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Structural study of Be43HfxZr57-x metallic glasses by X-ray and neutron diffraction
M. Maret, C.N.J. Wagner, G. Etherington, A. Soper, L.E. Tanner
To cite this version:
M. Maret, C.N.J. Wagner, G. Etherington, A. Soper, L.E. Tanner. Structural study of Be43HfxZr57- x metallic glasses by X-ray and neutron diffraction. Journal de Physique, 1986, 47 (5), pp.863-871.
�10.1051/jphys:01986004705086300�. �jpa-00210269�
Structural study of Be43HfxZr57-x metallic glasses by X-ray and neutron diffraction
M. Maret
(+),
C. N. J.Wagner (+ +),
G.Etherington (+ +),
A. Soper(*)
and L. E. Tanner(**)
(+) Institut Laue-Langevin, 156X, 38042 Grenoble, France(+ +) Materials Science and Engineering Department, University of California,
Los Angeles, California 90024, U.S.A.
(*) Los Alamos National Laboratory, Los Alamos, New Mexico 87545, U.S.A. (1)
(**) Lawrence Livermore National Laboratory, University of California, Livermore, California 94551, U.S.A.
(Rep le 23 septembre 1985, révisé le 27 dgcembre 1985, accepti le 10 janvier 1986)
Résumé. 2014 Les facteurs de structure partiels de Faber-Ziman des amorphes Be43HfxZr57-x sont calculés à partir
de la combinaison d’une mesure de diffraction neutronique en temps de vol dans l’alliage avec x = 25 at % et trois
mesures de diffraction X dans les alliages avec x = 5, 25 et 54 at % en utilisant la substitution isomorphe entre
les atomes d’hafnium et de zirconium. Les facteurs de structure partiels de Bhatia-Thornton sont ensuite déduits.
A partir des fonctions de distribution radiale partielles, les nombres de coordination partiels sont calculés et per- mettent de déterminer le paramètre d’ordre chimique généralisé de Warren 03B11 dans la première couche de coor-
dination. Le rayon extérieur de la première couche est bien défini par la position du premier minimum de la fonc- tion GNN situé à 3,8 A. Nous trouvons ainsi une valeur de - 0,033 pour 03B11, qui montre une faible tendance de mise en ordre chimique.
Abstract. - The Faber-Ziman partial structure factors of the Be43HfxZr57-x glasses are calculated from the com-
bination of one time-of-flight neutron diffraction measurement in the alloy with x = 25 at % and three X-ray dif-
fraction measurements in the alloys with x = 5, 25, and 54 at % using the isomorphous substitution between Hf and Zr atoms. The Bhatia-Thornton partial structure factors are then deduced. From the partial radial distribution functions the partial coordination numbers are calculated and allow the generalized Warren chemical order parameter 03B11 in the first coordination shell to be determined. The upper radius of the first shell is well defined by
the position of the first minimum of the GNN function located at 3.8 A. Thus, we find a value of - 0.033 for 03B11 which indicates a slight tendency of chemical ordering.
Classification Physics Abstracts
61. lOF - 61.12D - 61.40D
1. Introduction
Binary
BeHf, BeZr and BeTi, and ternary BeHfZr and BeTiZramorphous alloys
have beenproduced by ultra-rapid liquid quenching
forcomposition
ranges
surrounding
therespective
eutectics 34 at%
Be-Zr, 33 at%
Be-Hf and 37.5 at%
Be-Ti. All theseglasses
but BeTi arereadily
fabricable in continuous ribbon form andthey
are ofparticular
interest because of theirgood
mechanicalproperties,
such ashigh specific strength [1].
A detailedunderstanding
of themechanical or
magnetic properties
of metallicglasses requires
structural information.In this paper, we present the determination of the
local structure of the
Be43HfxZr57-.
ternaryglasses
which is
basically
describedby
a set of sixpartial
structure factors
IiJ{K).
However the Hf and Zr elements have similar metallic atomic radii(rw =
1.585
A,
rZr = 1.597A)
and possess the samehcp
structure; moreover
they
exhibit a similar chemicalbehaviour when
alloyed
with Be, characterizedby
very close eutectic
compositions
(asspecified above)
and the same intermetallic
compounds Be2Hf(Be2Zr)
and
Be5Hf (BesZr).
For these reasons, we can assumethat zirconium and hafnium are
isomorphous
ele-ments in the BeHfZr
glasses.
Then we may treat the ternary glassesBe43HfxZr57 - x
aspseudo-binary glas-
ses, formulated
Be43MT 57 (MT
= Hf orZr).
Conse-quently
their structure issimply
describedby
threepartial
structure factors(PSF).
For the determination of PSF’s we use theisomorphous
substitution method.Article published online by EDP Sciences and available at http://dx.doi.org/10.1051/jphys:01986004705086300
864
This method was
already applied
for extracting partial functions from X-rayexperiments,
such as inLa (AIGa) glasses
[2] orNi (ZrHf) glasses
[3] Janotet al. [4] have also used this method for neutron
experiments
in thepseudo-ternary (FeMn),5P,5clo
glass. Since Fe and Mn have coherent scatteringlengths
of opposite signs, the substitution between Fe and Mn
drastically
changes the contrast between metal and metalloid atoms andconsequently,
theweights
ofthe
partial
functions in the total interference function.When
using only
X-rays, the contrastbrought by
the
isomorphous
substitution method is insufficient to extract all thepartial
structure factors, andgenerally
this method is
applied
with a combination of X-rayand neutron measurements [3]. Moreover, it is often
judicious
to check theconsistency
of thepartial
structure factors extracted from three measurements
by
redundant measurements.For the structural
analysis
of theBe 43 HfZr . 57-., glasses,
weperformed
three X-ray diffractionexperi-
ments in the
alloys
with x = 5, 25 and 54%
which correspondapproximately
to the minimum, maximumand intermediate
compositions
in hafnium. Since thelight
element (Be) is not visibleby
X-rays, werealized one
time-of-flight
neutronexperiment
inthe
Be43Hf25Zr32 amorphous alloy
which is the mosteasily
fabricableglass
in ribbon form. From the four total interference functions, first the Faber-Ziman par- tial structure factorsIij(K)
are determined, and then the Bhatia-Thornton functions are deduced fromIij(K).
The calculation of all thepartial
coordination numbers from the radial distribution functionsRDFij(r)
areperformed,
estimates of some of themwere
previously given by
us in[5].
Finally
thegeneralized
Warren chemical parameter ai is calculated in the first coordination shell, and anextension of this parameter is
proposed
fordescribing
the chemical
ordering
as a function of the distance r.2.
Experimental technique
and dataanalysis.
The ribbons of
Be43Hf,,Zr,7-,, glasses
35 J.1m thick and 1.5 mm wide wereprepared by
themelt-spinning
process. The average atomic
density
of these ternaryglasses
is takenequal
to 0.0565at/A3 (value
of theBe43Zr57 glass
measuredby
Tanner et al.[1]).
Wechecked that this value was in agreement with those deduced from the
slope
of the reduced distribution functionsG(r)
at small r.2. 1 X-RAY DIFFRACTION MEASUREMENTS. - The scattered X-ray intensities of the
alloys
with x = 5, 25 and 54 at%
were measured in transmissionusing AgKa
radiation(with A
= 0.5594A)
in the conven-tional
scanning
20-method, described in[6].
TheX-ray samples
were formedby sticking
ribbonsparallel
to one another, thuscovering
the wholeopening
of the holder of 12.5 x 12.5 mm2. Thesamples
were
placed, initially perpendicular
to the incidentbeam, in a vacuum chamber for
minimizing
airscattering.
X-ray diffracted were selectedby
aSi(Li)
solid-state detector in
conjunction
with asingle
channel pulse height analyser which permitted removal
of the white spectrum, the fluorescent radiation and a
large
part of the Comptonscattering.
Raw data wereregistered
on a multichannelanalyser
for diffractionangles
between 20 and 1000 in step of 0.250. The measured intensities were then corrected forsample absorption, polarization,
andCompton scattering,
asdescribed elsewhere in
[7].
The values ofCompton scattering
were calculated for Hf and Zr from the ana-lytic expressions given by
Palinkas[8]
while those of Be wereinterpolated
from the tables of Cromeret al. [9]. The normalization of the scattered intensities
was done using the sum rule of the interference function
I(K)
whichyielded
the coherentscattering
per atom
Ia(K).
2.2 NEUTRON DIFFRACTION MEASUREMENT. - The
time-of-flight neutron diffraction measurement on the
Be43Hf25Zr32
glass wasperformed
on the GeneralPurpose Diffractometer at the
pulsed
neutronspal-
lation source of the WNR
Facility
in Los Alamos,utilizing
thehigh epithermal
flux to extend measure-ments to
higher
values of K than arepossible
withconventional neutron sources. We recall the relation between the
scattering
vector K and thetime-of-flight
of neutron t(À)
given by :
where mn is the mass of neutron, h is Planck’s constant, 2 0 the
scattering angle, Lo
the incidentflight path
between the moderator and the
sample
and L thediffracted
flight path
between thesample
and thedetector.
The neutron specimen was prepared
by
wrappingmelt-spun
ribbons around a frame such that the finalshape of the
sample
was acylinder
of 6 mm diameterand 6 cm
height.
The mass ofwrapped
ribbons(5.7 g)
and the
cylinder
volume lead to an effective atomicdensity peff
of 0.026at/A’.
This value was used for the calculation of theabsorption
andself-shielding
coef-ficients. The scattered
intensity
was measuredby
three banks of 16 detectors each, located at the average
scattering angles
of 1 4.4°, 40.5° and 1 5 1 . 1 ° andcovering respectively
theK-ranges
of 0.5 to 5A-1,
1.4 to10 A-’ and 7 to 25 A -1
(the
upper limits were deter- minedby
a strong resonance of Hf around an incident energy of 1 eV). The neutron data of each bank wereseparately
corrected first forbackground, sample absorption, self-shielding
andmultiple scattering.
The correction factors for
absorption Aa(6, R)
andself-shielding ASS(8, R)
are calculatedusing
the relationfor
cylinders given by
Rouse et al.[10] ; they
arefunction of the radius of the
sample cylinder
R, theeffective atomic
density peff
and theabsorption
cross-section for
Aa(9, R)
or the totalscattering
cross-section for
ASS(e, R).
Data were then corrected for incoherentscattering
and for deviations from the staticapproximation using
Placzek’s method, whichwas
applied by
A. C. Wright [11] totime-of-flight
measurements for a detector with an
energy-dependent efficiency.
Theefficiency
of He3 detectors is repre- sentedby
1 -exp( -
0.794 A). In table I, wegive
thecoherent scattering
lengths,
the incoherent andabsorp-
tion cross-sections for the pure elements taken in the data
analysis.
The
scattering
from a vanadium rod of known incoherentscattering
allowed, on the one hand, to determine the incident neutron spectrum necessary for Placzek’s correction, and on the other hand to normalize the scatteredintensity
of theBe43Hf2sZr 32
glass. Theoverlappings
of the normalized intensities of the detector banks at 14.40 and 40.50, and of thebanks at 40.50 and 151° was checked
by complemen-
tary neutron measurements on the same
sample
res-pectively
on the DIB and D2 spectrometers at the HFR at the ILL in Grenoble,using
therespective wavelengths
of 2.52 and 0.94 A. Asupplementary
cor-rection was
applied
to remove incoherentscattering
due to the presence of
hydrogen
in the ribbons.Using
the values for differential
scattering
cross-section of anH20
molecule measuredby Beyster [12]
ahydrogen
concentration of about 2 mol
%
was evaluated toaccount for the observed
background.
3. Results and discussion.
3.1 TOTAL INTERFERENCE FUNCTIONS AND PAIR DISTRI- BUTION FUNCTIONS. - When
using
the Faber-Ziman formalism [13], it is usual to define the total inter- ference function I(K) from the coherentscattering intensity
per atom,I.(K), by
thefollowing
normaliza-tion :
where
,fi
are the atomicscattering amplitudes (called bi
forneutrons, and
fMT = (xjf
+ (57 - x)fZr)/57). Ci
arethe atomic concentrations
(note CMT
=0.57).
I(K)
is a linear combination of the threepair partial
structure factorsI ij( K).
Table I. - Values
of
coherent scattering lengths,incoherent and
absorption
cross-sections (givenfor
A = 1.8
A) for
the Be, Zr and Hf elements.In some cases the Bhatia-Thomton formalism [14] is
more
advantageous
and the total interference functionor total structure factor, noted
S(K),
which is a linearcombination of the three number-concentration struc- ture factors
SN,c(K),
is obtainedby
thefollowing
normalization :
and
with
The normalization
(3)
is moregeneral
than the norma-lization
(1),
since it is stillapplicable
to a zeroalloy (i.e. when b > = 0).
The relation between I(K) and S(K) is givenby :
The contribution of each PSF in the total interference function
I(K)
orS(K)
isstrongly dependent
on thevalue of the
Wij
factors. In table II, wegive
the valuesof
Wij
in both formalisms for the different glassesstudied when
using X-rays
or neutrons.Figure
1 shows theI(K)
functions for themelt-spun alloys
obtained from X-ray(Ix(K))
and neutron(IN(K»)
data. It is clear from table II that theIX(K)
functions are dominated
by
the MT-MT pairs, whilethe contribution of
IBeBe(K)
canalways
beneglected.
The three X-ray curves are identical and present a well defined first
peak
at 2.56 Å -1. The neutron curveIN(K)
is
equivalent
toSNN(K),
becauseIN (K)
andSN(K)
areTable II. - Values
of the Wijfactorsfor
theBe43HfxZrS7-x
glasses usingX-rays(XR) for
K = 0, and neutrons (N).866
Fig. 1. - Total interference functions I(K) of the Be43HfxZrs7-x glasses measured by X-rays for x = 5, 25, 54 at % and by neutrons for x = 25 at %.
identical since the ratio
b )2/ b2 )
inequation (5)
isequal
to 0.9994 and the co-factorsWNc
andWcc
arevery small in the
SN(K)
function(see
TableII).
Thefirst
peak
ofIN (K)
is centred at 2.69 Å - 1 and a smallprepeak
can be observed around1.4 A-1;
the shiftof the first
peak
tohigher
K,compared
to this one ofIX(K),
results from thelarger
contribution of the Be- MTpairs.
The uncorrelated La.ue termf ’ > _ f >2
in the normalization
(1), equal
also toCBe CMTCfBe - fMT)2
islarge
forX-rays
and almostnegligible
forneutrons
(see
values of TableI).
Itexplains
the diffe-rence in
sign
of the limitsIx(O)
andIN(0) .
The Fourier transform ofK [I(K) - 1] yields
the reduced distribu- tion functionG(r) :
Figure
2 shows the curves ofG(r)
for theBe43Hf2sZr32 glass
obtained fromX-rays
and neu-trons,
using
the upperintegration
limits of 15.45 Å - 1and 15.15 Å -1
respectively.
These valuescorrespond
to nodes in the
K(I(K) - 1)
functions.Fig. 2. 2013 Reduced distribution functions G(r) of the Be,3Hf,,Zr3l glass obtained from X-rays and neutrons.
The three
G X (r)
functions(only
oneshown)
areidentical with a first
peak
at 3.18A,
whichcorresponds
to the MT-MT interatomic distances. This confirms the
isomorphous
behaviour of the Hf and Zr elements.The
G N(r)
function shows thesplitting
of the firstpeak
into three maxima at 2.2, 2.72 and 3.15 A. Since these three distances are very close to those found in the
Be2Hf
orBe2Zr compounds (see
Table III),they
mustcorrespond respectively
to the first BeBe, BeMT and MTMT interatomic distances. Such asplitting
isquite
seldom because it
requires
animportant
size effect and atomic concentrations close to 50%.
3.2 PARTIAL STRUCTURE FACTORS AND ATOMIC CORRE- LATION FUNCTIONS. - The
partial
structure factorscannot be obtained
simultaneously by solving
a system of three linearequations
such as(2)
or(3),
chosen among the four total interference functions,
because any combination
yields
a very small deter- minant of the matrix formedby
the factorsWij.
Therefore, we used the
following procedure concerning
the Faber-Ziman formalism :
- first, the function
IMTMT(K)
is derived from theIx(K) 1
function ofBe43HfsZrs2
andI;(K)
ofBe43Hf54Zr3 by neglecting
the contribution ofI BeBe (K).
- then the function
IBMT(K) is
determined from the two other interference functionsIx(K)
andIN (K)
of
Be43Hf25Zr32,
and thepartial
functionIMTMT(K), using
analgorithm
similar to the oneproposed by
Edwards et ale [ 15] ;
-
lastly,
the functionIB.B.(K)
is deduced fromIN(K),
whenknowing
the two other functionsIMTMT(K)
andIBw(K).
The Bhatia-Thornton PSFare deduced from the
IiJ{K)’s using
the well knownlinear relations
given
in[14].
- Faber-Ziman formalism :
The function
ImTmT(K),
shown infigure
3,strongly
resembles the
I’(K)’s
with a firstpeak
centred at2.55 Å - 1 .
The two other functions
IBeBe(K)
andIBeMT(K)
which are obtained
by solving
the two linearequations
formed
by I3X(K)
andIN(K)
andusing
the values ofIMTMT previously
determined, exhibit verylarge
oscilla-tions and cannot be retained.
Indeed it is necessary to take into consideration the
errors of
13 (K),1N(K)
andIMTMT(K).
The solutions ofIBeMT(K)
andIBeBe(K)
are thengiven by :
A-1 is the inverse matrix of A =
the coefficients are relative to x = 25 at
%.
After the data treatment, we estimate the relative
errors in the total interference function at 6
%.
Thisquite large
error takes account the absence of cor-rections for the different resolution in K of the three banks of detectors of the
time-of-flight
spectro-meter and also for the different resolutions of X-ray
and neutrons methods.
By neglecting
errors in the co-factors
Wij,
the absolute error inIMTMT(K) is equal
to±
(I
(XII 0.061 lx(K)
I +I (X12
0.06If(K) I).
x 11and a12
are the inverse matrices formed
by
the factorsWin
related to
I1X(K)
andI2X(K).
For instance, atK =
10 A-1,
an = - 1.36 and (Xt2 = 2.36 and theerror in
IMTMT(K)
isapproximately
22%.
In the solution
(6), bx(K), 6’(K)
andbmT(K)
areallowed to vary
respectively
between ±0.06 1 Ix(K) [
±
0.06 I IN(K) I
andWe
keep
the solutions ofIB,,MT(K)
andIBeBe(K)
obtained
by equation (6)
which both fall inside the range defined infigure
4 and check thefollowing inequalities :
and
For each K an average value of these retained solu- tions is calculated. The function
IBeMT(K),
so obtained,is shown in
figure
3 and presents a minimum at 2.2 Å - 1 and a firstpeak
at 2.75 Å - 1. The oscillations of the functionIBeBe(K)
evaluatedby
the same pro- ceduredamp
down toorapidly;
so it is better tofinally
deduceIBeBe(K)
fromequation
(2)using
thevalues of
IN(K), IMTMT(K)
andI...(K).
The functionIBeBe(K)
exhibits aprepeak
around 1.70Å -1,
whichFig. 3. - Faber-Ziman partial structure factors
Iij(K)
of the Be43HfxZr S 7 - x glasses.indicates a
pseudo-periodicity
Be-MT-Be, and a first peak centred at3.4 Å - 1.
The limits of thepartial
functions relative to homoatomic
pairs
arenegative,
while the limit of the function relative to heteroatomic
pairs
ispositive;
these features characterizechemically
ordered systems
(such
NiB [16] or NiTi[17] glasses).
For
liquid alloys
these limits are related to the thermo-dynamic
data[18].
We mustprecise
that the functionsIB.B. (K)
andIB.mT(K)
shown infigure
3 areonly
868
Fig. 4. - Range of allowed structure factors versus K.
approximate
solutions. The Fourier transforms ofIMTMT(K), IBeMT(K),
andIBeBe(K),
calculated with the upperintegration
limits of13 Å - 1,
12.9 Å - 1 and9.4A-’
respectively, yield
the reduced atomicpair
distribution functions
GiJ{r),
shown infigure
5. Thepartial
radial distribution functions are then deduced fromGij(r) by :
The fitting of the nearest
neighbour regions ofRDFij(r)
by
Gaussian components(as
shown inFig. 6) permits
to divide the first shell into sub-shells and also to
Fig. 5. - Reduced atomic pair distribution functions
Gij(r)
of the Be43HfxZrs-x glasses.
Fig. 6. - Partial radial distribution functions
RDFij(r)
ofthe Be43HfxZr 57 - x glasses and Gaussian components of the
nearest neighbour regions.
discard the
spurious ripples
due to the truncation in the Fourier transform, such as the oscillation ofRDFB.mT(r)
around 2.2 A. Thepartial
coordination number4r)
are calculated from theheight
and thewidth at
half-height
of the Gaussianpeaks
centred atrT).
The values ofziP
are summed up in table III. Forcomparison,
the interatomic distances and the coor-dination numbers found in the
crystalline compounds Be2Hf
andBe2Zr
are alsogiven
in table III. The lattice constants ofBe2Hf
andBe2Zr
with thehexago-
nal
AIB2
structure type arerespectively
ao = 3.786A,
Co = 3.163 A
and
= 3.81A, co
= 3.23 A.The distribution of the first
pairs
BeBe isquite large
and can be divided around the
positions
2.2 and2.86 A.
Concerning
the distribution of the firstpairs
BeMT and MTMT,
they
areasymmetric
and can berepresented by
two Gaussians; nevertheless theposi-
tion of the small second Gaussian is
certainly
affectedby
truncation errors in the Fourier transform. It canbe also noted that there is an inversion of the coordina- tion numbers
ZgtMT
andz(2)MTMT
between theglass
andthe
crystalline compounds.
In average, the distanceTable III. - Interatomic distances and coordination numbers in the
Be43HfxZrS7-x
glasses and thecrystalline compounds Be2Hf
andBe2Zr.
(*) Errors are only related to the Gaussian parameters and do not account for the inaccuracy of the
RDFij
functions.Fig. 7. - Bhatia-Thornton partial structure factors
SN,c(K)
of the Be43HfxZrs7 -x glasses.
MTMT is shorter in the amorphous phase than in
Be2Hf
orBe2Zr compounds.
As shown in table III, the first interatomic distances in the
Be43Hf,,Zr57-x glasses
are very close to those of thecrystalline compounds Be2Zr
(orBe2Hf),
except for the distance BeBe at 2.86 A which lies
between the distances of 3.16
(or
3.23A)
inBe2Hf (or Be2Zr)
and 2.635 A of thecrystalline compound Be5Zr.
- Bhatia-Thornton formalism
The Bhatia-Thornton number-concentration struc- ture factors
SN,c(K)
are deduced from theIij(K)’s
using the linear relations in
[14],
and shown infigure
7.The
equivalence
betweenSNN(K)
andIN(K)
is wellchecked, with a first
peak
inSNN(K)
at 2.69 A-1and a
prepeak
around 1.4 A-1. The firstpeak
ofScc(K)
isquite pronounced,
centred at2.3 A - I ;
the oscillations of
SNC(K)
around zero reflect the size effect between the two atomicspecies
but remain weakcompared
to those ofSNN(K)
inspite
of ahigh
ratioof atomic radii of 1.4.
The Fourier transforms of
K[SNN(K) - 1], K[Scc(Kl ’ 1]
andKSNc(K),
are calculated with truncation values of 15, 11.4 and 13 A-1 respectively,which
correspond
to nodes in these functions. The number-concentration correlation functionsGN.c(r),
so obtained, arepresented
infigure
8. The functionGNN(R)
is similar toGN(r) ;
the maximum ofGNN(r)
at2.72 A
corresponds
to a minimum inGcc(r)
betterpronounced
than the positivepeaks
at 2.3 A and 3.17 Aindicating
apreference
for unlike atom pairs.3.3 CHEMICAL SHORT-RANGE ORDER
(CSRO)
PARA-METER. - The
generalized
Warren CSRO parametera1 relative to the first shell is
given according
to [6]by :
where
zie
andzMT
are the total coordination numbers of each species. The value pf ai isdirectly dependent
on the way of
defining
the shell of the firstneighbours,
870
Fig. 8. - Number-concentration correlation functions
GN,,(r) of the Be,, Hf.Zrl 7 -., glasses.
since the numbers
zij
are, obtained from :The upper radius of the first shell,
r’,
is definedby
the abscissa of the first minimum of
GNN
located at3.8 A. The lower limits
r""
allow to discard thespurious ripples
inRDFJ. Using
theintegrand (9)
with rl = 3.8A, I Z1BeMT
andz1MTMT
areequal
to 4.2,7.4 and 8.2
respectively.
Thus, a1 isslightly negative
with a value of - 0.035. This value is very different from - 0.16, our
previous
estimate, which was deduced from a functionARDF(R) containing
bothcontributions of BeBe and BeMT and calculated for a
first shell limited at
3.4 A (radius
definedby
theposition
of the first minimum ofARDF(r)).
Thisdiscrepancy clearly
shows that the limit of the first shelllargely
influences the chemical short range order parameter ai.The value of - 0.035 for the
Be4:5Hf ., Zr 5 7 -., glasses
is similar to that calculated for the
Be37.5Ti62.5
Fig. 9. - Evolution of the generalized Warren chemical
order parameter a(r) as a function of r.
glass [19]
withpartial
coordination numbersequal
toZB.B. = 2.9, ZB.TI = 6.9 and ZTiTi = 8.
In this series of
glasses,
the chemicalordering
is weakcompared
to thoseexisting
in metal-metalloidglasses :
(Ni8oB20 [16])
or, metal-metalglasses (Ni33 Y 67 [20]).
We must
emphasize
that in mostprevious
structuralstudies of metallic
glasses,
thezi’j
numbers are calculat-ed with different upper
integration
limitsr’
whichcorrespond
each to theposition
of the first minimum inRDFiï
If the twospecies
are different atomic radii,the three minima do not coincide with the minimum of
GNN
andconsequently,
the CSRO parameter ai calculated withspecific r1ij
can be somewhat different from the value obtained with aunique
value rl.Therefore for
binary
systems with strong size effect,the
importance
of the chemicalordering
and itsextent could be described
by
a functiona(r)
definedin the same way as al, i.e. :
with
Figure
9 shows the variation ofa(r)
for theBe43HfxZrs7_x glasses.
Between 3 and 4.25 Aa(r)
is an
increasing
function, which becomespositive beyond
3.9 A. The oscillations ofa(r)
around 0damp
down
rapidly beyond
4.5 A and it shows the localcharacter of the chemical
ordering.
This function could beeasily
used for acomparison
of chemicalorders in different
glasses.
Acknowledgments.
This research was
supported
in partby
grant DMR80- 07939 and 83-10025 from the National Science Foun- dation. Thanks are due to the WNRFacility
in LosAlamos and to the Institut
Laue-Langevin
for theallocation of beam time at their
respective
neutronsources.