnstein New Series lil/??A

Referencesfor 1.4.2 86B1 86Cl 86Ml 86M2 86M3 86M4 86N 1 86Wl 87Ml 87N1 87Yl

383

Bbni, P., Shirane, G., Grier, B.H., Ishikawa, Y.: J. Phys. Sot. Jpn. 55 (1986) 3596 Cadeville, M.C., Dahmani, C.E., Kern, F.: J. Magn. Magn. Mater. 54-57 (1986) 1055 Matsui, M., Kuang, J.P., Totani, T, Adachi, K:J.: Magn. Magn. Mater. 54-57 (1986) 911 Miyata, N., Tomotsune, K., Nakada, H., Hagiwara, M., Kadomatsu, H, Fujiwara, H.: J. Phys. Sot. Jpn. 55 (1986) 946 Miyata, N, Kamimori, T., Goto, M.: J. Phys. Sot. Jpn. 55 (1986) 2037 Miyata, N., Hagiwara, M. Ichiyanagi, Y., Kuwahara, K., Matsufuji, H.: J. Phys. Sot. Jpn. 55 (1986) 961 Nishihara, Y ., Yamaguchi, Y., Tokumoto, M., Takeda, K. Fukamichi, K.: Phys. Rev. B 34 (1986) 3446 Williams, D.E.G., Jezierski, A.: J. Magn. Magn. Mater. 59 (1986) 41 Menshikov, A.Z., Antropov, V.P., Gasnikova, G.P., Dorofeyev, Yu.A., Kazantsev, V.A.: J. Magn. Magn. Mater. 65 (1987) 159 Nevdacha, V.V.: Fiz. Met. Metalloved. 63 (1987) 410; Phys. Met. Metallogr. (Engl. Transl.) 63 (1987) No. 2 187 Yasui, H., Kaneko, T., Yoshida, H., Abe, S., Kamigaki, K., Mori, N.: J. Phys. Sot. Jpn. 56 (1987) 4532

88Kl 88Ml

Kuang, J.P., Kontani, M., Matsui, M., Adachi, K.: Physica B 149 (1988) 209 Menshikov, A.Z., Gasnikova, G.P., Baranov, N.V., Bogdanov, S.G.: Fiz. Met. Metalloved. 66 (1988) 714; Phys. Met. Metallogr. (Engl. Transl.) 66 (1988) No. 479

89Al 89Hl 89Z1

Abd-Elmeguid, M.M. Micklitz, H.: Phys. Rev. B 40 (1989) 7395 High, G.L., Alberts, H.L., Smit, P.: J. Magn. Magn. Mater. 78 (1989) 384 Zatoplyaev, A.K., Menshikov, A.Z.: Fiz. Tverd. Tela. 31 (1989) 203; Sov. Phys. Solid State (Engl. Transl.) 31 (1989) 289

90Dl 90Gl

Durusoy, H.Z., Oner, Y.: Phys. Rev. B 42 (1990) 6831 Gasnikova, G.P., Menshikov, A.Z.: Fiz. Met. Metalloved. 69 (1990) 74; Phys. Met. Metallogr. (Engl. Transl.) 69 (1990) No. 6 69 Nikitin, S.A., Myalikgulyev, G., Tishin, A.M., Annaorazov, M.P., Asatryan, K.A., Tyurin, A.L.: Phys. Lett A 148 (1990) 363 Tomiyoshi, S., Yasui, H., Kaneko, T., Yamaguchi, Y., Ikeda, H., Todate, Y.: J. Magn. Magn. Mater. 90-91 (1990) 203 Zatoplyayev, A.K., Menshikov, A.Z.: Fiz. Met. Metalloved. 70 (1990) 73; Phys. Met. Metallogr. 70 (1990) No. 2 65

90Nl 90T1 9oz1 91Bl 91Pl 91Rl 91Sl 92Ml 9201 92M1 92Yl

Baranov, N.V., Barabanova, Ye.A., Kozlov, AI.: Fiz. Met. Metalloved. 72 (1991) 72; Phys. Met. Metallogr. (Engl. Transl.) 72 (1991) No. 5 65 Podgorny, M.: Phys. Rev. B 43 (1991) 11300 Rodic, D., Ahlzen, P.-J., Andersson, Y., Tellgren, R., Bouree-Vigneron, F.: Solid State Commun. 78 (199 1) 767 Sarkissian, B.V.B., Rainford, B.D.: Solid StateCommun. 78 (1991) 185 Moruzzi, V.L., Marcus, P.M.: Phys. Rev. B 46 (1992) 2864 ijzcelik, B., Kiymac, K., Verstelle, J.C., van Duyneveldt, A.J., Mydosh, J.A.: J. Phys. Condens. Matter 4 (1992) 5801 Miyajima, H., Yuasa, S.: J. Magn. Magn. Mater. 104-107 (1992) 2025 Yasui, H., Ohashi, M., Abe, S., Yoshida, H., Kaneko, T., Yamaguchi, Y., Suzuki, T.: J. Magn. Magn. Mater. 104-107 (1992) 927

Landolt-Bbmstein New Series IIV32A

384

Referencesfor 1.4.2

93Ml

Miyajima, H., Yuasa, S., Otani, Y.: Jpn. J. Appl. Phys. 32 (1993) Suppl. 32-3,232

9411

Ibarra, M.R., Algarabel, P.A.: Phys. Rev. B 50 (1994) 4196 Menshikov, A.Z., Gasnikova, G.P.: J. Phys. Condens.Matter 6 (1994) 791 Makhlouf, S.A., Nakamura, T., Shiga, M.: J. Magn. Magn. Mater. 135 (1994) 257 Saha,D.K., Ohshima, K., Wey, M.Y., Miida, R., Kimoto, T.: Phys. Rev. B 49 (1994) 15715 Yuasa, S., Miyajima, H., Otani, Y.: J. Phys. Sot. Jpn. 63 (1994) 3 129

94Ml 94M2

94Sl 94Yl

Landoh-Barnstein New Series 111132A

Landbolt-Börnstein Numerical Data and Functional Relationshps in Science and Technology Volume 19 Magnetic Properties of Metals Subvolume a 3d, 4d and 5d Elements, Alloys and Compounds

Landbolt-Börnstein Numerical Data and Functional Relationshps in Science and Technology Volume 19 Magnetic Properties of Metals Subvolume a 3d, 4d and 5d Elements, Alloys and Compounds

Adsorption on Surfaces and Surface Diffusion of Adsorbates (Landolt-Börnstein: Numerical Data and Functional Relationships in Science and Technology - New Series Condensed Matter)

Adsorption on Surfaces and Surface Diffusion of Adsorbates (Landolt-Börnstein: Numerical Data and Functional Relationships in Science and Technology - New Series Condensed Matter)

Interactions of Photons and Electrons with Atoms (Numerical Data and Functional Relationships in Science and Technology - New Series)

Interactions of Photons and Electrons with Atoms (Numerical Data and Functional Relationships in Science and Technology - New Series)

Laser Applications (Landolt-Börnstein: Numerical Data and Functional Relationships in Science and Technology - New Series Advanced Materials and Technologies)

Laser Applications (Landolt-Börnstein: Numerical Data and Functional Relationships in Science and Technology - New Series Advanced Materials and Technologies)

Landolt-Börnstein: Numerical Data and Functional Relationships in Science and Technology Part 2

Landolt-Börnstein: Numerical Data and Functional Relationships in Science and Technology Part 2

Virial Coefficients of Pure Gases (Landolt-Bornstein: Numerical Data and Functional Relationships in Science and Technology - New Series Physical Chemistry)

Virial Coefficients of Pure Gases (Landolt-Bornstein: Numerical Data and Functional Relationships in Science and Technology - New Series Physical Chemistry)

Thermochemical Data of Elements and Compounds

Thermochemical Data of Elements and Compounds

Thermochemical data of elements and compounds

Thermochemical data of elements and compounds

Densities of Aromatic Hydrocarbons (Landolt-Bornstein, Numerical Data and Functional Relationships in Science and Technology , Vol 8)

Densities of Aromatic Hydrocarbons (Landolt-Bornstein, Numerical Data and Functional Relationships in Science and Technology , Vol 8)

Collisions of Electrons with Atomic Ions (Landolt-Börnstein: Numerical Data and Functional Relationships in Science and Technology - New Series Elementary Particles, Nuclei and Atoms)

Collisions of Electrons with Atomic Ions (Landolt-Börnstein: Numerical Data and Functional Relationships in Science and Technology - New Series Elementary Particles, Nuclei and Atoms)

Symmetry and Condensed Matter Physics

Symmetry and Condensed Matter Physics

Gamma Titanium Aluminide Alloys: Science and Technology

Gamma Titanium Aluminide Alloys: Science and Technology

Selected Systems from Al-Fe-V to Al-Ni-Zr (Landolt-Börnstein: Numerical Data and Functional Relationships in Science and Technology - New Series Physical Chemistry)

Selected Systems from Al-Fe-V to Al-Ni-Zr (Landolt-Börnstein: Numerical Data and Functional Relationships in Science and Technology - New Series Physical Chemistry)

Understanding Soft Condensed Matter Via Modeling and Computation (Series in Soft Condensed Matter 3)

Understanding Soft Condensed Matter Via Modeling and Computation (Series in Soft Condensed Matter 3)

Structural and Functional Relationships in Prokaryotes

Structural and Functional Relationships in Prokaryotes

Structural and Functional Relationships in Prokaryotes

Structural and Functional Relationships in Prokaryotes

Mathematical Analysis and Numerical Methods for Science and Technology: Volume 2: Functional and Variational Methods

Mathematical Analysis and Numerical Methods for Science and Technology: Volume 2: Functional and Variational Methods

Functional and Speciality Beverage Technology (Woodhead Publishing Series in Food Science, Technology and Nutrition)

Functional and Speciality Beverage Technology (Woodhead Publishing Series in Food Science, Technology and Nutrition)

Functional Foods: Principles and Technology (Woodhead Publishing Series in Food Science, Technology and Nutrition)

Functional Foods: Principles and Technology (Woodhead Publishing Series in Food Science, Technology and Nutrition)

Mathematical Analysis and Numerical Methods for Science and Technology: Volume 2: Functional and Variational Methods

Mathematical Analysis and Numerical Methods for Science and Technology: Volume 2: Functional and Variational Methods

Asian Functional Foods (Nutraceutical Science and Technology)

Asian Functional Foods (Nutraceutical Science and Technology)

Interaction of space and matter elements during melting and cristalization of metals and alloys

Interaction of space and matter elements during melting and cristalization of metals and alloys

Springer Handbook of Condensed Matter and Materials Data

Springer Handbook of Condensed Matter and Materials Data

Springer Handbook of Condensed Matter and Materials Data

Springer Handbook of Condensed Matter and Materials Data

Elements of Metallurgy and Engineering Alloys

Elements of Metallurgy and Engineering Alloys

Marine Nutraceuticals and Functional Foods (Nutraceutical Science and Technology)

Marine Nutraceuticals and Functional Foods (Nutraceutical Science and Technology)

Anti-Angiogenic Functional and Medicinal Foods (Nutraceutical Science and Technology)

Anti-Angiogenic Functional and Medicinal Foods (Nutraceutical Science and Technology)

Functional Foods and Biotechnology (Food Science and Technology)

Functional Foods and Biotechnology (Food Science and Technology)

Optical Properties of Condensed Matter and Applications

Optical Properties of Condensed Matter and Applications

Optical Properties of Condensed Matter and Applications

Optical Properties of Condensed Matter and Applications

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