CN118256791A - NIALCRFETA hypoeutectic high-entropy alloy with high strength performance and method - Google Patents
NIALCRFETA hypoeutectic high-entropy alloy with high strength performance and method Download PDFInfo
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- 239000000956 alloy Substances 0.000 title claims abstract description 99
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 98
- 238000000034 method Methods 0.000 title claims abstract description 11
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims abstract description 26
- 239000002994 raw material Substances 0.000 claims abstract description 16
- 229910052786 argon Inorganic materials 0.000 claims abstract description 13
- 238000002844 melting Methods 0.000 claims abstract description 12
- 230000008018 melting Effects 0.000 claims abstract description 12
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims abstract description 11
- 229910052802 copper Inorganic materials 0.000 claims abstract description 11
- 239000010949 copper Substances 0.000 claims abstract description 11
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 9
- 238000003723 Smelting Methods 0.000 claims description 16
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 10
- 239000001301 oxygen Substances 0.000 claims description 10
- 229910052760 oxygen Inorganic materials 0.000 claims description 10
- 239000007789 gas Substances 0.000 claims description 9
- 238000002360 preparation method Methods 0.000 claims description 9
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 8
- 230000001681 protective effect Effects 0.000 claims description 8
- 239000010936 titanium Substances 0.000 claims description 8
- 229910052719 titanium Inorganic materials 0.000 claims description 8
- 238000011049 filling Methods 0.000 claims description 6
- 238000010891 electric arc Methods 0.000 claims description 2
- 239000012856 weighed raw material Substances 0.000 claims description 2
- 238000004519 manufacturing process Methods 0.000 claims 1
- 230000006835 compression Effects 0.000 abstract description 9
- 238000007906 compression Methods 0.000 abstract description 9
- 230000000694 effects Effects 0.000 abstract description 6
- 229910052715 tantalum Inorganic materials 0.000 abstract description 6
- 229910000943 NiAl Inorganic materials 0.000 abstract description 3
- NPXOKRUENSOPAO-UHFFFAOYSA-N Raney nickel Chemical compound [Al].[Ni] NPXOKRUENSOPAO-UHFFFAOYSA-N 0.000 abstract description 3
- 229910001068 laves phase Inorganic materials 0.000 abstract description 3
- 238000005728 strengthening Methods 0.000 abstract description 2
- 239000012071 phase Substances 0.000 description 27
- 230000005496 eutectics Effects 0.000 description 14
- 238000002474 experimental method Methods 0.000 description 5
- 239000000203 mixture Substances 0.000 description 5
- 238000002441 X-ray diffraction Methods 0.000 description 4
- 239000006023 eutectic alloy Substances 0.000 description 4
- 238000003466 welding Methods 0.000 description 4
- 238000005520 cutting process Methods 0.000 description 3
- VEXZGXHMUGYJMC-UHFFFAOYSA-N Hydrochloric acid Chemical compound Cl VEXZGXHMUGYJMC-UHFFFAOYSA-N 0.000 description 2
- 244000137852 Petrea volubilis Species 0.000 description 2
- 238000010521 absorption reaction Methods 0.000 description 2
- 239000000470 constituent Substances 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 229910000765 intermetallic Inorganic materials 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
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- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 230000003287 optical effect Effects 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- 238000005498 polishing Methods 0.000 description 2
- GRYLNZFGIOXLOG-UHFFFAOYSA-N Nitric acid Chemical compound O[N+]([O-])=O GRYLNZFGIOXLOG-UHFFFAOYSA-N 0.000 description 1
- QZPSXPBJTPJTSZ-UHFFFAOYSA-N aqua regia Chemical compound Cl.O[N+]([O-])=O QZPSXPBJTPJTSZ-UHFFFAOYSA-N 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
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- 229910003460 diamond Inorganic materials 0.000 description 1
- 239000010432 diamond Substances 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 229910001325 element alloy Inorganic materials 0.000 description 1
- 238000000227 grinding Methods 0.000 description 1
- 238000007731 hot pressing Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 230000001788 irregular Effects 0.000 description 1
- 239000007791 liquid phase Substances 0.000 description 1
- 239000002932 luster Substances 0.000 description 1
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- 229910017604 nitric acid Inorganic materials 0.000 description 1
- 229910052755 nonmetal Inorganic materials 0.000 description 1
- 239000000843 powder Substances 0.000 description 1
- 238000011160 research Methods 0.000 description 1
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- 239000006104 solid solution Substances 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 238000005303 weighing Methods 0.000 description 1
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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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- 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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Abstract
The invention provides NIALCRFETA hypoeutectic high-entropy alloy with high strength performance and a method, wherein the element components of the hypoeutectic high-entropy alloy are Ni, al, cr, fe and Ta, the mol percentage expression of the hypoeutectic high-entropy alloy is Ni 25AlxCr20Fe(50‑x)Ta5, and the value of x is 0-20. Raw materials are prepared according to the mole percentage of each element in the alloy, then the raw materials are put into a water-cooled copper crucible, and the alloy is prepared by using a high-vacuum non-consumable arc melting furnace under the argon condition. The hypoeutectic high-entropy alloy prepared by the method disclosed by the invention contains an FCC phase, a B2 phase (NiAl phase) and a Laves phase at room temperature, so that a plurality of excellent strengthening effects of the high-entropy alloy can be exerted, the compression strength and hardness of the hypoeutectic high-entropy alloy are obviously improved, and meanwhile, the compression rate is still kept at a higher level.
Description
Technical Field
The invention relates to the field of alloy materials, in particular to NIALCRFETA hypoeutectic high-entropy alloy with high-strength performance and a method.
Background
The high-entropy alloy breaks the design concept of the traditional alloy, and five or more elements are fused, and the atomic percentage of each element is between 5 and 35 percent, so the high-entropy alloy is also called as multi-principal element alloy, and the atomic structural arrangement of the high-entropy alloy is different from that of the traditional alloy. The high-entropy alloy has a plurality of good effects because of more elements and a plurality of components which are participated in the composition compared with the traditional alloy. The high entropy effect is a high entropy alloy landmark concept, and ideal entropy formation and enthalpy of pure metal can be known that in near equimolar alloys with five or more elements, solid solutions rather than intermetallic compounds tend to be more formed; the slow diffusion effect enables the nano-phase to be separated out in a large amount; strengthening is produced by the effect of lattice distortion. These effects create structural features that are different from conventional alloys, resulting in high-entropy alloys with some unique properties and performance. Although the high-entropy alloy has a large number of main constituent elements, the phase formed is relatively single, so that it is difficult to balance the strength and ductility of the alloy, and the high-entropy alloy has poor casting properties and is liable to cause component separation.
Eutectic structures are more specific in microstructure, which is the product of simultaneous crystallization of two different components or mechanical mixing of different crystals in a liquid phase at constant temperature. The form of the eutectic structure is very large, and the metal-metal type two-phase eutectic structure is often lamellar or rod-shaped, and the metal-nonmetal type two-phase eutectic structure is usually dendritic, needle-like or skeletal. Most binary eutectic alloys are limited by their fixed eutectic point, phase volume fraction, and limited phase composition, resulting in a eutectic alloy with poor performance.
In 2014 Lu et al, the concept of eutectic high-entropy alloy was first proposed, i.e., HEAs with a composite structure was designed using the concept of eutectic alloy to achieve a balance of high strength and high ductility, and an alcocrfeni2.1 eutectic high-entropy alloy containing eutectic structures with soft FCC phases and hard BCC phases combined together in regular lamellar phases was prepared, which had significantly improved strength and ductility compared to NiAl eutectic alloys. Due to the addition of more constituent elements, the eutectic composition is expanded into a certain composition interval from one point, so that various performances of the eutectic high-entropy alloy have a larger regulation and control range and a wide application prospect.
Disclosure of Invention
The invention aims to solve the technical problem of providing NIALCRFETA hypoeutectic high-entropy alloy with high-strength performance and a method thereof, wherein the alloy has a eutectic structure formed by two phases or three phases at room temperature, so that the alloy has high-strength comprehensive mechanical property.
In order to solve the technical problems, the invention adopts the following technical scheme: the NIALCRFETA hypoeutectic high-entropy alloy with high strength performance comprises non-equimolar percent of Ni element, cr element, fe element, ta element and selectively added Al element, wherein the molar percent expression is Ni 25AlxCr20Fe(50-x)Ta5, and the value of x is 0-20.
In a preferred scheme, the mole percentage of Ni element is 25%, the mole percentage of Cr element is 20%, the mole percentage of Fe element is 50% -30%, the mole percentage of Ta element is 5%, and Al element is selectively added or not added, and when Al element is included, the mole percentage of Al element is 0% -20%.
In a preferred embodiment, the value of x is 0 or 5 or 10 or 12.5 or 15 or 17.5 or 20.
The invention also provides a preparation method of NIALCRFETA hypoeutectic high-entropy alloy with high-strength performance, which comprises the following steps:
firstly, sequentially placing weighed raw materials into a water-cooled copper crucible in an electric arc melting furnace according to the sequence from low melting point to high melting point, namely Al, ni, fe, cr, ta, and placing pure titanium into the other groove pit of the water-cooled copper crucible;
step two, charging protective gas argon after primary vacuumizing in a vacuum arc furnace;
step three, filling protective gas argon after vacuumizing for the second time;
Smelting: to eliminate residual oxygen, smelting pure titanium to eliminate residual oxygen; and then, increasing the current to 200A-300A in a copper crucible filled with alloy raw materials for arc striking, after all the raw materials are liquefied, stably smelting for 3-5 min, closing the arc, after the alloy is cooled, turning over the cooled alloy, and repeating the smelting operation for 5-6 times to obtain NIALCRFETA hypoeutectic high-entropy alloy.
In the preferred scheme, in the first step, the purity of the required raw materials Ni, al, cr, fe, ta is higher than 99.96%, the mixture ratio is carried out according to the mole percentage of each element, the mole percentage of Ni element is 25%, the mole percentage of Cr element is 20%, the mole percentage of Fe element is 30% -50%, the mole percentage of Ta element is 5%, and Al element is selectively added or not added, and the mole percentage of Al element is 0% -20% when selectively added.
In a preferred embodiment, the mole percentage of the Al element is 0 or 5% or 10% or 12.5% or 15% or 17.5% or 20%.
In the preferred scheme, in the second step, when the vacuum arc furnace performs primary vacuumizing treatment, the vacuum degree of 0.7-0.8 pa in the furnace chamber is achieved, and then argon as a protective gas is filled to-0.06 Mpa.
In the preferred scheme, in the third step, secondary vacuumizing treatment is carried out, so that the vacuum degree in the furnace chamber reaches 10 -3～10-4 Pa, and argon is filled to-0.06 Mpa.
According to the NIALCRFETA hypoeutectic high-entropy alloy with high-strength performance and the method, the microstructure of the alloy is effectively adjusted by adjusting the content of the Al element, the compressive strength and the compression rate of the prepared alloy are simultaneously improved along with the increase of the content of the Al element, the content of B2 phase in the alloy is increased by the increase of the content of the Al, the FCC phase is relatively reduced, the mechanical property of the alloy is improved, and the prepared hypoeutectic high-entropy alloy has high-strength comprehensive mechanical property.
Drawings
The invention is further illustrated by the following examples in conjunction with the accompanying drawings:
FIG. 1 is a flow chart of an experiment in an embodiment of the present invention;
FIG. 2 is an X-ray diffraction diagram of a high entropy alloy in an embodiment of the present invention;
FIG. 3 is a microstructure of a high entropy alloy in an embodiment of the invention;
FIG. 4 is a graph of room temperature compressive stress versus strain for a high entropy alloy in an embodiment of the invention.
Detailed Description
The specific embodiments of the present invention will be described in further detail with reference to fig. 1 to 4.
The NIALCRFETA hypoeutectic high-entropy alloy with high strength performance comprises non-equimolar percent of Ni element, cr element, fe element, ta element and selectively added Al element, wherein the molar percent expression is Ni 25AlxCr20Fe(50-x)Ta5, and the value of x is 0-20. The mol percent of Ni element is 25%, the mol percent of Cr element is 20%, the mol percent of Fe element is 50% -30%, the mol percent of Ta element is 5%, and Al element is selectively added or not added, and when Al element is included, the mol percent of Al element is 0% -20%.
Example 1
A NIALCRFETA hypoeutectic high-entropy alloy with high-strength property is measured by mole percentage and comprises 25% of Ni element, 20% of Cr element, 50% of Fe element and 5% of Ta element, wherein the mole percentage expression is Ni 25Cr20Fe50Ta5. The preparation method of the high-entropy alloy in the embodiment is as follows:
Granular or massive Ni, cr, fe and Ta with purity higher than 99.6% are taken as raw materials, and are weighed according to the proportion, so as to prepare an alloy raw material with total weight of 30 g.
The raw materials are put into a water-cooled copper crucible of an arc melting furnace in turn from low to high melting point, namely Ni, fe, cr and Ta, and pure titanium for oxygen measurement and oxygen absorption is put into the other pit of the water-cooled copper crucible. Performing primary vacuumizing treatment in a vacuum arc furnace to enable the vacuum degree in the furnace chamber to reach 0.7-0.8 Pa; then filling the protective gas argon to about-0.06 Mpa. Then carrying out the second vacuumizing treatment to ensure that the vacuum degree of 10 -3～10-4 Pa is achieved in the furnace chamber, and filling argon to about-0.06 MPa; before smelting, smelting pure titanium for 2-3 min to eliminate residual oxygen in the furnace chamber and avoid oxidation of alloy during smelting.
Starting smelting, and adjusting a welding gun to a position which is 1-2cm above the center of the alloy raw material pile so as to successfully strike an arc; the current is slowly increased from about 20A to about 300A, and the position of the welding gun is adjusted to enable flame to tend to be stable; after the alloy is completely liquefied, the arc is closed after the alloy is stably smelted for 5min, the alloy is turned over after being cooled, and the operation is repeated for six times to obtain the alloy with uniform components.
Example 2
A NIALCRFETA hypoeutectic high-entropy alloy with high-strength property is calculated by mole percentage and comprises 25% of Ni element, 5% of Al element, 20% of Cr element, 45% of Fe element and 5% of Ta element, wherein the mole percentage expression is Ni 25Al5Cr20Fe45Ta5. The preparation method of the high-entropy alloy in the embodiment is as follows:
Granular or block Ni, al, cr, fe with purity higher than 99.6% and Ta are taken as raw materials, and the alloy raw materials with total weight of 30g are prepared by weighing based on the proportion.
The raw materials are sequentially put into a water-cooled copper crucible of an arc melting furnace according to the sequence from low melting point to high melting point, namely Al, ni, cr, fe and Ta, and pure titanium for oxygen measurement and oxygen absorption is put into the other groove pit of the water-cooled copper crucible. Performing primary vacuumizing treatment in a vacuum arc furnace to enable the vacuum degree in the furnace chamber to reach 0.7-0.8 Pa; then filling the protective gas argon to about-0.06 Mpa. Then carrying out the second vacuumizing treatment to ensure that the vacuum degree of 10 -3～10-4 Pa is achieved in the furnace chamber, and filling argon to about-0.06 MPa; before smelting, smelting pure titanium for 2-3 min to eliminate residual oxygen in the furnace chamber and avoid oxidation of alloy during smelting.
Starting smelting, and adjusting a welding gun to a position which is 1-2cm above the center of the alloy raw material pile so as to successfully strike an arc; the current is slowly increased from about 20A to about 300A, and the position of the welding gun is adjusted to enable flame to tend to be stable; after the alloy is completely liquefied, the arc is closed after the alloy is stably smelted for 5min, the alloy is turned over after being cooled, and the operation is repeated for six times to obtain the alloy with uniform components.
Example 3
A NIALCRFETA hypoeutectic high-entropy alloy with high-strength property is measured by mole percentage and comprises 25% of Ni element, 10% of Al element, 20% of Cr element, 40% of Fe element and 5% of Ta element, wherein the mole percentage expression is Ni 25Al10Cr20Fe40Ta5.
The preparation method of the high-entropy alloy of this example is the same as that of example 2.
Example 4
A NIALCRFETA hypoeutectic high-entropy alloy with high-strength property is measured by mole percentage and comprises 25% of Ni element, 12.5% of Al element, 20% of Cr element, 37.5% of Fe element and 5% of Ta element, wherein the mole percentage expression is Ni 25Al12.5Cr20Fe37.5Ta5.
The preparation method of the high-entropy alloy of this example is the same as that of example 2.
Example 5
A NIALCRFETA hypoeutectic high-entropy alloy with high-strength property is measured by mole percentage and comprises 25% of Ni element, 15% of Al element, 20% of Cr element, 35% of Fe element and 5% of Ta element, wherein the mole percentage expression is Ni 25Al15Cr20Fe35Ta5.
The preparation method of the high-entropy alloy of this example is the same as that of example 2.
Example 6
A NIALCRFETA hypoeutectic high-entropy alloy with high-strength property is measured by mole percentage and comprises 25% of Ni element, 17.5% of Al element, 20% of Cr element, 32.5% of Fe element and 5% of Ta element, wherein the mole percentage expression is Ni 25Al17.5Cr20Fe32.5Ta5.
The preparation method of the high-entropy alloy of this example is the same as that of example 2.
Example 7
A NIALCRFETA hypoeutectic high-entropy alloy with high-strength property is measured by mole percentage and comprises 25% of Ni element, 20% of Al element, 20% of Cr element, 30% of Fe element and 5% of Ta element, wherein the mole percentage expression is Ni 25Al20Cr20Fe30Ta5.
The preparation method of the high-entropy alloy of this example is the same as that of example 2.
As shown in fig. 1, the high-entropy alloy prepared in the above example was subjected to the following operations:
1. X-ray diffraction experiment
Cylindrical samples with the size of ⌀ X5 mm are cut in an ingot by using a wire cutting technology, and are polished to a silvery white luster on the surface by using 400-mesh 800-mesh, 1200-mesh and 2000-mesh sand paper, and then an X-ray diffraction experiment is carried out.
As shown in fig. 2, XRD test results of examples 1-7 show that the alloy microstructure consists of FCC phase (face-centered cubic lattice), B2 phase (NiAl phase) (stable intermetallic compound) and Laves phase (mainly Ta element).
2. Microscopic tissue observation
Cutting a cylindrical sample with the size of ⌀ X5 mm from an ingot by using a wire cutting technology, performing hot-pressing mosaic (the model of metallographic mosaic powder is XYX-601H; the mosaic pressure is 30+/-5 Mpa; the mosaic temperature is 135+/-5 ℃, the mosaic time is 10-15 minutes, and the cooling time is 10 minutes), polishing by using 400-mesh, 800-mesh, 1200-mesh and 2000-mesh sand paper respectively, and polishing by using W1.0 diamond grinding paste until the surface of the sample is free from scratches under an optical microscope. And (3) corroding the polished sample by using aqua regia (concentrated hydrochloric acid: concentrated nitric acid=3:1) solution until the surface of the sample is obviously observed to have the tissue morphology under an optical microscope.
As shown in fig. 3, the microstructure maps of examples 1 to 7 correspond to: examples 1-a, 2-b, 3-c, 4-d, 5-e, 6-f, 7-g.
The microstructure images a-g are SEM scanning electron microscope images, and are identified by scientific instruments, wherein the bright color phase is Laves phase, the gray color phase is FCC phase, and the black color phase is B2 phase. From the microstructure of examples a and B, it is apparent that the eutectic structure is in a regular lamellar structure and a small portion of coarse-grained eutectic (irregular lamellar structure) in examples a to g by combining the XRD patterns, and as is apparent from the microstructure of examples a and B, examples 1 and 2 are in lamellar eutectic structure in which a gray phase is used as a matrix and a bright phase is combined together, and as the content of Al element increases, a black phase, namely B2, is gradually precipitated in the alloy matrix, as shown in figures c to d. When the Al content is high enough, the grey phase in the alloy gradually disappears to change to black, i.e., the FCC phase gradually changes to B2 phase, as shown in figures e-g.
3. Room temperature compression experiment
A cylindrical sample of size ⌀ X6 mm was cut into ingots using wire-cut technique for compression experiments at a compression rate of 0.36mm/min.
Table 1 compressive strength and compressibility of examples 1-7 and prior art high entropy alloys.
| Group of | Pressure resistance (MPa) | Compression ratio (%) |
| Example 1 | - | - |
| Example 2 | - | - |
| Example 3 | 2380.37507 | 36.33133 |
| Example 4 | 2405.57391 | 30.03333 |
| Example 5 | 2696.15547 | 26.56667 |
| Example 6 | 2997.48883 | 31.815 |
| Example 7 | 2974.00463 | 25.15833 |
| CrFeNi2B0. 4 | 1080.1 | 32.2 |
| CrFeNi2B0. 6 | 1082.3 | 12.1 |
| Al1.2Co1.6CrFeNi | 2361 | 22.5 |
| Al1.2Co2.2CrFeNi | 2120 | 23 |
| Al1.2Co2.8CrFeNi | 1913 | 30 |
As can be seen from FIG. 4 and Table 1, the hypoeutectic high-entropy alloy of the invention has high room temperature compressive strength and good compression efficiency, has obvious advantages compared with the high-entropy alloy in the prior art, and shows high comprehensive mechanical properties. Example 6 has a compressive strength of 2997Mpa and a compression ratio of 31.8%, and has the best overall properties.
The hypoeutectic high-entropy alloy has high comprehensive mechanical properties through reasonable element selection and component adjustment, enriches research results of the hypoeutectic high-entropy alloy, and expands the application range of the alloy.
Claims (8)
1. A NIALCRFETA hypoeutectic high-entropy alloy with high strength performance is characterized in that the elements of the alloy are Ni element, cr element, fe element, ta element and selectively added Al element in non-equimolar percentage, the molar percentage expression is Ni 25AlxCr20Fe(50-x)Ta5, and the value of x is 0-20.
2. The NIALCRFETA hypoeutectic high-entropy alloy with high strength properties according to claim 1, wherein the mole percentage of Ni element is 25%, the mole percentage of Cr element is 20%, the mole percentage of Fe element is 50% -30%, the mole percentage of Ta element is 5%, and Al element is selectively added or not added, and when Al element is included, the mole percentage of Al element is 0% -20%.
3. The NIALCRFETA hypoeutectic high-entropy alloy with high strength properties according to claim 2, wherein x has a value of 0 or 5 or 10 or 12.5 or 15 or 17.5 or 20.
4. A preparation method of NIALCRFETA hypoeutectic high-entropy alloy with high-strength performance is characterized by comprising the following steps:
firstly, sequentially placing weighed raw materials into a water-cooled copper crucible in an electric arc melting furnace according to the sequence from low melting point to high melting point, namely Al, ni, fe, cr, ta, and placing pure titanium into the other groove pit of the water-cooled copper crucible;
step two, charging protective gas argon after primary vacuumizing in a vacuum arc furnace;
step three, filling protective gas argon after vacuumizing for the second time;
Smelting: to eliminate residual oxygen, smelting pure titanium to eliminate residual oxygen; and then, increasing the current to 200A-300A in a copper crucible filled with alloy raw materials for arc striking, after all the raw materials are liquefied, stably smelting for 3-5 min, closing the arc, after the alloy is cooled, turning over the cooled alloy, and repeating the smelting operation for 5-6 times to obtain NIALCRFETA hypoeutectic high-entropy alloy.
5. The method for preparing NIALCRFETA hypoeutectic high-entropy alloy with high-strength property according to claim 4, wherein in the first step, the purity of the required raw material Ni, al, cr, fe, ta is higher than 99.96%, the mole percentage of Ni element is 25%, the mole percentage of Cr element is 20%, the mole percentage of Fe element is 30% -50%, the mole percentage of Ta element is 5%, and Al element is selectively added or not added, and the mole percentage of Al element is 0% -20% when selectively added.
6. The method for producing NIALCRFETA hypoeutectic high-entropy alloy with high strength property according to claim 4, wherein the mole percentage of Al element is 0 or 5% or 10% or 12.5% or 15% or 17.5% or 20%.
7. The method for preparing NIALCRFETA hypoeutectic high-entropy alloy with high-strength property as claimed in claim 4, wherein in the second step, when the vacuum arc furnace performs the primary vacuumizing treatment, the vacuum degree of 0.7-0.8 pa is achieved in the furnace chamber, and then argon gas as protective gas is filled to-0.06 Mpa.
8. The method for preparing NIALCRFETA hypoeutectic high-entropy alloy with high strength according to claim 4, wherein in the third step, the vacuum is pumped for the second time to reach 10 -3～10-4 pa vacuum degree in the furnace chamber, and argon is filled to-0.06 Mpa.
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