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Magnetization of an electroless deposited nickel-phosphorus alloy
J. Fléchon, S. Karbal, F. Machizaud, E. Du Trémolet de Lacheisserie
To cite this version:
J. Fléchon, S. Karbal, F. Machizaud, E. Du Trémolet de Lacheisserie. Magnetization of an electroless deposited nickel-phosphorus alloy. Journal de Physique, 1985, 46 (8), pp.1405-1409.
�10.1051/jphys:019850046080140500�. �jpa-00210084�
Magnetization of
anelectroless deposited nickel-phosphorus alloy
J. Fléchon, S. Karbal, F. Machizaud
Laboratoire de Physique des Dépôts Métalliques, Université Nancy I, B.P. 239, 54506 Vandoeuvre-Lès-Nancy Cedex, France
and E. du Trémolet de Lacheisserie
Laboratoire Louis Néel, CNRS-USMG, 166X, 38042 Grenoble Cedex, France
(Reçu le 19 décembre 1984, révisé le 15 février 1985, accepté le 28 mars 1985)
Résumé. 2014 On étudie l’influence de différents recuits sur l’aimantation d’un alliage partiellement désordonné Ni91P9. Le moment magnétique
03C3*o,o
et la température de Curie Tc varient linéairement avec la température de recuit, Ta, jusqu’à Ta = 523 K et le comportement reste celui d’un faible ferromagnétique. Lorsque Ta devient égale ou supérieure à 573 K, il apparait sur les diagrammes de rayons X la raie (200) du nickel c.f.c. et l’on observeune brusque augmentation de
03C3*o,o
et de Tc. Ces résultats sont en accord avec une étudethermomagnétique
ancienne qui montrait que cet alliage se transforme en un mélange cristallin de nickel pur et de phosphure de nickel Ni3P après un recuit à 773 K. Nous avons confirmé l’existence à basse température d’une anomalie dans la variationthermique de l’aimantation.
Abstract. 2014 The influence of various annealings on the magnetization of a partially disordered Ni91P9 alloy has
been investigated. The magnetic moment
03C3*o,o
and the Curie temperature Tc are found to vary linearly with the annealing temperature Ta up to Ta = 523 K and the alloy behaves like a weak ferromagnet. With Ta > 573 K, the (200) reflexion of the f.c.c. nickel appears in the X-ray patterns and a sharp increase in Tc and03C3*o,o
is observed.These results agree with previous thermomagnetic data which showed the alloy to be completely crystallized in a
mixture of pure nickel and Ni3P alloy after heating to Ta = 773 K. Anomalous thermal variation of the magnetiza-
tion is observed below 50 K, as previously observed by other researchers.
Classification Physics Abstracts
75.30
1. Introduction.
The
magnetic properties
of nickelphosphides
havebeen
already
studied for a long time : asearly
as 1960, athermomagnetic study
of disorderedNi1-xP x alloys
has beenperformed by
one of us[1].
In 1967,IBM
laboratoriesinvestigated
bothcrystalline Ni3P
found to be a Pauli paramagnet [2] and
amorphous Ni1-xP x alloys [3].
More recent works on thesealloys [4-6]
were extended in athorough
paper[7]
devoted to the concentration range
0.15
x0.25.
Last, some anomalies were
pointed
out in the thermalvariation of the
magnetization
of electrolessdeposited amorphous
NiPalloys
[8].Recently
a structural model foramorphous Ni1-xP x alloys
wasproposed,
with a local ordervarying
withincreasing
x[9]. Starting
from a f.c.c.-like structure at lower x values, it was shown that for x >0.15,
a
hexagonal ordering
ofpseudo-dodecahedra
gra-dually changes
into a continuous randompacking
of relaxed dodecahedra
[10].
The f.c.c.-like structurewas
actually
observedby
EXAFS studies on electro-deposited
NiPalloys [11].
As most of themagnetic
studies have been
performed
withalloys containing
more than 15 at.
% phosphorus,
we decided here tostudy
a low P contentalloy, namely Ni91 P9.
Thepreparation
and mainproperties
of this electrolessdeposited alloy
arepresented
in a recent paper[12],
where the influence of
annealing
onphysical
pro-perties
isemphasized.
2.
Experiments.
The
powders
have beenprepared by
theliquid phase
oxidoreduction
technique usually employed
in ourlaboratory [1].
Afterbeing carefully
washed and dried,they
have beenanalysed
with an accuracy within afew percent
by
means of anabsorption spectrophoto-
meter. Last,
they
have been annealedduring
5 hoursin a vacuum of 10-6 torr at various temperatures
Ta :
seven
samples,
labelledhereafter
1 to 7, have been annealed;sample
1 five hours atTa
= 323 K ;sample
2Article published online by EDP Sciences and available at http://dx.doi.org/10.1051/jphys:019850046080140500
1406
five hours at 323 K and then five hours at
Ta
= 373 K ;sample
3 threeannealings during
five hours at 323 K, 373 K andTa
= 423 K, and so on... up toTa
= 623 Kfor sample 7.
Both
magnetic
and structuralproperties
of thesefive samples were
investigated
in order to correlatetheir evolution with
Ta :
- the
magnetic
momentsQ(H, T)
were measuredby
an extraction method from 4.2 to 300 K in a super- conductive coil up to 6 tesla ;- the X-ray
analyses
wereperformed
in an auto-matic CGR 060 diffractometer.
3.
Magnetic properties.
Illustrative Arrott
plots
are drawn infigure
1 for thetwo
samples
withTa
= 523 K and 323 K : since theH/y
scale has beenmagnified
in order togive
adrawing
as clear aspossible,
thehigh
field data forTa
= 323 K do not appear but theirextrapolation
down to zero
(HI u)
isgiven by
dotted lines. Theslopes
of these asymptotes remain constant from 80 to 300 K, but increasemarkedly
below 80 K forevery
sample.
. Fig. 1. - Isothermal
u,T(H/ u)
plots for two annealed amorphous Ni91 P 9 alloys. Open circles, T a = 323 K ;closed circles, Ta = 523 K.
The
experimental
resultsconcerning
thesamples
1to 5 are summarized in
figure
2, where(a*, T)’
isplotted
against the
squared
temperature. The Curie tempe-rature is deduced from linear
extrapolation
aboveroom temperature of our
experimental
data. At low temperature, below 50 K, an excessmagnetization
appears which cannot be
expected
in a weak homo-geneous ferromagnet :
assuming
this anomalous effect to beparasitic (we
shall discuss it in a furthersection),
we defineJg o
as theextrapolation
downto 0 K of the linear parts of the
U*2 (T 2) plots.
Wenote that
sample
2 (withTa
= 373K)
does not differmarkedly
fromsample
1.This behaviour is not
surprising
because the struc- tural states stabilized at 323 and 373 K are very similar : differential thermalanalysis experiments
have shown that the first exothermal
phenomena
observable when
heating
thesealloys
appearonly
near 420 K. The same is true for the temperature coefficient of the electrical
resistivity,
thatbegins
to increase at this same temperature
[14].
We
give
infigure
3 the variations ofT c
andQo,o
as functions of the
annealing
temperatureTa.
It hasbeen
pointed
outpreviously [1]
that thosesamples,
Fig. 2. - Thermal dependences of
C1, T’
defined as the inter-section of the dotted lines with the H / C1 = 0 axis in figure 1.
The curves labelled 1, 2, 3, 4, 5 were observed with samples
annealed at Ta = 323, 373, 423, 473, 523 K, respectively.
when annealed at 773 K, became
crystalline powders consisting
of pure nickel andNi3P phosphide.
SinceNi3P
is notferromagnetic [2],
thesecrystalline powders
should exhibit the Curie temperature
Tc
= 631 Kof pure nickel, and a
magnetic
moment that can besimply
derived as 0.67 times that of pure nickbl(UNi
= 58.4 emu g-1),
i.e. co, 0 = 39 emug - 1.
(Indeedin
Ni9 I Pg,
we find 4.96 wt%
P, hence 33.17 wt% Ni3P
and 66.83 wt
%
Ni afterannealing.)
So, we have alsoplotted
infigure
3 thosecalculated
values(squares)
for
T c
andQo,o
atTa
= 773 K, which arealigned
with our
experimental
results(circles). Experimental
values for
T, and a*,o
atTa
= 773 K have beenmeasured for various nickel
phosphides [1],
and thoseconcerning
thealloy
with 5 wt%
P aregiven
infigure
3(triangles) :
the agreement with the calculated values is correct.Last, for
samples
6 and 7,quite
a different behaviour is observed :a(H,
T) is saturatedbeyond
10 k0eand a small
high
fieldsusceptibility
remains viz.a-’ OulOH - 0.15 x 10-6 Oe-’
above 80 K and0.25 x 10-6 Oe-1 at 4.2 K, that is one order
of magni-
tude smaller than for samples 1 to 5. The
a*,o
valuesgiven
in thefigure
3 forTa
= 573 K and 623 K aresimply
the saturationmagnetic
moment( a 0,0
#30 emu
g-’).
ForTc
it was nolonger possible
toderive an
extrapolated
Curie temperature form the Q2 =f«(J2) plot,
where 0 =TIT ,
since themagnetic
moment deviates from
the.Jl - (J2
law(weak
ferro-magnet)
and varies rather as the moment of thecrystalline
nickel, i.e.as.J (1 - (J2) (1
+8 )
to withina few percent
[15].
So, we measureddirectly Tc
forthese two
samples by
means of a balance in amagnetic
field of 500 Oe and found
T,, - ,
621 K, i.e. a valueclose to that of pure nickel (631
K);
these data aregiven
also infigure
3.Fig. 3. - Dependence on the annealing temperature of the Curie temperature Tc (closed symbols) and of
a*,O,
whichis defined by extrapolating to T2 = 0 the linear part of the
(QO,T)2
= f(T2) curves in figure 2 (open symbols)for samples 1 to 5, and is the saturation magnetization
for samples 6 and 7. Circles : our present data. Squares : calculated values for a crystalline mixing of 66:8 wt % Ni
and 33.2 wt % Ni3P, i.e. (Ni91 P 9). Triangles : observed
values for Ta = 773 K, from reference [1].
4. Structural
properties.
The structural state of an
as-prepared sample
isgiven by
the X-raydiagram given
infigure
4. The material appears to bepartially
disordered : the nickel reflexions exist except the(200)
one, but are broadened.The nearest
neighbours
between(111) planes
areobserved from R.D.F.
[14],
but3.60 A. away
insteadof 3.56 A in the f.c.c. structure of nickel. This disorder
might
arise, in the above-cited structural model[9],
from the
regions
where the local order ispseudoico-
saedral : these ones induce stresses in the
neighbouring regions
with f.c.c. structure, which extend over widezones for this metalloid concentration.
Figure
5 illustrates the noticeable structural modi- fications due to a thermal treatment at 573 K : the(200)
reflexion is observed and wasalready
percep- tible withTa
= 523 K.Last, after an
annealing
at 723 K, we can observe infigure
6sharper
lines which indicate the existence ofonly
two wellcrystallized phases, namely
pure nickel andNi3P.
5. Discussion.
Below 50 K, we also observe a large
magnetization deviating
from the linearrelationship
between(UO,T )2
Fig. 4. - Diffraction curve giving the intensity as a function
of the angle 0, 1 = f (0), at room temperature (CuKa radiation) for an as-prepared sample.
1408
Fig. 5. 2013 7 = f (0) for a sample annealed at 573 K.
and T2 in
figure
2. The same effect seems to occurin an
amorphous electro-deposited Ni84P,6 alloy,
as can be seen in the inset of
figure
2 taken fromreference
[7],
where asharp
increase of a2 is observed below 0.3T,,
i.e. about 50 K also. A similarproblem
was raised
recently by
Iida [8], who observed an ano-malous
concavity
of the(1(T)
curves inamorphous
nickel
phosphides : unfortunately
hisstudy
was limitedto above 77 K, and
only
thephosphorus
richeralloys
did exhibit this
anomaly
above this temperature.By
decreasing
thephosphorus
content, thisanomaly
was shifted towards lower temperatures and could
no
longer
be observed. Our measurements,together
with those of Berrada et al.
[7],
have shown that this anomalous effect exists also in the nickel-rich chemicalnickel-phosphorus alloys.
We note that this low temperatureanomaly
does notdisappear,
even afterfurther
annealings
at 573 K and 623 K(samples
6and
7), although
it is reduced aboutby
a factor 2.This anomalous contribution is also associated with
a marked increase of the
high
fieldsusceptibility (see § 3).
Above 50 K, the
samples
labelled 1 to 5 behaveas weak
homogeneous
ferromagnets except at lowmagnetic
fields as in the case of nickel-rich Ni-Yamorphous alloys [13].
The values ofTr
andyo (circles
inFig. 3)
are seen to varylinearly
withTa
Fig. 6. - I = f (9) for a sample annealed at 723 K.
up to 523 K and
extrapolate
forTa
= 773 K to thevalues 631 K and 39 emu
g-’ expected
forcrystal-
line
alloy
of initialcomposition Ni91 P 9 (squared symbols).
On the other hand,
T c jumps
from 463 K(sample 5)
to 621 K
(sample 6) and a*,o
from 21.5 (5) to30 emu
g-l (6)
after anannealing
atTa
= 573 K.Moreover,
sample
6 nolonger
behaves as a weakferromagnet.
These drasticchanges
are associatedwith the appearance of the
(200)
reflexion in the X-raydiagram (Fig. 5). Sample
7 does not differmarkedly
from sample 6, and the observed values of
T, and a*
for these
samples
are close to the valuesgiven
in[1]
for the
fully crystalline alloy
that was obtainedby annealing
up to 773 K(triangled symbols).
In conclusion, this
study
indicates that a strong correlation exists between the evolution of the local order and that of themagnetic
parameters(magne-
tization and Curie
temperature)
in the disorderedNi9,Pg alloys; magnetic
anomalies are observedbelow
80
K,namely
an increase of themagnetization
and of the
high
fieldsusceptibility : they
can berelated with the fact that co,o =
30
emug-l
when thestructural
changes
occur(Ta
> 600K),
instead of39 emu
g-l
asexpected
for amixing
ofcrystalline Ni3P
+ Ni. Themissing
nickel isperhaps
involvedin
heterogeneous regions exhibiting
acomposition
Ni,,P
(x > 3). Due to a different structural order,these
regions
could order at low temperature. Unfor-tunately,
no data ispresently
available expect forNi3P,
known to be a Pauli paramagnet.Acknowledgments.
We thank MM. A. Barlet and M. Maeder for the
magnetization
and Curie measurements.References
[1] FLECHON, J., Thesis, Nancy (1960).
[2] GAMBINO, R. J., MCGUIRE, T. R., NAKAMURA, Y.,
J. Appl. Phys. 38, 3 (1967) 1253-5.
[3] ALBERT, P. A., KOVAC, Z., LILIENTHAL, H. R., MCGUIRE, T. R., NAKAMURA, Y., J. Appl. Phys.
38,
3 (1967) 1258-9.[4] SIMPSON, A. W., BRAMBLEY, D. R., Phys. Status Solidi b 49 (1972) 685-91.
[5] PAN, D., TURNBULL, D., J. Appl. Phys. 45 (1974)
1406-12.
[6] NELSON, J. R., TOTH, L. E., JUDY, J. H., J. Electron.
Mater. 7, 1 (1978) 123-132.
[7] BERRADA, A., LAPIERRE, M. F., LOEGEL, B., PANISSOD, P., ROBERT, C., J. Phys. F. 8, 5 (1978) 845-57.
[8] IIDA, K., J. Magn. Magn. Mater. 35 (1983) 226-8.
[9] MACHIZAUD, F., KUHNAST, F. A., FLECHON, J., Conf.
on Amorphous Metals and Non-Equilibrium Pro- cessing, 5-8 June 1984, Strasbourg (Ed. de Phy- sique) 1984, p. 255-60.
[10] MACHIZAUD, F., KUHNAST, F. A., FLECHON, J., J.
Non-Cryst. Solids 68 (1984) 271-80.
[11] OKAMOTO, T., FUKUSHIMA, Y., J. Non-Cryst. Solids 61-62, 1 (1984) 379-84.
[12 ] FLECHON, J., KARBAL, S., MBEMBA, G., submitted for
publication in Mater. Chem. Phys. (Elsevier).
[13] LIENARD, A., REBOUILLAT, J. P., J. Appl. Phys. 49 (1978) 1680-2.
[14] MACHIZAUD, F., Thesis, Nancy (1973).
[15] DU TREMOLET DE LACHEISSERIE, E., ROUCHY, J., J.
Magn. Magn. Mater. 28 (1928) 77-87.