Mat. Res. Bull. Vol. 3, pp. 159-168, 1968.
P e r g a m o n Press, Inc. Printed
in the United States.
CHARACTERIZATION OF AMORPHOUS ALLOY FILMS B. G. Bagley , H. S. Chen and D. Turnbull Division of Engineering and Applied Physics, Harvard University, Cambridge, Massachusetts Now at Bell Telephone Laboratories, Murray Hill, New Jersey
(Received
December
Z~., 1967; R e f e r e e d )
ABSTRACT It is difficult to distinguish between the microcrystallite and c o n t i n u o u s random m o d e l s f o r amorphous a l l o y f i l m s . The application of X-ray diffraction, electron microscopy, calorimetry and v i s c o m e t r y t o t h i s p r o b l e m a r e d i s c u s s e d . In particular, the use of these techniques for the characterization o f amorphous n i c k e l - p h o s p h o r u s and g o l d - s i l i c o n - g e r m a n i u m a l l o y s a r e d e s c r i b e d .
Introduction In this
p a p e r we s h a l l
characterization ditions
discuss
o f amorphous a l l o y
c a n amorphous a l l o y
of this
films.
i n amorphous f i l m s ?
problems in the
The f i r s t
f i l m s be c l a s s i f i e d
The s e c o n d i s w h a t c o n f i g u r a t i o n a l arrangement
two i n t e r r e l a t e d
is under what con-
operationally
model b e s t c h a r a c t e r i z e s We s h a l l
p r o b l e m h a v i n g t o do w i t h s p a t i a l
give most attention
as glasses? the atomic to the aspect
a r r a n g e m e n t w i t h some comment on
component d i s t r i b u t i o n . T h e r e a r e p e r h a p s two l i m i t i n g solids.
One i s t h e o r y s t a l l i t e
models for the structure
model(1)and the other
random model s u c h a s t h e model o f Z a c h a r i a s e n B e r n a l model ~ )
as a p p l i e d
In view of the variety
(2)
o f amorphous
is the continuous
for oxide glasses
or the
t o monatomic o r s i m p l e m o l e c u l a r amorphous s o l i d s °
o f c o m p o s i t i o n and p r e p a r a t i o n
159
techniques
o f amorphous
160
AMORPHOUS
solids
there
structures
ts~ o f c o u r s e ,
ALLOY
FILMS
Vol. 3, No. 7
no r e a s o n t o s u p p o s e t h a t
would be c h a r a c t e r i z e d
exclusively
all
amorphous s o l i d
by J u s t one o f t h e s e two t y p e s
o f model. In contrast have rarely,
with undercooled
i f ever~ been p r e p a r e d
d e f i n e d or i n i n t e r n a l history
liquids,
equilibrium.
their
slow i s o t h e r m a l
in a state
which is thermodynamically
T h i s i s m a n i f e s t e d by t h e thermal
dependence of the properties
conditions#
it a p p e a r s t h a t amorphous s o l i d s
o f amorphous s o l i d s
drift with t i m e .
t h e r m o d y n a m i c a l l y d e f i n e d amorphous s t a t e ,
a n d , u n d e r some
The c o n c e p t o f an " i d e a l "
distinct
from t h e c r y s t a l l i n e ¢
was d e v e l o p e d f o r m o l e c u l a r l y
c o m p l e x s y s t e m s by G i b b s and Di M a r z i o ~4j and
f o r s i m p l e and m o n a t o m i c s y s t e m s by Cohen and T u r n b u l l ( 5 ) . the structure continuous
solidification process ture
is usually
of a liquid.
or increasing
pressure~
uished from crystallization To be c l a s s i f i e d
possible,
a liquid
from fluid
it
to solid
viscosity~
values.
be amorphous i n a d i f f r a c t i o n
preferably
the broad halos qualitatively
repeatable,
that
discontinuously. the solid
examination.
the liquid
tempera-
This is disting-
increases
is not sufficient
To c o n f i r m t h e c l a s s i f i c a t i o n
we mean a homogeneous
continuously~ with falling
in which the viscosity
as a glass
formed by c o n t i n u o u s
solidification
to an extremely fine grained crystalline
would e x h i b i t
structure.
states
increases
owing t o c o p i o u s n u c l e a t i o n I t h a t
continuously pattern
By c o n t i n u o u s
by a
or B e r n a l t y p e .
d e f i n e d a s a n amorphous s o l i d
in which the viscosity
by chilling
It appears that
o f an i d e a l amorphous s o l i d w o u l d be c h a r a c t e r i z e d
random model o f t h e Z a c h a r i a s e n
A glass
state,
%
formed
For it
solidified
is
dis-
s o l i d whose d i f f r a c t i o n associated
a continuous
between the metastable
with the glass
transition liquid
in
and g l a s s
s h o u l d be d e m o n s t r a t e d . By t h e u s u a l d e f i n i t i o n
vapor or electrodeposition,
many amorphous s o l i d s j w o u l d n o t be c l a s s i f i e d
e.g.
t h o s e formed by
as glasses.
It
seems
Vol. 3, No. Z
AMORPHOUS
ALLOY
FILMS
161
that the amorphous solid state of some substances, at least, would have essentially the same structure whether formed by vapor deposition or by chilling the liquid.
Actually there may be some merit in distinguishing
glasses from other amorphous solids for, as we shall see, the distinction in physical properties between different amorphous structures with the same composition may be subtle.
However, we think it reasonable to broaden the
definition of a glass to include those amorphous solids, however formed, which can be brought into a state in internal equilibrium having properties, viscosity, That is,
heat capacity, the transition,
etc.,
clearly
amorphous s o l i d
demonstrated.
We n o t e ,
not in itself
prove that
condensation
is different
though,
form.
However,
it
<
of a metastable
> metastable
liquid,
non-appearance of this
transition
the structure
o f an amorphous s o l i d
formed by
from that
liquid.
s h o u l d be
that
The E x i s t e n c e It appears that
characteristic
does
of a g l a s s . of Alloy Glasses
pure metals have rarely is well established
that
been prepared
i n amorphous s o l i d
the admixture of certain
impurities to metals greatly facilitates their formation in an amorphous solid
state.
the relative
Probably the principal stability
role of the impurities
o f t h e amorphous s t a t e
and t o r e t a r d
is to increase nucleation
of the
crystal. The t r a n s i t i o n fested
f r o m amorphous s o l i d
by t h e v i s c o s i t y
Cp, b e h a v i o r . equilibrium 1013 poise.
behavior,
to metastable
as noted earlier,
liquid
and by t h e h e a t c a p a c i t y ,
I n o r d e r f o r an amorphous s u b s t a n c e t o a c h i e v e in a relatively
short period
its
c a n be m a n i -
viscosity
internal
s h o u l d be l e s s
than
In the transition from the glass to the metastable liquid state
Cp usually rises abruptly. Amorphous alloys have not been explored extensively for the liquid : glass transition.
>
In the explorations which have been made the alloys often
16Z
AMORPHOUS
crystalllzed
ALLOY
FILMS
Vol. 3, No. Z
upon h e a t i n g w i t h o u t g i v i n g any c o n c l u s i v e i n d i c a t i o n s
transition.
However, t h e t r a n s i t i o n
of this
might have o c c u r r e d i n some o f t h e s e
s y s t e m s a t some h i g h e r t e m p e r a t u r e i f c r y s t a l
nucleation
and growth had n o t
intervened.
(6)
Duwez and a s s o c i a t e s
demonstrated that
a p p r o x i m a t e c o m p o s i t i o n 18-25 a t .
~ sillcon,
liquid gold-silicon
c a n be r a p i d l y c h i l l e d
form whlch was amorphous i n X - r a y e x a m i n a t i o n s .
warmed to J u s t below room t e m p e r a t u r e some r e l a x a t i o n
an i n t e r m e t a l l i c
~
~ liquid
transition
k~en t h e a l l o y was
effects
suggestive of
i n t h e a l l o y was
p r o c e s s was r e t a r d e d
was e x h i b i t e d
to
was f u l l y m a n i f e s t .
However~ Chen f o u n d t h a t when r o u g h l y h a l f o f t h e s i l i c o n
that the glass
to a solld
were observed but crystallization
p h a s e o c c u r r e d b e f o r e any t r a n s i t i o n
r e p l a c e d by germanium t h e c r y s t a l l i z a t i o n
of
Chen ( 7 ' 8 ) m e a s u r e d t h e h e a t
c a p a c i t y o f t h e s e amorphous a l l o y s a t low t e m p e r a t u r e s ,
the onset of a glass ~ liquid transition
alloys,
sufficiently
both theologically
so
and
thermally. In particular Ge0. 136Si0.09&. little
e x t e n s i v e m e a s u r e m e n t s w e r e made on t h e a l l o y Au0.77 At low t e m p e r a t u r e s Cp o f t h e amorphous a l l o y i s o n l y a
higher than that of the equilibrium mixture.
to rise
sharply with increasing
v a l u e s a b o u t 5. S c a l / g m , fall
t e m p e r a t u r e and t h e n l e v e l s n e a r 300°K t o
atom above Cp o f t h e e q u i l i b r i u m m i x t u r e and which
r e a s o n a b l y w e l l on t h e e x t r a p o l a t i o n
relation exhibit
for the liquid alloy. this
transition
o f t h e h i g h t e m p e r a t u r e Cp- T
I t was d e m o n s t r a t e d t h a t a specimen c o u l d
two o r more t i m e s when a f t e r
transition
i t was c h i l l e d
transition
t e m p e r a t u r e was s h i f t e d
factor
Near 295°K Cp b e g i n s
and a g a i n r e h e a t e d .
being taken through the
The t h e r m a l l y i n d i c a t e d g l a s s
o f t h e o r d e r o f 1-2 ° by changes o f a
o f 16 i n t h e r a t e o f b e a t i n g .
The a l l o y was h a r d and b r i t t l e and a f t e r
crystallization.
i n t h e amorphous s t a t e
However, i t
a t low t e m p e r a t u r e
i s s o f t and f l o w s e a s i l y
in the
Vol. 3, No.
Z
AMORPHOUS
ALLOY
FILMS
163
temperature range in which the glass transition is thermally manifested. Chen (7~8) measured the creep rate of the alloy over this temperature range, 12 to 32°C.
A steady creep rate, which increased linearly with the stress
over the range 3 to 140 Kg/mm 2, was reached almost instantaneously at the high temperatures and more slowly at the lower temperatures.
The viscosity
calculated from these results ranged from 1013 at the lowest temperature to 109 at the highest and its temperature variation was described by an equation of the Fulcher form: ffi 0.52 exp[1360/(T - 241.3)}
poise
The time constant 3 T~ for configurational relaxation was found to be T ffi I0-i0~ seconds.
Thus at viscosities lower than 1013 the liquid clearly
had achieved an internal equilibrium state in our experiments. Presumably the viscosity of the alloy will continue to fall rapidly with rising temperature to values in the range 10 -2 poise usually typical for molten metals.
This form of the viscosity variation with temperature,
especially the Fulcher behavlor I is qualitatively similar to that of other glass forming liquids. We think that these results clearly demonstrate the existence of a metallic glass.
They suggest also that many other amorphous solid alloys may
be in conflgurational states best characterized as glassy even though the glass ~
# liquid transition is unobserved because of the intervention of
rapid crystallization processes.
The binary amorphous alloy of gold-sillcon,
for example, probably belongs in this category. It is interesting that the metallic radii of silicon and germanium are not very different
(2 to 5%) from that of gold.
Also the metallic radii of
nickel and phosphorus~ which can be easily combined at certain compositions into an amorphous solid alloy 3 differ only by 3%.
These results indicate
that glassy and amorphous alloys can form when the atomic size disparities
164
AMORPHOUS
are rather tions
small.
ALLOY
Of c o u r s e ,
Vol. 3, No. Z
FILMS
the valences
o f t h e members o f t h e s e c o m b i n a -
are very different. Characterization
Of 9 o n f i ~ u r a t i q n s
i n Amorphous A l l o y s
Both c o n t i n u o u s random and m i c r o c r y s t a l l i n e exhibit
qualitatively
sJJuilar diffraction
by a few b r o a d h a l o s .
is very small it
resolution
to distinguish
It
is expected that
X-ray scattering density
is difficult
microcrystallites
have calculated
and t h e c r y s t a l l i t e
boundaries.
are packed like
in
Warren (9)
small angle scattering
from a silica
"pebbles in a pail".
full
of pebbles.
However,
B i e n e n s t o c k and B a g l e y (10)
t h e u p p e r bound o f t h e s m a l l a n g l e s c a t t e r i n g
gromcrystallite
assemblies with varying proportions
They showed~ a s an e x a m p l e , t h a t from a crystallite
model f o r f u s e d s i l i c a 1
and c r i s t o b a l i t e ~
t o be e x p e c t e d
of boundary void space.
t h e u p p e r bound o f s m a l l a n g l e s c a t t e r i n g
and a v o i d volume e q u a l t o t h e d i f f e r e n c e
with a crystallite
size of 8
i n volume (ca. 3~) b e t w e e n f u s e d
would be t o o s m a l l f o r d e t e c t i o n
with the present
resolution.
However, t o a s s e s s o f t h e minimum d e n s i t y continuities
of structure.
c a n be p a c k e d i n a s o l i d body w i t h a much s m a l l e r p r o p o r t i o n
of void space than in a pail
experimental
experimental
body due t o any n o n - u n i f o r m i t y
is indeed a large
gel in which small particles
characterized
s h o u l d be some e n h a n c e m e n t i n t h e s m a l l a n g l e
between the crystallites there
patterns
to achieve sufficient
b e t w e e n t h e two s o r t s there
i.e.
are expected to
size of the microcrystalline
from a mtcrocrystalline
demonstrated that
silica
patterns,
If the crystallite
structure
structures
the full deficit
significance
required
in the microcrystallite
types of glass
forming systems.
of these results
the problem
t o accommodate t h e s t r u c t u r a l
dis-
model n e e d s t o be s o l v e d f o r t h e v a r i o u s In a system of hard unattracting
spheres at
O°K the density d~f!c!t due t~ 5ound~r!e~ ~p~r~t~g ~!o~e-pe~e~ e r y . t = 1 ~ . m £ s o r i e n K e a t h r o u g h ~ a r g e a n g l e s mxgn~ De ~ p = ~ c u
~u u= u~ ~,= u~u=~ ux v~=
Vol. 3, No. Z
half
AMORPHOUS
o f a monoatomic l a y e r ( 1 1 ) .
m o d e l s o f such b o u n d a r i e s order of density
Inspection
suggests
that
of a m i c r o c r y s t a l l i t e
crystal.
evaluate
the density
measuring the density structure
associated
of solids
with a specified
Although its crystallite
deficit
utility
and c o n t i n u o u s
deficit
of the corresponding
is doubtful structures
deficit
with crystallite
that
the
s i z e 4 atoms a c r o s s 3 bulk single
becomes 15 t o
i t would be i n t e r e s t i n g
definitely
crystallite
is indeed of the
T h i s means, f o r e x a m p l e ,
3 a t o m s wide t h e d e n s i t y
In view of these considerations,
165
of soap-bubble or hard sphere
system 3 with a crystallite than the density
For c r y s t a l l i t e s
FILMS
the density
1/3 t o 1/2 o f a monoatomic l a y e r .
o u g h t t o be 12 t o 17% l e s s
23~.
ALLOY
to try
to
b o u n d a r i e s by
known t o h a v e a m i c r o c r y s t a l l i n e
size. for distinguishing in a s i n g l e
between micro-
phase system,
the small
angle scattering technique can be an extremely sensitive tool for determining whether or not a solid has a microcrystalline polyphase structure.
For
examplej Bagley (12) found a strong enhancement of the small angle X-ray scattering upon crystallizing an originally amorphous nlckel-phosphorus alloy.
These results indicate that~ as formed, the nlckel-phosphorus alloys,
whatever their state of structural continuity 3 were essentially homogeneous in composition. A mlcrocrystalline body might be expected to "crystallize" by a "normal" grain growth process in which many grains grow at the expense of a few. this process the average crystalllte size increases continuously during an isothermal anneal and concurrently the diffuse diffraction halos sharpen continuously.
However, the appearance, microscopically, of an extremely
flne-gralned crystallite structure is not, in itself, unequivocal evidence for a mlcrocrystallite model of the amorphous state for it might have r=cu!tcd fr=~ ce;i~u~ h .....o ....~uc nuc!~atien ~f ~ry~ta!~ in ~ cent!nuous ~K~UCEUr~.
In
166
AMORPHOUS
In contrast
Vol. 3, No. Z
o f an amorphous body i n w h i c h w e l l s e p a r a t e d
and grow t o r e l a t i v e l y
on t h e d i f f u s e
diffraction
crystallization
structure.
pattern
from t h e c r y s t a l s
halo of the matrlxwhich
progresses.
of crystallization
mode o f
crystals
appear
l a r g e s i z e s w i t h no a p p a r e n t c h a n g e s in t h e i n t e r v e n i n g
The s h a r p d i f f r a c t i o n
This nucleation
appear superimposed
remains unchanged as
and growth i s t h e e x p e c t e d mode
o f a n amorphous s o l i d w i t h a c o n t i n u o u s random t y p e o f
It
is not expected in a microcrystalline
analogous to secondary recrystallizatton preferential
FILMS
w i t h n o r m a l g r a i n growth i s t h e d i s c o n t i n u o u s
crystallization
matrix.
ALLOY
segregation
solid
unless a process
i s somehow e f f e c t e d
o f one o f t h e a l l o y
owing t o i n i t i a l
components at the crystallite
boundaries. B a g l e y (12) h a s o b s e r v e d w i t h t r a n s m i s s i o n interesting content,
differences
in the crystallization
of vapor deposited
heat treating diameter)
compositions
crystalline
with a well-defined to change.
crystals
was s u p p o s e d t h a t the crystalline very difficult
crystals
crystallizing,
At
appears not
( 0 . 2 atom ~) o f Ni t o t h e
during heat treatment,
The a p p e a r a n c e o f t h i s
t o a few w i d e l y
morphology.
m o r p h o l o g y was imposed by t h e r e j e c t i o n
to reconcile
(50
a p p e a r and grow
f o r m i n t o a m a t r t x whose s t r u c t u r e
of a very small excess
Ni3P p h a s e .
Upon
i s f o r m e d which t h e n c o a r s e n s u n i f o r m l y .
w h i c h grow w t t h a w e l l d e f i n e d d e n d r i t i c this
alloy.
a p p r o x i m a t i n g Ni4P , a v e r y f i n e - g r a i n e d
polyhedral
amorphous Ni3P l e d t o i t s separated
mode, d e p e n d i n g on p h o s p h o r u s
h o w e v e r , a few w i d e l y s e p a r a t e d
The a d d i t i o n
m i c r o s c o p y some
f i l m s o f amorphous n i c k e l - p h o s p h o r u s
structure
the N~P composition,
electron
dendritic
of nickel
It by
morphology is
w i t h any b u t a c o n t i n u o u s model f o r t h e amorphous
structure. Other observations alloy
of nucleation
films are those reported
formed f i l m s .
and g r o w t h m o r p h o l o g i e s i n amorphous (13) by Duwez a t t h i s c o n f e r e n c e on some s p l a t -
A l s o Nowick (14) and a s s o c i a t e s
have inferred
from t h e i r
Vol. 3, No. Z
kinetic alloys
analysis
AMORPHOUS
a nucleation
of copper-silver
ALLOY
FILMS
167
and g r o w t h mode o f c r y s t a l l i z a t i o n
deposited
o f amorphous
from the vapor.
Acknow led~ement The r e s e a r c h
at Harvard University
alluded
t o in t h i s
r e p o r t was
supported in part by the Office of Naval Research under Contract Nonr 1866(50) and by the Advanced Research Projects Agency under Contract ARPA SD-88. Also B. G. Bagley was a Xerox Corporation Fellow 1964-1966, and an A.S.T.M. Fellow 1966-1967. References I. (a)N. Valenkov and E.A. Poraj-Koslc, Z. Krlst. ~
196 (1936).
(b)N.F. Mott and R.W. Gurney, Rept. Progr. Phys. 5_j 46 (1938). 2.
W.H. Zachariasen, J. Am. Chem. Soc. ~
3841 (1932).
3.
J.D.
4.
J.H. Gibbs and E.A. Di Marzio~ J. Chem. Phys. ~
5.
M.H. Cohen and D. Turnbullj J. Chem. Phys. ~
Bernal, Nature 185, 68 (1960).
120 (1960);
Nature ~
373 (1958). 1164 (1959);
ibid. 34,
964 (1964).
6.
W. Klement~ Jr., R.H. Willens and P. Duwez, Nature 187, 869 (1960).
7.
H.S. Chen, Ph.D. thesis, Division of Engineering and Applied Physlcs~ Harvard University (1967).
8.
H.S. Chen and D. Turnbull~ in press~ J. Chem. Phys., 1968.
See also
Appl. Phys. Letters I0~ 284 (1967) and J. Appl. Phys. 38, 3646 (1967). 9.
B.E. Warren, J. Appl. Phys. 8~ 645 (1937).
I0.
A. Bienenstock and B.G. Bagley, J. Appl. Phys. ~
II.
D. Turnbull, pp. 6-25, in Liquids:
4840 (1966).
Structures, Properties, Solid Inter-
actions, ed. Thomas J. Hughel, Elsevier Publishing Company~ Amsterdam (1965). 12.
B.G. Bagley, Ph.D. thesis, Division of Engineering and Applied Physics, Harvard University (1967).
168
13.
AMORPHOUS
ALLOY
FILMS
Vol. 3, No. Z
P. Duwez, '~morphous Metallic Alloy Phases", 2nd Conference on Characterization of Materials, Rochester, N.Y., 1967.
14.
A.S. Nowlck, "Amorphous Alloys Produced by Vacuum Evaporation", 2nd Conference on Characterization of Materials, Rochester, N.Y., 1967.
This
paper
was
presented
at the Second
International
Conference
on the
Characterization of l~aterials, Rochester, N e w York, N o v e m b e r 8- 10, 1967.