CN117587314A - Ultrahigh-hardness high Wen Gaoshang alloy and preparation method thereof - Google Patents
Ultrahigh-hardness high Wen Gaoshang alloy and preparation method thereof Download PDFInfo
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- C22C30/00—Alloys containing less than 50% by weight of each constituent
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- C22B—PRODUCTION AND REFINING OF METALS; PRETREATMENT OF RAW MATERIALS
- C22B9/00—General processes of refining or remelting of metals; Apparatus for electroslag or arc remelting of metals
- C22B9/003—General processes of refining or remelting of metals; Apparatus for electroslag or arc remelting of metals by induction
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- C22B—PRODUCTION AND REFINING OF METALS; PRETREATMENT OF RAW MATERIALS
- C22B9/00—General processes of refining or remelting of metals; Apparatus for electroslag or arc remelting of metals
- C22B9/04—Refining by applying a vacuum
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22B—PRODUCTION AND REFINING OF METALS; PRETREATMENT OF RAW MATERIALS
- C22B9/00—General processes of refining or remelting of metals; Apparatus for electroslag or arc remelting of metals
- C22B9/16—Remelting metals
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- C22C27/00—Alloys based on rhenium or a refractory metal not mentioned in groups C22C14/00 or C22C16/00
- C22C27/02—Alloys based on vanadium, niobium, or tantalum
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
- C22C32/0052—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only carbides
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Abstract
The invention discloses an ultrahigh-hardness high Wen Gaoshang alloy and a preparation method thereof, and belongs to the technical field of alloy materials. The alloy component is Nb a Mo b Ta c Ti d V e C f The subscripts are the atomic ratios of the corresponding elements, a is 15-30, b is 0-20, c is 15-25, d is 15-30, e is 10-25, f is 10-20, and a+b+c+d+e+f=100. The alloy has excellent comprehensive mechanical properties: the room temperature compressive strength is higher than 1900MPa, and the maximum deformation can be achievedUp to 20%, the high temperature 1273K can still maintain the compressive strength 476.1MPa, and the plastic deformation behavior is shown; the average Vickers hardness value can reach 1492.9HV, is 7.1 times of that of 304 stainless steel (the hardness is 210.0 HV), and can be used in the fields of aerospace, national defense and military industry and the like. Meanwhile, the preparation method of the alloy is simple and safe to operate and has a good preparation effect.
Description
Technical Field
The invention belongs to the technical field of alloy materials, and particularly relates to an ultrahigh-hardness high Wen Gaoshang alloy and a preparation method thereof.
Background
In the fields of aerospace, chemistry, power systems, automobiles, ocean development, petrochemical industry and the like, a large number of important metal parts such as bearings, valves, rotors and the like manufactured by traditional carbon steel bear continuous abrasion due to severe service conditions, so that the service life of the important metal parts is obviously reduced and even fails. This not only reduces production efficiency but also increases maintenance time and cost. Therefore, the design of new special alloy materials with excellent comprehensive performance and the development of a high-quality preparation method are particularly important.
Cantor and Yeh et al propose a new concept of High Entropy Alloys (HEA), prepared by alloying 5 and more elements, each element in a ratio of 5% -35% (molar ratio). The randomly mixed elements increase the configurational entropy, inhibit the free energy of compound formation, and thus more tend to form disordered solid solutions of simple face-centered cubic (FCC), body-centered cubic (BCC) or close-packed Hexagonal (HCP) structures, thereby inhibiting intermetallic compound formation. With the continuous and deep research, the high-entropy alloy is applied in many engineering application fields such as chemistry, nuclear, energy, biomedical fields, automobiles, aerospace and the like. Due to the actions of slow diffusion effect, high entropy effect, cocktail effect and lattice distortion effect, the high entropy alloy can show excellent performances such as high strength, ultrahigh hardness, good high temperature oxidation resistance, corrosion resistance, wear resistance, thermal stability and the like. The proposal of the high-entropy alloy breaks through the limit of the performance of the modern material, expands the prospect of the combination of material science and metallurgy, gradually meets the high-end material requirement of the current design practice, and provides a wide space for the development of the wear-resistant alloy.
The invention patent publication No. CN111020339A discloses a high-entropy alloy for an ultra-high hardness gear coating and a manufacturing method thereof, and discloses an ultra-high-entropy alloy with the chemical composition of FeMoCrVTiSi X X is more than or equal to 0 and less than or equal to 0.5. By changing the content of Si element, the hardness of the system can reach more than 900 HV.
The invention patent with application publication number of CN111364040A discloses a high-hardness high-entropy alloy coating and a preparation method and application thereof, and discloses a high-entropy alloy coating which comprises the following chemical components in percentage by atom: coCrFeMnNiTi x V y Wherein x=0.3 to 1 and y=0.1 to 1. Consisting of a V-rich BCC1 phase and a Ti-rich BCC2 phase, the average hardness of the coating reaches 942.8HV 0.3 。
The invention patent with application publication number of CN116904790A discloses a preparation method of a high-hardness WC/CoVTiB high-entropy alloy composite material, which comprises the following components: 60-70% of WC, 10-15% of Co, 3-5% of V, 4-7% of Ti and 13-17% of B, wherein the average microhardness of the composite material reaches 950HV.
The high-temperature high-entropy alloy is a novel high-temperature alloy, has the advantages of unique crystal structure, ultrahigh hardness, high strength, excellent high-temperature performance and the like, and has great development potential in the field of wear-resistant materials. Compared with the traditional alloy, the high Wen Gaoshang alloy can maintain higher high-temperature strength, ultrahigh hardness, excellent oxidation resistance and corrosion resistance, good fracture toughness and fatigue performance even in complex and changeable working environments. In order to enable the alloy to meet the use requirements of wear-resistant parts such as drills, studs and the like, the design and preparation of the novel ultrahigh-hardness high-entropy alloy material with excellent comprehensive mechanical properties have important engineering and research significance.
Disclosure of Invention
The technical problems to be solved are as follows: aiming at the technical problems, the invention provides the alloy with high hardness and Wen Gaoshang and the preparation method thereof, wherein the alloy has high plasticity, high strength and high hardness, has excellent high-temperature mechanical properties and can meet the requirements of advanced hardness materials; meanwhile, the preparation method is simple and safe to operate and good in preparation effect.
The technical scheme is as follows: an alloy with superhigh hardness and high Wen Gaoshang, the alloy component is Nb a Mo b Ta c Ti d V e C f Wherein a, b, c, d, e, f is the atomic percentage of the corresponding elements, a is 15-30, b is 0-20, c is 15-25, d is 15-30, e is 10-25, f is 10-20, and a+b+c+d+e+f=100.
Preferably, the alloy component of the high-temperature high-entropy alloy is Nb 22.2 Ta 22.0 Ti 23.9 V 21.2 C 10.7 。
Preferably, the alloy component of the high-temperature high-entropy alloy is Nb 17.7 Mo 16.4 Ta 17.6 Ti 19.1 V 17.0 C 12.2 。
Preferably, the high-entropy alloy consists of a high-entropy alloy phase of a BCC structure and a carbide ceramic phase of an FCC structure; the high-entropy alloy phase is a solid solution composed of Nb, ta, ti and V elements, and the carbide ceramic phase is (Ti, ta) C high-entropy carbide.
Preferably, the high-entropy alloy takes a solid solution phase with a BCC structure as a matrix, and carbide ceramic phases with a near-elliptical FCC structure are uniformly distributed on the matrix.
The preparation method of the ultra-high hardness high Wen Gaoshang alloy comprises the following steps:
s1, weighing raw materials Nb, mo, ta, ti, V and TaC according to an atomic ratio, and paving the raw materials in a copper crucible of a vacuum arc melting furnace in sequence from low melting point to high melting point;
s2, putting the titanium ingot into another copper crucible of the vacuum arc melting furnace, and melting the titanium ingot for 3-5 min under the argon atmosphere;
s3, smelting the raw materials in the step S1, starting electromagnetic stirring after the raw materials are melted, wherein the stirring current is 6A, obtaining an alloy cast ingot, and turning over the cast ingot after cooling;
s4, repeating the step S3 to obtain the alloy with ultrahigh hardness and high Wen Gaoshang.
Preferably, the raw material Nb, mo, ta, ti, V is simple substance particles corresponding to each element, and the purity of the simple substance particles is more than or equal to 99.9 wt%.
Preferably, the raw material TaC is powder, and the purity of the raw material TaC is more than or equal to 99.5 wt%.
Preferably, in the step S2, after the titanium ingot is placed, the titanium ingot is vacuumized to 5×10 -3 Pa or below, and then argon with purity of 99.99% is filled to 0.05-0.06 MPa.
Preferably, in the step S3, the smelting current is 300-400A, and the arc is maintained for 4-5 min after each smelting of the alloy.
The beneficial effects are that: 1. the invention prepares the high-temperature high-entropy alloy with ultra-high hardness Nb-Mo-Ta-Ti-V-C and provides a new material of special alloy with excellent comprehensive performance. The microcosmic appearance is that carbide with a more regular round FCC structure is uniformly distributed on a high-entropy alloy matrix with a BCC structure. Consists of a high entropy alloy solid solution phase of a BCC structure and an in situ generated carbide ceramic phase with an FCC structure. The alloy has excellent mechanical properties, and combines good plastic deformation capability with ultrahigh strength and hardness. The room temperature compressive engineering stress of example 1 can reach 1900MPa, the engineering strain can reach 20%, the average ultra-high hardness of 1492.9HV is shown, and the hardness is about 7.1 times that of 304 stainless steel (hardness 210.0 HV).
2. The DSC curve of the alloy prepared by the invention proves that the alloy has stable crystal structure in the range of room temperature to 1450 ℃, does not generate phase change, is not easy to damage under the high-temperature condition due to good phase stability, and has good application safety. The alloy has good high-temperature mechanical property and can still maintain the compressive strength of 476.1MPa at the high temperature of 1273K.
3. The invention adopts the arc melting method for preparation, has simple preparation process, high reaction temperature and high element diffusion rate at high temperature, can effectively promote the diffusion of metal elements and carbon elements, and is beneficial to in-situ generation of carbide reinforcing phases; the high-temperature smelting can effectively remove trace impurities such as oxides, and the phase interface is clean and the bonding strength is high; the preparation method is simple and safe to operate and good in preparation effect. The operation process only comprises one step of vacuum arc melting, and the Nb-Mo-Ta-Ti-V-C alloy cast ingot with uniform components and ultrahigh hardness and high Wen Gaoshang can be prepared.
4. The high-temperature high-entropy alloy with ultra-high hardness Nb-Mo-Ta-Ti-V-C is characterized in that a large amount of C element (more than 10 at.%) is added, and when smelting, the C element and refractory metal element (Nb, mo, ta, ti, V) in raw materials generate a large amount of carbide reinforcing phases in situ, and the carbide phases have high melting point and high thermal stability and are uniformly distributed on the refractory metal solid solution phase. Due to the combined action of a large amount of carbide phases generated in situ and refractory high-entropy alloy solid solution phases, the alloy has high plasticity, high strength and ultra-high hardness, and excellent high-temperature mechanical properties, and can be used in the fields of aerospace, national defense and military industry and the like.
Drawings
FIG. 1 is a drawing of example 1Nb 22.2 Ta 22.0 Ti 23.9 V 21.2 C 10.7 XRD diffraction pattern of high-temperature high-entropy alloy;
FIG. 2 is a drawing of example 1Nb 22.2 Ta 22.0 Ti 23.9 V 21.2 C 10.7 SEM images of high temperature high entropy alloy;
FIG. 3 is a drawing of example 1Nb 22.2 Ta 22.0 Ti 23.9 V 21.2 C 10.7 EPMA element distribution diagram of high-temperature high-entropy alloy;
FIG. 4 is a drawing of example 1Nb 22.2 Ta 22.0 Ti 23.9 V 21.2 C 10.7 DSC curve of high-temperature high-entropy alloy;
FIG. 5 is a drawing of example 1Nb 22.2 Ta 22.0 Ti 23.9 V 21.2 C 10.7 Room temperature compression engineering stress-strain curve of high temperature high entropy alloy;
FIG. 6 is a drawing of example 1Nb 22.2 Ta 22.0 Ti 23.9 V 21.2 C 10.7 Room temperature compression engineering stress-strain curve of 1473K heat treatment of high temperature high entropy alloy for 2 h;
FIG. 7 is a drawing of example 1Nb 22.2 Ta 22.0 Ti 23.9 V 21.2 C 10.7 1273K high-temperature compressive true stress of high-temperature high-entropy alloy-a strain curve;
FIG. 8 is a diagram of example 2Nb 17.7 Mo 16.4 Ta 17.6 Ti 19.1 V 17.0 C 12.2 XRD diffraction pattern of high-temperature high-entropy alloy;
FIG. 9 is a diagram of example 2Nb 17.7 Mo 16.4 Ta 17.6 Ti 19.1 V 17.0 C 12.2 SEM images of high temperature high entropy alloy;
FIG. 10 is a drawing of example 2Nb 17.7 Mo 16.4 Ta 17.6 Ti 19.1 V 17.0 C 12.2 DSC curve of high-temperature high-entropy alloy;
FIG. 11 is a drawing of example 2Nb 17.7 Mo 16.4 Ta 17.6 Ti 19.1 V 17.0 C 12.2 Room temperature compression engineering stress-strain curve for high temperature high entropy alloys.
Detailed Description
The invention is further described below with reference to the drawings and specific embodiments. The raw materials used in the invention are purchased from the market without special description. The detection means used in the invention are all conventional technical means in the field and are not repeated.
Example 1
The alloy component of the ultra-high hardness Nb-Mo-Ta-Ti-V-C high-temperature high-entropy alloy of the embodiment is Nb a Mo b Ta c Ti d V e C f Where a=22.2%, b=0%, c=22.0%, d=23.9%, e=21.2%, f=10.7%, i.e. Nb 22.2 Ta 22.0 Ti 23.9 V 21.2 C 10.7 。
The preparation method of the Nb-Mo-Ta-Ti-V-C high-temperature high-entropy alloy comprises the following steps: the Nb, ta, ti, V metal simple substance raw material is subjected to acid washing before being weighed so as to remove oxide skin on the surface of the raw material, ultrasonic cleaning is performed on the raw material by using absolute ethyl alcohol after the acid washing, and the raw material is dried to obtain the metal raw material with the purity of more than or equal to 99.9wt.%, then the raw material is weighed according to the atomic percentage, taC powder with the purity of more than or equal to 99.5wt.% is weighed, the cleaned raw material is accurately weighed according to the proportion, and the error is +/-0.0005 g; sequentially placing the weighed raw materials in order of melting point from low to highPlacing the molten copper into a water-cooled copper crucible of an arc melting furnace, wherein the element with the lowest melting point is placed at the lowest layer, and the element with the highest melting point is placed at the uppermost layer; then placing the pure titanium ingot in another water-cooled copper crucible, closing the furnace door after all the pure titanium ingot is placed, and vacuumizing to 5 multiplied by 10 -3 Pa, and then filling pure argon to 0.05-0.06 MPa; the pure titanium ingot is smelted for 3-5 minutes before the alloy is smelted, so as to remove residual oxygen in a smelting furnace, then the alloy is smelted, the smelting current is 300-400A, after each smelting of the alloy, the electric arc is kept for 4-5 minutes, after the raw materials are smelted, electromagnetic stirring is started to enable smelting to be more uniform, and the stirring current is 6A. After the alloy ingot is cooled, turning over the ingot, repeatedly smelting for more than 5 times to ensure smelting uniformity, and cooling to obtain Nb 22.2 Ta 22.0 Ti 23.9 V 21.2 C 10.7 High-temperature high-entropy alloy.
The XRD diffraction pattern of this example is shown in FIG. 1, and the ultra-high hardness and high Wen Gaoshang alloy consists of a high-entropy alloy solid solution phase of BCC structure and a (Ti, ta) C high-entropy carbide ceramic phase of FCC structure; FIG. 2 is an SEM image of example 1, showing that the alloy has microscopic morphology characterized by relatively regular rounded carbides uniformly distributed on the high entropy alloy substrate; FIG. 3 is an EPMA element distribution diagram of example 1, wherein the carbide ceramic phase in dark gray is rich in Ti, ta, C, the solid solution phase in light gray high-entropy alloy is rich in Nb, V, and V, C element is also rich at the grain boundary; FIG. 4 is a DSC curve of example 1 showing a nearly straight line indicating Nb 22.2 Ta 22.0 Ti 23.9 V 21.2 C 10.7 The high-temperature high-entropy alloy has stable crystal structure in the range of room temperature to 1450 ℃, does not generate phase change, is not easy to damage under the high-temperature condition due to good phase stability, and has good application safety; FIG. 5 is a graph of room temperature compressive engineering stress-strain, with a compressive ultimate strength of 1900.1MPa and a maximum deformation of 20.1%; FIG. 6 is a graph showing the stress-strain curve of room temperature compression engineering after heat treatment for 2 hours at 1473K of example 1, with a compressive ultimate strength of 1712.3MPa and a maximum deformation of 18.4%; FIG. 7 is a 1273K high temperature compressive true stress-strain curve of example 1, with a compressive ultimate strength of 476.1MPa, showing plastic deformation behavior.
The hardness test was conducted on example 1, and the results are shown in table 1.
The hardness testing method comprises the following steps: smashing an alloy ingot into small blocks by using a large hammer, performing thermal mosaic by using a metallographic mosaic machine, sequentially polishing by using sand paper according to the sequence of 400, 800, 1000, 1500 and 2000 meshes, and polishing until no scratch exists on the surface after polishing; after polishing, ultrasonically cleaning the surface with absolute ethyl alcohol to remove surface stains, and then starting to test hardness; hardness test A Vickers hardness tester, model Wilson VH1102, was used, the pressure was 100g, for 10s, 15 different points were randomly pressed together, and the average was calculated.
TABLE 1 Vickers hardness test results for example 1
Nb is obtained from Table 1 22.2 Ta 22.0 Ti 23.9 V 21.2 C 10.7 The high-temperature high-entropy alloy has an ultra-high hardness of average 1492.9HV, which is about 7.1 times that of 304 stainless steel (hardness 210.0 HV).
Example 2
The alloy component of the ultra-high hardness Nb-Mo-Ta-Ti-V-C high-temperature high-entropy alloy of the embodiment is Nb a Mo b Ta c Ti d V e C f Where a=17.7%, b=16.4%, c=17.6%, d=19.1%, e=17.0%, f=12.2%, i.e. Nb 17.7 Mo 16.4 Ta 17.6 Ti 19.1 V 17.0 C 12.2 。
The preparation method of the Nb-Mo-Ta-Ti-V-C high-temperature high-entropy alloy comprises the following steps: the Nb, mo, ta, ti, V metal simple substance raw material is subjected to acid washing before being weighed so as to remove oxide skin on the surface of the raw material, ultrasonic cleaning is performed on the raw material by using absolute ethyl alcohol after the acid washing, and the raw material is dried to obtain the metal raw material with the purity of more than or equal to 99.9wt.%, then the raw material is weighed according to the atomic percentage, taC powder with the purity of more than or equal to 99.5wt.% is weighed, the cleaned raw material is accurately weighed according to the proportion, and the error is +/-0.0005 g; the weighed raw materials are sequentially put into the furnace according to the sequence from low melting point to high melting pointIn a water-cooled copper crucible of an arc melting furnace, the element with the lowest melting point is arranged at the lowest layer, and the element with the highest melting point is arranged at the uppermost layer; then placing the pure titanium ingot in another water-cooled copper crucible, closing the furnace door after all the pure titanium ingot is placed, and vacuumizing to 5 multiplied by 10 -3 Pa, and then filling pure argon to 0.05-0.06 MPa; the pure titanium ingot is smelted for 3-5 minutes before the alloy is smelted, so as to remove residual oxygen in a smelting furnace, then the alloy is smelted, the smelting current is 300-400A, after each smelting of the alloy, the electric arc is kept for 4-5 minutes, after the raw materials are smelted, electromagnetic stirring is started to enable smelting to be more uniform, and the stirring current is 6A. After the alloy ingot is cooled, turning over the ingot, repeatedly smelting for more than 5 times to ensure smelting uniformity, and cooling to obtain Nb 17.7 Mo 16.4 Ta 17.6 Ti 19.1 V 17.0 C 12.2 High-temperature high-entropy alloy.
The XRD diffraction pattern of this example is shown in FIG. 8, and the high Wen Gaoshang alloy consists of a high entropy alloy solid solution phase of BCC structure and a (Ti, ta) C high entropy carbide ceramic phase of FCC structure; FIG. 9 is an SEM image of the high Wen Gaoshang alloy, showing that the alloy has microscopic morphology characterized by relatively regular rounded carbides uniformly distributed on the high entropy alloy substrate; FIG. 10 is a DSC curve of example 2 showing a nearly straight line indicating Nb 17.7 Mo 16.4 Ta 17.6 Ti 19.1 V 17.0 C 12.2 The high-temperature high-entropy alloy has stable crystal structure in the range of room temperature to 1450 ℃, does not generate phase change, is not easy to damage under the high-temperature condition due to good phase stability, and has good application safety. FIG. 11 is a graph of room temperature compressive engineering stress-strain for example 2, with a compressive ultimate strength of 2122.3MPa and a maximum deformation of 10.4%.
The hardness test was conducted on example 2, and the results are shown in table 2.
The hardness testing method comprises the following steps: smashing an alloy ingot into small blocks by using a large hammer, performing thermal mosaic by using a metallographic mosaic machine, sequentially polishing by using sand paper according to the sequence of 400, 800, 1000, 1500 and 2000 meshes, and polishing until no scratch exists on the surface after polishing; after polishing, ultrasonically cleaning the surface with absolute ethyl alcohol to remove surface stains, and then starting to test hardness; hardness test A Vickers hardness tester, model Wilson VH1102, was used, the pressure was 100g, for 10s, 15 different points were randomly pressed together, and the average was calculated.
TABLE 2 Vickers hardness test results for example 2
Nb is obtained from Table 2 17.7 Mo 16.4 Ta 17.6 Ti 19.1 V 17.0 C 12.2 The high-temperature high-entropy alloy has an ultra-high hardness of average 1278.3HV, which is about 6.1 times that of 304 stainless steel (hardness 210.0 HV).
The foregoing is merely a preferred embodiment of the present invention and it should be noted that modifications and adaptations to those skilled in the art may be made without departing from the principles of the present invention, which are intended to be comprehended within the scope of the present invention.
Claims (10)
1. An ultra-high hardness high Wen Gaoshang alloy is characterized by comprising the following alloy components of Nb a Mo b Ta c Ti d V e C f Wherein a, b, c, d, e, f is the atomic percentage of the corresponding elements, a is 15-30, b is 0-20, c is 15-25, d is 15-30, e is 10-25, f is 10-20, and a+b+c+d+e+f=100.
2. The ultra-high hardness and high Wen Gaoshang alloy according to claim 1, wherein said high temperature and high entropy alloy has an alloy composition of Nb 22.2 Ta 22.0 Ti 23.9 V 21.2 C 10.7 。
3. An ultra-high hardness high Wen Gaoshang alloy according to claim 1Characterized in that the alloy component of the high-temperature high-entropy alloy is Nb 17.7 Mo 16.4 Ta 17.6 Ti 19.1 V 17.0 C 12.2 。
4. The ultra-high hardness high Wen Gaoshang alloy of claim 1, wherein said high entropy alloy is comprised of a BCC structure high entropy alloy phase and an FCC structure carbide ceramic phase; the high-entropy alloy phase is a solid solution composed of Nb, ta, ti and V elements, and the carbide ceramic phase is (Ti, ta) C high-entropy carbide.
5. The ultra-high hardness high Wen Gaoshang alloy according to claim 1, wherein said high entropy alloy comprises a solid solution phase having a BCC structure as a matrix, and carbide ceramic phases having a near-elliptical FCC structure are uniformly distributed on the matrix.
6. The method for preparing the ultra-high hardness high Wen Gaoshang alloy as claimed in claim 1, comprising the steps of:
s1, weighing raw materials Nb, mo, ta, ti, V and TaC according to an atomic ratio, and paving the raw materials in a copper crucible of a vacuum arc melting furnace in sequence from low melting point to high melting point;
s2, placing the titanium ingot into another copper crucible of the vacuum arc melting furnace, and melting the titanium ingot for 3-5 min under the argon atmosphere;
s3, smelting the raw materials in the step S1, starting electromagnetic stirring after the raw materials are melted, wherein the stirring current is 6A, obtaining an alloy cast ingot, and turning over the cast ingot after cooling;
s4, repeating the step S3 to obtain the alloy with ultrahigh hardness and high Wen Gaoshang.
7. The method for preparing an alloy with ultrahigh hardness and high Wen Gaoshang according to claim 6, wherein the raw material Nb, mo, ta, ti, V is elemental particles corresponding to each element, and the purity of the elemental particles is not less than 99.9 wt%.
8. The method for producing an alloy of high hardness Wen Gaoshang according to claim 6, wherein said raw material TaC is a powder having a purity of 99.5% or more and wt% or less.
9. The method of producing an ultra-high hardness high Wen Gaoshang alloy according to claim 6, wherein in step S2, after the titanium ingot is placed, the vacuum is applied to 5X 10 -3 And (3) filling argon with the purity of 99.99% to 0.05-0.06 Mpa under Pa.
10. The method of producing an ultra-high hardness high Wen Gaoshang alloy according to claim 6, wherein the melting current in step S3 is 300 to 400a and the arc is maintained for 4 to 5 minutes after each melting of the alloy.
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