U.S. patent application number 17/209589 was filed with the patent office on 2022-09-29 for high entropy alloy, method of preparation and use of the same.
The applicant listed for this patent is City University of Hong Kong. Invention is credited to Quanfeng He, Hang Wang, Tianyu Wang, Yong Yang.
Application Number | 20220307114 17/209589 |
Document ID | / |
Family ID | 1000005569358 |
Filed Date | 2022-09-29 |
United States Patent
Application |
20220307114 |
Kind Code |
A1 |
Yang; Yong ; et al. |
September 29, 2022 |
HIGH ENTROPY ALLOY, METHOD OF PREPARATION AND USE OF THE SAME
Abstract
A high entropy alloy includes at least five elements selected
from Cobalt, Nickel, Titanium, Zirconium, and Hafnium, wherein two
of the five elements have a total atomic percentage of 100-x, and
the remainder elements have a total atomic percentage of x, where
0<x<100. A method of producing the high entropy alloy. A
component for use in a mechanical timepiece. The component is made
of the high entropy alloy.
Inventors: |
Yang; Yong; (Kowloon Tong,
HK) ; He; Quanfeng; (Kowloon Tong, HK) ; Wang;
Tianyu; (Kowloon Tong, HK) ; Wang; Hang;
(Kowloon Tong, HK) |
|
Applicant: |
Name |
City |
State |
Country |
Type |
City University of Hong Kong |
Kowloon |
|
HK |
|
|
Family ID: |
1000005569358 |
Appl. No.: |
17/209589 |
Filed: |
March 23, 2021 |
Current U.S.
Class: |
1/1 |
Current CPC
Class: |
C22C 30/00 20130101;
B22C 9/061 20130101; C22C 1/02 20130101 |
International
Class: |
C22C 30/00 20060101
C22C030/00; C22C 1/02 20060101 C22C001/02; B22C 9/06 20060101
B22C009/06 |
Claims
1. A high entropy alloy comprising at least five elements selected
from Cobalt, Nickel, Titanium, Zirconium, and Hafnium, wherein two
of the five elements have a total atomic percentage of 100-x, and
the remainder elements have a total atomic percentage of x, where
0<x<100.
2. The high entropy alloy of claim 1, wherein the high entropy
alloy is represented by a chemical formula of
(CoNi).sub.100-x(HfTiZr).sub.x, where x is an atomic percentage and
0<x<100.
3. The high entropy alloy of claim 1, wherein the high entropy
alloy is represented by a chemical formula of
(CoNi).sub.100-x(HfTiZr).sub.x, where 45.ltoreq.x.ltoreq.55.
4. The high entropy alloy of claim 1, wherein the high entropy
alloy has an elastic module that is substantially constant with
respect to a temperature change from 300K to 900K.
5. The high entropy alloy of claim 1, wherein the high entropy
alloy comprises a body centred cubic (BCC) structure.
6. The high entropy alloy of claim 5, wherein atoms of the high
entropy alloy are accommodated within the BCC structure by
atomic-scale chemical ordering.
7. The high entropy alloy of claim 1, wherein the high entropy
alloy comprises a distorted lattice structure.
8. The high entropy alloy of claim 1, wherein the high entropy
alloy has an atomic size difference of about 11%.
9. The high entropy alloy of claim 1, wherein the high entropy
alloy has an elastic limit of about 2%.
10. A method of preparing the high entropy alloy of claim 1,
comprising the steps of: preparing an alloy precursor by arc
melting a predetermined amount of raw materials of each elements
constituting the high entropy alloy in an inert atmosphere; and
casting the melted alloy precursor into a cooled mold to obtain the
high entropy alloy.
11. The method of claim 10, wherein the raw materials comprises
Cobalt, Nickel, Titanium, Zirconium, and Hafnium.
12. The method of claim 11, wherein the raw materials are in atomic
percentages of: 0-50% Cobalt, 0-50% Nickel, 0-33.3% Titanium,
0-33.3% Zirconium, and 0-33.3% Hafnium.
13. The method of claim 10, wherein the raw materials have a purity
of >99.9%.
14. The method of claim 10, further comprising the step of flipping
and remelting the alloy precursor in a repetitive manner.
15. The method of claim 10, wherein the arc melting is conducted
under a Ti-gettered argon atmosphere with a pressure below
8.times.10.sup.-4 Pa.
16. The method of claim 10, wherein the mold is a copper mold.
17. The method of claim 16, wherein the copper mold is a cylinder
or a plate.
18. The method of claim 17, wherein the cylindrical copper mold has
a diameter of 5 mm and a length of 100 mm.
19. The method of claim 17, wherein the plate copper mold has a
dimension of 5.times.10.times.60 mm.sup.3.
20. A component for use in a mechanical timepiece, wherein the
component is made of the high entropy alloy of claim 1.
21. The component of claim 20, wherein the component is a
mainspring and/or a hairspring.
22. The component of claim 20, wherein the mechanical timepiece is
selected from the list comprising mechanical watches, mechanical
chronometers, and marine chronometers.
Description
TECHNICAL FIELD
[0001] The present invention relates to a high entropy alloy in
particular a high entropy alloy comprising at least five elements.
The present invention also pertains to a method of preparing and
use of said alloy.
BACKGROUND OF THE INVENTION
[0002] It is appreciated that metallic materials is particularly
important in various industrial applications, including but not
limiting to actuators, medical devices, and high precision
instruments. Several metallic materials may be generally used for
the aforementioned applications, yet each of them possesses
different kinds of defects.
[0003] For example, bulk crystalline metals plastically deform
through dislocations, twinning and/or grain boundary sliding, which
limit the elastic strain of bulk crystalline metals to .about.0.2%
at room temperature. The use of bulk amorphous alloys in industrial
applications may be hindered by the high cooling rate requirement
which severely limits the size of the alloys to be produced. On the
other hand, whilst shape memory alloys and gum metals may be
capable of achieving a large elastic strain limit (.about.2%), such
a high strain limit is generally associated with significant
mechanical hysteresis and energy dissipation.
[0004] Accordingly, there remains a strong need for developing
metallic materials such as alloy materials that are capable of
exhibiting linear elastic response to very high strains without
hysteresis, and elastic properties which are
temperature-insensitive (to high temperature).
SUMMARY OF THE INVENTION
[0005] The first aspect of the present invention relates to a high
entropy alloy comprising at least five elements selected from
Cobalt, Nickel, Titanium, Zirconium, and Hafnium, wherein two of
the five elements have a total atomic percentage of 100-x, and the
remainder elements have a total atomic percentage of x, where
0<x<100.
[0006] Advantageously, the inventors have first devised that by
tuning the chemical composition of the high entropy alloy, it may
engineer the disorder of the high entropy alloy, thereby providing
a new route to create temperature-independent, ultra-elastic
behavior in a wide range of materials.
[0007] In particular, the high entropy alloy is represented by a
chemical formula of (CoNi).sub.100-x(TiZrHf).sub.x, where x is an
atomic percentage and 0<x<100.
[0008] Preferably, the high entropy alloy is represented by a
chemical formula of (CoNi).sub.100-x(TiZrHf).sub.x, where
45.ltoreq.x.ltoreq.55.
[0009] In an embodiment, the high entropy alloy has an elastic
module that is substantially constant with respect to a temperature
change from 300K to 900K.
[0010] In another embodiment, the high entropy alloy comprises a
body centred cubic (BCC) structure. In particular, atoms of the
high entropy alloy are accommodated within the BCC structure by
atomic-scale chemical ordering.
[0011] In another embodiment, the high entropy alloy comprises a
distorted lattice structure.
[0012] In another embodiment, the high entropy alloy has an atomic
size difference of about 11%.
[0013] In another embodiment, the high entropy alloy has an elastic
limit of about 2%.
[0014] The present invention in another aspect provides a method of
producing a high entropy alloy as described above. The method
comprises the steps of: [0015] preparing an alloy precursor by arc
melting a predetermined amount of raw materials of each elements
constituting the high entropy alloy in an inert atmosphere; and
[0016] casting the melted alloy precursor into a cooled mold to
obtain the high entropy alloy.
[0017] In an embodiment, the raw materials comprises Cobalt,
Nickel, Titanium, Zirconium, and Hafnium. In particular, the raw
materials are in atomic percentages of: 0-50% Cobalt, 0-50% Nickel,
0-33.3% Titanium, 0-33.3% Zirconium, and 0-33.3% Hafnium.
[0018] In another embodiment, the raw materials have a purity of
>99.9%.
[0019] In another embodiment, the method further comprises the step
of flipping and remelting the alloy precursor in a repetitive
manner.
[0020] In another embodiment, the arc melting is conducted under a
Ti-gettered argon atmosphere with a pressure below
8.times.10.sup.-4 Pa.
[0021] In another embodiment, the mold is a copper mold. In
particular, the copper mold is a cylinder or a plate.
[0022] In another embodiment, the cylindrical copper mold has a
diameter of 5 mm and a length of 100 mm.
[0023] In another embodiment, the plate copper mold has a dimension
of 5.times.10.times.60 mm.sup.3.
[0024] Further provided with the present invention is a component
made of the high entropy alloy as described above for use in a
mechanical timepiece. In particular, the component is a mainspring
and/or a hairspring.
[0025] In an embodiment, the mechanical timepiece is selected from
the list comprising mechanical watches, mechanical chronometers,
and marine chronometers.
[0026] Those skilled in the art will appreciate that the invention
described herein is susceptible to variations and modifications
other than those specifically described. The invention includes all
such variations and modifications. The invention also includes all
steps and features referred to or indicated in the specification,
individually or collectively, and any and all combinations of the
steps or features.
[0027] Other features and aspects of the invention will become
apparent by consideration of the following detailed description and
accompanying drawings.
BRIEF DESCRIPTION OF THE DRAWINGS
[0028] FIG. 1 is a plot showing the X-ray Diffraction (XRD)
patterns of different alloys having a chemical formula of
(CoNi).sub.100-x(TiZrHf).sub.x.
[0029] FIG. 2 is a bar chart showing the microhardness of different
alloys having a chemical formula of
(CoNi).sub.100-x(TiZrHf).sub.x.
[0030] FIG. 3 is a bar chart showing the Young's modulus of
different alloys having a chemical formula of
(CoNi).sub.100-x(TiZrHf).sub.x.
[0031] FIG. 4 is a plot showing the storage modulus against
different temperature of different alloys having a chemical formula
of (CoNi).sub.100-x(TiZrHf).sub.x.
DETAILED DESCRIPTION OF THE INVENTION
[0032] Unless otherwise defined, all technical terms used herein
have the same meaning as commonly understood by one skilled in the
art to which the invention belongs.
[0033] As used herein, "comprising" means including the following
elements but not excluding others. "Essentially consisting of"
means that the material consists of the respective element along
with usually and unavoidable impurities such as side products and
components usually resulting from the respective preparation or
method for obtaining the material such as traces of further
components or solvents. The expression that a material is certain
element is to be understood for meaning "essentially consists of"
said element. As used herein, the forms "a," "an," and "the," are
intended to include the singular and plural forms unless the
context clearly indicates otherwise.
[0034] It is intended that reference to a range of numbers
disclosed herein (for example, 1 to 10) also incorporates reference
to all rational numbers within that range (for example, 1, 1.1, 2,
3, 3.9, 4, 5, 6, 6.5, 7, 8, 9 and 10) and also any range of
rational numbers within that range (for example, 2 to 8, 1.5 to 5.5
and 3.1 to 4.7) and, therefore, all sub-ranges of all ranges
expressly disclosed herein are hereby expressly disclosed. These
are only examples of what is specifically intended and all possible
combinations of numerical values between the lowest value and the
highest value enumerated are to be considered to be expressly
stated in this application in a similar manner.
[0035] In general, it is appreciated that the formation of
concentrated multi-component alloys (i.e. high entropy alloys,
HEAs) requires minimization of overall atomic size misfit in these
alloys so as to form single-phase solid solutions, or otherwise it
would favors the formation of amorphous phase structure.
[0036] Without wishing to be bound by theories, the inventors have,
through their own research, trials, and experiments, devised a high
entropy alloy in which the atomic size misfit may be considered to
be too large in view of the conventional solid solution alloy
design rules. The high entropy alloy of the present invention may
also have an atomic-scale distortions within a single crystalline
phase, which renders the high entropy alloy an ultra-large elastic
strain limit and negligible internal friction at room temperature,
and substantially constant elastic properties up to 900K.
[0037] The high entropy alloy provided by the present invention
comprises at least five elements selected from Cobalt, Nickel,
Titanium, Zirconium, and Hafnium. In particular, two of the five
elements have a total atomic percentage of 100-x, and the remainder
elements have a total atomic percentage of x, where 0<x<100.
In other words, the high entropy alloy may be represented by a
chemical formula of (AB).sub.100-x(CDE).sub.x, where A, B, C, D,
and E are not identical and each of which is selected from Cobalt,
Nickel, Titanium, Zirconium, and Hafnium.
[0038] In one example, the high entropy alloy may be represented by
a chemical formula of (CoNi).sub.100-x(TiZrHf).sub.x, where x is an
atomic percentage and 0<x<100. Preferably, the high entropy
alloy may be represented by a chemical formula of
(CoNi).sub.100-x(TiZrHf).sub.x, where 45.ltoreq.x.ltoreq.55.
[0039] In one example embodiment, the inventors have applied the
following equation (Eq. 1) and devised that the high entropy alloy
of the present invention may have an atomic size difference that is
considered to be too large for forming a stable, single phase
structure:
Delta= {square root over (.SIGMA..sub.i=1.sup.Nc.sub.i(1-r.sub.i
{square root over (r)}).sup.2)} (Eq. 1),
[0040] where N is the number of constituent elements in the alloy,
c.sub.i the atomic fraction of the i-th component, r.sub.i the
atomic radius of the i-th component and r the average atomic
radius; the atomic radii of the constituent elements are 1.251
.ANG. for Co, 1.246 .ANG. for Ni, 1.578 .ANG. for Hf, 1.462 .ANG.
for Ti and 1.603 .ANG. for Zr.
[0041] For example, the value of x may be equal to 50, i.e. the
high entropy alloy may have a chemical formula of
(CoNi).sub.50(TiZrHf).sub.50, the atomic size difference may be
calculated to be about 11%. It is appreciated that in general the
Delta value may be of 5 or even less in conventional solid solution
alloy design rules/theories. The atomic size difference of the high
entropy alloy in the present disclosure would therefore have been
considered significantly large and such a large atomic size
difference would have destabilized the crystalline structure of the
as-formed HEAs, leading to either phase separation or the formation
of a single, amorphous structure.
[0042] Unexpectedly, the inventors found that the high entropy
alloy of the present invention generally comprises a stable, single
phase structure. With reference to FIG. 1, there is provided with a
plot showing the X-ray diffraction (XRD) patterns of various
alloys. As shown, all the high entropy alloys of
(CoNi).sub.45(TiZrHf).sub.55, (CoNi).sub.50(TiZrHf).sub.50, and
(CoNi).sub.55(TiZrHf).sub.45 possess a single phase structure
without any substantial phase separation as compared with the
conventional alloys of (CoNi).sub.100 and (TiZrHf).sub.100, which
have a single phase face centred cubic (FCC) and a single phase
hexagonal closely packed (HCP) structure, respectively. In
particular, the high entropy alloys have a single phase body
centred cubic (BCC) structure, particularly an ordered BCC-like
structure, i.e. a B2 structure.
[0043] Within the BCC structure, atoms of the high entropy alloy
may be accommodated by atomic-scale chemical ordering. In one
example, the atoms may be accommodated within the BCC structure in
an ordered manner. For example, sites in sublattice A of the B2
structure (corner sites of BCC unit cell) may be occupied at random
with {Co, Ni} and sites in sublattice B (center sites of the BCC
unit cell) may be occupied at random with {Hf, Ti, Zr}. In another
example, the atoms may be accommodated in a partially ordered
manner such as with 25% of Zr atoms from sublattice A exchanging
with Co and Ni atoms on sublattice B.
[0044] In addition to the atomic-scale chemical ordering, the high
entropy alloy of the present invention may have a distorted lattice
structure. Namely, the structure of the high entropy alloy may have
a combination of atomic-scale chemical ordering and lattice
distortion.
[0045] The combination of atomic-scale chemical ordering and
lattice distortion within the single phase structure of the high
entropy alloy may be advantageous for said high entropy alloy to
offer outstanding mechanical properties as compared with
conventional alloys and/or HEAs with minimized atomic size
difference. For example, with reference to FIGS. 2-4, there are
provided with a plurality of plots illustrating the microhardness
and Young's modulus of the different alloys. As shown in FIG. 2,
all the high entropy alloys possess a microhardness of at least 480
HV, which is apparently higher than those of the conventional
alloys (CoNi).sub.100 and (TiZrHf).sub.100. In particular, the
microhardness of (CoNi).sub.45(TiZrHf).sub.55 is about 800 HV,
which is the highest among the three high entropy alloys.
[0046] Turning now to FIG. 3, there is provided with a plot
illustrating the Young's modulus of the different alloys at room
temperature. The term "Young's Modulus" generally refers as
"elastic modulus" which defines a material's resistance to
non-permanent, or elastic, deformation. "Elastic deformation"
generally refers to the change of physical state such as shape of
the material when an external force is applied thereto, and the
material will return to its original state after the stress is
removed. It is appreciated that once a material experiences an
external force that could overcome such resistance, the material
will deform permanently, i.e. the material no longer be able to
return to its original state even the external force is removed.
Namely, a material with a higher modulus would require a larger
amount of external force to overcome such resistance, or in other
words a material with a small modulus would deform permanently
under such the same amount of external force. As shown in FIG. 3,
the high entropy alloys of (CoNi).sub.45(TiZrHf).sub.55,
(CoNi).sub.50(TiZrHf).sub.50, and (CoNi).sub.55(TiZrHf).sub.45
possess a Young's modulus at room temperature ranging from about
100 to 130 GPa, which is comparable to the conventional alloys
(CoNi).sub.100 and (TiZrHf).sub.100. That is, the high entropy
alloys have a comparable resistance to non-permanent, or elastic,
deformation as if the conventional alloys at room temperature.
[0047] In addition to the comparable Young's modulus at room
temperature, it is advantageous that the high entropy alloys may
have an elastic module that is substantially constant with respect
to a temperature change up to a temperature of at least 600 K,
particularly at least 700 K, preferably at least 800 K, most
preferably at least 900 K. For example, with reference to FIG. 4,
there is provided a plot illustrating a change of Young's modulus
of different alloys against different temperatures. As shown, the
Young's modulus of the conventional alloys decreases gradually
toward 0 as the temperature increases from 300 K to 900 K, in which
(CoNi).sub.100 decreases sharply toward 0 at about 550 K whereas
(TiZrHf).sub.100 decreases toward 0 at a constant rate with the
temperature increase. In sharp contrast, all the high entropy
alloys showed a substantially constant Young's modulus when the
temperature increases from 300 K to 900 K. In other words, it may
be considered that the elasticity of the high entropy alloys of the
present invention remains substantially unchanged with respect to a
wide range of temperature, or the high entropy alloys have an
Elinvar effect over a temperature of 300 K to 900 K.
[0048] The present invention in another aspect provides a method of
preparing the high entropy alloy as described above. The method
comprises the steps of: preparing an alloy precursor by arc melting
a predetermined amount of raw materials of each elements
constituting the high entropy alloy in an inert atmosphere; and
casting the melted alloy precursor into a cooled mold to obtain the
high entropy alloy.
[0049] In one example, the alloy precursor may be prepared by
providing the raw materials in atomic percentages of: 0-50% Cobalt,
0-50% Nickel, 0-33.3% Titanium, 0-33.3% Zirconium, and 0-33.3%
Hafnium in an arc furnace. The raw materials may be of a high
purity such as >90%, particularly >95%, preferably >99%,
most preferably >99.90%.
[0050] The aforementioned raw materials may be melted in an arc
furnace under an inert atmosphere. Preferably, the arc furnace is
pump-filled with Ti-gettered argon gas, for example, 5 times such
that the pressure inside the furnace is less than 8.times.10.sup.-4
Pa.
[0051] During the arc melting process, the raw materials may be
flipped and remelted in a repetitive manner so as to ensure
chemical homogeneity. In other words, to ensure each of the raw
material components are uniformly distributed. Preferably, the raw
materials are flipped and re-melted for at least five times.
[0052] Once the raw materials are completely arc melted, the
resultant material, that is the melted alloy precursor, may be
casted into a cooled mold to form the high entropy alloy. In
particular, the melted alloy precursor may be casted into a copper
mold of different shapes and dimensions so as to obtain a high
entropy alloy of desired shape and dimension. In one example, the
melted alloy precursor may be casted into a cylindrical copper mold
having a diameter of 5 mm and a length of 100 mm. In another
example, the melted alloy precursor may be casted into a plate
copper mold having a dimension of 5.times.10.times.60 mm.sup.3.
[0053] As mentioned above, the high entropy alloy of the present
invention is advantageous as its mechanical properties,
particularly the elastic properties remain substantially unchanged
over a wide range of temperature. This property may render the high
entropy alloy of the present invention particularly suitable for
use in components that require to be operated in harsh
environments. Thus, further provided with the present invention is
a component for use in a mechanical timepiece, where the component
is made of the high entropy alloy as described above.
[0054] In one example, the component may be a mainspring and/or a
hairspring of a mechanical timepiece. In particular, the mechanical
timepiece may be selected from the list comprising mechanical
watches, mechanical chronometers, and marine chronometers. It is
appreciated that mechanical timepieces are generally driven by a
mainspring of which the force is transmitted through a series of
gears to power the balance wheel (including a balance spring (i.e.
hairspring)), a weighted wheel which oscillates back and forth at a
constant rate.
[0055] As temperature increases, it would significantly affect the
timekeeping of the balance wheel and the balance spring as a result
of decrease in Young's modulus of the balance spring. Whilst it may
be overcome by using a temperature-compensated balance wheel, said
temperature-compensated balance wheel is generally inoperable at
extremes of temperature. Meanwhile, although some "auxiliary
compensation" mechanisms may be used to avoid this situation, all
of them suffer from being complex and hard to adjust.
[0056] With the high entropy alloy of the present invention to be
used in the mechanical timepiece components, the
temperature-insensitive elastic property of the high entropy alloy
may allow the component to be operated over a wide range of
temperature without the need of "temperature compensation" even at
an extreme temperature such as at 900 K. Thus, advantageously, it
may simplify the mechanical mechanism and therefore the
manufacturing process of the mechanical timepieces.
EXAMPLES
Materials and Reagents Used
[0057] The polycrystalline samples of the high entropy alloy
Co.sub.25Ni.sub.25(HfTiZr).sub.50 (atomic %) were prepared through
arc-melting in a high purity argon atmosphere. The purities of the
raw materials for each element were at least 99.9 wt. %. The ingots
were remelted at least four times to ensure the chemical
homogeneity, and then suction cast into a copper mold. Two
different types of copper mold (rod and plate) were used. The
dimension of the cylindrical mold was 5 mm in diameter and 100 mm
in length while that of the plate mold was 5.times.10.times.60
mm.sup.3. The single crystal Co.sub.25Ni.sub.25(HfTiZr).sub.50
alloys were prepared by a high rate directional solidification
method following the standard procedure.
Instrumentation and Methods Applied
[0058] The X-ray diffraction (XRD) instrument (Rigaku Smartlab) was
used to identify the crystalline structure.
[0059] Dynamical mechanical analyses were performed in the
commercial DMA equipment (Mettler Toledo, DMA1 STAR System). The
experiments were carried out by applying a sinusoidal stress at the
fixed frequency of 1 Hz during continuous heating at the constant
heating rate of 5 K/min. The testing samples had a dimension of
30.times.3.times.1.5 mm.sup.3. The testing was performed in
three-point bending mode.
Example 1
Synthesis and Characterization of
Co.sub.25Ni.sub.25(HfTiZr).sub.50
[0060] The high entropy alloy Co.sub.25Ni.sub.25(HfTiZr).sub.50
(atomic %) (i.e. (CoNi).sub.50(HfTiZr).sub.50) was prepared via arc
melting method. Unlike conventional single phase HEAs, the atomic
size difference of Co.sub.25Ni.sub.25(HfTiZr).sub.50 alloy is
extremely large, which is calculated to be about 11% based on Eq.1,
relative to standard approaches used for single phase alloy design.
It is appreciated that the established alloy phase rules/theories
suggest that such a large atomic size misfit will destabilize the
crystalline structure, leading to either phase separation or the
formation of a single phase, amorphous structure. X-ray diffraction
(XRD) result demonstrated that the
Co.sub.25Ni.sub.25(HfTiZr).sub.50 high entropy alloy is a
single-phase crystal with a nominally body-centered cubic (BCC)
like structure.
Example 2
Mechanical Properties of Co.sub.25Ni.sub.25(HfTiZr).sub.50
[0061] The mechanical properties were characterized by
microhardness device. The hardness and young's modulus values of
these alloys are presented in FIG. 2 and FIG. 3. The elastic strain
limit of the Co.sub.25Ni.sub.25(HfTiZr).sub.50 high entropy alloy
is about 2%.
Example 3
Elinvar Effect of Co.sub.25Ni.sub.25(HfTiZr).sub.50
[0062] With reference to the FIG. 4, the elastic modulus of the
Co.sub.25Ni.sub.25(HfTiZr).sub.50 alloy remained constant as the
temperature increases, suggestive of an Elinvar effect
(temperature-independent elastic constants). Similarly, the elastic
modulus of (CoNi).sub.100-x(HfTiZr).sub.x, where x=45 and 55 are
nearly constant with increasing temperature.
* * * * *