1
Magne ocalo ic e ec enhancemen d i en by in insic de ec s in Ni-Mn-Sn-
Co alloys
V. Sánchez-Ala cos1,2*, J. López-Ga cía1,3, I. Unzue a4,5, J. I. Pé ez-Landazábal1,2, V.
Reca e1,2, J.J. Bea o-López1,2, J.A. Ga cía5,6, F. Plazaola4 and J. A. Rod íguez-
Velamazán3
1 Depa amen o Física. Uni e sidad Pública de Na a a, Campus de A osadia, 31006 Pamplona, Spain
2 Ins i u e o Ad anced Ma e ials (INAMAT), Uni e sidad Pública de Na a a, Campus de A osadía,
31006 Pamplona, Spain
3 Ins i u Laue Lange in, 71, A enue des Ma y s, 38042 G enoble Cedex, F ance
4 Elek izi a e e a Elek onika Saila, Euskal He iko Unibe si a ea UPV/EHU, p.k. 644, 48080 Bilbao,
Spain
5 BC Ma e ials (Basque Cen e o Ma e ials, Applica ions and Nanos uc u es), 48080 Leioa, Spain
6 Fisika Aplika ua II Saila, Euskal He iko Unibe si a ea UPV/EHU, p.k. 644, 48080 Bilbao, Spain
*Co esponding au ho : Tel.: +34 948 169582; Fax.: +34 948 169565
E-mail add ess: ice[email p o ec ed]
Abs ac .
The in luence o mechanically-induced de ec s on he magne os uc u al p ope ies is analyzed in
a Ni-Co-Mn-Sn alloy subjec ed o so milling and subsequen annealing ea men s. I is ound
ha , opposi e o wha occu s in Ni-Mn-Sn e na y alloys, he annealing ea men a ec s he
magne ic p ope ies in a di e en way in ma ensi e and in aus eni e. In pa icula , he sa u a ion
magne iza ion signi ican ly inc eases in ma ensi e a e annealing whe eas jus a e y sligh
a ia ion is obse ed in aus eni e. This leads o he in e es ing ac ha he p esence o
mic os uc u al de ec s, a o wo sening, makes he magne ocalo ic e ec o be highe in he as-
milled s a e han a e annealing. This beha io is explained as he esul o he combina ion o
he e ec o de ec s on he Mn-Mn dis ance, he e ec Co on he magne ic exchange coupling
be ween Mn a oms, and he e ec o de ec s on he ib a ional en opy change a he ma ens ic
ans o ma ion.
Keywo ds: Ni-Mn-Sn-Co, magne ocalo ic e ec , de ec s, ib a ional en opy
This documen is he Accep ed Manusc ip e sion o a Published Wo k ha appea ed in inal o m in Jou nal o Alloys and
Compounds 774(1) : 586-592 (2019), © 2019 Else ie unde CC BY-NC-ND license (h p://c ea i ecommons.o g/licenses/by-nc-
nd/4.0/). To access he inal edi ed and published wo k see h ps://doi.o g/10.1016/j.jallcom.2018.10.016
2
1. INTRODUCTION
Ni-Mn-based me amagne ic shape memo y alloys a e being widely s udied du ing he las decade
because o he unique mul i unc ional ea u es hey show as a esul o he in e play be ween a
s uc u al ans o ma ion and a complex magne ic o de ing. Due o he s ong dependence o he
magne ic exchange in e ac ions on he Mn-Mn dis ances [1-3], he change in he in e a omic
dis ances caused by he occu ence o a he moelas ic ma ensi ic ans o ma ion (MT) in some
o hese alloys esul s in a la ge magne iza ion change (ΔM) a he ans o ma ion empe a u e
ha a o s he induc ion o he s uc u al ans o ma ion by an applied magne ic ield [4-7]. Such
magne ic induc ion o he MT, and he di e en ea u es o he di e en s uc u al phases
(aus eni e and ma ensi e), gi e ise o in e es ing p ope ies such as he magne ic shape memo y
e ec , la ge magne o esis ance o gian in e se magne ocalo ic e ec , ha make hese alloys e y
a ac i e o p ac ical applica ions in sensing and magne ic e ige a ion [8-14].
The mos p omising alloys o magne ocalo ic applica ions a e hose alloys in he Ni-Mn-X
(X=In, Sn, and Sb) sys ems in which he MT akes place be ween a e omagne ic aus eni e and
a weake -magne ic ma ensi e. The MT cha ac e is ics and he magne ic p ope ies o hese alloys
depend on composi ion, a omic o de and, o a lesse ex en , on mic os uc u e. The composi ional
dependence has been widely s udied, being he comple e phase diag ams o he appea ing
s uc u al and magne ic phases well s ablished [15-18]. A omic o de has been also sys ema ically
s udied. In Ni-Mn-In and Ni-Mn-In-Co alloys i has been shown ha he magne os uc u al
p ope ies can be p ope ly uned a ying he long- ange a omic o de , which can be easily
con olled by means o he mal ea men s [19-21]. In Ni-Mn-Sn and Ni-Mn-Sb alloys, in u n,
he L21 s uc u e is highly s able and he a omic o de is hen ha dly modi iable by means o
con en ional he mal ea men s [22]. In hese alloys, he modi ica ion o he mic os uc u al
pa ame e s (g ain size, de ec s, in e nal s esses…) appea s as almos he only way o modi y he
unc ional p ope ies o a selec ed alloy composi ion. Mechanical milling and subsequen
annealing ea men s a e one o he simples and mos used me hod o modi y he mic os uc u e.
Typically, he g ain size educ ion and he p esence o de ec s and in e nal s esses induced by
3
milling deg ade he MT and he magne ic p ope ies, which can be hen pa ially es o ed upon
mic os uc u al eco e y p ocesses b ough by subsequen annealing [23-28]. In his espec , by
compa ing a Ni-Mn-Sn alloy in bo h he as-milled and he annealed s a es, we ha e ecen ly
shown ha , e en hough no app eciable long- ange a omic diso de was induced by milling, he
sa u a ion magne iza ion o bo h ma ensi ic and aus eni ic phases a e conside ably highe a e
annealing, due o he educ ion o he densi y o he an i-phase bounda ies (linked o disloca ions)
which p omo e he an i e omagne ic coupling be ween Mn momen s [28]. A simila magne ic
de e io a ion a an i-phase bounda ies was indeed e alua ed in Ni-Mn-Al-Ga alloys by elec on
holog aphy, and explained as a consequence o a local a omic diso de ing in he bounda y egion
[29].
The addi ion o Cobal has been shown o enhance he magne ism o he aus eni e and o hinde
e omagne ic o de ing in ma ensi e in Ni-Mn-X alloys, hus leading o an inc ease o ΔM and
he e o e o la ge magne ically-induced shi s o he MT empe a u e and highe associa ed
magne ocalo ic e ec s [4, 30-33]. In pa icula , in Ni-Mn-Sn alloys i has been also shown ha
he magne ic coupling be ween he Mn momen s on he 4a (Mn subla ice) and 4b si es (Sn
subla ice) o he aus eni ic cubic s uc u e changes om being an i e omagne ic o
e omagne ic because o he subs i u ion o Ni by Co [33] (while he magne ic coupling be ween
Mn a oms on he 4a si es is e omagne ic bo h in he e na y and he qua e na y alloys). In his
ega d, i could be hough ha he in luence o he p esence o an i-phase bounda ies (and any
o he mic os uc u al de ec esul ing in local a omic diso de ing) on he magne ic p ope ies will
be di e en in he qua e na y Co-doped alloys o ha in he e na y ones. In his sense, he e ec
o mechanically-induced de ec s on he magne os uc u al p ope ies, and in pa icula on he
magne ocalo ic e ec , is analyzed on a qua e na y Ni-Co-Mn-Sn alloy subjec ed o so milling
and subsequen annealing. I is ound ha he p esence o mic os uc u al de ec s, a o
wo sening, can make he magne ocalo ic e ec o be highe in he as-milled s a e han a e
subsequen annealing. This unusual bene icial p esence o de ec s is explained as he esul o he
combina ion o he e ec o de ec s on he Mn-Mn dis ance, he e ec Co on he magne ic
4
exchange coupling be ween Mn a oms, and he e ec o de ec s on he ib a ional en opy change
a he ma ens ic ans o ma ion.
2. EXPERIMENTAL
A Ni45Co5Mn35Sn15 alloy was p epa ed om high pu i y elemen s by a c mel ing unde
p o ec i e A a mosphe e. The as-cas ingo was homogenized a 1173 K du ing 24h and hen
slowly cooled o RT. The composi ion was analyzed by EDS in a Jeol JSM-5610LV Scanning
Elec on Mic oscope (SEM). In o de o induce de ec s, he alloy was subjec ed o hand milling
in an aga e mo a un il eaching a uni o m pa icle-size dis ibu ion. The mean pa icle size o
he powde , es ima ed om SEM images, was 60 ± 20 μm. A pa o he ob ained powde was
hen annealed a 673 K o 5 minu es in o de o emo e some o he de ec s induced by milling.
The mic os uc u al s a es ob ained in he as-milled and he annealed samples we e hen analyzed
and compa ed: he ma ensi ic ans o ma ions we e cha ac e ized by di e en ial scanning
calo ime y (Q-100 DSC, TA Ins umen s), he magne ic p ope ies by SQUID magne ome y
(QD MPMS XL-7), and he c ys allog aphic and magne ic s uc u es we e de e mined om
powde neu on di ac ion measu emen s pe o med on he D1B di ac ome e , a he Ins i u e
Laue-Lange in (G enoble, F ance), using a neu on wa eleng h o 1.28 Å. The s uc u es we e
e ined by he Rie eld me hod using he FullP o package p og ams [34].
3. RESULTS AND DISCUSSION
Figu e 1a shows he empe a u e dependence o he magne iza ion in he as-milled and annealed
samples unde 100 Oe and 60 kOe applied magne ic ields. The sequences o magne os uc u al
ans o ma ions can be clea ly de e mined om he low- ield M(T) cu es: in bo h samples, he
high empe a u e pa amagne ic aus eni e becomes e omagne ic a ound 360 K and a subsequen
magne iza ion jump akes place a ound 180 K linked o he ma ensi ic ans o ma ion o a
weake -magne ic ma ensi e. The occu ence o such ma ensi ic ans o ma ion is con i med
5
om he appea ance o exo he mic and endo he mic peaks, associa ed o he o wa d and e e se
MT, espec i ely, in calo ime ic measu emen s (see inse ). The ans o ma ion empe a u es and
he magne iza ion change a he MT ob ained om he di e en M(T) cu es a e summa ized in
Table 1 along wi h he en opy change a MT, ∆S, es ima ed om he DSC he mog ams. As i
occu ed in e na y Ni-Mn-Sn alloys [28], nei he he Cu ie empe a u e, TCa, no he MT
empe a u e, TM, seem o e ol e subs an ially wi h he annealing ea men . Taking in o accoun
he high sensibili y o hese ansi ion empe a u es o long- ange a omic o de [35], he absence
o e olu ion sugges s a sca ce e ec o annealing on a omic o de , as i could be indeed expec ed
gi en he high s abili y o he L21 s uc u e in he Ni-Mn-Sn sys em [22]. Likewise, he he mal
hys e esis linked o he MT is also p ac ically una ec ed by annealing (in ac , i is sligh ly la ge
in he annealed sample). As shown in Figu e 1b, he MT shi s owa d lowe empe a u es unde
he applica ion o a 60 kOe magne ic ield, being he shi (wi h espec o TM ob ained a 100 Oe)
almos he same in bo h he as-milled and he annealed samples. On he con a y, he
magne iza ion change a he MT, ∆M, is de ini i ely a ec ed by annealing, being ∆M qui e lowe
in he annealed sample.
The e ec o annealing on he sa u a ion magne iza ion, MS, o he wo s uc u al phases is
illus a ed in Figu e 2, whe e he magne ic- ield dependence o magne iza ion is shown o bo h
phases in bo h he as-milled and he annealed s a es. In all cases, he magne iza ion shows an
ini ial ab up inc ease and a subsequen end o sa u a ion, ypical o e omagne ic beha io .
In e es ingly, he annealing ea men a ec s he ne alue in a di e en way in ma ensi e and in
aus eni e. In pa icula , he sa u a ion magne iza ion signi ican ly inc eases in ma ensi e a e
annealing (∆MSma / MSma ~ 28%) whe eas a e y sligh a ia ion (∆MSaus / MSaus ~ 3%) is
obse ed in aus eni e. This beha io is qui e su p ising as long as i is opposi e o wha is ound
in simila ly-milled e na y Ni-Mn-Sn alloys, o which he high- ield magne iza ion inc ease
linked o annealing is simila (e en la ge ) in aus eni e o ha in ma ensi e [31].
In o de o asce ain he o igin o he di e en e olu ion o he sa u a ion magne iza ion in
ma ensi e and aus eni e upon annealing, neu on di ac ion measu emen s ha e been pe o med
6
in bo h phases o he as-milled and annealed samples. Figu e 3 shows he ob ained di ac og ams
oge he wi h he Rie eld e inemen o he di ac ion pa e ns. The nuclea s uc u es ha e been
i s e ined om di ac og ams ob ained a 400 K in pa amagne ic aus eni e, which allowed a
mo e accu a e de e mina ion o he si e occupancy, and hen a combined nuclea and magne ic
e inemen has been pe o med o e omagne ic aus eni e a 300 K and e omagne ic ma ensi e
a 10K. The s uc u al and magne ic pa ame e s ob ained a e Rie eld e inemen a e shown in
Table 2. Bo h in ma ensi e and in aus eni e, he c ys allog aphic s uc u e is he same be o e and
a e annealing. The aus eni ic phases show he ypical cubic L21 s uc u e (space g oup Fm3m)
wi h almos he same la ice pa ame e . As expec ed, no signi ican a ia ion o he a omic o de
is obse ed, in ag eemen wi h he null e olu ion o he s uc u al and magne ic ansi ion
empe a u es. Likewise, he ma ensi ic s uc u e is he same in bo h samples; a 3M modula ed
monoclinic s uc u e (space g oup P2/m) wi h simila la ice pa ame e s. Wi h espec o he
magne ic s uc u e, i is i s wo h no ing ha he magne ic momen s o Mn a oms a e all posi i e
in aus eni e, hus con i ming he e omagne ic coupling be ween Mn a oms, e en be ween hose
in he 4a and 4b si es. On he con a y, nega i es momen s a e ob ained in ma ensi e o Mn
a oms in hose si es esul ing om he monoclinic dis o ion o he 4b si es (as expec ed due o
he weakening o he exchange in e ac ions as a consequence o he ab up change in he Mn–Mn
in e a omic dis ances upon he MT [36]). In e es ingly, he ne magne ic momen s in aus eni e a e
una ec ed by annealing whe eas a signi ican in luence o annealing is obse ed on he magne ic
momen s in ma ensi e, in which a ma ked dec ease in he nega i e an i e omagne ic con ibu ion
is obse ed.
Since nei he c ys allog aphic s uc u e no la ice pa ame e s no long- ange a omic o de
e ol e upon annealing, he obse ed e olu ion o he sa u a ion magne iza ion and he magne ic
momen s in ma ensi e mus be pu ely a ibu able o a mic os uc u al elaxa ion, jus as i occu s
in a simila ly-milled e na y Ni-Mn-Sn alloy [31]. In ha case, he inc ease o he sa u a ion
magne iza ion o aus eni e and ma ensi e a e annealing was asc ibed o a educ ion o he
densi y o an i-phase bounda ies as a esul o he annihila ion o supe la ice disloca ions. In he
7
cubic phase o he e na y Ni-Mn-Sn alloys, he magne ic coupling be ween Mn a oms in he 4a
si es is e omagne ic whe eas i is an i e omagne ic be ween Mn a oms in he 4a and 4b si es
[21]. Hence, he magne ic coupling be ween Mn a oms may change om e omagne ic o
an i e omagne ic ac oss linea o plana de ec s, hus leading o a dec ease in he ne magne ic
momen . In he aus enic phase o he qua e na y alloy, in u n, he p esence o Co on he Ni si es
makes he Mn a oms a he 4a and 4b si es o couple e omagne ically, and he e o e he magne ic
coupling be ween Mn a oms (whe he nea es o nex -nea es neighbo s) will be always
e omagne ic, i espec i ely o he p esence o de ec s. The e o e, assuming ha a simila
annihila ion p ocess occu s on annealing he qua e na y alloy, he almos null e olu ion o he
sa u a ion magne iza ion o aus eni e can be explained as a di ec consequence o he
e omagne ic coupling be ween Mn a oms. Wi h espec o he ma ensi ic phase, he weakening
o he magne ic exchange in e ac ions upon he ma ensi ic ans o ma ion makes he Mn a oms
in he ma ensi ic s uc u e o couple an i e omagne ically o e omagne ically depending on
whe he hey a e nea es o nex -nea es neighbo s, espec i ely, bo h in he e na y and he
qua e na y alloys. The e o e, he change o he Mn-Mn dis ance associa ed o he p esence o
de ec s (o e en o in e nal s esses) may explain he lowe an i e omagne ic con ibu ion in he
annealed sample, whe e he amoun o de ec s is p esumably lowe han in he as-milled one.
The e ec o de ec s on he magne ic p ope ies can be quali a i ely es ima ed om he i ing o
he ield-dependence o he magne iza ion o he classical law o app oach o sa u a ion o
magne iza ion
(1)
whe e H is he applied ield, MS he sa u a ion magne iza ion, χ he ield independen suscep ibili y
and a and b a e coe icien s ela ed o magne ic and s uc u al p ope ies o he sample [36-39].
In pa icula , he pa ame e a depends on he s esses ield c ea ed by disloca ions and non-
magne ic inclusions and i can be app oxima ed o a ≈ 4πρMSPe , whe e ρ is he densi y o he
ma e ial and Pe is he e ec i e ac ion o po osi y and non-magne ic inclusions [40]. F om he
2
1
S
ab
MM H
HH
c
æö
=--+
ç÷
èø
8
i ing o he magne iza ion cu es in ma ensi e o he law o app oach o sa u a ion, shown in
Figu e 4, Pe alues o 0.021 and 0.014 a e ob ained o he as-milled and annealed samples,
espec i ely. The highe alue o e ec i e ac ion o non-magne ic inclusions in he as milled
sample poin s ou ha he densi y o disloca ions whe e he e omagne ic coupling is los by he
local a omic diso de ing is highe in he as-milled sample han in he annealed one, in ag eemen
wi h he expec ed educ ion o de ec s upon hea ing ea men .
Since he magne ically-induced shi o TM is di ec ly ela ed o ∆M h ough he Clausius-
Clapey on equa ion
(2)
(whe e H is he applied magne ic ield), he obse ed e ec o annealing on he magne ic
momen s, and in pa icula on ∆M, sugges s a possible in luence o he mechanically-induced
de ec s on he magne ic induc ion o he MT and he e o e on he magne ocalo ic e ec (MCE).
The e ec o magne ic ield on he MT empe a u e has been analyzed om he empe a u e
dependence o magne iza ion unde di e en applied magne ic ields. Figu e 5a shows he M(T)
cu es ob ained on hea ing unde applied magne ic ields anging om 100 Oe o 60 kOe a ound
he ma ensi ic ans o ma ion o he as-milled and he annealed samples. As expec ed, in bo h
cases he magne iza ion jump associa ed o he MT occu s a lowe empe a u es on inc easing
he magne ic ield, because o he magne ic s abiliza ion o he aus eni e. The shi o TM
(de e mined om he peaks o he de i a i e cu e o magne iza ion measu emen s) is shown in
Figu e 5b as a unc ion o he applied ield. The ans o ma ion empe a u es linea ly dec ease
wi h he inc easing applied ield, being he slope he same in bo h samples,
𝑑𝑇!/𝑑𝐻 ≈
0.5)
K/kOe. I is wo h no ing ha his slope is in ag eemen wi h he
)𝑑𝑇!/𝑑𝐻
alues calcula ed
by subs i u ing in o Equa ion 1 he alues o ∆M and ∆S shown in Table 1.
The MCE, which can be de ined as he en opy change in iso he mal condi ions, ∆Siso, has been
calcula ed om he ZFC magne iza ion measu emen s shown in Figu e 5a by nume ical
in eg a ion o he de i a i e o he magne iza ion wi h espec o empe a u e, acco ding o he
exp ession
0
M
dT M
dH S
µ
D
=-
D
9
(3)
The ob ained ∆Siso alues a e shown in Figu e 6 as a unc ion o bo h empe a u e and applied
magne ic ield. In bo h cases, a posi i e peak (in e se MCE) is obse ed linked o he
magne os uc u al ans o ma ion a TM e . The MCE alues inc ease wi h he inc easing magne ic
ield, being he highes calcula ed alues o he magne ically-induced en opy change hose
ob ained o he highes applied ield. In o de o be e compa e he magni ude o he MCE, he
∆Siso alues ob ained unde 60 kOe in bo h samples a e plo ed oge he as a unc ion o
empe a u e in Figu e 7. I can be seen ha he magne ocalo ic e ec is conside ably highe in he
as-milled sample (∆SisoA-M ≈ 8 J/kgK and ∆SisoAnn ≈ 6 J/kgK) in spi e o con aining p esumably a
highe amoun o de ec s. In e es ingly, his esul sugges ha he p esence o de ec s, a o
wo sening, may be bene icial o MCE in me amagne ic Heusle alloys.
Since he magne ically-induced en opy change ( ha is, he MCE) in his alloy comes om he
magne ic induc ion o he MT (due o di e en exchange in e ac ions in ma ensi e and aus eni e),
he ac ha bo h he magne ically-induced shi o he MT empe a u e and he wid h o he MT
empe a u e ange is almos he same in bo h samples implies ha a simila ac ion o he MT is
induced by he applica ion o he magne ic ield in bo h samples. The e o e, he highe ∆Siso
ob ained in he as-milled sample mus be due o i s highe o al en opy change a he MT wi h
espec o ha in he annealed sample (see able 1). The en opy change linked o he MT (which
is he limi alue o he a ainable ∆Siso) can be conside ed as he sum o a ib a ional, ∆S ib, and
a magne ic, ∆Smag, e m, in such a way ha ∆S ≈ ∆S ib + ∆Smag ( he small elec onic e m is usually
neglec ed) [42]. Fo he ma ensi e o aus eni e ans o ma ion in me amagne ic shape memo y
alloys (in which ∆M > 0), he ib a ional and he magne ic e ms a e posi i e and nega i e,
espec i ely, he ib a ional one being necessa ily highe [42]. Since ∆Smag is di ec ly ela ed o
∆M, and i is highe in he as-milled sample, a highe magne ic con ibu ion opposing he
ib a ional one should be expec ed in he as-milled sample, which would lead o a lowe ne ∆S.
In his sense, he ci cums ance ha ∆S is ac ually highe in he as-milled sample implies ha ∆S ib
mus be conside ably highe in he as-milled sample han in he ea ed one. Taking in o accoun
( ) ( )
0
,,0
H
iso
H
M
S S T H S T dH
T
¶
æö
D=-=
ç÷
¶
èø
ò
16
Fig.3
Sánchez-Ala cos e al.
0
10
20
30
20 40 60 80
0
10
20
30
40
Yobs
Ycal
Yobs-Ycal
As-milled (b)
In ensi y (a.u.)
2
q
(º)
Annealed
0
40
80
20 40 60 80 100 120
0
20
40 Yobs
Ycal
Yobs-Ycal
Annealed (a)
In ensi y (a.u.)
2
q
(º)
As-milled
17
Fig.4
Sánchez-Ala cos e al.
020000 40000 60000
40
45
50
55
60
PA-m
e = 0.021
As-milled
Annealed
App oach Sa . law
M (emu/g)
H (Oe)
PAnn
e = 0.014
18
Fig.5
Sánchez-Ala cos e al.
0
20
40
60
80
100
100 150 200 250
0
20
40
60
80
100
Annealed
As-milled
(a)
M (emu/g)
T (K)
010 20 30 40 50 60
-35
-30
-25
-20
-15
-10
-5
0
As-milled
Annealed
D
TM (K)
H (kOe)
(b)
19
Fig.6
Sánchez-Ala cos e al.
20
Fig.7
Sánchez-Ala cos e al.
100 150 200 250
-2
0
2
4
6
8 As-milled
Annealed
D
Siso (J/kgK)
T (K)
21
Table 1
Sánchez-Ala cos e al.
Sample
TM e (100 Oe)
(K)
TM e (60 kOe)
(K)
TCa
(K)
∆M
(emu/g)
∆S
(J/kgK)
As-milled
187
159
362
52
9.8
Annealed
188
159
360
40
8.1
22
Table 2
Sánchez-Ala cos e al.
S a e
Cubic 𝐹𝑚3
-𝑚
Monoclinic 𝑃2/𝑚
a = 5.9697 (0002)
a=4.309(001) b=5.583(001) c=13.176(003)
β=92.479(016)
Si e
A om
μ (μB)
Si e
μ (μB)
As-
milled
4a
0.94Mn+0.06Sn
3.11(2)
1a, 1h, 2n, 2m
2.47 (10)
4b
0.47Mn+0.53Sn
1.14(2)
1b, 1g, 2m’, 2n’
-0.91(10)
8c
0.88Ni+0.12Co
0.296*
2j, 2k, 4o, 4o’
0.296*
Annealed
4a
0.97Mn+0.03Sn
3.11(2)
1a, 1h, 2n, 2m
2.50(21)
4b
0.49Mn+0.51Sn
1.19(2)
1b, 1g, 2m’, 2n’
-0.56(41)
8c
0.90Ni+0.10Co
0.28*
2j, 2k, 4o, 4o’
0.28*
A omic posi ions: 2n: x = 0.397(1), z = 0.201 (1); 2m: x = 0.032(1), z = 0.326 (1); 2m’: x = -0.034(4), z = 0.201 (1);
2n’: x = 0.453(5), z = 0.326 (1); 2j: y = 0.245(13); 2k: y = 0.221(7); 4o: z = 0.201 (1); 4o’: z = 0.326 (1)
