High-entropy interfacial-induced cermet material and preparation method thereof

Abstract

The application provides a high-entropy interface-induced cermet material, relates to the field of cermet materials, and comprises a hard phase of Ti(C, N), a nickel-based bonding phase and a wetting regulation phase of a high-entropy solid solution, wherein the high-entropy solid solution is (M1, M2, M3, M4, M5)C, M1-M5 are five kinds of transition metals selected from tungsten, molybdenum, tantalum, niobium, zirconium, nickel, manganese, chromium and rhenium, and the mixing entropy of the five kinds of transition metals; the cermet material is obtained through base powder pretreatment, amorphous nickel-based alloy preparation, high-entropy solid solution preparation, high-entropy solid solution pretreatment, powder mixing forming and sintering. The cermet material is optimized by constructing a high-entropy wetting phase to induce an interface structure, so that the crack passivation capacity is improved, the interface strength is enhanced, and the synchronous improvement of the fracture toughness and the strength of the cermet material is realized.

Description

Technical Field

[0001] This invention relates to the field of metal-ceramic materials technology, and in particular to a high-entropy interface-induced metal-ceramic material and its preparation method. Background Technology

[0002] Ti(C,N)-based cermets are composite materials prepared by powder metallurgy, consisting of titanium carbide (TiC) and titanium nitride (TiN) solid solutions as hard phases, combined with metallic binder phases (such as Ni and Co) and auxiliary carbides. They combine the high hardness and high temperature resistance of ceramics with the toughness of metals and are widely used in cutting tools, wear-resistant parts and other fields. However, because the core hard phase of Ti(C,N)-based cermets is a solid solution formed by titanium carbide and titanium nitride, it is essentially a covalently bond-dominated (i.e., titanium carbide and titanium nitride are predominantly covalently bonded) ceramic phase. This phase has high bond energy but strong directionality, resulting in high atomic slip resistance. It cannot dissipate stress through plastic deformation (such as dislocation movement), leading to localized stress concentration and crack initiation and propagation. Furthermore, when Ti(C,N) particles are large or unevenly distributed, stress concentration points easily form between the particles, creating weak areas. Under stress, these weak areas preferentially crack and propagate rapidly. In addition, the large difference in thermal expansion coefficients between the Ti(C,N) hard phase and the metal bonding phase generates thermal mismatch stress during sintering and cooling, leading to microcracks and other defects within the material. All of these factors contribute to insufficient toughness in Ti(C,N)-based cermets, severely limiting their service life and application range.

[0003] Traditional toughening methods, such as simple coating structures or single additive regulation, are problematic. Simple coating typically involves coating the surface of the Ti(C,N) hard phase with a layer of metal or alloy to form a "core-ring" structure, thereby improving interfacial bonding and inhibiting grain growth. However, this method suffers from difficulties in precisely controlling interfacial strength, performance fluctuations due to uneven coating structure, and the inability to solve problems such as agglomeration or coarseness of hard phase particles. Single additives usually improve toughness by adjusting composition, but the addition of a single additive can easily disrupt the performance balance (e.g., adding a single highly ductile metal like Co can improve the toughness of the binder phase but significantly reduce the material's hardness; adding a single tungsten carbide can improve toughness through grain refinement, but excessive tungsten carbide can easily form a brittle (W,Ti)(C,N) solid solution, leading to interfacial defects). In short, traditional toughening methods struggle to effectively balance high hardness and high toughness, and the regulation methods suffer from poor stability and consistency. Summary of the Invention

[0004] To address the problems existing in the prior art, the present invention aims to provide a high-entropy interface-induced metal-ceramic material. This ceramic material improves crack passivation capability and enhances interface strength by constructing a high-entropy wetting phase-induced interface structure optimization, thereby achieving a simultaneous improvement in the fracture toughness and strength of the ceramic material.

[0005] Another object of the present invention is to provide a method for preparing the above-mentioned high-entropy interface-induced metal-ceramic material.

[0006] The objective of this invention is achieved through the following technical solution:

[0007] A high-entropy interface-induced cermet material comprises a Ti(C,N) hard phase, a nickel (Ni)-based binder phase, and a high-entropy solid solution wetting-regulating phase. The high-entropy solid solution is (M1, M2, M3, M4, M5)C, where M1–M5 are any five selected from nine transition metals: tungsten (W), molybdenum (Mo), tantalum (Ta), niobium (Nb), zirconium (Zr), nickel (Ni), manganese (Mn), chromium (Cr), and rhenium (Re). The mixing entropy of the five transition metals is... .

[0008] Based on further optimization of the above scheme, the hard phase of the Ti(C,N) is Ti(C) 0.7 N 0.3 The matrix powder; the nickel-based binder phase is an amorphous alloy of the Ni-Cr-B-Si system; the mass percentages of the hard phase, binder phase and wetting control phase are 45%–50%, 18%–22%, and 28%–33%, respectively.

[0009] Based on further optimization of the above scheme, the amorphous nickel-based alloy uses Ni 75 Cr 10 B 10 Si5; the high-entropy solid solution adopts (W,Mo,Ta,Nb,Zr)C, and the atomic molar ratio of tungsten, molybdenum, tantalum, niobium, zirconium and carbon is 4.0~5.5:2.5~3.5:1.0~1.8:0.8~1.5:0.5~1.2:9.0~12.0.

[0010] A method for preparing a high-entropy interface-induced metal-ceramic material includes:

[0011] Step S1, Pretreatment of matrix powder: Pretreatment of Ti(C) powder 0.7 N 0.3 The matrix powder (particle size 200-400 nm) was vacuum dried and stored for later use.

[0012] Step S2, Preparation of amorphous nickel-based alloy: Amorphous nickel-based alloys are prepared by solution quenching method;

[0013] Step S3, Preparation of high-entropy solid solution: First, a high-entropy carbide precursor is prepared by sol-gel synthesis, and then a high-entropy solid solution of (W,Mo,Ta,Nb,Zr)C is synthesized by laser solid-state synthesis.

[0014] Step S4, Pretreatment of high-entropy solid solution: Core-shell structure powder of niobium-encapsulated high-entropy solid solution was prepared by ball milling;

[0015] Step S5, Powder Mixing and Molding: The pretreated matrix powder, amorphous nickel-based alloy, and pretreated high-entropy solid solution are sequentially mixed and ball-milled, pretreated with a gradient magnetic field, and bidirectional molding to obtain a compact.

[0016] Step S6, Sintering: The pressed blank is placed in a sintering furnace and subjected to low-temperature pre-sintering, three-stage solid-state sintering, and liquid-phase sintering in sequence. In the three-stage solid-state sintering and liquid-phase sintering, magnetic field control is introduced. After cooling and demagnetization, the metal ceramic material is obtained.

[0017] Based on further optimization of the above scheme, the vacuum drying in step S1 is carried out at a temperature of 90-110℃ and a vacuum degree of 2-6Pa for 1.5-2.5 hours to remove adsorbed water from the surface of the matrix powder; after drying, it is transferred to a sealed container protected by argon gas for storage and to avoid secondary moisture absorption.

[0018] Based on further optimization of the above scheme, the specific method for preparing amorphous nickel-based alloys using the solution quenching method is as follows: metallic nickel, chromium, boron, and silicon are proportioned according to the atomic ratios in the amorphous alloy system, added to a vacuum arc furnace, and quenched under a vacuum degree not exceeding 10. -3 The amorphous ribbon is melted at a melting temperature of 1500–1560℃. Then, an amorphous ribbon with a thickness of 20–50 μm is prepared using a single-roller rapid quenching device with a copper roller speed of 28–32 m / s. Finally, the amorphous ribbon is crushed into small particles using an agate mortar and sieved using a 200-mesh sieve. The sieved particles are then vacuum-sealed in aluminum foil bags for later use.

[0019] Based on further optimization of the above scheme, the preparation of high-entropy carbide precursors by the sol-gel synthesis method is specifically as follows:

[0020] First, weigh WCl6 (tungsten hexachloride), MoCl5 (molybdenum pentachloride), TaCl5 (tantalum pentachloride), NbCl5 (niobium pentachloride), ZrCl4 (zirconium tetrachloride), and a carbon source in atomic molar ratios. Dissolve the metal chlorides in a mixed solvent of ethanol and deionized water, with a volume ratio of ethanol to deionized water of 3–4:1 and a mass ratio of metal chlorides to the mixed solvent of 1:5–10. Stir at 300–400 rpm for 28–32 minutes. Then add the carbon source to the stirred solution. In a mixed solution, the pH was adjusted to 3.0 with nitric acid; the mixture was stirred for 1.8–2.2 h in a water bath at 55–65 °C and 250–350 rpm to form a wet gel; the wet gel was then transferred to an oven and dried at 115–125 °C for 11–13 h to obtain a dry gel; finally, the dry gel was placed in an argon atmosphere calcination furnace and heated to 1350–1450 °C at a rate of 4.5–5.5 °C / min and held for 1.8–2.2 h to obtain a high-entropy carbide precursor.

[0021] Based on further optimization of the above scheme, the carbon source can be any one of furfuryl alcohol, glucose, or phenolic resin.

[0022] Based on further optimization of the above scheme, the specific method for synthesizing high-entropy solid solutions using laser solid-state technology is as follows: a high-entropy carbide precursor is laid flat on a 5mm thick graphite substrate, and a pulsed Nd:YAG laser is used for scanning. The laser wavelength is 1064nm, the power is 2.5kW, the pulse frequency is 50Hz, the laser spot diameter is 2mm, and the scanning speed is 8mm / s, achieving 10 7 The cooling rate is K / s; after laser scanning, the powder is collected to obtain a high-entropy solid solution.

[0023] Based on further optimization of the above scheme, the specific preparation method for the core-shell structure powder of niobium-encapsulated high-entropy solid solution by ball milling is as follows:

[0024] First, weigh 5%–8% of the high-entropy solid solution niobium powder (particle size 100–300 nm, purity 99.99%) and add it together with the high-entropy solid solution powder into a planetary ball mill. Use anhydrous ethanol as the dispersant and tungsten carbide balls (5 mm in diameter) as the ball milling medium. The ball-to-material ratio is 6–8:1, the rotation speed is 350–450 rpm, and the milling time is 3.5–4.5 h. After milling, vacuum dry at a temperature of 80–100 °C and a vacuum degree of 2–6 Pa for 2–4 h to obtain the core-shell structure powder.

[0025] Based on further optimization of the above scheme, the mass percentages of the pretreated matrix powder, amorphous nickel-based alloy, and pretreated high-entropy solid solution in step S5 are: 45%–50%, 18%–22%, and 28%–33%, respectively; the mixing and ball milling specifically involves: loading each raw material into a stainless steel ball mill jar and evacuating it to 10... -3 After Pa, argon gas is introduced to 0.1 MPa. Carbide (5 mm in diameter) is used as the ball milling medium, with a ball-to-material ratio of 8-10:1, a rotation speed of 250-350 rpm, and ball milling for 11-13 hours (during ball milling, after every 30 minutes of ball milling, the machine is stopped for 10 minutes for heat dissipation) to achieve mixed ball milling of raw materials. The gradient magnetic field pretreatment is as follows: after mixed ball milling, the ball milled powder is placed in a multi-layer NdFeB magnet array (that is, multiple NdFeB magnets are combined by layering and stacking), and a gradient magnetic field of 0.8 T with a magnetic field gradient of 10 T / m is applied. The powder is left to stand at room temperature for 25-35 minutes to guide paramagnetic elements such as W and Nb to migrate to the preset interface. The bidirectional molding is as follows: the powder after gradient magnetic field pretreatment is loaded into a graphite mold and molded using a bidirectional press. A pressure of 140-160 MPa is applied bidirectionally and held for 4-6 minutes. After molding, water is circulated to cool the mold to ensure that the mold temperature does not exceed 50℃.

[0026] Based on further optimization of the above scheme, in step S6, the low-temperature pre-sintering specifically involves: heating to 590-610℃ at a heating rate of 8-10℃ / min and holding at that temperature for 0.9-1.1h.

[0027] The three-stage solid-state sintering process is as follows: First, the temperature is increased to 1080–1120℃ at a heating rate of 10–12℃ / min, held for 1.3–1.7 h, and simultaneously the axial gradient magnetic field is activated, applying an axial gradient magnetic field of 0.6T with a gradient of 8T / m. Then, the temperature is increased to 1180–1220℃ at a heating rate of 14–16℃ / min, held for 1.3–1.7 h, and an axial gradient magnetic field of 0.8T with a gradient of 8T / m is applied. Finally, the temperature is increased to 1280–1320℃ at a heating rate of 10–12℃ / min, held for 1.8–2.2 h, and the magnetic field is switched from axial to radial, applying a radial gradient magnetic field of 0.8T with a gradient of 10T / m.

[0028] The liquid phase sintering process specifically involves heating the temperature to 1410–1500℃ at a heating rate of 4–6℃ / min, holding the temperature for 0.8–1.2 h, and simultaneously applying an axial gradient magnetic field of 1.0T with a gradient of 8T / m.

[0029] Based on further optimization of the above scheme, in step S6, cooling demagnetization specifically involves cooling to 750-850°C at a cooling rate of 2.5-3.5°C / min, and then cooling to room temperature with the furnace; simultaneously using an alternating magnetic field for demagnetization to ensure that the residual magnetism of the finished product is no greater than 0.01T.

[0030] The following are the technical effects of this solution:

[0031] This invention achieves the preparation of high-entropy solid solutions through sol-gel synthesis and laser solid-state synthesis, replacing the traditional combination of high-energy ball milling and thermal reaction. This not only avoids the problem of dispersion of hard and binder phases in the high-entropy solid solution components during ball milling, making it difficult to form a uniform high-entropy alloy, but also avoids the problem of local segregation caused by insufficient diffusion of refractory metals (tungsten, molybdenum, etc.) due to low thermal reaction temperature after high-energy ball milling. Subsequently, by utilizing the preparation of amorphous nickel-based alloys and high-entropy solid solution core-shell structures, the amorphous phase preferentially forms a good liquid phase during sintering, filling the interparticle gaps between the matrix and the high-entropy solid solution and improving the overall density of the material. Simultaneously, the amorphous nickel-based alloy crystallizes during sintering, effectively hindering the diffusion of hard phase elements such as Ti, C, and N from the Ti(C,N) matrix to the binder phase, while reducing the loss of strong carbides from the high-entropy solid solution to the nickel-based phase, improving the interfacial bonding strength and ensuring the overall mechanical properties of the cermet material. In addition, the amorphous alloy not only provides an efficient medium for the diffusion of the core-shell structure and promotes the uniform formation of the high-melting-point phase transition layer (the transition layer anchors the migration path of the high-entropy solid solution and enhances the metallurgical bonding of the interface through lattice matching), its crystallization products also provide good plasticity and toughness, reduce interfacial stress concentration, thereby avoiding problems such as local brittleness or corrosion failure caused by component segregation and ensuring the consistency of material properties.

[0032] This invention combines a Ti(C,N) hard phase, a nickel (Ni)-based binder phase, and a high-entropy solid solution wetting control phase to form a metal-ceramic material with high hardness, high fracture toughness, and high flexural strength, effectively improving crack passivation ability and enhancing interface strength, thus realizing the construction of high-performance ceramic materials. Attached Figure Description

[0033] Figure 1 This is a scanning electron microscope image of the metal-ceramic material in an embodiment of the present invention. Detailed Implementation

[0034] To make the objectives, technical solutions, and advantages of the embodiments of the present invention clearer, the technical solutions of the embodiments of the present invention will be clearly described below. Obviously, the described embodiments are some embodiments of the present invention, but not all embodiments.

[0035] Example 1:

[0036] A high-entropy interface-induced metal-ceramic material comprises a Ti(C,N) hard phase, a nickel (Ni)-based binder phase, and a high-entropy solid solution wetting-regulating phase, wherein the mass percentages of the hard phase, binder phase, and wetting-regulating phase are 45%, 22%, and 33%, respectively; wherein the Ti(C,N) hard phase is Ti(C) 0.7 N 0.3 ) Matrix powder; nickel-based binder phase using Ni 75 Cr 10 B 10 Si5 is an amorphous alloy; the high-entropy solid solution is (W,Mo,Ta,Nb,Zr)C, and the atomic molar ratio of tungsten, molybdenum, tantalum, niobium, zirconium and carbon is 4.0:2.5:1.0:0.8:0.5:9.0.

[0037] A method for preparing a high-entropy interface-induced metal-ceramic material includes:

[0038] Step S1, Pretreatment of matrix powder: Pretreatment of Ti(C) powder 0.7 N 0.3 The matrix powder (particle size 200-400 nm) was vacuum dried at 90 °C and 2 Pa for 2.5 h to remove adsorbed water from the surface of the matrix powder. After drying, it was transferred to a sealed container under argon protection for storage to avoid secondary moisture absorption.

[0039] Step S2, Preparation of Amorphous Nickel-Based Alloy: An amorphous nickel-based alloy is prepared using a solution quenching method. Specifically, metallic nickel, chromium, boron, and silicon are proportioned according to the atomic ratios required for an amorphous alloy system, added to a vacuum arc furnace, and heated under a vacuum of no more than 10... -3 At Pa and a melting temperature of 1500℃, the material is melted (until all raw materials are completely melted and mixed); then, an amorphous ribbon with a thickness of 20μm is prepared using a single-roller rapid quenching device with a copper roller speed of 28m / s; finally, the amorphous ribbon is crushed into small particles using an agate mortar and sieved using a 200-mesh sieve, and the sieved particles are vacuum-sealed in aluminum foil bags for later use.

[0040] Step S3, Preparation of High-Entropy Solid Solution: First, a high-entropy carbide precursor is prepared using the sol-gel synthesis method, specifically as follows:

[0041] First, WCl6, MoCl5, TaCl5, NbCl5, ZrCl4, and glucose were weighed sequentially according to atomic molar ratios. The metal chlorides (WCl6, MoCl5, TaCl5, NbCl5, and ZrCl4) were dissolved in a mixed solvent of ethanol and deionized water, with a volume ratio of ethanol to deionized water of 3:1 and a mass ratio of metal chlorides to the mixed solvent of 1:5. The mixture was stirred at 300 rpm for 32 min. Then, glucose was added to the stirred mixture, and the pH was adjusted to 3.0 with nitric acid. The mixture was stirred at 250 rpm for 2.2 h in a water bath at 55 °C to form a wet gel. The wet gel was then transferred to an oven and dried at 115 °C for 13 h to obtain a dry gel. Finally, the dry gel was placed in an argon atmosphere furnace and heated to 1350 °C at a rate of 4.5 °C / min and held at that temperature for 2.2 h to obtain a high-entropy carbide precursor (precursor particle size 50–100 nm).

[0042] High-entropy solid solutions of (W, Mo, Ta, Nb, Zr)C were then synthesized using laser solid-state technology. Specifically, a high-entropy carbide precursor was laid flat on a 5mm thick graphite substrate, and a pulsed Nd:YAG laser was used for scanning. The laser wavelength was 1064nm, the power was 2.5kW, the pulse frequency was 50Hz, the laser spot diameter was 2mm, and the scanning speed was 8mm / s, achieving a 10... 7 The cooling rate is K / s; after laser scanning, the powder is collected to obtain a high-entropy solid solution.

[0043] Step S4, Pretreatment of High-Entropy Solid Solution: Core-shell structured powder of niobium-encapsulated high-entropy solid solution was prepared by ball milling, specifically as follows:

[0044] First, 5% of the mass of the high-entropy solid solution was weighed niobium powder (particle size 100-300 nm, purity 99.99%), and added together with the high-entropy solid solution powder into a planetary ball mill. Anhydrous ethanol was used as the dispersant, tungsten carbide balls (5 mm in diameter) were used as the ball milling medium, the ball-to-material ratio was 6:1, the rotation speed was 350 rpm, and the milling was carried out for 4.5 h. After milling, the powder was vacuum dried at 80 °C and 2 Pa for 4 h to obtain the core-shell structure powder.

[0045] Step S5, Powder Mixing and Molding: The pretreated matrix powder, amorphous nickel-based alloy, and pretreated high-entropy solid solution are mixed and ball-milled in batches of 45%, 22%, and 33% by mass, respectively, followed by gradient magnetic field pretreatment and bidirectional molding to obtain a compact; wherein, the mixing and ball milling specifically involves: loading each raw material into a stainless steel ball mill jar and evacuating it to 10... -3After Pa, argon gas is introduced to 0.1 MPa. Carbide (5 mm in diameter) is used as the ball milling medium, with a ball-to-material ratio of 8:1 and a rotation speed of 250 rpm. The ball milling is carried out for 13 hours (during the ball milling process, after every 30 minutes of ball milling, the machine is stopped for 10 minutes for heat dissipation) to achieve the mixing and ball milling of the raw materials. The gradient magnetic field pretreatment is as follows: after mixing and ball milling, the ball milled powder is placed in a multi-layer NdFeB magnet array (that is, multiple NdFeB magnets are combined by layering and stacking), and a gradient magnetic field of 0.8 T with a magnetic field gradient of 10 T / m is applied. The powder is left to stand at room temperature for 25 minutes to guide paramagnetic elements such as W and Nb to migrate to the preset interface. The bidirectional molding is as follows: the powder after gradient magnetic field pretreatment is loaded into a graphite mold and molded using a bidirectional press. A pressure of 140 MPa is applied in both directions and held for 6 minutes. After molding, water is circulated to cool the mold to ensure that the mold temperature does not exceed 50℃.

[0046] Step S6, Sintering: Place the pressed billet into the sintering furnace (using a graphite mold, the inner wall of which is coated with boron nitride release agent for easy demolding after sintering; a layered NdFeB magnet array is embedded at the bottom of the mold, and the magnets can switch between axial and radial magnetic fields, with Hall sensors for real-time monitoring of magnetic field strength), and evacuate the sintering furnace to ≤10. -4 Pa, and then successively perform low-temperature pre-sintering, three-stage solid-state sintering, and liquid-phase sintering, specifically as follows:

[0047] Low-temperature pre-sintering: heating to 590℃ at a heating rate of 8℃ / min and holding at that temperature for 1.1h;

[0048] The three-stage solid-state sintering process is as follows: First, the temperature is increased to 1080℃ at a heating rate of 10℃ / min, held for 1.7h, and simultaneously the axial gradient magnetic field is activated, applying an axial gradient magnetic field of 0.6T with a gradient of 8T / m. Then, the temperature is increased to 1180℃ at a heating rate of 14℃ / min, held for 1.7h, and an axial gradient magnetic field of 0.8T with a gradient of 8T / m is applied. Finally, the temperature is increased to 1280℃ at a heating rate of 10℃ / min, held for 2.2h, and the magnetic field is switched from axial to radial, applying a radial gradient magnetic field of 0.8T with a gradient of 10T / m.

[0049] The liquid phase sintering process specifically involves heating to 1410℃ at a heating rate of 4℃ / min, holding at that temperature for 1.2h, and simultaneously applying an axial gradient magnetic field of 1.0T with a gradient of 8T / m.

[0050] After cooling and demagnetization, a metal-ceramic material is obtained. The cooling and demagnetization process involves cooling the material to 850°C at a rate of 2.5°C / min, and then cooling it to room temperature in the furnace. Simultaneously, an alternating magnetic field is used for demagnetization to ensure that the residual magnetism of the finished product is no greater than 0.01T.

[0051] Example 2:

[0052] A high-entropy interface-induced cermet material comprises a Ti(C,N) hard phase, a nickel (Ni)-based binder phase, and a high-entropy solid solution wetting-regulating phase, wherein the mass percentages of the hard phase, binder phase, and wetting-regulating phase are 48%, 20%, and 32%, respectively; wherein the Ti(C,N) hard phase is Ti(C) 0.7 N 0.3 ) Matrix powder; nickel-based binder phase using Ni 75 Cr 10 B 10 Si5 is an amorphous alloy; the high-entropy solid solution is (W,Mo,Ta,Nb,Zr)C, and the atomic molar ratio of tungsten, molybdenum, tantalum, niobium, zirconium and carbon is 4.7:3.0:1.4:1.2:0.8:11.5.

[0053] A method for preparing a high-entropy interface-induced metal-ceramic material includes:

[0054] Step S1, Pretreatment of matrix powder: Pretreatment of Ti(C) powder 0.7 N 0.3 The matrix powder (particle size 200-400nm) was vacuum dried at 100℃ and 4Pa for 2 hours to remove adsorbed water from the surface of the matrix powder. After drying, it was transferred to a sealed container under argon protection for storage to avoid secondary moisture absorption.

[0055] Step S2, Preparation of Amorphous Nickel-Based Alloy: An amorphous nickel-based alloy is prepared using a solution quenching method. Specifically, metallic nickel, chromium, boron, and silicon are proportioned according to the atomic ratios required for an amorphous alloy system, added to a vacuum arc furnace, and heated under a vacuum of no more than 10... -3 At Pa and a melting temperature of 1530℃, the material is melted (until all raw materials are completely melted and mixed); then, an amorphous ribbon with a thickness of 35μm is prepared using a single-roller rapid quenching device with a copper roller speed of 30m / s; finally, the amorphous ribbon is crushed into small particles using an agate mortar and sieved using a 200-mesh sieve, and the sieved particles are vacuum-sealed in aluminum foil bags for later use.

[0056] Step S3, Preparation of High-Entropy Solid Solution: First, a high-entropy carbide precursor is prepared using the sol-gel synthesis method, specifically as follows:

[0057] First, WCl6, MoCl5, TaCl5, NbCl5, ZrCl4, and furfuryl alcohol were weighed out sequentially according to atomic molar ratios. The metal chlorides (WCl6, MoCl5, TaCl5, NbCl5, and ZrCl4) were dissolved in a mixed solvent of ethanol and deionized water, with a volume ratio of ethanol to deionized water of 3:1 and a mass ratio of metal chlorides to the mixed solvent of 1:7. The mixture was stirred at 350 rpm for 30 min. Then, furfuryl alcohol was added to the stirred mixture, and the pH was adjusted to 3.0 with nitric acid. The mixture was stirred at 300 rpm for 2 h in a water bath at 60 °C to form a wet gel. The wet gel was then transferred to an oven and dried at 120 °C for 12 h to obtain a dry gel. Finally, the dry gel was placed in an argon atmosphere furnace and heated to 1400 °C at a rate of 5 °C / min and held for 2 h to obtain a high-entropy carbide precursor (precursor particle size 50–100 nm).

[0058] High-entropy solid solutions of (W, Mo, Ta, Nb, Zr)C were then synthesized using laser solid-state technology. Specifically, a high-entropy carbide precursor was laid flat on a 5mm thick graphite substrate, and a pulsed Nd:YAG laser was used for scanning. The laser wavelength was 1064nm, the power was 2.5kW, the pulse frequency was 50Hz, the laser spot diameter was 2mm, and the scanning speed was 8mm / s, achieving a 10... 7 The cooling rate is K / s; after laser scanning, the powder is collected to obtain a high-entropy solid solution.

[0059] Step S4, Pretreatment of High-Entropy Solid Solution: Core-shell structured powder of niobium-encapsulated high-entropy solid solution was prepared by ball milling, specifically as follows:

[0060] First, 6.5% of the mass of the high-entropy solid solution was weighed niobium powder (particle size 100-300 nm, purity 99.99%), and added together with the high-entropy solid solution powder into a planetary ball mill. Anhydrous ethanol was used as the dispersant, tungsten carbide balls (5 mm in diameter) were used as the ball milling medium, the ball-to-material ratio was 7:1, the rotation speed was 400 rpm, and the milling was carried out for 4 hours. After milling, the powder was vacuum dried at 90℃ and 4 Pa ​​for 3 hours to obtain the core-shell structure powder.

[0061] Step S5, Powder Mixing and Molding: The pretreated matrix powder, amorphous nickel-based alloy, and pretreated high-entropy solid solution are mixed and ball-milled in batches of 48%, 20%, and 32% by mass, respectively, followed by gradient magnetic field pretreatment and bidirectional molding to obtain a compact; wherein, the mixing and ball milling specifically involves: loading each raw material into a stainless steel ball mill jar, and evacuating to 10... -3After Pa, argon gas is introduced to 0.1 MPa. Carbide (5 mm in diameter) is used as the ball milling medium, with a ball-to-material ratio of 9:1, a rotation speed of 300 rpm, and ball milling for 12 hours (during ball milling, after every 30 minutes of ball milling, the machine is stopped for 10 minutes for heat dissipation) to achieve mixed ball milling of raw materials. The gradient magnetic field pretreatment is as follows: after mixed ball milling, the ball milled powder is placed in a multi-layer NdFeB magnet array (that is, multiple NdFeB magnets are combined by layering and stacking), and a gradient magnetic field of 0.8 T with a magnetic field gradient of 10 T / m is applied. The mixture is left to stand at room temperature for 30 minutes to guide paramagnetic elements such as W and Nb to migrate to the preset interface. The bidirectional molding is as follows: the powder after gradient magnetic field pretreatment is loaded into a graphite mold and molded using a bidirectional press. A pressure of 150 MPa is applied in both directions and held for 5 minutes. After molding, water is circulated to cool the mold to ensure that the mold temperature does not exceed 50℃.

[0062] Step S6, Sintering: Place the pressed billet into the sintering furnace (using a graphite mold, the inner wall of which is coated with boron nitride release agent for easy demolding after sintering; a layered NdFeB magnet array is embedded at the bottom of the mold, and the magnets can switch between axial and radial magnetic fields, with Hall sensors for real-time monitoring of magnetic field strength), and evacuate the sintering furnace to ≤10. -4 Pa, and then successively perform low-temperature pre-sintering, three-stage solid-state sintering, and liquid-phase sintering, specifically as follows:

[0063] Low-temperature pre-sintering: Heat to 600℃ at a heating rate of 9℃ / min and hold for 1 hour;

[0064] The three-stage solid-state sintering process is as follows: First, the temperature is increased to 1100℃ at a heating rate of 11℃ / min, held for 1.5 hours, and simultaneously the axial gradient magnetic field is activated, applying an axial gradient magnetic field of 0.6T with a gradient of 8T / m. Then, the temperature is increased to 1200℃ at a heating rate of 15℃ / min, held for 1.5 hours, and an axial gradient magnetic field of 0.8T with a gradient of 8T / m is applied. Finally, the temperature is increased to 1300℃ at a heating rate of 11℃ / min, held for 2 hours, and the magnetic field is switched from axial to radial, applying a radial gradient magnetic field of 0.8T with a gradient of 10T / m.

[0065] The liquid phase sintering process is as follows: the temperature is raised to 1455℃ at a heating rate of 5℃ / min and held for 1h, while an axial gradient magnetic field of 1.0T and a gradient of 8T / m is applied simultaneously.

[0066] After cooling and demagnetization, a metal-ceramic material is obtained. The cooling and demagnetization process involves cooling the material to 800°C at a rate of 3°C / min, and then cooling it to room temperature in the furnace. Simultaneously, an alternating magnetic field is used for demagnetization to ensure that the residual magnetism of the finished product is no greater than 0.01T.

[0067] Example 3:

[0068] A high-entropy interface-induced cermet material comprises a Ti(C,N) hard phase, a nickel (Ni)-based binder phase, and a high-entropy solid solution wetting-regulating phase, wherein the mass percentages of the hard phase, binder phase, and wetting-regulating phase are 50%, 21%, and 29%, respectively; wherein the Ti(C,N) hard phase is Ti(C) 0.7 N 0.3 ) Matrix powder; nickel-based binder phase using Ni 75 Cr 10 B 10 Si5 is an amorphous alloy; the high-entropy solid solution is (W,Mo,Ta,Nb,Zr)C, and the atomic molar ratio of tungsten, molybdenum, tantalum, niobium, zirconium and carbon is 5.5:3.5:1.8:1.5:1.2:12.0.

[0069] A method for preparing a high-entropy interface-induced metal-ceramic material includes:

[0070] Step S1, Pretreatment of matrix powder: Pretreatment of Ti(C) powder 0.7 N 0.3 The matrix powder (particle size 200-400 nm) was vacuum dried at 110 °C and 6 Pa for 1.5 h to remove adsorbed water from the surface of the matrix powder. After drying, it was transferred to a sealed container under argon protection for storage to avoid secondary moisture absorption.

[0071] Step S2, Preparation of Amorphous Nickel-Based Alloy: An amorphous nickel-based alloy is prepared using a solution quenching method. Specifically, metallic nickel, chromium, boron, and silicon are proportioned according to the atomic ratios required for an amorphous alloy system, added to a vacuum arc furnace, and heated under a vacuum of no more than 10... -3 At Pa and a melting temperature of 1560℃, the material is melted (until all raw materials are completely melted and mixed); then, an amorphous ribbon with a thickness of 50μm is prepared using a single-roller rapid quenching device with a copper roller speed of 32m / s; finally, the amorphous ribbon is crushed into small particles using an agate mortar and sieved using a 200-mesh sieve, and the sieved particles are vacuum-sealed in aluminum foil bags for later use.

[0072] Step S3, Preparation of High-Entropy Solid Solution: First, a high-entropy carbide precursor is prepared using the sol-gel synthesis method, specifically as follows:

[0073] First, WCl6, MoCl5, TaCl5, NbCl5, ZrCl4, and phenolic resin were weighed out sequentially according to atomic molar ratios. The metal chlorides (WCl6, MoCl5, TaCl5, NbCl5, and ZrCl4) were dissolved in a mixed solvent of ethanol and deionized water, with a volume ratio of ethanol to deionized water of 4:1 and a mass ratio of metal chlorides to the mixed solvent of 1:10. The mixture was stirred at 400 rpm for 28 minutes. Then, the phenolic resin was added to the stirred mixture, and the pH was adjusted to 3.0 using nitric acid. A wet gel was formed by stirring at 350 rpm for 1.8 h in a water bath at 65℃. The wet gel was then transferred to an oven and dried at 125℃ for 11 h to obtain a dry gel. Finally, the dry gel was placed in an argon atmosphere calcination furnace and heated to 1450℃ at a rate of 5.5℃ / min and held for 1.8 h to obtain a high-entropy carbide precursor (precursor particle size 50-100 nm).

[0074] High-entropy solid solutions of (W, Mo, Ta, Nb, Zr)C were then synthesized using laser solid-state technology. Specifically, a high-entropy carbide precursor was laid flat on a 5mm thick graphite substrate, and a pulsed Nd:YAG laser was used for scanning. The laser wavelength was 1064nm, the power was 2.5kW, the pulse frequency was 50Hz, the laser spot diameter was 2mm, and the scanning speed was 8mm / s, achieving a 10... 7 The cooling rate is K / s; after laser scanning, the powder is collected to obtain a high-entropy solid solution.

[0075] Step S4, Pretreatment of High-Entropy Solid Solution: Core-shell structured powder of niobium-encapsulated high-entropy solid solution was prepared by ball milling, specifically as follows:

[0076] First, 8% of the mass of the high-entropy solid solution was weighed niobium powder (particle size 100-300 nm, purity 99.99%), and added together with the high-entropy solid solution powder into a planetary ball mill. Anhydrous ethanol was used as the dispersant, tungsten carbide balls (5 mm in diameter) were used as the ball milling medium, the ball-to-material ratio was 8:1, the rotation speed was 450 rpm, and the milling was carried out for 3.5 h. After milling, the powder was vacuum dried at 100℃ and 6 Pa for 2 h to obtain the core-shell structure powder.

[0077] Step S5, Powder Mixing and Molding: The pretreated matrix powder, amorphous nickel-based alloy, and pretreated high-entropy solid solution are mixed and ball-milled in batches of 50%, 21%, and 29% by mass, respectively, followed by gradient magnetic field pretreatment and bidirectional molding to obtain a compact; wherein, the mixing and ball milling specifically involves: loading each raw material into a stainless steel ball mill jar, and evacuating to 10... -3After Pa, argon gas is introduced to 0.1 MPa. Carbide (5 mm in diameter) is used as the ball milling medium, with a ball-to-material ratio of 10:1 and a rotation speed of 350 rpm. The ball milling is carried out for 11 hours (during the ball milling process, after every 30 minutes of ball milling, the machine is stopped for 10 minutes for heat dissipation) to achieve the mixing and ball milling of the raw materials. The gradient magnetic field pretreatment is as follows: after mixing and ball milling, the ball milled powder is placed in a multi-layer NdFeB magnet array (that is, multiple NdFeB magnets are combined by layering and stacking), and a gradient magnetic field of 0.8 T with a magnetic field gradient of 10 T / m is applied. The powder is left to stand at room temperature for 35 minutes to guide paramagnetic elements such as W and Nb to migrate to the preset interface. The bidirectional molding is as follows: the powder after gradient magnetic field pretreatment is loaded into a graphite mold and molded using a bidirectional press. A pressure of 160 MPa is applied in both directions and held for 4 minutes. After molding, water is circulated to cool the mold to ensure that the mold temperature does not exceed 50℃.

[0078] Step S6, Sintering: Place the pressed billet into the sintering furnace (using a graphite mold, the inner wall of which is coated with boron nitride release agent for easy demolding after sintering; a layered NdFeB magnet array is embedded at the bottom of the mold, and the magnets can switch between axial and radial magnetic fields, with Hall sensors for real-time monitoring of magnetic field strength), and evacuate the sintering furnace to ≤10. -4 Pa, and then successively perform low-temperature pre-sintering, three-stage solid-state sintering, and liquid-phase sintering, specifically as follows:

[0079] Low-temperature pre-sintering: heating to 610℃ at a heating rate of 10℃ / min and holding at that temperature for 0.9h;

[0080] The three-stage solid-state sintering process is as follows: First, the temperature is increased to 1120℃ at a heating rate of 12℃ / min, held for 1.3 hours, and simultaneously the axial gradient magnetic field is activated, applying an axial gradient magnetic field of 0.6T with a gradient of 8T / m. Then, the temperature is increased to 1220℃ at a heating rate of 16℃ / min, held for 1.3 hours, and an axial gradient magnetic field of 0.8T with a gradient of 8T / m is applied. Finally, the temperature is increased to 1320℃ at a heating rate of 12℃ / min, held for 1.8 hours, and the magnetic field is switched from axial to radial, applying a radial gradient magnetic field of 0.8T with a gradient of 10T / m.

[0081] The liquid phase sintering process specifically involves heating to 1500℃ at a heating rate of 6℃ / min, holding at that temperature for 0.8h, and simultaneously applying an axial gradient magnetic field of 1.0T with a gradient of 8T / m.

[0082] After cooling and demagnetization, a metal-ceramic material is obtained. The cooling and demagnetization process involves cooling the material to 750°C at a rate of 3.5°C / min, and then cooling it to room temperature in the furnace. Simultaneously, an alternating magnetic field is used for demagnetization to ensure that the residual magnetism of the finished product is no greater than 0.01T.

[0083] Comparative Example 1:

[0084] A metal-ceramic material comprises a hard phase of Ti(C,N), a binder phase of nickel powder (particle size 100-300 nm), and a wetting-regulating phase of a high-entropy solid solution. The mass percentages of the hard phase, binder phase, and wetting-regulating phase are 48%, 20%, and 32%, respectively. The hard phase of Ti(C,N) is Ti(C... 0.7 N 0.3 The matrix powder; the high-entropy solid solution is (W,Mo,Ta,Nb,Zr)C, and the atomic molar ratio of tungsten, molybdenum, tantalum, niobium, zirconium and carbon is 4.7:3.0:1.4:1.2:0.8:11.5.

[0085] The preparation method of the above-mentioned metal-ceramic material includes:

[0086] Step S1, Pretreatment of matrix powder: Same as step S1 in Example 2.

[0087] Step S2, preparation of high-entropy solid solution: consistent with step S3 in Example 2.

[0088] Step S3, High-entropy solid solution pretreatment: Same as step S4 in Example 2.

[0089] Step S4, Powder Mixing and Molding: The pretreated matrix powder, nickel powder, and pretreated high-entropy solid solution at mass percentages of 48%, 20%, and 32% are sequentially mixed and ball-milled, subjected to gradient magnetic field pretreatment, and bidirectional molding to obtain a compact; wherein, the mixing and ball milling, gradient magnetic field pretreatment, and bidirectional molding are all consistent with step S5 in Example 2.

[0090] Step S5, sintering: Same as step S6 in Example 2.

[0091] Comparative Example 2:

[0092] A metal-ceramic material comprises a Ti(C,N) hard phase, a nickel (Ni)-based binder phase, and a high-entropy solid solution wetting-regulating phase, wherein the mass percentages of the hard phase, binder phase, and wetting-regulating phase are 48%, 20%, and 32%, respectively; wherein the Ti(C,N) hard phase is Ti(C) 0.7 N 0.3 ) Matrix powder; nickel-based binder phase using Ni 75 Cr 10 B 10 Si5 is an amorphous alloy; the high-entropy solid solution is (W,Mo,Ta,Nb,Zr)C, and the atomic molar ratio of tungsten, molybdenum, tantalum, niobium, zirconium and carbon is 4.7:3.0:1.4:1.2:0.8:11.5.

[0093] The preparation method of the above-mentioned metal-ceramic material includes:

[0094] Step S1, Pretreatment of matrix powder: Same as step S1 in Example 2.

[0095] Step S2, Preparation of amorphous nickel-based alloy: Same as step S2 in Example 2.

[0096] Step S3, Preparation of High-Entropy Solid Solution: First, weigh tungsten powder, molybdenum powder, tantalum powder, niobium powder, zirconium powder, and graphite powder in the atomic molar ratio of tungsten, molybdenum, tantalum, niobium, zirconium, and carbon, respectively. Add oxides of rare earth elements, which are at least one of the cerium group rare earth elements (i.e., lanthanum (La), cerium (Ce), praseodymium (Pr), neodymium (Nd), promethium (Pm), samarium (Sm), europium (Eu), and gadolinium (Gd). The amount of rare earth element oxides used is determined according to the actual situation. Then, mix the raw materials with tungsten carbide spheres (diameter... The powder (5 mm) was loaded into a stainless steel vacuum ball mill jar and ball-to-powder ratio of 10:1 at a vacuum of no more than 0.1 Pa and a rotation speed of 250-350 rpm for 12-18 hours (during the ball milling process, the ball milling was stopped for 1 hour and then stopped for 10 minutes to dissipate heat). The ball-milled powder was placed in a high-temperature atmosphere furnace and subjected to a thermal chemical reaction at a temperature of 800-900℃ under a nitrogen-hydrogen mixed gas atmosphere (volume ratio of 3:1) to obtain a high-entropy solid solution powder.

[0097] Step S4, High-entropy solid solution pretreatment: Same as step S4 in Example 2.

[0098] Step S5, Powder Mixing and Molding: Same as step S5 in Example 2.

[0099] Step S6, sintering: Same as step S6 in Example 2.

[0100] Comparative Example 3:

[0101] A metal-ceramic material comprises a Ti(C,N) hard phase, a nickel (Ni)-based binder phase, and a high-entropy solid solution wetting-regulating phase, wherein the mass percentages of the hard phase, binder phase, and wetting-regulating phase are 48%, 20%, and 32%, respectively; wherein the Ti(C,N) hard phase is Ti(C) 0.7 N 0.3 ) Matrix powder; nickel-based binder phase using Ni 75 Cr 10 B 10 Si5 is an amorphous alloy; the high-entropy solid solution is (W,Mo,Ta,Nb,Zr)C, and the atomic molar ratio of tungsten, molybdenum, tantalum, niobium, zirconium and carbon is 4.7:3.0:1.4:1.2:0.8:11.5.

[0102] The preparation method of the above-mentioned metal-ceramic material includes:

[0103] Step S1, Pretreatment of matrix powder: Same as step S1 in Example 2.

[0104] Step S2, Preparation of amorphous nickel-based alloy: Same as step S2 in Example 2.

[0105] Step S3, preparation of high-entropy solid solution: consistent with step S3 in Example 2.

[0106] Step S4, Powder Mixing and Molding: The pretreated matrix powder, amorphous nickel-based alloy, and high-entropy solid solution are mixed and ball-milled, pretreated with a gradient magnetic field, and bidirectionally molded in mass percentages of 48%, 20%, and 32% respectively to obtain a compact; wherein, the mixing and ball milling, gradient magnetic field pretreatment, and bidirectional molding are all the same as step S5 in Example 2.

[0107] Step S5, sintering: Same as step S6 in Example 2.

[0108] Comparative Example 4:

[0109] A metal-ceramic material comprises a Ti(C,N) hard phase, a nickel (Ni)-based binder phase, and a high-entropy solid solution wetting-regulating phase, wherein the mass percentages of the hard phase, binder phase, and wetting-regulating phase are 48%, 20%, and 32%, respectively; wherein the Ti(C,N) hard phase is Ti(C) 0.7 N 0.3 ) Matrix powder; nickel-based binder phase using Ni 75 Cr 10 B 10 Si5 is an amorphous alloy; the high-entropy solid solution is (W,Mo,Ta,Nb,Zr)C, and the atomic molar ratio of tungsten, molybdenum, tantalum, niobium, zirconium and carbon is 4.7:3.0:1.4:1.2:0.8:11.5.

[0110] The preparation method of the above-mentioned metal-ceramic material includes:

[0111] Step S1, Pretreatment of matrix powder: Same as step S1 in Example 2.

[0112] Step S2, Preparation of amorphous nickel-based alloy: Same as step S2 in Example 2.

[0113] Step S3, preparation of high-entropy solid solution: consistent with step S3 in Example 2.

[0114] Step S4, High-entropy solid solution pretreatment: Same as step S4 in Example 2.

[0115] Step S5, Powder Mixing and Molding: The pretreated matrix powder, amorphous nickel-based alloy, and pretreated high-entropy solid solution are mixed and ball-milled and bidirectionally molded at mass percentages of 48%, 20%, and 32% respectively to obtain a compact; wherein, the mixing and ball milling specifically involves: loading each raw material into a stainless steel ball mill jar and evacuating it to 10... -3After Pa, argon gas is introduced to 0.1 MPa. Carbide (5 mm in diameter) is used as the ball milling medium, with a ball-to-material ratio of 9:1, a rotation speed of 300 rpm, and ball milling for 12 hours (during the ball milling process, after every 30 minutes of ball milling, the machine is stopped for 10 minutes for heat dissipation) to achieve the mixing and ball milling of the raw materials. The bidirectional molding process is as follows: the mixed and ball-milled powder is loaded into a graphite mold and molded using a bidirectional press. A pressure of 150 MPa is applied in both directions and held for 5 minutes. After molding, water is circulated to cool the mold to ensure that the mold temperature does not exceed 50°C.

[0116] Step S6, Sintering: Place the pressed billet into the sintering furnace (using a graphite mold, with the inner wall of the mold coated with boron nitride release agent to facilitate demolding after sintering), and evacuate the sintering furnace to ≤10. -4 Pa, and then successively perform low-temperature pre-sintering, three-stage solid-state sintering, and liquid-phase sintering, specifically as follows:

[0117] Low-temperature pre-sintering: Heat to 600℃ at a heating rate of 9℃ / min and hold for 1 hour;

[0118] The three-stage solid-state sintering process is as follows: heating to 1100℃ at a heating rate of 11℃ / min and holding for 1.5h; heating to 1200℃ at a heating rate of 15℃ / min and holding for 1.5h; and finally heating to 1300℃ at a heating rate of 11℃ / min and holding for 2h.

[0119] The liquid phase sintering process specifically involves heating to 1455℃ at a heating rate of 5℃ / min and holding at that temperature for 1 hour.

[0120] After cooling, a metal-ceramic material is obtained; the cooling process is as follows: the temperature is reduced to 800°C at a rate of 3°C / min, and then cooled to room temperature in the furnace.

[0121] The hardness, fracture toughness, flexural strength, and wear resistance of the cermet material specimens (all prepared as φ30mm x 10mm specimens) prepared in Examples 1 to 3 and Comparative Examples 1 to 4 were tested using the test methods of GB / T 230.1-2018, GB / T 23806-2025, GB / T 4740-2024, and ASTM B611-21, respectively. The test results are shown in the table below:

[0122]

[0123] As shown in the table above, this invention achieves interfacial bonding between the hard phase, the bonding phase, and the wetting-regulating phase through the preparation of amorphous nickel-based alloys, the preparation of high-entropy solid solutions, the formation of a core-shell structure by encapsulating high-entropy solid solutions with niobium, and the magnetic field gradient constructed by a multi-layer permanent magnet array during sintering. This not only improves the density of the metal ceramic material but also obtains a three-phase synergistic gradient structure, thereby significantly improving mechanical properties such as hardness, fracture toughness, bending strength, and wear resistance.

Claims

1. A method of producing a high entropy interfacially induced cermets material, characterized by: The cermet material comprises a hard phase of Ti(C,N), a binder phase of nickel base and a wetting regulation phase of high-entropy solid solution, and the mass percentage of the hard phase, the binder phase and the wetting regulation phase is 45-50%, 18-22% and 28-33% respectively; the hard phase of Ti(C,N) adopts Ti(C 0.7 ,N 0.3 ) base powder, the binder phase of nickel base adopts amorphous alloy of Ni-Cr-B-Si system, and the high-entropy solid solution adopts (W, Mo, Ta, Nb, Zr) C, and the atomic mole ratio of tungsten, molybdenum, tantalum, niobium, zirconium and carbon is 4.0-5.5:2.5-3.5:1.0-1.8:0.8-1.5:0.5-1.2:9.0-12.

0. The specific preparation method comprises the following steps: Step S1, base powder pretreatment: vacuum drying Ti(C 0.7 ,N 0.3 ) base powder, and storing for standby use; Step S2, preparation of amorphous nickel-based alloy: the amorphous nickel-based alloy is prepared by using a melt quenching method; Step S3, preparation of high-entropy solid solution: first, a high-entropy carbide precursor is prepared by using a sol-gel synthesis method, and then a high-entropy solid solution of (W, Mo, Ta, Nb, Zr) C is prepared by using a laser solid-phase synthesis method; Step S4, pretreatment of high-entropy solid solution: a core-shell structure powder of high-entropy solid solution wrapped by niobium is prepared by using a ball milling method; Step S5, powder mixing and forming: the pretreated base powder, the amorphous nickel-based alloy and the pretreated high-entropy solid solution are sequentially mixed, ball milled, gradient magnetic field pretreated and bidirectionally die pressed to obtain a compact; Step S6, sintering: the compact is placed in a sintering furnace, and is sequentially subjected to low-temperature pre-sintering, three-stage solid-phase sintering and liquid-phase sintering, wherein a magnetic field is introduced for regulation and control in the three-stage solid-phase sintering and the liquid-phase sintering, and after cooling and demagnetization, a cermet material is obtained.

2. The method for preparing a high-entropy interface-induced metal-ceramic material according to claim 1, characterized in that: The amorphous alloy employs Ni 75 Cr 10 B 10 Si5。 3. The method for preparing a high-entropy interface-induced metal-ceramic material according to claim 1, characterized in that: In the step S1, the vacuum drying is performed at a temperature of 90-110 ℃ and a vacuum degree of 2-6 Pa for 1.5-2.5 h, and then the dried product is transferred into an argon-protected sealed container for storage.

4. The method for preparing a high-entropy interface-induced metal-ceramic material according to claim 1, characterized in that: The preparation of the amorphous nickel-based alloy by the melt quenching method is specifically as follows: metal nickel and chromium are mixed with elemental boron and silicon according to the atomic proportion in the amorphous alloy system, and are added into a vacuum arc furnace, and are melted at a temperature of 1500-1560 ℃ under a vacuum degree of not more than 10 -3 Pa, and melting is performed at a temperature of 1500-1560 ℃; then, the amorphous thin strip with a thickness of 20-50 μm is prepared by using a single-roller quenching device, the rotating speed of the copper roller of the single-roller quenching device is 28-32 m / s; finally, the amorphous thin strip is crushed into small particles by using an agate mortar, and is screened by using a 200-mesh screen, and the screened particles are vacuum packaged in aluminum foil bags for standby use.

5. The method for preparing a high-entropy interface-induced metal-ceramic material according to claim 1, characterized in that: The sol-gel synthesis method for preparing the high-entropy carbide precursor comprises the following steps: First, WCl6, MoCl5, TaCl5, NbCl5, ZrCl4 and a carbon source are weighed according to the atomic molar ratio, the metal chlorides are dissolved in a mixed solvent of ethanol and deionized water, the volume ratio of ethanol to deionized water is 3-4:1, the mass ratio of the metal chlorides to the mixed solvent is 1:5-10, and the stirring is performed at a rotating speed of 300-400 rpm for 28-32 min; then the carbon source is added into the stirred mixed solution, and nitric acid is used to adjust the pH to 3.0; the wet gel is formed by stirring in a water bath at 55-65 ℃ and at a rotating speed of 250-350 rpm for 1.8-2.2 h; then the wet gel is transferred into an oven and dried at 115-125 ℃ for 11-13 h to obtain a dry gel; finally, the dry gel is placed in an argon atmosphere calcination furnace, heated to 1350-1450 ℃ at a rate of 4.5-5.5 ℃ / min, and kept at this temperature for 1.8-2.2 h to obtain the high-entropy carbide precursor.

6. The method for preparing a high-entropy interface-induced metal-ceramic material according to claim 5, characterized in that: The carbon source is any one of furfuryl alcohol, glucose or phenol formaldehyde resin.

7. The method for preparing a high-entropy interface-induced metal-ceramic material according to claim 5, characterized in that: The high-entropy solid solution synthesized by the laser solid synthesis is specifically as follows: a high-entropy carbide precursor is laid on a graphite substrate with a thickness of 5 mm, a pulsed Nd:YAG laser is used for scanning treatment, the laser wavelength is 1064 nm, the power is 2.5 kW, the pulse frequency is 50 Hz, the laser spot diameter is 2 mm, the scanning speed is 8 mm / s, and the cooling rate is 10 7 K / s; after the laser scanning is completed, the powder is collected to obtain a high-entropy solid solution.

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