CN113430444A - High-plasticity high-strength high-entropy alloy and preparation method thereof - Google Patents
High-plasticity high-strength high-entropy alloy and preparation method thereof Download PDFInfo
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- 239000002184 metal Substances 0.000 claims description 53
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- 238000005266 casting Methods 0.000 claims description 28
- 239000010955 niobium Substances 0.000 claims description 27
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C30/00—Alloys containing less than 50% by weight of each constituent
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
Abstract
The invention discloses a high-plasticity high-strength high-entropy alloy and a preparation method thereof, wherein the expression of the high-entropy alloy is NiaCobFecNbdVe,In the alloy expression, a, b, c, d and e respectively represent the atom percentage content of each corresponding principal component, and the following conditions are satisfied: a is 40-30, b is 35-25, c is 35-25, d is 10-3, e is 10-3, and a + b + c + d + e is 100. The high-entropy alloy provided by the invention adjusts the content of each principal element to regulate and control the stacking fault energy of the alloy and the precipitation volume fraction of a nano precipitation phase, so as to obtain high plasticity and high strength. Of the high-entropy alloyThe yield strength reaches 1000MPa, the tensile strength reaches 1300MPa, and the elongation rate reaches 50 percent. The high-strength high-plasticity high-entropy alloy can be used in the key high-technology fields of nuclear power, aviation, aerospace, navigation and the like.
Description
Technical Field
The invention relates to a high-plasticity high-strength high-entropy alloy and a preparation method thereof, belonging to the technical field of high-entropy alloys.
Background
The conventional alloy usually takes one element as a main component, and other minor elements are added to improve the comprehensive performance of the alloy, but according to Gibbs Phase Rule, excessive addition of the alloy element species can cause excessive intermetallic compounds to be generated in the alloy, and once a brittle compound is generated, the alloy performance is seriously affected, and the alloy performance is deteriorated. Therefore, in the design concept of the traditional alloy, on the premise of meeting the performance of the alloy, the types of alloy elements should be reduced as much as possible.
However, the design concept of the high-entropy alloy is completely different from that of the traditional alloy. In 2004, leaves all propose the concept of high entropy alloy, which contains at least 5 elements, and the content of each element is 5% -35% (at.%), i.e. there is no major and minor components among elements, solvent and solute. Although the type and content of the elements in the alloy deviate from the gibbs phase fraction, excessive phase numbers and harmful intermetallic compounds are not generated in the high entropy alloy. For example, representative CrCoFeMnNi and other high-entropy alloys with atomic ratio such as Cantor alloy and CoCrCuFeNi are single-phase FCC structures.
The high-entropy alloy with the FCC structure can show more excellent radiation resistance and corrosion resistance, but the mechanical property at room temperature is still to be improved, and taking the classic "Cantor" alloy (CrMnFeCoNi) as an example, the five-element high-entropy alloy has lower yield strength of about 350MPa, tensile strength of about 650MPa and fracture ductility of about 55% at room temperature. The precipitation strengthening is oneA method for effectively reinforcing a metal material. The metal material is subjected to aging treatment at a proper temperature, and a precipitation phase can be precipitated from a matrix phase so as to achieve a strengthening effect. However, the high-entropy alloy strengthened by the method has the condition of strength-plasticity 'contradiction'. Although the strengthening effect of the alloy can reach a new height after the precipitation size of the precipitated phase is optimized to be nano-scale, the plasticity of the alloy is seriously influenced, and the comprehensive mechanical property of the alloy is poor. At present, Ni is mainly used as a nano phase in the reinforced high-entropy alloy3Al、Ni3L1 of (Al, Ti)2Structure and Ni3Nb D022The structure is mainly. Such as Ni produced by He et al2CoCrFeNb0.15The tensile test of the alloy at room temperature shows that the yield strength of the alloy is 954MPa, the tensile strength of the alloy is 1230MPa, the fracture ductility of the alloy is 27 percent, and the alloy is high-strength and medium-ductility. While Al prepared by Liang et Al0.5Cr0.9FeNi2.5V0.2The yield strength of the high-entropy alloy at room temperature is up to 1810MPa, the tensile strength is 1905MPa, but the fracture ductility is only 9-10%, and the alloy is high in strength and low in ductility on the whole. The invention takes NiCoFe as a matrix, and the developed Ni-Co-Fe-Nb-V five-principal-element high-entropy alloy consists of an FCC matrix and Nb-rich L12The structural precipitated phase composition is low in the fault energy of the alloy, so that a TRIP (transformation Induced plasticity) effect is easily generated in the deformation process, the high-strength alloy has high strength and excellent plasticity, and the defect that the high-entropy alloy has poor plastic deformation capability under the condition of high strength is overcome.
The invention patent application with publication number CN 110952041A discloses a Fe-Mn-Ni-Cr four-component high-entropy alloy and a manufacturing method thereof, wherein the high-entropy alloy comprises the components (at.%), FeaMnbNicCrdIn the alloy expression, a, b, c and d respectively represent the atom percentage content of each corresponding component, and the following conditions are met: a is 38-57, b is 18-37, c is 8-15, d is 10-17, and a + b + c + d is 100. The tensile strength of the material at room temperature can reach 563.75MPa, and the plasticity of the material is 26-58%. The alloy can induce Twinning at room temperature, i.e. TWIP (Twinning Induced Plasticity)) The effect is that the mechanical property of the alloy at room temperature is effectively improved. This is in contrast to the plasticization mechanism of the present invention, which has a lower stacking fault energy and induces a phase change at room temperature, i.e., a TRIP effect. The alloy has lower strength at room temperature, and the comprehensive mechanical property is difficult to meet the engineering application.
The invention patent application with publication number CN 111593250A discloses a L12A precipitation strengthening high-entropy alloy and a preparation method thereof. The L12The precipitation strengthening high-entropy alloy is formed by directly doping TiN ceramic phase into A1CoCrFeNi high-entropy alloy with body-centered cubic structure to obtain alloy containing nano structure (Ni)3[A1，Ti]) The A1CoCrFeNi (TiN) x high entropy alloy of (1) is 0.2, 0.4, 0.6, 0.8, 1.0. The compressive strength of the high-entropy alloy is 546-1864 MPa, and the elongation is 6-20%. L1 used in the alloy2The type precipitates are completely different from those in the alloy of the present invention, and the precipitate used in the present invention is Nb-rich L12The precipitated phase can strengthen the alloy and ensure that the plastic loss rate of the alloy is small. The high-entropy alloy disclosed by the invention has higher strength, but the plasticity of the alloy is lower, and the comprehensive mechanical properties of the alloy are difficult to meet the requirements of engineering application.
Disclosure of Invention
The invention aims to solve the problem that the existing high-entropy alloy cannot simultaneously have high plasticity and high strength, provides a high-entropy alloy with high plasticity and high strength, so that the high-entropy alloy has great application potential, and provides a preparation method of the high-entropy alloy.
The purpose of the invention is realized as follows:
the invention relates to a high-plasticity high-strength high-entropy alloy and a preparation method thereof, wherein the expression of the high-entropy alloy is NiaCobFecNbdVe,In the alloy expression, a, b, c, d and e respectively represent the atom percentage content of each corresponding principal element, and the following conditions are satisfied: a is 40-30, b is 35-25, c is 35-25, d is 10-3, e is 10-3, and a + b + c + d + e is 100.
The invention principle and the component design of the high-strength high-plasticity high-entropy alloy are as follows:
the invention principle is as follows: the high-entropy alloy disclosed by the invention has the advantages that the yield strength can reach 1000MPa, the tensile strength can reach 1300MPa, the elongation rate is up to 50%, and the comprehensive mechanical property is excellent. Compared with other high-entropy alloys, the high-entropy alloy has lower stacking fault energy, the microstructure of the high-entropy alloy presents a fully annealed equiaxial crystal structure with low stacking fault energy, and annealing twin crystals with more volume fractions can be generated in crystal grains. This results from a rational design of the composition and the working process of cold rolling with large deformation and intermediate annealing. The lower stacking fault energy can lead the alloy to generate phase transformation from a matrix of an FCC phase to an HCP phase in the external force loading process, namely the alloy generates TRIP effect in the deformation process, and small isometric crystals are coordinately deformed in the deformation process, thus being beneficial to the improvement of the plasticity of the alloy; by regulating the contents of Ni, Nb and V elements and the dislocation introduced in the small deformation rolling process, energy is provided for the precipitation of a precipitation phase, and the Ni can be quickly formed in the aging process of the alloy3A precipitated phase of (Nb, V) to achieve an improvement in strength.
The basis of component design is as follows: the high-plasticity high-strength high-entropy alloy selects Ni, Co and Fe as matrix phase elements, and the atomic radius difference among the three elements is small, so that the high solid solubility can be ensured. And because the contents are close, the alloy can show higher mixing entropy, thereby inhibiting the effect of mixing enthalpy among elements, and the high-entropy alloy can form a typical FCC single-phase structure.
Ni is not only a constituent element of the matrix phase but also a precipitated phase Ni3Important forming elements of (Nb, V). Co and Fe may also be dissolved in small amounts into the precipitation phase Ni3(Nb, V) and occupy the sites of Nb, V, which contributes to the enhancement of the precipitated phase. And because of the addition of a large amount of Co element, the stacking fault energy of the alloy can be effectively reduced, so that the alloy is very easy to generate TRIP effect in the deformation process, a single-phase FCC matrix is converted into HCP phase, and the alloy is ensured to have good plasticity.
Nb, V being precipitated phases Ni3Important forming elements of (Nb, V). By adjusting the contents of the two elements, the method is effectiveThe precipitation quantity density of the precipitation phase is controlled, so that the strength of the alloy is greatly improved. And the addition of V can also effectively reduce the stacking fault energy of the alloy.
The invention relates to a high-plasticity high-strength high-entropy alloy and a preparation method thereof, which comprises the following steps:
(1) according to the atomic percentage of each element in the high-entropy alloy, selecting metal nickel, metal cobalt, metal iron, metal niobium and metal vanadium, and smelting and casting the metal nickel, the metal cobalt, the metal iron, the metal niobium and the metal vanadium to form an alloy ingot;
(2) cold rolling and intermediate annealing;
(3) and (6) heat treatment.
After the alloy is smelted, cooling and forming to room temperature, cutting off a riser, removing the skin, and then entering a thermal mechanical treatment process. After large deformation cold rolling, intermediate annealing, small deformation cold rolling and heat treatment, matrix structure with uniform and fine size and uniformly precipitated precipitation phase can be obtained, so that the material has high plasticity and strength.
In the step (1), smelting and casting processes are carried out in vacuum or argon protection, and a magnetic stirring technology is utilized to uniformly mix metal solution in the smelting process. The metal solution can be uniformly mixed by using a magnetic stirring technology in the smelting process.
In the step (2), the cold rolling and the intermediate annealing can be cast or rolled into square ingots or round ingots in size; the process conditions of the cold rolling and the intermediate annealing are as follows: heating the casting blank to 1000-1300 ℃, preserving heat for 10-24 h, discharging and quenching; cold rolling with large deformation amount of more than or equal to 60% at room temperature; then carrying out high-temperature annealing at 800-1200 ℃ and then quenching; and cold rolling with small deformation of more than or equal to 5% at room temperature.
Further, in the step (3), the process conditions of the heat treatment are as follows: after cold rolling deformation, according to the performance requirement, aging is carried out for 30 min-50 h at 600-800 ℃, and quenching is carried out to room temperature.
Compared with the prior art, the invention has the beneficial effects that:
(1) the precipitated volume fraction of a precipitated phase is controlled by adjusting the contents of Nb and V, the stacking fault energy of the alloy is reduced by introducing Co and V, and high plasticity and high strength are obtained simultaneously, the elongation of the high-entropy alloy is up to 50%, the yield strength can reach 1000MPa, and the tensile strength can reach 1300 MPa. (2) The preparation method of the high-plasticity high-strength high-entropy alloy is simple, the process controllability is strong, and the industrial production is easy to realize.
Drawings
FIG. 1 is an EBSD map of example 1 aged for 8h under heat treatment conditions;
FIG. 2 is an XRD plot of example 2 aged for 12h under a heat treatment process;
FIG. 3 is the engineering stress-strain curve of example 3;
FIG. 4 XRD curves before and after stretching for example 3 aged for 30min under heat treatment process;
FIG. 5 metallographic morphology of example 4 after aging for 4h under a heat treatment process.
Detailed Description
The present invention will be described in further detail with reference to the accompanying drawings and specific embodiments.
Example 1
Selecting metal nickel, metal cobalt, metal iron, metal niobium and metal vanadium, wherein the high-entropy alloy comprises the following components (atom percentage): ni-40.0, Co-27.0, Fe-27.0, Nb-3.0, V-3.0.
Casting into alloy cast ingots through arc melting or induction melting; smelting is carried out in vacuum or under the protection of argon, and a magnetic stirring technology is utilized to uniformly mix the metal solution in the smelting process; casting under vacuum or argon protection to form square ingot or round ingot;
heating the ingot casting blank to 1300 +/-10 ℃, preserving heat for 10 hours, and then discharging and quenching;
cold rolling the ingot casting blank at room temperature, wherein the primary large-deformation cold rolling amount is 60%;
carrying out intermediate annealing at 1200 +/-10 ℃ on the cold-rolled plate with large deformation, keeping the temperature for 3h, and quenching;
performing cold rolling with small deformation of 5% on the plate subjected to intermediate annealing again;
then aging for 8h at 700 ℃, and quenching to room temperature.
FIG. 1 is an EBSD graph of aging for 8h under the heat treatment process, and the fully annealed equiaxed crystal structure with low stacking fault energy is obtained by the process, and due to the lower stacking fault energy of the alloy, a plurality of volume fractions of annealing twin crystals are generated in crystal grains.
The mechanical properties of example 1 are shown in Table 1, and the average hardness at 8h of aging is 311HV, the yield strength is 830MPa, the tensile strength is 1148MPa, and the elongation is 27%.
Example 2
Selecting metal nickel, metal cobalt, metal iron, metal niobium and metal vanadium, wherein the high-entropy alloy comprises the following components (atom percentage): ni 30.0, Co 25.0, Fe 25.0, Nb 10.0, V10.0.
Casting into alloy cast ingots through arc melting or induction melting; smelting is carried out in vacuum or under the protection of argon, and a magnetic stirring technology is utilized to uniformly mix the metal solution in the smelting process; casting under vacuum or argon protection to form square ingot or round ingot;
heating the ingot casting blank to 1000 +/-10 ℃, preserving heat for 24 hours, and then discharging and quenching;
cold rolling the cast ingot casting blank at room temperature, wherein the primary large-deformation cold rolling amount is 85%;
carrying out intermediate annealing at 1000 +/-10 ℃ on the cold-rolled plate with large deformation, keeping the temperature for 3 hours, and quenching;
performing cold rolling on the plate subjected to intermediate annealing again with small deformation of 9%;
then aging at 600 ℃ for 12h, and quenching to room temperature.
Figure 2 is an XRD profile for 12h of ageing under this heat treatment process, which allows to obtain a single phase FCC structure.
The mechanical properties of example 2 are shown in Table 1, and the average hardness is 299HV, the yield strength is 720MPa, the tensile strength is 1008MPa, and the elongation is 52% at aging for 12 hours.
Example 3
Selecting metal nickel, metal cobalt, metal iron, metal niobium and metal vanadium, wherein the high-entropy alloy comprises the following components (atom percentage): ni 35.0, Co 27.5, Fe 27.5, Nb 5.0, V5.0.
Casting into alloy cast ingots through arc melting or induction melting; smelting is carried out in vacuum or under the protection of argon, and a magnetic stirring technology is utilized to uniformly mix the metal solution in the smelting process; casting under vacuum or argon protection to form square ingot or round ingot;
heating the ingot casting blank to 1200 +/-10 ℃, preserving heat for 15h, and then discharging and quenching;
cold rolling the ingot casting blank at room temperature, wherein the first large-deformation cold rolling amount is 90%;
carrying out intermediate annealing at 1200 +/-10 ℃ on the cold-rolled plate with large deformation, keeping the temperature for 1h, and quenching;
performing cold rolling on the plate subjected to intermediate annealing again with small deformation of 10%;
aging at 650 deg.C for 30min, and quenching to room temperature.
Figure 3 the engineering stress-strain curve of example 3, where it can be seen that significant work hardening occurs.
Fig. 4 XRD curves before and after stretching of example 3, it can be seen that the alloy produces TRIP effect during deformation, which also laterally demonstrates the origin of the apparent work hardening in fig. 3.
The mechanical properties of example 3 are shown in Table 1, and the average hardness is 322HV, the yield strength is 1021MPa, the tensile strength is 1303MPa, and the elongation is 49% at 30min of aging.
EXAMPLE 4
Selecting metal nickel, metal cobalt, metal iron, metal niobium and metal vanadium, wherein the high-entropy alloy comprises the following components (atom percentage): ni 30.0, Co 35.0, Fe 26.0, Nb 5.0, V4.0.
Casting into alloy cast ingots through arc melting or induction melting; smelting is carried out in vacuum or under the protection of argon, and a magnetic stirring technology is utilized to uniformly mix the metal solution in the smelting process; casting under vacuum or argon protection to form square ingot or round ingot;
heating the ingot casting blank to 1200 +/-10 ℃, preserving heat for 24 hours, and then discharging and quenching;
cold rolling the ingot casting blank at room temperature, wherein the first large-deformation cold rolling amount is 90%;
carrying out intermediate annealing at 800 +/-10 ℃ on the cold-rolled plate with large deformation, keeping the temperature for 3h, and quenching;
performing cold rolling on the plate subjected to intermediate annealing again with small deformation of 10%;
then aging for 24h at 750 ℃, and quenching to room temperature.
FIG. 5 shows the metallographic morphology of example 4 after aging for 4h under a heat treatment process.
The mechanical properties of example 4 are shown in Table 1, and at 4h of aging, the average hardness is 308HV, the yield strength is 810MPa, the tensile strength is 1022MPa, and the elongation is 30%.
Example 5
Selecting metal nickel, metal cobalt, metal iron, metal niobium and metal vanadium, wherein the high-entropy alloy comprises the following components (atom percentage): ni 34.5, Co 20.5, Fe 35, Nb 6.0, V4.0.
Casting into alloy cast ingots through arc melting or induction melting; smelting is carried out in vacuum or under the protection of argon, and a magnetic stirring technology is utilized to uniformly mix the metal solution in the smelting process; casting under vacuum or argon protection to form square ingot or round ingot;
heating the ingot casting blank to 1300 +/-10 ℃, preserving heat for 10 hours, and then discharging and quenching;
cold rolling the ingot casting blank at room temperature, wherein the primary large-deformation cold rolling quantity is 87%;
carrying out intermediate annealing at 1100 +/-10 ℃ on the cold-rolled plate with large deformation, keeping the temperature for 1h, and quenching;
performing cold rolling on the plate subjected to intermediate annealing again with small deformation of 10%;
then aging for 50h at 800 ℃, and quenching to room temperature.
The mechanical properties of example 5 are shown in Table 1, and at 2h of aging, the average hardness is 350HV, the yield strength is 1348MPa, the tensile strength is 1422MPa, and the elongation is 15%.
The hardness and tensile mechanical properties of the high-plasticity high-strength high-entropy alloy in the above examples are tested as follows.
(1) Hardness: the hardness test was carried out using an HVS-50 Vickers hardness tester with a load of 1Kg, and 5 points were hit and averaged, as shown in Table 1.
(2) Tensile mechanical properties: an electronic universal tester is adopted for carrying out a tensile test, a rectangular sample with the nominal section size of 2-3 multiplied by 4 multiplied by 20.6mm is taken, and the average values of the tensile strength, the yield strength and the elongation of 3 samples treated in the same way are listed in table 1.
TABLE 1 compositions, hardness, tensile properties and elongation of the examples
The invention discloses a high-plasticity high-strength high-entropy alloy and a preparation method thereof, wherein the expression of the high-entropy alloy is NiaCobFecNbdVeIn the alloy expression, a, b, c, d and e respectively represent the atom percentage content of each corresponding principal element, and the following conditions are satisfied: a is 40-30, b is 35-25, c is 35-25, d is 10-3, e is 10-3, and a + b + c + d + e is 100. The preparation method of the high-plasticity high-strength high-entropy alloy comprises the following steps: (1) smelting and casting the high-entropy alloy; (2) cold rolling and intermediate annealing; (3) and (6) heat treatment. The high-entropy alloy provided by the invention adjusts the content of each principal element to regulate and control the stacking fault energy of the alloy and the precipitation volume fraction of a nano precipitation phase, so as to obtain high plasticity and high strength. The yield strength of the high-entropy alloy reaches 1000MPa, the tensile strength reaches 1300MPa, and the elongation rate reaches 50%. The high-strength high-plasticity high-entropy alloy can be used in the key high-technology fields of nuclear power, aviation, aerospace, navigation and the like.
Claims (7)
1. The high-plasticity high-strength high-entropy alloy is characterized in that the expression of the high-entropy alloy is NiaCobFecNbdVeIn the alloy expression, a, b, c, d and e respectively represent the atom percentage content of each corresponding principal element, and the following conditions are satisfied: a is40 to 30, b is 35 to 25, c is 35 to 25, d is 10 to 3, e is 10 to 3, and a + b + c + d + e is 100; the preparation method of the high-plasticity high-strength high-entropy alloy comprises the following steps: (1) smelting and casting the high-entropy alloy; (2) cold rolling and intermediate annealing; (3) and (6) heat treatment.
2. A method for preparing a high-plasticity high-strength high-entropy alloy according to claim 1, which is characterized by comprising the following steps:
(1) according to the atomic percentage of each element in the high-entropy alloy, selecting metal nickel, metal cobalt, metal iron, metal niobium and metal vanadium, and smelting and casting the metal nickel, the metal cobalt, the metal iron, the metal niobium and the metal vanadium to form an alloy ingot;
(2) cold rolling and intermediate annealing;
(3) and (6) heat treatment.
3. A method for preparing a high-plasticity high-strength high-entropy alloy according to claim 2, wherein in the step (1), the smelting and casting processes are carried out in vacuum or under the protection of argon, and a magnetic stirring technology is used for uniformly mixing metal solutions in the smelting process.
4. A method for preparing a high-plasticity high-strength high-entropy alloy according to claim 2, wherein in the step (2), the cold rolling and the intermediate annealing can be cast or rolled into square ingots or round ingots in size; the process conditions of the cold rolling and the intermediate annealing are as follows: heating the casting blank to 1000-1300 ℃, preserving heat for 10-24 h, discharging and quenching; cold rolling with large deformation amount of more than or equal to 60% at room temperature; then carrying out high-temperature annealing and quenching; and cold rolling with small deformation of more than or equal to 5% at room temperature.
5. A method for preparing a high-plasticity high-strength high-entropy alloy according to claim 2, wherein in the step (3), the heat treatment process is aging treatment at different temperatures and time.
6. The intermediate annealing method of high-plasticity and high-strength high-entropy alloy as claimed in claim 4, wherein the annealing temperature is 800-1200 ℃ and the temperature is kept for 0.5-3 h.
7. The heat treatment method of high-plasticity high-strength high-entropy alloy as claimed in claim 5, wherein the aging treatment temperature is 600-800 ℃, the aging time is 30 min-50 h, and the alloy is quenched to room temperature.
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