CN1341771A - Large-block amorphous alloy component design method - Google Patents
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Abstract
The design method of large-block amorphous alloy composition, belonging to the field of new material technology, is characterized by that: (1) formation of large-block amorphous body must meet the isoelectronic concentration and isoatomic size criterion; and (2) accordingly it can accurately and quantitatively design the amorphous component. As an implemented example, in Zr-Al-Ni-Cu system the optimum amorphous component is approaching to Zr 63.8 Al 11.4 No.17.2 Cu 7.6. Said invention first advances the quantized amorphous alloy component criterion, and features simple and easy application, accurate reliability and clear theoretical basis, can be extensively used for component optimization of amorphous alloys of Zr, Ti, Pd, Al and rare earth, etc. and designing new amorphous alloy.
Description
The invention belongs to field of new.Specially refer to Zr base alloy system be representative the large-block amorphous alloy component design quantivative approach and come from the new Zr-Al-Ni-Cu amorphous of this method.
Amorphous metal alloy is owing to the randomness of its structure has very high comprehensive mechanical property and extraordinary physical and chemical performance.Yet because the influence of amorphous formation ability prepares the higher rate of cooling of such material require, general critical cooling rate is 10
5K/s.With cooling rate is preface from high to low, and chilling technique commonly used has: melt atomizing, film deposition techniques and copper roller chilling get rid of the band machine, and material shape is powder, strip etc., and therefore its range of application is restricted.
Since the beginning of the nineties, headed by the Japan and the U.S., a series of alloying constituents have been found with big amorphous formation ability, wherein be easy to the most make with the Zr base, its critical cooling rate is only in the 1K/s magnitude, can cast and method such as shrend is prepared into block materials with copper mold, therefore obtain extensive concern, be called as large block amorphous.Representational composition has Inoue alloy Zr
65Al
7.5Ni
10Cu
17.5And the serial Zr-Al-Ni-Cu-Be alloy of U.S. Johnson release, wherein the former supercooling liquid phase region reaches known maximum value, is 127K, casts with copper mold and can make non-crystal bar or the plate of size in centimetre magnitude.These materials obtain practical application at aspects such as golf club head, armour piercing shots.
But up to now, still Nobody Knows for the composition rule of non-crystaline amorphous metal, can't definitely predict amorphous component, can not confirm to comprise whether the known non-crystaline amorphous metal of Inoue non-crystaline amorphous metal is best amorphous component.Its reason mainly contains 2 points, and the one, these materials are multicomponent system, are generally ternary, and the Inoue alloy is a quaternary, and the Johnson alloy is five yuan, one of the every increase of element kind, the variable number that consider is a square increase, and the complex nature of the problem sharply strengthens; The 2nd, non-crystaline amorphous metal has many underlying issues unintelligible, from the atomic structure to the electronic structure, also has the problem of many materialogies and physics intercrossing.
The quantifying design method that the purpose of this invention is to provide a kind of large-block amorphous alloy component of practicality, this method is to utilize multicomponent system and the electronic structure of subgroup unit system and the contact on the atomic structure, predict that from the characteristics of subgroup unit system the amorphous of multicomponent system becomes rule, and be designed to example with the composition of Zr-Al-Ni and Zr-Al-Ni-Cu non-crystaline amorphous metal, its principle and using method are described, provide Zr-Al-Ni-Cu bulk amorphous alloys new constituent series simultaneously with high amorphous formation ability by its acquisition.
Realize that method of the present invention is, at first multicomponent system is considered as the combination of the first system of a plurality of subgroups, as ternary amorphous system is decomposed into binary amorphous system, the amorphous of analyzing in the subgroup unit system becomes rule, finds the composition of known amorphous formation ability maximum; Secondly, obtain the atomic size and the electron density information of the first amorphous of these best subgroups, with its criterion as polynary amorphous component; At last, on phasor, find out the composition of the desirable amorphous that satisfies these two kinds of criterions simultaneously.Desirable amorphous refers to have the amorphous of maximum amorphous formation ability in a given alloy system, its composition need satisfy the requirement on atomic size and the electron density.
Principle of the present invention is as follows.
In the stability influence factor of alloy phase, electronic structure and atomic size are the most common.For all alloy phases, these two kinds of factors all work simultaneously, are called as the electronics phase based on the former alloy phase, or the Hume-Rothery phase, have specific valence electron concentration; Alloy phase based on the latter mainly contains the Laves phase, and its structure is a feature with topological Mi Dui, and atomic arrangement has high coordination.
Non-crystaline amorphous metal with high amorphous formation ability can be regarded the alloy phase with frozen composition as, and its formation depends on electronic structure and atomic size.
By to M
1-xX
xThe experiment of binary alloy, here, M refers to transition group or precious metal, X refers to the 4th or pentels, it is found that the desirable amorphous correspondence with maximum amorphous formation ability a fixed electron density value e/a=∑ C
i* N
i, C wherein
iAnd N
iBe respectively the contribution of the atomic percent mark of i constituent element and valence electron, ∑ represent to add and, the valence electron number that on behalf of average each atom, e/a then had.In theory, the Fermi surface of desirable amorphous is called as the Nagel-Tauc rule with tangent by the defined pseudo-brillouin zone of strong diffraction, and mathematical expression can be expressed as k
p≈ 2k
f, wherein, k
fBe the Fermi sphere radius, k
pBe the length of the pairing reciprocal vector in brillouin zone, about equal sign ≈ shows this equation approximately equal, and usually, Fermi sphere will overflow the brillouin zone, so 2k
fBe greater than k
p, but the degree that departs from is very little, and embodiments of the invention will specify.This rule illustrates that desirable amorphous is a kind of Hume-Rothery phase, and its stability depends primarily on the interaction of Fermi sphere and brillouin zone.
Large block amorphous being present in the above alloy system of ternary, generally has sizable supercooled liquid district Δ T
x, the thermostability of this parameter characterization amorphous.In the Zr-Al-Ni-Cu alloy system, Inoue alloy Zr
65Al
7.5Ni
10Cu
17.5Be one of known best non-crystaline amorphous metal, its Δ T
xValue is 127K.System experimentation research by to the Zr-Al-Ni-Cu alloy system it is found that amorphous phase and several crystal are the Hume-Rothery phase with close electron density mutually, illustrates that they have confidential relation on electronic structure.In view of the above, from the angle of electronic structure, the present invention sets up first new criterion that acquisition has the amorphous alloy component of big amorphous formation ability: the composition of desirable amorphous satisfies specific electron density in a given alloy system.In ternary alloy phase diagram, this electron density is represented a constant electron concentration line; In the quad alloy phasor, this electron density is corresponding to a constant electron concentration face.This new criterion is supported by known amorphous component, amorphous component and aforesaid crystal in the amorphous component in ternary Zr-Al-Ni, the Zr-Al-Cu alloy system and the Zr-Al-Ni-Cu alloy system of quaternary all have proximate electron density mutually, be reflected in the Zr-Al-Ni-Cu quarternary phase diagram, their one-tenth branch is positioned at e/a=1.4-1.5 constant electron concentration face scope.
The composition of above-mentioned non-crystaline amorphous metal and crystal phase is concentrated near the straight line that is distributed on the constant electron concentration face, illustrates to have another influence factor.The atoms of elements size of forming non-crystaline amorphous metal has material impact to amorphous formation ability, but, people have only considered the difference in size between the individual element, do not consider the comprehensive action of the element size of component alloy, at this, the present invention introduces second new criterion that acquisition has the amorphous alloy component of big amorphous formation ability: the composition of desirable amorphous satisfies specific average atom size R in a given alloy system
a, be defined as alloy composition atoms of elements size becomes branch with it long-pending and R
a=∑ C
i* R
i, R wherein
iIt is the Goldschmidt atomic radius of i constituent element.Constant atomic size is meant that some kinds of different alloys of composition have identical average atom size in the alloy system, like this, can define the constant atomic size face in quarternary phase diagram.For example in the Zr-Al-Ni-Cu alloy phase diagram, the one-tenth branch of known non-crystaline amorphous metal and relevant crystal phase all drops on e/a=1.38 constant electron concentration face and R
aThe intersection zone of=0.1496nm constant atomic size face.So far, the present invention has set up the new criterion system of electron density and average atom size, and the alloy that satisfies these two requirements has big amorphous formation ability, and is defined as desirable amorphous.For quaternary system, these two criterions can only provide the optimal components line; For ternary system, this criterion directly provides best amorphous component point.
Effect of the present invention and benefit are to have proposed amorphous alloy component design method first, this method has and is simple and easy to can be widely used in the design of the optimizing components and the new non-crystaline amorphous metal of all kinds of non-crystaline amorphous metals such as Zr, Ti, Pd, Al, rare earth with, accurate reliable, theoretical basis characteristics clearly.
Accompanying drawing and subordinate list explanation.
Accompanying drawing is a Zr-Al-Ni-Cu quad alloy phasor.The one-tenth branch that marks among the figure be known amorphous with crystal mutually, wherein the a-c point is a Zr-Al-Ni ternary amorphous, among the figure by
Sign, d-f is a Zr-Al-Cu ternary amorphous, by the ◇ sign, g-h is ZrCu among the figure
2Type and Al
2NiZr
6Type crystallization phase, among the figure by
Sign, I is Inoue amorphous component Zr
65Al
7.5Ni
10Cu
17.5, among the figure by
Sign.The light color face is an e/a=1.38 constant electron concentration face, and dark face is R
a=0.1496nm constant atomic size face.
Subordinate list is the composition of Zr-Al-Ni-Cu non-crystaline amorphous metal and the characteristic temperature table that records.
| Sequence number | Alloy | ??T g | ??T x | ??ΔT x | ????T m | ????T l | ??T g/T m | ??T g/T l | T l-T m |
| ??1 | ??Zr 65.5Al 5.6Ni 6.5Cu 22.4 | ??636 | ??733 | ??97 | ?1089.4 | ??1210.9 | ??0.584 | ??0.525 | ??121.5 |
| ??2 | ??Zr 65.3Al 6.5Ni 8.2Cu 20 | ??640 | ??745 | ??105 | ?1089.1 | ??1188.3 | ??0.588 | ??0.539 | ??99.2 |
| ??3 | ??Zr 65Al 7.5Ni 10Cu 17.5 | ??650 | ??750 | ??100 | ?1093.7 | ??1153.3 | ??0.594 | ??0.564 | ??59.6 |
| ??4 | ??Zr 64.8Al 8.3Ni 11.4Cu 15.5 | ??653 | ??752 | ??99 | ?1085.5 | ??1142.7 | ??0.602 | ??0.572 | ??57.2 |
| ??5 | ??Zr 64.5Al 9.2Ni 13.2Cu 13.1 | ??658 | ??757 | ??99 | ?1090.0 | ??1137.6 | ??0.604 | ??0.578 | ??47.6 |
| ??6 | ??Zr 63.8Al 11.4Ni 17.2Cu 7.6 | ??671 | ??758 | ??87 | ?1100.1 | ??1153.3 | ??0.610 | ??0.582 | ??53.2 |
T in the subordinate list
gSecond-order transition temperature, T
xCrystallization temperature, supercooling liquid phase region Δ T
x, T
mSolidus, T
lLiquidus point, T
g/ T
mOr T
g/ T
lThe reduction glass transformation temperature, T between liquid phase region
l-T
m
Below in conjunction with accompanying drawing and subordinate list, describe two most preferred embodiments determining the desirable amorphous component in Zr-Al-Ni and the Zr-Al-Ni-Cu system in detail.
Embodiment one: the desirable amorphous among the Zr-Al-Ni
Step 1: ternary system is decomposed into binary amorphous system, is Zr-Ni and Zr-Al system here.
Step 2: obtain best amorphous component point in the binary amorphous system, amorphous forms has a Composition Region, in order to judge best binary amorphous component point, need to understand dark eutectic point and other auxiliary data, as whether satisfying the Nagel-Tauc rule, whether whether the amorphous volumetric shrinkage is minimum, dark eutectic point etc.For the Zr-Ni system, it is Zr that people have known its best amorphous component
9Ni
4For Zr-Al system, its composition is Zr
2Al
3For Zr-Cu system, its composition is Zr
2Cu.
Step 3: the average atom size R that calculates these best binary amorphous components
aIf numerical value is close, then with the R of its mean value as relevant ternary non-crystaline amorphous metal
aValue.For Zr
9Ni
4, R
a=0.1492nm; For Zr
2Al
3, R
a=0.1498nm; For Zr
2Cu, R
a=0.1493nm, they all have close equal atomic size, and R averages
a=0.1494nm, its composition is followed 0.1494=C
Zr* R
Zr+ C
Al* R
Al+ C
Ni* R
Ni, or C
Al+ 2.06 * C
Ni=0.6235, this claims the constant atomic size line corresponding to straight line on ternary phase diagrams.Consider the composition deviation, R in given alloy system
aError at ± 0.001nm.Notice that in the different alloy systems, all atomic size is different, its value is relevant with amorphous neighbour structure with the element kind.
Step 4: calculate electron density e/a, investigate k
p≈ 2k
f, promptly see the requirement of whether satisfying desirable amorphous.For present embodiment, the electron density of these binary amorphous is different, and e/a is respectively 1.04 and 2.4, all is not desirable amorphous, does not satisfy k
p≈ 2k
fTherefore also must find out the electron density value of desirable amorphous.
Contain 3d transiting group metal elements Ni and 4d transiting group metal elements Zr in the element of component alloy, their valence electron number determines it is very important, and according to Theoretical Calculation and experimental result, the valence electron number of Zr is+1.5, the valence electron number of Ni is 0, the valence electron number of Al and Cu is respectively+and 3 and+1.
Desirable amorphous satisfies k
p≈ 2k
f, wherein, k
pBe the length of the pairing reciprocal vector in amorphous diffuse diffraction peak, can measure k from diffractogram
fBe the Fermi sphere radius, can calculate according to free-electron model: k
f=(3 π
2N)
1/3, wherein N is the valence electron number in the unit volume, N=ρ * (e/a), ρ is the atomicity in the unit volume, can obtain by crystalline structure data or density.For binary Zr
70Ni
30Amorphous, its ρ value is 51.76nm
-3, k
pBe 25.8nm
-1, according to k
p≈ 2k
fThe ideal electron density that calculates should be e/a=1.40, corresponding to Zr
93Ni
7Composition departs from the actual constituent of alloy far away, that is to say that the Zr-Ni system can not produce the desirable amorphous that satisfies atomic size and electron density simultaneously.For known Zr
60Al
20Ni
20Ternary amorphous, ρ are 51.95nm
-3, k
pBe 25.67nm
-1, according to k
f=(3 π
2N)
1/3=k
p/ 2 calculate, and its e/a should be 1.37, and e/a=1.5 is approaching with actual value.Here there are 2 practical situation to be illustrated.The one, Fermi sphere should overflow the brillouin zone, i.e. Fermi sphere diameter 2k
fShould be greater than the length k of the pairing reciprocal vector in amorphous diffuse diffraction peak that records in the experiment
p, therefore above-mentioned e/a deviation is normal; The 2nd, the peak position measurement of amorphous diffuse diffraction has error, adds the deviation on alloy density and the composition, and the error of actual electron density is in ± 0.1 scope.In conjunction with above-mentioned consideration, the electron density of the desirable amorphous in Zr-Al-Ni is the 1.4-1.5 scope.Correspondingly, its composition is at two straight line 1.4=C
Zr* 1.5+C
Al* 3+C
Ni* 0 and 1.5=C
Zr* 1.5+C
Al* 3+C
NiBetween * 0, these two parallel lines equations can be reduced to C
Ni-C
Al=0.067 and C
Ni-C
Al=0.
Step 5: the intersection area of constant atomic size line and constant electron concentration line is the Composition Region of desirable amorphous, satisfies electron density and atomic size requirement simultaneously.Desirable amorphous corresponding to e/a=1.4 is Zr
62Al
16Ni
22, be Zr corresponding to the composition of the desirable amorphous of e/a=1.5
60Al
20Ni
20, the latter is known amorphous component.
The present invention's design has also prepared serial Zr-Al-Ni non-crystaline amorphous metal, confirms at e/a=1.37-1.53 R
aForm amorphous in=0.1496～0.1505nm scope, corresponding composition range is Zr
62.9 ± 1.6Al
16.9 ± 35Ni
20.2 ± 1.9, and Zr
60Al
20Ni
20The formation ability of amorphous is the strongest, its e/a=1.5, R
a=0.1496nm.
Embodiment two: the desirable amorphous in the Zr-Al-Ni-Cu system
Step 1: quaternary system is decomposed into ternary amorphous system, and wherein Zr-Al-Ni and Zr-Al-Cu are main ternary amorphous systems.
Step 2: obtain best amorphous component point in the ternary amorphous system, as described in embodiment one, the desirable amorphous component of Zr-Al-Ni is Zr
60Al
20Ni
20
Step 3: the average atom size R that calculates desirable ternary amorphous component
a, for Zr
60Al
20Ni
20, R
a=0.1496nm is corresponding to 0.1496=C
Zr* R
Zr+ C
Al* R
Al+ C
Ni* R
Ni+ C
Cu* R
Cu, or C
Al+ 2.06 * C
Ni+ 1.88 * C
Cu=0.61, on quarternary phase diagram,, claim the constant atomic size face corresponding to a plane.
Step 4: calculate electron density e/a, see the k that requires that whether satisfies desirable amorphous
p≈ 2k
fShown in embodiment one, Zr
60Al
20Ni
20Be desirable amorphous, satisfy k
p≈ 2k
f, so e/a gets 1.5, known best non-crystaline amorphous metal Zr in this value and the body series
65Al
7.5Ni
10Cu
L7.5The e/a=1.4 value coincide, show value accurately.Be similar to Zr-Al-Ni, actual e/a value should be in the 1.4-1.5 scope, and e/a=1.4 is corresponding to plane 1.5 * C
Zr+ 3 * C
Al+ 0 * C
Ni+ l * C
Cu=1.4, e/a=1.5 is corresponding to plane 1.5 * C
Zr+ 3 * C
Al+ 0 * C
Ni+ 1 * C
Cu=1.5, be reduced to respectively-3C
Al+ 3C
Ni+ C
Cu=0.2 and-3C
Al+ 3C
Ni+ C
Cu=0.
Step 5: the intersection area of constant atomic size face and constant electron concentration face is the Composition Region of desirable amorphous, satisfies electron density and atomic size requirement simultaneously.Because e/a is in the 1.4-1.5 scope, corresponding composition also is a variation range, Inoue alloying constituent Zr
65AlNi
10Cu
17.5Be located in this zone, when Ni content constant, Zr around it
65.0-65.9Al
7.5-12.3Ni
10Cu
11.8-17.5The zone is desirable amorphous.
The present invention has designed six kinds of alloys that satisfy the mentioned component requirement, its e/a=1.38, and wherein No. 3 is the Inoue alloy, other is new constituent.Subordinate list has been listed their nominal alloying constituent, is atomic percent.The position of six kinds of alloying constituents is: No. 1 alloying constituent is positioned at the top position of intersection, promptly near a side of Zr-Al-Cu three component system, No. 6 alloying constituents are positioned at the lower position of intersection, promptly near a side of Zr-Al-Ni three component system, total rule is from No. 1 alloying constituent to 6 alloying constituent, the content of Zr is very little, and Al, Ni content increase, and Cu content reduces.
The present invention's suction casting method is prepared the sample that diameter is 3mm.Be made up of by amorphous XRD and TEM experiment confirm, the quality of these amorphous is analyzed DSC, DTA Experimental Characterization by heat, and sign amorphous stability that therefrom obtains and the temperature data that forms ability are given in the attached table.
Supercooling liquid phase region Δ T
xWhat value characterized is the stability of amorphous, removes the Δ T of No. 6 alloys
xOutside 85K, the Δ T of all the other five kinds of alloys
xValue is all greater than 97K, and maximum is No. 2 alloys, and its value reaches 105K, shows that these alloys are have wide supercooling liquid phase region scope large block amorphous.
T
g, T
xAlso characterize amorphous stability, its value increase shows the anti-crystallization ability reinforcement of amorphous, and the thermostability of amorphous increases, if with T
g, T
xBe stability criterion, alloy then from No. 1 to No. 6, the thermostability of amorphous progressively improves, and best composition should be No. 6 alloys, rather than No. 3 Inoue alloying constituents.
Reduction glass transformation temperature T
Rg=T
g/ T
mOr T
Rg=T
g/ T
lIt is the significant parameter that characterizes amorphous formation ability.From No. 1 alloy to 6 alloy, T
mBe worth more approachingly, wherein the value of No. 6 alloys exceeds other sample 10K approximately, and notices, from No. 1 alloy to 5 alloy, and their liquidus temperature T
lWith temperature of fusion T
mDifference drop to 47.6K from 121.5K, illustrate that No. 5 alloys are near eutectic composition.Then rising to some extent again with respect to No. 5 alloys of No. 6 alloys, the composition that eutectic is described is between No. 5 and No. 6, with T
g, T
xGiven amorphous stability trend is the same, and No. 6 alloys are best amorphous component.
By present embodiment, the above-mentioned six kinds of alloys of analysis-by-synthesis draw following result: at first, these six kinds of alloying constituents all have big Δ T
xValue and T
RgValue, show that series alloy on the intersection that is positioned at constant electron concentration face and constant atomic size face becomes big amorphous formation ability that branch possesses and high thermostability, and then proved the feasibility and the exactness of the method for the design amorphous alloy component that proposes with the present invention.Secondly, has maximum Δ T in them
xValue be No. 2 alloys, reach 105K, but and do not correspond to maximum reduction glass transformation temperature T
Rg, amorphous thermostability and amorphous formation ability and not quite identical are described.At last, judge that best amorphous component is between No. 5 alloys and No. 6 alloys and near No. 6 alloys according to the result of DTA.
Above-mentioned two most preferred embodiments have fully proved the success of this method in design Zr base amorphous.Simultaneously, this method also is applicable to the amorphous component design in all amorphous systems such as comprising Ti base, Al base, Pd base, rare earth based.Though electron density and atomic size and Zr base are variant, its corresponding physical mechanism is constant, and electron density depends on the interaction of Fermi sphere and brillouin zone, and all atomic size is decided by concrete element and amorphous neighbour structure.
Claims (4)
1, large-block amorphous alloy component design method is made of constant electron concentration and two of constant atomic sizes, and the former refers to that desirable non-crystaline amorphous metal will satisfy the Nagel-Tauc rule, and promptly Fermi surface is with tangent by the defined pseudo-brillouin zone of strong diffraction, and mathematical expression can be expressed as k
p≈ 2k
f, wherein, k
fBe the Fermi sphere radius, k
pBe the length of the pairing reciprocal vector in brillouin zone; The latter refers to that desirable non-crystaline amorphous metal satisfies the equal atomic radius requirement of determining, its numerical value depends on the neighbour's structure and the component of amorphous, it is characterized in that:
A) for Zr base amorphous, its electron density is the 1.4-1.5 scope, and its equal atomic size is 0.1496 ± 0.001nm;
B) the concrete implementation step of determining desirable amorphous is: one, multicomponent system is decomposed into subgroup unit system, and two, determine amorphous component point in the subgroup unit system, three, calculate the average atom size R of these amorphous components
aWith electron density e/a, four, judge whether to satisfy the Nagel-Tauc rule, i.e. k
p≈ 2k
f, five, the composition that satisfies these two criterions simultaneously will have the desirable amorphous of big amorphous formation ability;
C) this method is equally applicable to Zr base bulk amorphous alloys system in addition.
2, large block amorphous composition design method according to claim 1 and the new large block amorphous composition of Zr-Al-Ni-Cu of series designed satisfy electron density 1.4-1.5 scope and equal atomic size 0.1496 ± 0.001nm simultaneously, and the embodiment composition is Zr
65.5Al
5.6Ni
6.5Cu
22.4, Zr
65.3Al
6.5Ni
8.2Cu
20, Zr
64.8Al
8.3Ni
11.4Cu
15.5, Zr
64.5Al
9.2Ni
13.2Cu
13.1And Zr
63.8Al
11.4Ni
17.2Cu
7.6
3, large block amorphous composition design method according to claim 1 is characterized in that: best Zr-Al-Ni-Cu amorphous component is positioned at Zr
64.5Al
9.2Ni
13.2Cu
13.1And Zr
63.8Al
11.4Ni
17.2Cu
7.6Between.
4, large block amorphous composition design method according to claim 1, its feature also is: for a given alloy system, valence electron concentration error scope is ± 0.1, and atom mean sizes limit of error is at ± 0.001nm.
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| CN1294285C (en) * | 2005-01-13 | 2007-01-10 | 中国科学院物理研究所 | Scandium-base large amorphous alloy and method for preparing same |
| WO2007004991A1 (en) * | 2005-06-30 | 2007-01-11 | National University Of Singapore | Alloys, bulk metallic glass, and methods of forming the same |
| GB2441330A (en) * | 2005-06-30 | 2008-03-05 | Univ Singapore | Alloys, bulk metallic glass, and methods of forming the same |
| GB2441330B (en) * | 2005-06-30 | 2011-02-09 | Univ Singapore | Alloys, bulk metallic glass, and methods of forming the same |
| US9290829B2 (en) | 2005-06-30 | 2016-03-22 | National University Of Singapore | Alloys, bulk metallic glass, and methods of forming the same |
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| CN101613843B (en) * | 2009-07-24 | 2011-01-26 | 厦门大学 | Component design method of multi-component bulk iron-based amorphous alloy material |
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| CN103668177A (en) * | 2013-11-21 | 2014-03-26 | 太原理工大学 | Method adopting laser cladding to form amorphous alloy coating on surface of carbon steel |
| CN103668177B (en) * | 2013-11-21 | 2015-10-28 | 太原理工大学 | A kind of method of steel surface laser melting coating amorphous alloy coating |
| CN103938126A (en) * | 2014-04-10 | 2014-07-23 | 北京科技大学 | Ce-Al-Cu-Ag bulk amorphous alloy and preparation method thereof |
| CN103938126B (en) * | 2014-04-10 | 2015-11-25 | 北京科技大学 | A kind of Ce-Al-Cu-Ag Al-Cu-Zn block amorphous alloy and preparation method |
| CN105950946A (en) * | 2016-07-01 | 2016-09-21 | 广西大学 | Method for designing components of high-entropy alloy based on segregation condition among components |
| CN106868430A (en) * | 2017-02-17 | 2017-06-20 | 中国科学院金属研究所 | A kind of alloy component design method of regulation and control aluminium-based amorphous alloy Forming ability |
| CN107619982A (en) * | 2017-11-03 | 2018-01-23 | 北京理工大学 | Hexa-atomic the infusibility high-entropy alloy and its verification method of a kind of high-ductility high intensity |
| CN107619982B (en) * | 2017-11-03 | 2019-05-17 | 北京理工大学 | A kind of hexa-atomic infusibility high-entropy alloy and its verification method of high-ductility high intensity |
| CN112981279A (en) * | 2021-02-04 | 2021-06-18 | 江苏科技大学 | Quinary high-entropy amorphous alloy based on combination of three ternary amorphous alloy elements and preparation method thereof |
| CN112981279B (en) * | 2021-02-04 | 2022-08-16 | 江苏科技大学 | Quinary high-entropy amorphous alloy based on combination of three ternary amorphous alloy elements and preparation method thereof |
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