Glass- o ming abili y and so magne ic p ope ies o FeCoSiAlGaPCB amo phous
alloys
J. M. Bo ego, A. Conde, S. Ro h, and J. Ecke
Ci a ion: Jou nal o Applied Physics 92, 2073 (2002); doi: 10.1063/1.1494848
View online: h p://dx.doi.o g/10.1063/1.1494848
View Table o Con en s: h p://sci a ion.aip.o g/con en /aip/jou nal/jap/92/4? e =pd co
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Glass- o ming abili y and so magne ic p ope ies o FeCoSiAlGaPCB
amo phous alloys
J. M. Bo ego and A. Condea)
Depa amen o de Fı
´sica de la Ma e ia Condensada, Ins i u o de Ciencia de Ma e iales, CSIC, Uni e sidad
de Se illa, P.O. Box 1065, 41080 Se illa, Spain
S. Ro h and J. Ecke
Ins i u u
¨ Me alische We ks o e, IFW D esden, Pos ach 270016, D-01171 D esden, Ge many
共Recei ed 21 Feb ua y 2002; accep ed o publica ion 29 May 2002兲
The glass- o ming abili y o (FexCoyBzCu)80Si3Al5Ga2P10 wi h x⫽5–70, y⫽0–63, z⫽5–12, and
u⫽0–5 amo phous alloys has been analyzed in e ms o he wid h o he supe cooled liquid egion,
he educed glass ansi ion empe a u e, and he Vogel–Fulche –Tammann pa ame e s. Subs i u ion
o Fe by Co sligh ly dec eases he glass- o ming abili y o he s udied alloys. The alue o he
agili y pa ame e mis discussed in he ame o he gene al classi ica ion scheme o glass- o ming
liquids. The c ys alline phases o med du ing he i s c ys alliza ion s ep a e iden i ied. Magne ic
momen a low and oom empe a u e, Cu ie empe a u e, oom empe a u e magne os ic ion, and
coe ci i y dec ease wi h inc easing Co con en . © 2002 Ame ican Ins i u e o Physics.
关DOI: 10.1063/1.1494848兴
I. INTRODUCTION
The de elopmen o amo phous so magne ic ma e ials
wi h a wide supe cooled liquid egion be o e c ys alliza ion
has become an impo an esea ch opic in ecen yea s.1,2
The dec ease o he c i ical cooling a e o glass o ma ion
enables he ab ica ion o bulk amo phous alloys by con en-
ional cas ing p ocesses and he exis ence o a wide supe -
cooled liquid egion allows o measu emen s o he he mo-
physical p ope ies o he unde cooled me allic liquid in a
b oad ime and empe a u e ange.3,4
The glass- o ming abili y 共GFA兲o amo phous alloys
can be cha ac e ized by hei c i ical cooling a e, bu his
pa ame e is usually no easy o measu e and se e al o he
pa ame e s ha e been used o p edic he glass- o ming abil-
i y o me allic glasses. One o he mos widely used is he
wid h o he supe cooled liquid egion ⌬Tx(⫽Tx⫺Tg),
whe e Tgis he glass ansi ion empe a u e and Tx he onse
empe a u e o c ys alliza ion o he amo phous alloy. Inoue
and Zhang5ha e s a ed a close ela ion be ween ⌬Txand
GFA o a wide a ie y o bulk glassy alloys: he la ge he
wid h o he supe cooled liquid egion, he lowe he c i ical
cooling a e. Howe e , he impo ance o a chemical decom-
posi ion p ocess in he unde cooled liquid should be s essed
as a key pa ame e o e y good GFA.6The exis ence o
phase sepa a ion in he unde cooled liquid s a e was used o
explain he dispa i y be ween GFA and he mal s abili y in
he alloy se ies Z TiCuNiBe.7
Based on heo e ical wo k on c ys al nuclea ion in un-
de cooled liquid me als, Tu nbull8p oposed ha he glass-
o ming abili y should inc ease wi h inc easing educed glass
ansi ion empe a u e T g de ined as T g⫽Tg/Tl共Tlis liqui-
dus empe a u e兲. This co ela ion has been con i med in
many expe imen s 共see Re . 9 o a summa y兲.
The s udy o glass ansi ion kine ics can p o ide
complemen a y in o ma ion abou he glass- o ming abili y
o he amo phous alloys. I has been ound ha alloys wi h
high GFA, i.e., low c i ical cooling a e o glass o ma ion,
a e s onge me allic glass o me s in he ‘‘Angell plo ’’10
han he mally less s able me allic liquids.11 The e is only
one wo k abou he kine ics o he glass ansi ion o Fe-
based alloys wi h good glass- o ming abili y.12
Amo phous FeSiAlGaPCB alloys a e known o ha e in-
e es ing so magne ic p ope ies combined wi h good glass-
o ming abili y, p omising he o ma ion o bulk so mag-
ne ic ma e ials.1,2 The eplacemen o i on by o he ansi ion
me als may u he imp o e hese alloys. In his a icle, he
e ec o he subs i u ion o Fe by Co on he glass- o ming
abili y and he so magne ic p ope ies o amo phous
(FexCoyBzCu)80Si3Al5Ga2P10 wi h x⫽5–70, y⫽0–63, z
⫽5–12, and u⫽0–5 alloys is epo ed. The dependence o
he glass ansi ion empe a u e on he hea ing a e is ana-
lyzed in e ms o he Vogel–Fulche –Tammann 共VFT兲equa-
ion, and he alue o he agili y pa ame e mis discussed
in he amewo k o he gene al classi ica ion scheme o
glass- o ming liquids.10,13 The cha ac e iza ion o he c ys al-
line phases o med in he cou se o he de i i ica ion p ocess
was done by means o x- ay di ac ion 共XRD兲measu e-
men s.
II. EXPERIMENT
Mul icomponen alloys wi h composi ions
(FexCoyBzCu)80Si3Al5Ga2P10 共Table I兲we e p epa ed by a c
mel ing unde a gon a mosphe e. Raw ma e ials o high pu-
i y we e used; me als: 99.99%, FeC and FeB: 99.5%, and
FeP: 97.5%. F om hese alloys, 10 mm wide and 25
␮
m
hick ibbons we e p epa ed by single- olle mel spinning.
a兲Au ho o whom co espondence should be add essed; elec onic mail:
[email p o ec ed]
JOURNAL OF APPLIED PHYSICS VOLUME 92, NUMBER 4 15 AUGUST 2002
20730021-8979/2002/92(4)/2073/6/$19.00 © 2002 Ame ican Ins i u e o Physics
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The samples we e p o en o be ully amo phous in he as-
spun s a e by XRD measu emen s. The XRD pa e ns we e
eco ded a oom empe a u e using a Philips PW 1820 di -
ac ome e wi h CoK
␣
adia ion. The alues o he onse
glass ansi ion empe a u e Tg, he onse c ys alliza ion
empe a u e Tx, and he c ys alliza ion peak empe a u e Tp
we e de e mined by di e en ial scanning calo ime y 共DSC兲.
The onse glass ansi ion was de ined as he poin o in e -
sec ion be ween he linea ly ex apola ed cu e below he
ansi ion wi h he s eepes angen o he ise in hea low
signal.14 The expe imen s we e pe o med wi h a Pe kin–
Elme DSC-7 unde a con inuous a gon low a di e en
hea ing a es anging om 2.5 o 160 K/min. The mel ing
beha io was s udied wi h a Ne zsch 404 DSC calo ime e a
a hea ing a e o 20 K/min. The liquidus empe a u e Tlwas
de e mined as he in lec ion poin o he las endo he m o
he hea ing cu e 共high empe a u e side兲.
The magne iza ion as a unc ion o he empe a u e
M(T) was measu ed wi h a Fa aday magne ome e in a ield
o 460 kAm⫺1. The Cu ie empe a u e TCwas de e mined
om M(T) cu es, i ing he da a nea TC o a c i ical law
o he o m M(T)⬀(T⫺TC)
␤
wi h
␤
⫽0.36, and ex apola -
ing o M⫽0.
The coe ci e ield HCand he sa u a ion magne os ic-
ion cons an ␭swe e measu ed a oom empe a u e by a
Fo
¨ s e Koe zima and by he small-angle o a ion me hod
a e Na i a15 a 15 kAm⫺1, espec i ely. The sa u a ion po-
la iza ion Jsa oom empe a u e was measu ed wi h a i-
b a ing sample magne ome e , using a maximum ield
s eng h o 1500 kAm⫺1and a 10 K wi h a supe conduc ing
quan um in e e ence de ice magne ome e using an applied
magne ic ield o 4 MAm⫺1.
III. RESULTS AND DISCUSSION
A. Glass- o ming abili y and c ys alliza ion beha io
Figu e 1 shows he DSC cu es o he as-quenched al-
loys a a hea ing a e o 20 K/min. All cu es exhibi he
endo he mic e en cha ac e is ics o he glass ansi ion, ol-
lowed by a supe cooled liquid egion and se e al exo he mic
c ys alliza ion peaks a highe empe a u es. Below he glass
ansi ion a wide exo he mic e en can be obse ed o all
he alloys, which is due o s uc u al elaxa ion. As shown in
Fig. 1 a wide supe cooled liquid egion can be ound o all
he composi ions. The he mal s abili y o he amo phous
alloys does no show a mono onic dependence on Co con-
en : Txis no a ec ed by Co subs i u ion up o abou 26
a .% Co and shows a small inc ease o abou 20 K o sub-
s i u ion o mo e han 52 a .% Co 共Table I兲. I should be
no ed ha he changes in he B and C con en 共keeping he
o al me alloid con en cons an 兲may also a ec his beha -
io . Howe e , a simila endency was ound o
Fe73.5⫺xCoxSi15.5B7Cu1Nb3alloys whe e he B con en was
kep cons an .16 The glass ansi ion empe a u e inc eases
mono onically as he Co con en inc eases 共see Table I兲.
The e o e, he wid h o he supe cooled liquid egion ⌬Tx
sligh ly inc eases om 38 o 54 K as he Fe con en o he
alloy inc eases.
The mel ing cu es o all he alloys a a hea ing a e o
20 K/min a e shown in Fig. 2. The cu e co esponding o
he Co- ee alloy 共alloy A兲exhibi s a sha p single mel ing
e en , indica i e o a eu ec ic composi ion. The alloys wi h
he lowes 共alloy B兲and highes Co con en 共alloy F兲exhibi
a mel ing beha io e y nea o a eu ec ic poin while he
FIG. 1. DSC cu es o he as-quenched alloys a a hea ing a e o 20 K/min.
TABLE I. Glass ansi ion empe a u e Tg, c ys alliza ion onse empe a u e Tx, and liquidus empe a u e Tla
20 K/min and Cu ie empe a u e TCo (FexCoyBzCu)80Si3Al5Ga2P10 alloys.
Alloy A B C D E F
x70 56 43 29 17 5
y0 1426405263
z56891012
u543210
Tg(K)⫾5 755 760 762 764 782 790
Tx(K)⫾1 809 808 808 812 828 828
Tl(K)⫾5 1280 1300 1330 1330 1320 1340
S uc u es eu ec ic nea -
eu ec ic o -
eu ec ic o -
eu ec ic o -
eu ec ic nea -
eu ec ic
TC(K)⫾3 568 554 526 463 373 328
2074 J. Appl. Phys., Vol. 92, No. 4, 15 Augus 2002 Bo ego
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cu es co esponding o he alloys wi h in e media e compo-
si ions 共alloys C, D, and E兲display wo clea mel ing peaks
indica ing ha hey a e o eu ec ic. Acco ding o Tu nbull’s
analysis,8a liquid wi h T g⭓2/3 can only c ys allize wi hin a
e y na ow empe a u e ange, hus can be easily unde -
cooled a a low cooling a e o he glass s a e. The calcula ed
alues o T g , anging om 0.57 o 0.59, a e lowe han bu
close o 2/3, e lec ing he good glass- o ming abili y o he
p esen alloys.
The c ys alliza ion o he samples occu s in se e al
s ages 共Fig. 1兲. The appa en ac i a ion ene gy Ea, he e-
quency ac o Z, and he a e cons an o he c ys alliza ion
p ocess Kc can be e alua ed by using he Kissinge
me hod.17 The dependence o he peak empe a u e Tpon he
hea ing a e
␤
is desc ibed by
␤
/Tp
2⫽共ZkB/Ea兲exp共⫺Ea/kBTp兲,共1兲
whe e kBis he Bol zman cons an and he c ys alliza ion
a e cons an is de e mined om an A henius law
Kc 共T兲⫽Zexp共⫺Ea/kBT兲.共2兲
The alues o he appa en ac i a ion ene gy and he
equency ac o ound o he i s c ys alliza ion s age o
he s udied alloys ise in he same o de as he c ys alliza ion
onse empe a u e 共Table II兲. The equency ac o Zcan be
conside ed as a measu e o he p obabili y ha an a om ha -
ing ene gy Eapa icipa es in a c ys alliza ion eac ion.17 The
high a ia ion in Zbe ween he alloys wi h he lowes and
he highes Co con en could be explained om di e ences
in he c ys alliza ion p ocess, i.e., he appea ance o new
c ys alline phases, as will be epo ed below. Big di e ences
in he alue o Zha e been also epo ed o o he alloys
sys ems. As an example, in Z 41Ti14Cu12.5Ni10⫺xFexBe22.5
共x⫽0, 2, and 5兲alloys18 a subs i u ion o only 5 a .% o Ni
by Fe causes a di e ence in Eao 0.8 eV and in Zo 6 o de s
o magni ude. A co ela ion be ween he alue o he a e
cons an and he wid h o he supe cooled liquid egion was
ound in Z TiCuNiFeBe 共Re . 18兲and FeNbAlGaPCB 共Re .
12兲amo phous alloys: he smalle Kc , he la ge ⌬Tx. The
opposi e endency is ound in he p esen alloys, o which
he a e cons an e alua ed a he peak empe a u e Tpa 20
K/min dec eases wi h inc easing Co con en , in he same
o de as ⌬Tx共Table II兲.
The s udy o he elaxa ion dynamics o supe cooled liq-
uids can be discussed in e ms o he agili y, which is he
deg ee o depa u e om an A henius law o he empe a-
u e dependence o a cha ac e is ic elaxa ion ime.13 The
agili y concep is used as he basis o a classi ica ion o
liquids, o es ima e he sensi i i y o he liquid s uc u e o
empe a u e changes.10 Since iscosi y elaxa ion and he
glass ansi ion measu ed by calo ime ic me hods occu on
he same ime scale, he hea ing a e dependence o he glass
ansi ion can be used as a way o de e mine he agili y o
he ma e ial.11
P io o he DSC measu emen s he samples we e ully
elaxed, as comple e elaxa ion leads o a s a e ha is equi a-
len o a supe cooled liquid,11 and which is, he e o e, inde-
penden o he his o y o he sample. The condi ions o he
he mal ea men we e chosen in o de o ge he lowes
coe ci e ield: he samples we e iso he mally annealed a
733 K 共alloys A, B, C, and D兲,743K共alloy E兲, and 773 K
共alloy F兲 o 30 min.
Wi h inc easing hea ing a e, he glass ansi ion em-
pe a u e shi s o highe empe a u es. As an example Fig. 3
shows he cu es co esponding o he
Fe70B5C5Si3Al5Ga2P10 alloy 共alloy A兲. The dependence o
Tgon he hea ing a e
␤
gi en by he VFT equa ion can be
w i en in he o m14
␤
共Tg兲⫽BexpbDTg
0/共Tg
0⫺Tg兲c,共3兲
whe e Tg
0is he asymp o ic alue o Tg, usually app oxi-
ma ed as he onse o he glass ansi ion in he limi o
in ini ely slow cooling and hea ing a e, Bhas he dimension
o a hea ing a e, and Dis he s eng h pa ame e .
The i ing o he expe imen al da a was pe o med using
he equa ion
ln
␤
共Tg兲⫽lnB⫺DTg
0
共Tg⫺Tg
0兲,共4兲
FIG. 2. Mel ing cu es o all he alloys a a hea ing a e o 20 K/min.
TABLE II. Kissinge pa ame e s. The a e cons an Kc was e alua ed a T⫽Tpa 20 K/min.
Alloy A B C D E F
Ea(eV) 5.4共2兲5.4共2兲5.5共2兲6.0共2兲6.4共2兲7.1共2兲
Z(s⫺1)1(3)⫻1032 1(3)⫻1032 4(3)⫻1032 5(5)⫻1035 1(6)⫻1037 3(9)⫻1041
Kc (s⫺1)4(2)⫻10⫺24(2)⫻10⫺24(2)⫻10⫺27(2)⫻10⫺32(2)⫻10⫺31(2)⫻10⫺3
2075J. Appl. Phys., Vol. 92, No. 4, 15 Augus 2002 Bo ego
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wi h h ee adjus able VFT pa ame e s: B,D, and Tg
0. The
calcula ed alues a e gi en in Table III and he bes i s a e
shown by lines in Fig. 4.
The agili y can be quan i ied by he s eng h pa ame e
Din Eq. 共3兲, o by he agili y pa ame e de ined as19
m⫽dlog10
具
␶
典
d共Tg/T兲
冏
T⫽Tg
,共5兲
whe e Tis he empe a u e, Tg he glass ansi ion, and 具
␶
典is
he a e age elaxa ion ime. F om he VFT i s he agili y
pa ame e a a pa icula Tgcan be calcula ed om13
m⫽DTg
0Tg
共Tg⫺Tg
0兲2ln10.共6兲
The la ge he de ia ion om an A henius beha io , he
la ge he alue o m. The agili y index can be used o
classi y glass- o ming liquids in o h ee gene al ca ego ies:
s ong, in e media e, and agile.10 S ong liquids wi h ap-
p oxima ely A henius empe a u e dependence o elaxa ion
imes ha e alues o mlowe han 30 wi h an es ima ed
lowe limi o m⬇16. In con as , agile liquids such as
polyme s and ionic mel s display alues o mabo e 100.
I should be no ed ha al hough he unce ain y o he
alues o he pa ame e s Tg
0,B, and Dis qui e high 共also
poin ed ou in Re . 20兲, changes in he alue o Tg
0 esul in
changes in D ha keep he alue o m easonably cons an .
The ob ained alues o Da e close o hose ound o FeN-
bAlGaPCB alloys.12 The inc ease o he lowe limi o he
glass ansi ion Tg
0and he dec ease o he s eng h pa ame e
Dwi h inc easing Co con en poin in he same di ec ion as
he dec ease in he wid h o he supe cooled liquid egion.
The agili y pa ame e m, e alua ed a Tgco esponding o a
hea ing a e o 20 K/min, was ound o be a ound 35 o
alloys A, B, C, D, and E, and abou 63 o he alloy wi h he
highes Co con en 共alloy F兲. This esul indica es ha hese
alloys lie in he in e media e ca ego y acco ding o Angell’s
classi ica ion scheme, i.e., be ween he s ong and he agile
ex emes. A agili y mo abou 35 would sugges a e y
good glass- o ming abili y, a inding ha i is co obo a ed
by he ac ha Fe–共Al, Ga兲–共P, C, B, Si兲bulk glassy
samples wi h hickness o 1–15 mm ha e been ob ained.1
Simila alues o mha e been ound in se e al mul icompo-
nen amo phous sys ems such as Z TiCuNiBe and MgCuY
alloys,21 which a e epo ed o be excellen me allic glass
o me s.22,23 A agili y alue o abou 60 o he Co iches
alloy indica es a lowe glass- o ming abili y o his alloy.
In o de o cla i y he eason o he good glass- o ming
abili y o hese alloys, he c ys alline phases o med in he
i s c ys alliza ion s age we e analyzed. Figu e 5 shows he
XRD pa e ns co esponding o samples o all he alloys an-
nealed a 800 K o 1 h. The annealed samples A, B, C, and
D p esen he same c ys alline phases: 共i兲a bcc Fe solid
solu ion con aining Co and M, whe e M s ands o P, C, Al,
B, and Ga elemen s, wi h a la ice pa ame e ha dec eases
as he Fe con en o he amo phous alloy dec eases, indica -
ing changes in he composi ion 共a⫽0.2868 nm alloy A, a
⫽0.2857 nm alloy B; a⫽0.2853 nm alloy C, and a
⫽0.2852 nm alloy D兲;共ii兲a phase wi h a Ni3P-like e ago-
nal s uc u e 共space g oup: I4兲and la ice pa ame e s a
⫽0.893 nm and c⫽0.441 nm 共Re . 24兲and a composi ion
close o Fe3(M), and 共iii兲a phase wi h an Fe3(NiN)2-like
cubic s uc u e 共space g oup Pm3m兲, wi h a la ice pa am-
e e o abou 0.378 nm 共Re . 24兲and a composi ion close o
Fe3(M)2-like cubic s uc u e. The las wo phases we e p e-
iously ound in alloys wi h simila composi ions.25 The si-
mul aneous c ys alliza ion o hese h ee phases causes he
c ys alliza ion o be e a ded, and hus p omo e a wide su-
pe cooled liquid egion. The sligh ly highe c ys alliza ion
FIG. 3. DSC cu es o he alloy Fe70B5C5Si3Al5Ga2P10 a di e en hea ing
a es. The a ows indica e Tg.
FIG. 4. Glass ansi ion empe a u e as a unc ion o he hea ing a e
␤
and
VFT i o he da a 关Eq. 共4兲兴.
TABLE III. Vogel–Fulche –Tammann pa ame e s o he bes i o he
DSC da a acco ding o Eq. 共4兲.
Alloy ln B共K/s兲
⫾2D
⫾2.0 Tg
0共K兲
⫾30 Tg/Tg
0
⫾0.1 m
⫾10
A 13 3.2 620 1.2 34
B 10 1.6 660 1.2 35
C 8 1.3 670 1.1 35
D 7 1.1 680 1.1 35
E 6 0.8 710 1.1 37
F 5 0.5 745 1.1 63
2076 J. Appl. Phys., Vol. 92, No. 4, 15 Augus 2002 Bo ego
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empe a u e o he Co- iches alloys 共E and F兲migh be due
o he appea ance o new Co- ich phases: a phase Co2M wi h
an o ho hombic s uc u e 共space g oup Pnam兲wi h la ice
pa ame e s a⫽0.565 nm; b⫽0.660 nm, and c⫽0.351 nm
共Re . 24兲is ound in he wo alloys; and 共 兲a phase M5Co2
in alloy F.24 Howe e , his inc ease in Txin alloys E and F is
accompanied by an inc ease in Tg esul ing in a inal de-
c ease o he wid h o he supe cooled liquid egion.
B. Magne ic p ope ies
The sa u a ion magne iza ion a 300 and 10 K o as-cas
samples shows a linea dependence on he Fe con en 关Fig.
6共a兲兴 which e lec s he subs i u ion o Fe by Co momen s.
Simila esul s a e ob ained o Co75⫺xFexSi15B10 amo phous
alloys.26 The a e age magne ic momen pe magne ic a om
具
␮
典dec eases om 1.8 o 0.7
␮
Bas he Fe con en dec eases
关Fig. 6共b兲兴. These alues a e much lowe han hose epo ed
o c ys alline FeCo alloys27 and amo phous FeCoSiB
alloys28 wi h lowe me alloid concen a ion 共⬃20 a .%兲. The
low alues o 具
␮
典can be a ibu ed o he dec ease o he
numbe o nea es -neighbo magne ic a oms.29 Simila e-
sul s a e ound o alloys wi h me alloid con en close o 30
a .%.29,30
The Cu ie empe a u e TCo he as-quenched alloys de-
c eases mono onically as he Co con en in he alloy in-
c eases 共Table I兲. This esul can be mainly asc ibed o he
dec ease o he exchange in e ac ion be ween Co–Co pai s
p o oked by he p esence o me alloid a oms.29 The Cu ie
empe a u e and he coe ci e ield a e a ec ed by s uc u al
elaxa ion p ocesses:31 TCinc eases as he annealing em-
pe a u e inc eases and HCdec eases mono onically as he
elaxa ion p og esses. The lowes coe ci i y, HC(min), ob-
ained a e annealing he samples o 30 min a empe a u es
be ween 713 and 733 K, dec eases as he Co and B con en
o he alloy inc eases 关Fig. 6共c兲兴. This dependence co ela es
well wi h ha obse ed o he sa u a ion magne os ic ion
关Fig. 6共d兲兴.
IV. CONCLUSIONS
The GFA o (FexCoyBzCu)80Si3Al5Ga2P10 amo phous
alloys has been analyzed in e ms o di e en pa ame e s,
such as he wid h o he supe cooled liquid egion, he e-
duced glass ansi ion empe a u e, and he VFT i ing pa-
ame e s. Subs i u ion o Fe by Co sligh ly dec eases he
GFA. The alue o he agili y pa ame e mindica es ha
hese alloys lie in he in e media e ca ego y acco ding o An-
gell’s classi ica ion scheme, i.e., be ween he s ong and he
agile ex emes. Cu ie empe a u e, sa u a ion magne iza-
ion, coe ci i y, and magne os ic ion dec ease as he Co con-
en inc eases, he las eaching a nea ly ze o alue.
ACKNOWLEDGMENTS
The au ho s hank H. G ahl o he p epa a ion o he
samples and N. Ma e n and A. Os wald om IFW D esden
o he XRD measu emen s and hei aluable help o he
iden i ica ion o he c ys alline phases. This wo k was pa -
ially suppo ed by he Spanish Minis y o Science and
Technology and EU-FEDER 共P ojec Nos. PB97-1119-
C02-01 and MAT 2001-3175兲and by he PAI o he Jun a de
Andalucı
´a. J.M.B. acknowledges he IFW D esden and he
Jun a de Andalucı
´a o esea ch ellowships.
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FIG. 6. Sa u a ion magne iza ion Jsa 300 and 10 K 共a兲; magne ic momen
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