Mo, w co-doped non-equiatomic high-entropy carbide ceramic material and preparation method thereof

Abstract

The application relates to a Mo-W co-doped non-equiatomic high-entropy carbide ceramic material and a preparation method thereof. 1 / 2 W 1 / 2 ) 1‑x (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) x C (0 x <=0.4), wherein Mo and W are key elements for component and performance adjustment; the preparation method is that Mo2C powder, TiC powder, V8C7 powder, NbC powder, WC powder and graphite are used as raw materials, stearic acid is added after mixing, and the mixed powder is obtained through grinding under the protection of an inert atmosphere; the mixed powder is pressed and formed, and then hot-press sintering is carried out, and the target product is obtained after natural cooling to room temperature. The non-equiatomic high-entropy carbide ceramic is successfully synthesized by adjusting the content of Mo and W and the preparation process. The non-equiatomic high-entropy carbide ceramic not only expands the high-entropy carbide system, but also has potential application prospects under extreme harsh working conditions such as high temperature and high load.

Description

Technical Field

[0001] This invention belongs to the field of high-entropy compound preparation technology, and relates to a method for preparing non-uniform high-entropy carbides and their bulk ceramics, particularly a high-entropy carbide (Mo) with different Mo and W contents. 1 / 2 W 1 / 2 ) 1-x (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) x C(0< x The preparation method of ≤0.4) improves the mechanical and tribological properties of high-entropy carbides by adjusting the composition, thereby expanding the application of high-entropy carbides. Background Technology

[0002] High-entropy ceramics are multi-principal-element solid solutions composed of five or more elements (atoms or ions) in equiatomic or near-equiatomic ratios, and have attracted much attention due to their excellent physicochemical properties. Currently, research on high-entropy ceramic materials mainly focuses on carbides, oxides, borides, silicides, and nitrides. Among them, high-entropy carbides exhibit excellent properties, including high melting point, high hardness, and good wear resistance, making them promising candidates for structural materials. However, current research mainly focuses on equimetallic molar ratios and non-carbon stoichiometric deviations, with few reports on non-equimetallic molar ratios. The literature "Effects of Mo content on the microstructure and mechanical properties of laser cladded FeCoCrNiMox (x = 0.2, 0.5) high-entropy alloy coatings Surface and Coatings Technology 482 (2024): 130697" uses laser cladding technology to prepare high-entropy alloy coatings with different Mo contents on the surface of EA4T axle steel. The results show that the performance improves to some extent with increasing Mo content. Therefore, it is of great significance to explore different transition metal contents to prepare non-equimolar ratio high-entropy carbide ceramics in order to improve their mechanical and tribological properties. Summary of the Invention

[0003] This invention discloses a non-uniform high-entropy ceramic material (Mo). 1 / 2 W 1 / 2 ) 1-x (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) x C(0< x≤0.4) and its preparation method, by adjusting the content of Mo and W and the preparation process, a bulk ceramic material with a face-centered cubic structure was obtained. The non-equiproportional high-entropy carbide ceramic is a single-component ceramic, and its molecular formula is expressed as (Mo ≤0.4). 1 / 2 W 1 / 2 ) 1-x (Ti 1 / 3 V 1 / 3Nb 1 / 3 ) x C(0< x The composition of high-entropy carbides (≤0.4%) features non-equimolar ratios of metallic elements and controllable Mo and W content, with a total metallic element content of 1. A 2+3 composition control method was adopted, with Mo and W in equal proportions, and Ti, V, and Nb in equal proportions, thus maintaining a high configurational entropy. The increase in Mo improves the lubrication performance of the high-entropy carbides, while the increase in W enhances the strength of the ceramic. Simultaneously, Ti, V, Nb, Mo, and W have similar crystal structures and chemical properties in their carbide forms. This similarity allows them to form a stable solid solution structure, making it difficult for them to separate into different phases. By combining Ti, V, Nb with Mo and W, and utilizing the characteristics of each element and the high-entropy effect of their combination, non-equimolar high-entropy carbide ceramics with excellent performance under high temperature, high pressure, and corrosive environments can be prepared. This material has broad application prospects in aerospace, nuclear industry, and cutting tools. The aforementioned series of high-entropy carbide ceramics exhibits the crystallization characteristics of a rock salt structure. A schematic diagram of its crystal structure is shown below. Figure 1 As shown.

[0004] I. To achieve the above-mentioned non-uniform high-entropy carbide ceramics, the present invention adopts the following preparation scheme:

[0005] 1) Weigh out Mo2C powder, TiC powder, V8C7 powder, NbC powder, WC powder and graphite according to the stoichiometric ratio of each element in the molecular formula, and add stearic acid accounting for 1%~6% of the total weight of the mixed powder as the ball milling medium. Grind under inert gas protection to obtain mixed powder; the purity of the raw materials Mo2C powder, TiC powder, V8C7 powder, NbC powder, WC powder and graphite are all ≥99%, and the particle size is 1~3μm.

[0006] Grinding involves placing the raw material in the ball mill jar of a ball mill and adding tungsten carbide grinding balls to grind it into a mixed powder. During grinding, the mass ratio of grinding balls to the mixture is 5:1 to 20:1; the rotation speed of the ball mill is 200 to 600 r / min; and the grinding time is 8 to 48 h.

[0007] The purpose of ball milling is to make the powder and the grinding balls in the jar collide and rub against each other at high speed, so as to achieve the functions of crushing, grinding, mixing and dispersing the sample.

[0008] 2) The target mixed powder obtained in step 1) is pressed into a green body using a hydraulic press at 30 MPa. The green body is then hot-pressed and sintered. After sintering, it is cooled to obtain the target product (Mo). 1 / 2 W 1 / 2 ) 1-x (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) x C(0< x ≤0.4) Bulk ceramics;

[0009] The sintering process significantly impacts the structure and properties of synthesized non-isotropic high-entropy carbide ceramics. Too low a sintering temperature results in insufficient densification and the inability to synthesize a single phase, while too high a temperature leads to melting and molten metal outflow. Excessive holding time and pressure result in excessive grain growth, leading to poor performance. Therefore, the hot-pressing sintering process in this invention is as follows: heating rate 5~10℃ / min, sintering temperature 1700~2000℃, holding time 0.1~2h, pressure 1.5~30MPa, and vacuum degree <10. -1 Pa. During hot pressing and sintering, a vacuum is applied at a pressure of 1.5~30 MPa, with a vacuum degree <10. -1 Pa, heating rate of 5~10 ℃ / min, sintering temperature of 1700~2000 ℃, sintering time of 1h~2h.

[0010] The synthesis mechanism of this invention: using transition metal carbide TM (Mo2C, TiC, V8C7, NbC, WC) powders with different crystal structures and carbon stoichiometry, and graphite as raw materials, based on TM(s) + C(s) → HEC-(MoW). x (s) The reaction strategy involves controlling the content of Mo and W and using mechanical grinding and hot pressing sintering techniques to induce the in-situ synthesis of a series of high-entropy carbide ceramic materials with uniform microstructure distribution.

[0011] II. Non-uniform high-entropy ceramic materials (Mo) 1 / 2 W 1 / 2 ) 1-x (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) x C(0< x Structure and properties of ≤0.4).

[0012] This invention ingeniously adjusts the content of Mo and W and successfully designs and prepares a novel non-uniform high-entropy ceramic material using the HPS method, with the molecular formula (Mo). 1 / 2 W 1 / 2 ) 1-x (Ti 1 / 3 V 1 / 3Nb 1 / 3 ) x C(0< x (≤0.4), the crystal structure belongs to face-centered cubic structure.

[0013] 1. Structural characterization

[0014] Figure 2 The XRD pattern of the non-uniform high-entropy carbide ceramic material synthesized in this invention is shown below. Figure 2 It can be seen that the prepared (Mo) 1 / 2 W 1 / 2 ) 1-x (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) x C(0< x ≤0.4) The ceramic is a pure cubic phase with space group Fm-3m, without any other impurity phases, and the diffraction peaks show a regular shift with the change of Mo and W content.

[0015] Figure 3 shows the energy spectrum of the non-uniform high-entropy carbide ceramic material synthesized in this invention. As can be seen from Figure 3, the (Mo) synthesized by the method of this invention... 1 / 2 W 1 / 2 ) 1-x (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) x C(0< x ≤0.4) The proportion of ceramic elements conforms to the proportion of raw materials.

[0016] Figure 4 This is a SEM image of the non-uniform high-entropy carbide ceramic material synthesized in this invention. Figure 5 This is the EDS energy distribution diagram of the non-uniform high-entropy carbide ceramic material synthesized in this invention; from Figure 4 The microstructure of the synthesized (Mo) material in this invention shows that... 1 / 2 W 1 / 2 ) 1-x (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) x C(0< x ≤0.4) The ceramic is relatively dense with fewer defects; Figure 5 It can be seen that the (Mo) synthesized in this invention 1 / 2 W 1 / 2 ) 1-x (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) x C(0< x ≤0.4) The six constituent elements of ceramics are evenly distributed.

[0017] 2. Performance Evaluation

[0018] 2.1 Mechanical Properties

[0019] The hardness of Mo was tested using a Vickers microhardness tester. 1 / 2 W 1 / 2 ) 1-x (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) x C ( x ≠0.6, 0< x The hardness was <1). Test conditions were: load 500 gf, loading duration 10 s; test results are as follows: Figure 6 As shown.

[0020] 2.2 High-Temperature Tribological Properties

[0021] The high-temperature tribological properties were tested using a high-temperature reciprocating friction and wear testing machine. The test temperature was 800℃, Al2O3 balls were used as the friction pair, the load was 10N, the reciprocating length was 5mm, and the test time was 30min. Figure 7 For the prepared (Mo) 1 / 2W 1 / 2 ) 1-x (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) x C(0< x The friction coefficient curve of the prepared (Mo ≤0.4) ceramic at 800℃. Experimental results show that the prepared (Mo 1 / 2 W 1 / 2 ) 1-x (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) x C(0< x Ceramics with a molecular weight of ≤0.4% exhibit excellent tribological properties at high temperatures, among which (Mo) 1 / 2 W 1 / 2 ) 0.2 (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) 0.8 C has the lowest coefficient of friction.

[0022] III. Applications of Non-Uniform High-Entropy Ceramic Materials

[0023] This invention synthesizes non-uniform (Mo) ratios by adjusting the Mo and W contents. 1 / 2 W 1 / 2 ) 1-x (Ti 1 / 3V 1 / 3 Nb 1 / 3 ) x C(0< x ≤0.4) ceramics are currently unreported. Due to the high hardness of WC, it is used as a second phase to inhibit grain growth and thus improve the material's hardness. Mo2C, added as a second phase, improves wettability and enhances the material's sintering ability. Its synthesis series (Mo... 1 / 2 W 1 / 2 ) 1-x (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) x C(0< x ≤0.4) The Vickers hardness of ceramics increases with increasing W and Mo content. (Mo) 1 / 2 W 1 / 2 ) 1-x (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) x C(0< x With a molecular weight of ≤0.4%, it has excellent tribological properties at high temperatures and is expected to be used as a high-temperature thermal protection material and high-temperature structural component. It has great application potential in structural components that serve under extreme conditions in aerospace and marine engines.

[0024] In summary, the initial materials used in the method of this invention are relatively economical and cost-effective. The raw materials used are simple, common, commercially available, easy to obtain, and inexpensive, facilitating process implementation. Compared with existing high-entropy equiatomic high-entropy carbides, the non-equiatomic (Mo) carbides prepared by this invention... 1 / 2 W 1 / 2 ) 1-x (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) x C(0< x (≤0.4) Ceramic bulk materials, due to the presence of varying amounts of Mo and W, exhibit superior mechanical and tribological properties. Furthermore, the method of this invention offers advantages such as simple preparation process, high controllability, and ease of large-scale scalability. Attached Figure Description

[0025] Figure 1 The (Mo) prepared in the embodiments of the present invention 1 / 2 W 1 / 2 ) 1-x (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) xCrystal structure diagram of C (x=0.2; x=0.4; x=0.6; x=0.8) ceramics.

[0026] Figure 2 The (Mo) prepared in the embodiments of the present invention 1 / 2 W 1 / 2 ) 1-x (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) x XRD patterns of C (x=0.2; x=0.4; x=0.6; x=0.8) ceramics.

[0027] Figure 3 shows the (Mo) prepared in the embodiment of the present invention. 1 / 2 W 1 / 2 ) 1-x (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) x C(0< x Energy spectrum of ceramics with a value of ≤0.4; where a: x=0.2; b: x=0.4; c: x=0.6; d: x=0.8.

[0028] Figure 4 The (Mo) prepared in the embodiments of the present invention 1 / 2 W 1 / 2 ) 1-x (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) x SEM images of C (x=0.2; x=0.4; x=0.6; x=0.8) ceramics.

[0029] Figure 5 The (Mo) prepared in the embodiments of the present invention 1 / 2 W 1 / 2 ) 1-x (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) x EDS elemental distribution diagram of C (x=0.2; x=0.4; x=0.6; x=0.8) ceramics.

[0030] Figure 6 The (Mo) prepared in the embodiments of the present invention 1 / 2 W 1 / 2 ) 1-x (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) x Vickers hardness of C (x=0.2; x=0.4; x=0.6; x=0.8) ceramics.

[0031] Figure 7 The (Mo) prepared in the embodiments of the present invention 1 / 2 W 1 / 2 ) 1-x (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) x Friction curves of C (x=0.2; x=0.4; x=0.6; x=0.8) ceramics. Detailed Implementation

[0032] The present invention (Mo) will be illustrated below through examples. 1 / 2 W 1 / 2 ) 1-x (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) x C(0< x The synthesis method of ceramic bulk materials (≤ 0.4) will be described in detail.

[0033] Example 1 High Entropy (Mo) 1 / 2 W 1 / 2 ) 0.8 (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) 0.2 Preparation of C ceramics

[0034] (1) Mo2C powder, TiC powder, V8C7 powder, NbC powder, WC powder and graphite were mixed in a molar ratio of Mo, W, Ti, V, Nb and C of 4.0:4.0:0.67:0.67:0.67:10. The total weight of the original materials was about 20g. The original materials were placed in a ball mill jar with a tungsten carbide grinding ball:mixture ratio of 5:1. Stearic acid of 1% of the total weight of the materials was added as the ball milling medium. The ball mill jar was placed in a planetary ball mill and ball milled at a speed of 300 r / min for 8 h under argon protection to obtain mixed powder.

[0035] (2) The dried mixed powder obtained in step (1) is pre-pressed into a green body using a hydraulic press at 30 MPa, and then hot-pressed and sintered. Hot-pressing and sintering process conditions: The atmosphere furnace is evacuated to ensure that the vacuum reading is <10. -1 Pa, then the furnace temperature was increased from room temperature to 1700℃ at a heating rate of 5℃ / min and held for 1 hour; then the power was turned off and the furnace was allowed to cool naturally to room temperature to obtain (Mo). 1 / 2 W 1 / 2 ) 0.8 (Ti 1 / 3 V 1 / 3 Nb 1 / 3 )0.2 C ceramics. XRD pattern ( Figure 2 This indicates that the prepared (Mo) 1 / 2W 1 / 2 ) 0.8 (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) 0.2 C ceramics are a pure phase, containing no other impurities; the energy dispersive spectroscopy (EDS) spectrum (Figure 3) shows that (Mo) 1 / 2 W 1 / 2 ) 0.8 (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) 0.2 The proportion of C ceramic elements conforms to the raw material ratio; SEM image and element distribution map ( Figure 4 and Figure 5 The results show that the synthesized high entropy (Mo) 1 / 2 W 1 / 2 ) 0.8 (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) 0.2 C ceramics are relatively dense and have all six constituent elements evenly distributed.

[0036] The prepared (Mo) 1 / 2 W 1 / 2 ) 0.8 (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) 0.2 The Vickers hardness of C ceramic is 16.215±1.01GPa, and the coefficient of friction at 800℃ is about 0.4~0.5.

[0037] Example 2 High Entropy (Mo) 1 / 2 W 1 / 2 ) 0.6 (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) 0.4 Preparation of C ceramics

[0038] (1) Mo2C powder, TiC powder, V8C7 powder, NbC powder, WC powder and graphite were mixed in a molar ratio of Mo, W, Ti, V, Nb and C of 3.0:3.0:1.0:1.0:1.0:10, with a total weight of about 20g. The raw materials were placed in a ball mill jar with a tungsten carbide grinding ball:mixture ratio of 5:1. Stearic acid of 1.5% of the total weight of the raw materials was added as the ball milling medium. The ball mill jar was placed in a planetary ball mill and ball milled at a speed of 400 r / min for 9 h under argon protection to obtain mixed powder.

[0039] (2) The dried mixed powder obtained in step (1) is pre-pressed into a green body using a hydraulic press at 30 MPa, and then hot-pressed and sintered. Hot-pressing and sintering process conditions: The atmosphere furnace is evacuated to ensure that the vacuum reading is <10. -1 Pa, then the furnace temperature was increased from room temperature to 1800℃ at a heating rate of 10 ℃ / min and held for 2 hours; then the power was turned off and the furnace was allowed to cool naturally to room temperature to obtain (Mo). 1 / 2 W 1 / 2 ) 0.6 (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) 0.4 C ceramics. XRD pattern ( Figure 2 This indicates that the prepared (Mo) 1 / 2W 1 / 2 ) 0.6 (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) 0.4 C ceramics are a pure phase, containing no other impurities; the energy dispersive spectroscopy (EDS) spectrum (Figure 3) shows that (Mo) 1 / 2 W 1 / 2 ) 0.6 (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) 0.4 The proportion of C ceramic elements conforms to the raw material ratio; SEM image and element distribution map ( Figure 4 and Figure 5 The results show that the synthesized high entropy (Mo) 1 / 2 W 1 / 2 ) 0.6 (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) 0.4 C ceramics are relatively dense and have all six constituent elements evenly distributed.

[0040] The prepared (Mo) 1 / 2 W 1 / 2 ) 0.6 (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) 0.4 The Vickers hardness of C ceramic is 15.789±0.69 GPa, and the coefficient of friction at 800℃ is about 0.4~0.5.

[0041] Example 3 High Entropy (Mo) 1 / 2 W 1 / 2 ) 0.2 (Ti 1 / 3 V 1 / 3 Nb1 / 3 ) 0.8 Preparation of C ceramics

[0042] (1) Mo2C powder, TiC powder, V8C7 powder, NbC powder, WC powder and graphite were mixed in a molar ratio of Mo, W, Ti, V, Nb and C of 1.0:1.0:2.67:2.67:2.67:10, and the total weight of the original materials was about 20g. The original materials were placed in a ball mill jar, and the ratio of tungsten carbide grinding balls to mixed materials was 5:1. Stearic acid of 2% of the total weight of the materials was added as the ball milling medium. The ball mill jar was placed in a planetary ball mill and ball milled at a speed of 500 r / min for 10 h under argon protection to obtain mixed powder.

[0043] (2) The dried mixed powder obtained in step (1) is pre-pressed into a green body using a hydraulic press at 30 MPa, and then hot-pressed and sintered. Hot-pressing and sintering process conditions: The atmosphere furnace is evacuated to ensure that the vacuum reading is <10. -1 Pa, then the furnace temperature was increased from room temperature to 1900℃ at a heating rate of 10 ℃ / min and held for 2 hours; subsequently, the power was turned off and the furnace was allowed to cool naturally to room temperature to obtain (Mo). 1 / 2 W 1 / 2 ) 0.2 (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) 0.8 C ceramics. XRD pattern ( Figure 2 This indicates that the prepared (Mo) 1 / 2W 1 / 2 ) 0.2 (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) 0.8 C ceramics are a pure phase, containing no other impurities; the energy dispersive spectroscopy (EDS) spectrum (Figure 3) shows that (Mo) 1 / 2 W 1 / 2 ) 0.2 (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) 0.8 The proportion of C ceramic elements conforms to the raw material ratio; SEM image and element distribution map ( Figure 4 and Figure 5 The results show that the synthesized high entropy (Mo) 1 / 2 W 1 / 2 ) 0.2 (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) 0.8 C ceramics are relatively dense and have all six constituent elements evenly distributed.

[0044] The prepared (Mo)1 / 2 W 1 / 2 ) 0.2 (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) 0.8 The Vickers hardness of C ceramic is 14.459±0.534 GPa, and the coefficient of friction at 800℃ is about 0.4~0.5.

Claims

1. A Mo / W co-doped non-uniform high-entropy carbide ceramic material, characterized in that, The molecular formula is (Mo 1 / 2 W 1 / 2 ) 1-x (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) x C(0 < x ≤0.4), of which the total amount of metal elements is 1.

2. A method for preparing a Mo and W co-doped non-uniform high-entropy carbide ceramic material as described in claim 1, comprising the following steps: 1) Weigh Mo2C powder, TiC powder, V8C7 powder, NbC powder, WC powder and graphite as raw materials according to the stoichiometric ratio of each element in the above molecular formula, and add stearic acid accounting for 1% to 6% of the total weight of the mixed powder as ball milling media, and grind under an inert atmosphere to obtain mixed powder. 2) Press the target mixed powder obtained in step 1) into a green body, then hot press and sinter the green body, and cool it after sintering to obtain the target product (Mo). 1 / 2 W 1 / 2 ) 1-x (Ti 1 / 3 V 1 / 3 Nb 1 / 3 ) x C(0 < x ≤0.4) Bulk ceramics.

3. The method for preparing a non-uniform high-entropy carbide ceramic material as described in claim 2, characterized in that, In step 1), the purity of the raw materials Mo2C powder, TiC powder, V8C7 powder, NbC powder, WC powder and graphite are all ≥99%, and the particle size is 1~3μm.

4. The method for preparing a Mo / W co-doped non-uniform high-entropy carbide ceramic material as described in claim 2, characterized in that, In step 1), grinding involves placing the raw material in the tungsten carbide ball mill jar of a ball mill and adding tungsten carbide grinding balls to grind it into a mixed powder. During grinding, the mass ratio of grinding balls to the mixture is 5:1 to 20:

1. The rotation speed of the ball mill is 200 to 800 r / min. The grinding time is 8 to 48 h.

5. The method for preparing a Mo / W co-doped non-uniform high-entropy carbide ceramic material as described in claim 2, characterized in that, In step 2), a vacuum is drawn during the hot pressing sintering process, with a pressure of 1.5~30 MPa and a vacuum degree <10. -1 Pa, heating rate of 5~10 ℃ / min, sintering temperature of 1700~2000 ℃, sintering time of 1~2h.

6. The application of the Mo and W co-doped non-uniform high-entropy carbide ceramic material as described in claim 1 in high-temperature friction structural components.

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