Amplitude-splitting carbide powder precipitating nanometer wc in situ and its preparation method

Abstract

This invention belongs to the field of materials preparation technology, specifically relating to an in-situ precipitated nano-WC amplitude-modulated decomposition carbide powder and its preparation method. This invention uses commercial TiO2, ZrO2, WO3, and graphite powder as raw materials. The thoroughly mixed powder undergoes a carbonization-reduction reaction via pressureless sintering to obtain (Ti,Zr,W)C ceramic powder. Subsequently, the carbide ceramic powder is aged at 1200-1500℃ for 1-3 hours to obtain the final product. The sample after this specific aging treatment exhibits a phenomenon of coexistence of in-situ precipitated WC nanoparticles and amplitude-modulated decomposition. The process is simple and easy to control, the formation mechanism is clear and well-defined, and it has high potential for industrial application.

Description

Technical Field

[0001] This invention belongs to the field of materials preparation technology, and in particular relates to an amplitude-modulated decomposition carbide powder with in-situ precipitation of nano-WC and its preparation method. Background Technology

[0002] The information disclosed in this background section is intended only to enhance understanding of the overall background of the invention and is not necessarily to be construed as an admission or in any way implying that such information constitutes prior art known to those skilled in the art.

[0003] Transition metal carbides (such as TiC, TaC, NbC, Mo2C, ZrC, and HfC) possess high strength, high hardness, high thermal stability, and high chemical inertness, and are widely used in wear-resistant structural components of cutting tools and engines, typically in aerospace and military equipment. With increasingly stringent requirements for material performance, single-component carbides can no longer meet service requirements, while composite carbides can further enhance their overall performance through composition and structure control, leveraging their respective strengths and compensating for their weaknesses.

[0004] Recent studies have found that some composite carbides (such as TiC-ZrC and TiC-HfC) can form single-phase solid solutions at high temperatures, while at low temperatures, these single-phase solid solutions undergo amplitude modulation decomposition into dispersed nanostructures with the same structure but different compositions, which can further improve the performance of ceramic materials. For example, in existing technologies, Li et al. (Phase decomposition of TiC-ZrC solid solution prepared by spark plasma sintering, Ceram.Int., 2015, 41:14258-14262) found that (Ti,Zr)C composite carbides undergo amplitude modulation decomposition after heat treatment at 1573K to form Ti-rich and Zr-rich dispersed nanostructures, resulting in a synergistic improvement in the material's hardness and fracture toughness. Wang Xingang et al. disclosed a high-temperature resistant, high-strength (Ti,Zr,Hf)C medium-entropy ceramic material and its preparation method. The powder after amplitude modulation decomposition was obtained through a carbonization-reduction reaction, and a ceramic bulk with excellent high-temperature performance was obtained through hot pressing sintering. Ma et al. (Liquid Phase Sintering of (Ti,Zr)C with WC-Co, Materials, 2017, 10: 1-12) reported a series of methods for preparing (Ti,Zr)C amplitude-modulated decomposition composite powders, which can be added as hard phases to cemented carbides to improve the hardness and high-temperature stability of the alloys.

[0005] However, the inventors discovered that while the amplitude modulation decomposition of complex carbides in the aforementioned prior art can improve the mechanical properties of ceramic materials to some extent, the amplitude modulation decomposition structure is prone to coarsening at high temperatures, leading to performance degradation. Based on this, the inventors considered that the in-situ precipitation of nanoscale hard phases can generate new interfaces through the Hall-Page relationship to improve hardness, while the pinning of nanoparticles can also prevent crack propagation, thereby improving fracture toughness. However, currently, there is a lack of relevant preparation methods for amplitude modulation decomposition powders with in-situ precipitation of nano-hard particles in composite carbide ceramic materials, both domestically and internationally. Therefore, preparing a series of amplitude modulation decomposition carbide powders with nano-hard particle precipitation is a problem urgently needing to be solved by those skilled in the art. Summary of the Invention

[0006] To address the aforementioned technical problems, the present invention aims to provide an in-situ precipitated nano-WC amplitude-modulated decomposition carbide powder and its preparation method. The carbide powder has advantages such as fine WC precipitates and obvious amplitude-modulated decomposition structure, and can be used as a raw material for hard powders to improve the high-temperature comprehensive performance of wear-resistant materials such as cemented carbide and hard ceramics.

[0007] To achieve the above objectives, the present invention is implemented through the following technical solution:

[0008] In a first aspect, the present invention provides an amplitude-modulated decomposition carbide powder for in-situ precipitation of nano-WC, characterized in that the amplitude-modulated decomposition carbide powder is composed of a chemical formula of (Ti 0.5-x Zr 0.5-x W 2x The ceramic material is composed of WC, wherein 0.025≤x≤0.2, and the ceramic material contains nanoscale WC particles and amplitude modulation decomposition structure, wherein the microstructure of the amplitude modulation decomposition structure is striped.

[0009] Preferably, the (Ti) 0.5-x Zr 0.5-x W 2x In C, 0.05 ≤ x ≤ 0.075.

[0010] In a second aspect, the present invention provides a method for preparing amplitude-modulated decomposition carbide powder with in-situ precipitation of nano-WC, comprising the following preparation steps:

[0011] S1. Mix commercial TiO2, ZrO2, WO3 and graphite powder, and perform briquetting operation. After sintering, the green body is crushed to obtain (Ti,Zr,W)C ceramic powder.

[0012] S2. The ceramic powder obtained in step S1 is subjected to aging treatment to obtain the final product.

[0013] Preferably, in step S1, the molar ratio of TiO2, ZrO2, WO3 and graphite powder is 0.3–0.475:0.3–0.475:0.05–0.4:0.9; more preferably, the molar ratio of TiO2, ZrO2, WO3 and graphite powder is 0.425–0.45:0.425–0.45:0.1–0.15:0.9.

[0014] Preferably, in step S1, the average particle size of the TiO2, ZrO2, WO3 and graphite powder is 0.5-2 μm; more preferably, the average particle size is 0.8-1 μm.

[0015] Preferably, in step S1, the purity of the TiO2, ZrO2, WO3 and graphite powder raw materials is not less than 99%; more preferably, the purity of the raw materials is not less than 99.5%.

[0016] Preferably, the oxygen content of the (Ti,Zr,W)C ceramic powder is not greater than 1.0 wt%.

[0017] Preferably, in step S1, after mixing commercial TiO2, ZrO2, WO3 and graphite powder, the mixture is sequentially ground, dried and sieved.

[0018] The grinding mentioned refers to obtaining a mixed slurry by wet ball milling after adding grinding media;

[0019] The ball-to-material ratio (mass ratio of grinding balls to material) is 5:1-10:1; preferably, the ball-to-material ratio is 5:1.

[0020] The ball milling speed is 200-250 rpm, and the ball milling time is 12-48 h; preferably, the ball milling speed is 200 rpm, and the ball milling time is 36-48 h; more preferably, the ball milling time is 40 h.

[0021] The grinding medium is selected from one or more of anhydrous ethanol and acetone; preferably, the grinding medium is selected from anhydrous ethanol, and the amount added per gram of material is 2 mL.

[0022] The drying method is vacuum drying, followed by grinding and passing through a 200-mesh sieve.

[0023] The drying temperature is 80-100℃ and the time is 12-24h; preferably, the drying temperature is 80℃ and the time is 18h.

[0024] Preferably, in step S1, the pressing operation refers to loading the mixed powder into a mold for pressing; the pressing pressure is 280-320 MPa and the time is 8-15 min; more preferably, the pressing pressure is 300 MPa and the time is 10 min.

[0025] Preferably, in step S1, the sintering process is carried out under an inert atmosphere; the inert atmosphere is argon, helium, or a hydrogen-argon mixture.

[0026] Preferably, in step S1, the sintering process is pressureless sintering.

[0027] Preferably, in step S1, the sintering process involves first heating to 1200-1300°C at a heating rate of 15-20°C / min, then heating to 1800-2000°C at a heating rate of 8-10°C / min, and finally heating to 2200°C at a heating rate of 3-5°C / min, with a holding time of 1.5-2.5 hours.

[0028] More preferably, the sintering process involves first heating to 1200°C at a rate of 20°C / min, then heating to 2000°C at a rate of 10°C / min, and finally heating to 2200°C at a rate of 5°C / min, with a holding time of 2 hours.

[0029] Preferably, in step S1, the particle size of the powder obtained after crushing should be less than 200 mesh.

[0030] Preferably, in step S2, the aging treatment involves heating to 1200-1500℃ at a heating rate of 5-10℃ / min for 1-3 hours; more preferably, the aging treatment involves heating to 1500℃ at a heating rate of 5℃ / min for 2 hours.

[0031] In a third aspect, the present invention provides the application of the in-situ precipitated nano-WC amplitude-modulated decomposition carbide powder described in the first aspect in carbide wear-resistant ceramics.

[0032] The beneficial effects achieved by one or more technical solutions of the present invention are as follows:

[0033] (1) The present invention prepares (Ti,Zr,W)C ceramic powder with in-situ precipitated nano WC by aging treatment. The in-situ desolvation and precipitation of nanoscale WC can generate new interfaces through the Hall-Page relationship to improve hardness. The pinning of nanoparticles can also prevent crack propagation and thus improve fracture toughness.

[0034] (2) The process provided by the present invention is simple, easy to operate, and has great potential for industrial application. Attached Figure Description

[0035] Figure 1 The images shown are XRD patterns and enlarged views of samples synthesized in Comparative Example 1 and Examples 1-3 of this invention, without aging treatment.

[0036] Figure 2 These are scanning electron microscope (SEM) images of the carbide powders of Examples 1-12 and Comparative Examples 1-4 of the present invention.

[0037] Wherein, a: Comparative Example 1; b: Example 1; c: Example 2; d: Example 3; e: Comparative Example 2; f: Example 4; g: Example 5; h: Example 6; i: Comparative Example 3; j: Example 7; k: Example 8; l: Example 9. Detailed Implementation

[0038] It should be noted that the following detailed descriptions are exemplary and intended to provide further illustration of the invention. Unless otherwise specified, all technical and scientific terms used in this invention have the same meaning as commonly understood by one of ordinary skill in the art to which this invention pertains.

[0039] The present invention will be further described in detail below with reference to specific embodiments. It should be noted that the specific embodiments are explanations of the present invention and not limitations thereof.

[0040] Example 1 :

[0041] This embodiment provides an amplitude-modulated decomposition carbide powder with in-situ precipitation of nano-WC and its preparation method. The preparation method includes the following steps:

[0042] (1) Based on the carbonization reduction reaction to generate (Ti 0.475 Zr 0.475 W 0.05 The raw material powder was prepared according to formula C, with a carbon coefficient of 0.88. 17.388g TiO2, 26.827g ZrO2, 5.313g WO3 and 14.776g graphite powder were placed in a ball mill jar, 100mL anhydrous ethanol was added as the ball milling medium, zirconia balls were used, the ball-to-material ratio was 5:1, and the mixture was ball milled at 200rpm for 40h on a planetary ball mill.

[0043] (2) The mixed slurry obtained by ball milling was placed in a vacuum drying oven and dried at 80°C for 18 hours. It was then passed through a 200-mesh sieve to obtain a uniformly mixed powder.

[0044] (3) Place the mixed powder into a cold press mold and pre-press it with a pressure of 300MPa for 10min. Then transfer it to a graphite crucible for pressureless sintering. Then, the heating rate is 20℃ / min below 1200℃, then 10℃ / min to 2000℃, and finally 5℃ / min to 2200℃. After reaching 2200℃, hold it for 2h. After the holding is finished, cool it with the furnace.

[0045] (4) Grind and crush the sintered green body into uniform powder with smaller particle size;

[0046] (5) The obtained (Ti,Zr,W)C powder was aged in a tube furnace by passing flowing argon gas through it. The aging temperature was 1500℃ and the temperature was maintained for 1h.

[0047] Example 2 :

[0048] This embodiment provides an amplitude-modulated decomposition carbide powder with in-situ precipitation of nano-WC and its preparation method. The preparation method includes the following steps:

[0049] (1) Based on the carbonization reduction reaction to generate (Ti 0.425 Zr 0.425 W 0.15 The raw material powder was prepared according to formula C, with a carbon coefficient of 0.88. 13.756g TiO2, 21.224g ZrO2, 14.093g WO3 and 13.493g graphite powder were placed in a ball mill jar, 100mL anhydrous ethanol was added as the ball milling medium, zirconia balls were used, the ball-to-material ratio was 5:1, and the mixture was ball milled at 200rpm for 40h on a planetary ball mill.

[0050] (2) The mixed slurry obtained by ball milling is placed in a vacuum drying oven and dried at 80°C for 18 hours. It is then passed through a 200-mesh sieve to obtain a uniformly mixed powder.

[0051] (3) Place the mixed powder into a cold press mold and pre-press it with a pressure of 300MPa for 10min. Then transfer it to a graphite crucible for pressureless sintering. Then, the heating rate is 20℃ / min below 1200℃, then 10℃ / min to 2000℃, and finally 5℃ / min to 2200℃. After reaching 2200℃, hold it for 2h. After the holding is finished, cool it with the furnace.

[0052] (4) Grind and crush the sintered green body into uniform powder with smaller particle size;

[0053] (5) The obtained (Ti,Zr,W)C powder was aged in a tube furnace by passing flowing argon gas through it. The aging temperature was 1500℃ and the temperature was maintained for 1h.

[0054] Example 3 :

[0055] This embodiment provides an amplitude-modulated decomposition carbide powder with in-situ precipitation of nano-WC and its preparation method. The preparation method includes the following steps:

[0056] (1) Based on the carbonization reduction reaction to generate (Ti 0.35 Zr 0.35W 0.3 The raw material powder was prepared according to formula C, with a carbon coefficient of 0.88. 9.652g TiO2, 14.892g ZrO2, 24.015g WO3 and 12.044g graphite powder were placed in a ball mill jar, 100mL anhydrous ethanol was added as the ball milling medium, zirconia balls were used, the ball-to-material ratio was 5:1, and the mixture was ball-milled at 200rpm for 40h on a planetary ball mill.

[0057] (2) The mixed slurry obtained by ball milling was placed in a vacuum drying oven and dried at 80°C for 18 hours. It was then passed through a 200-mesh sieve to obtain a uniformly mixed powder.

[0058] (3) Place the mixed powder into a cold press mold and pre-press it with 300MPa pressure for 10min. Then transfer it to a graphite crucible for pressureless sintering. Then, the heating rate is 20℃ / min below 1200℃, then 10℃ / min to 2000℃, and finally 5℃ / min to 2200℃. After reaching 2200℃, hold it for 2h. After the holding is finished, cool it with the furnace.

[0059] (4) Grind and crush the sintered green body into uniform powder with smaller particle size;

[0060] (5) The obtained (Ti,Zr,W)C powder was aged in a tube furnace by passing flowing argon gas through it. The aging temperature was 1500℃ and the temperature was maintained for 1h.

[0061] Example 4 :

[0062] Compared with Example 1, the difference is that in this example, the obtained carbide powder is subjected to aging treatment by passing flowing argon gas through a tube furnace, the aging temperature is 1500℃, and the holding time is 2h.

[0063] Example 5 :

[0064] Compared with Example 2, the difference is that in this example, the obtained carbide powder is subjected to aging treatment by passing flowing argon gas through a tube furnace, the aging temperature is 1500℃, and the holding time is 2h.

[0065] Example 6 :

[0066] Compared with Example 3, the difference is that in this example, the obtained carbide powder is subjected to aging treatment by passing flowing argon gas through a tube furnace, the aging temperature is 1500℃, and the holding time is 2h.

[0067] Example 7 :

[0068] Compared with Example 1, the difference is that in this example, the obtained carbide powder is subjected to aging treatment by passing flowing argon gas through a tube furnace, the aging temperature is 1500℃, and the holding time is 3h.

[0069] Example 8 :

[0070] Compared with Example 2, the difference is that in this example, the obtained carbide powder is subjected to aging treatment by passing flowing argon gas through a tube furnace, the aging temperature is 1500℃, and the holding time is 3h.

[0071] Example 9 :

[0072] Compared with Example 3, the difference is that in this example, the obtained carbide powder is subjected to aging treatment by passing flowing argon gas through a tube furnace, the aging temperature is 1500℃, and the holding time is 3h.

[0073] Comparative Example 1 :

[0074] (1) Based on the carbonization reduction reaction to generate (Ti 0.5 Zr 0.5 The raw material powder was prepared according to formula C, with a carbon coefficient of 0.88. 19.585g TiO2, 30.218g ZrO2 and 15.905g graphite powder were placed in a ball mill jar, 100mL anhydrous ethanol was added as the ball milling medium, zirconia balls were used, the ball-to-material ratio was 5:1, and the mixture was ball milled at 200rpm for 40h on a planetary ball mill.

[0075] (2) The mixed slurry obtained by ball milling was placed in a vacuum drying oven and dried at 80°C for 18 hours. It was then passed through a 200-mesh sieve to obtain a uniformly mixed powder.

[0076] (3) Place the mixed powder into a cold press mold and pre-press it with a pressure of 300MPa for 10min. Then transfer it to a graphite crucible for pressureless sintering. The heating rate is 20℃ / min below 1200℃, then 10℃ / min to 2000℃, and finally 5℃ / min to 2200℃. After reaching 2200℃, hold it for 2h. After holding, cool it with the furnace.

[0077] (4) Grind and crush the sintered green body into uniform powder with smaller particle size;

[0078] (5) The obtained (Ti,Zr,W)C powder was aged in a tube furnace by passing flowing argon gas through it. The aging temperature was 1500℃ and the temperature was maintained for 1h.

[0079] Comparative Example 2 :

[0080] Compared with Comparative Example 1, the difference is that in this embodiment, the obtained carbide powder is subjected to aging treatment by passing flowing argon gas through a tube furnace, the aging temperature is 1500℃, and the holding time is 2h.

[0081] Comparative Example 3 :

[0082] Compared with Comparative Example 1, the difference is that in this embodiment, the obtained carbide powder is subjected to aging treatment by passing flowing argon gas through a tube furnace, the aging temperature is 1500℃, and the holding time is 3h.

[0083] Experimental Example 1 :

[0084] This experiment demonstrates X-ray diffraction (XRD) tests on the carbide ceramic powders obtained in Examples 1-3 and Comparative Example 1.

[0085] The results are as follows Figure 1 As shown, excluding W in Example 2 0.15 The sample underwent a small amount of amplitude-modulated decomposition, while the other carbide powders were all FCC single-phase solid solutions.

[0086] W in Example 1 0.05 The high carbon peak in the sample is due to the generation of CO2 during the carbothermic reduction process.

[0087] Furthermore, the magnified view clearly shows that as the W content increases, the characteristic peak shifts to a higher angle, indicating that the lattice constant of the solid solution decreases.

[0088] Experimental Example 2 :

[0089] This experiment describes the scanning electron microscopy measurements of the carbide powders from Examples 1-9 and Comparative Examples 1-3.

[0090] like Figure 2 As shown, the undoped comparative samples 1-3 did not exhibit significant amplitude decomposition or any product precipitation, and were characterized as single-phase solid solutions.

[0091] In Example 1, W 0.05 After aging at 1500℃ for 2 hours, the sample showed obvious amplitude-modulated decomposition structure, accompanied by the precipitation of a large number of WC nanoparticles. As the aging time increased, both the amplitude-modulated decomposition structure and WC grains entered the coarsening stage.

[0092] In Example 2, W 0.15 After aging at 1500℃ for 2 hours, WC desolvation and amplitude decomposition only occurred at some of the three-pointed grain boundaries. The precipitated WC particles were relatively large in diameter. As the aging time increased, the amplitude decomposition structure evolved completely, but it did not enter the coarsening stage. It was characterized by WC particles embedded in the striped amplitude decomposition structure.

[0093] In Example 3, W 0.3 After aging at 1500℃ for 2 hours, the sample showed significant WC desorption, both in quantity and grain size, compared to the sample with lower W content. Streak-like amplitude-modulated decomposition was also observed. As the aging time was extended to 3 hours, the W content increased further. 0.05 Samples with similar characteristics enter the coarsening stage.

[0094] Due to the significant difference in lattice constants between TiC and ZrC, a substantial solution hardening effect occurs after solid solution treatment. W further exacerbates lattice distortion. After appropriate heat treatment and amplitude modulation decomposition, the WC precipitated in situ disperses in the matrix at the nanoscale. This can generate new interfaces through the Hall-Page relation, thereby increasing hardness. Simultaneously, the pinning of nanoparticles can prevent crack propagation, thus improving fracture toughness. The combined effect of these factors gives this invention the potential to become a carbide wear-resistant ceramic.

[0095] The above description is merely a preferred embodiment of the present invention and is not intended to limit the invention. Various modifications and variations can be made to the present invention by those skilled in the art. Any modifications, equivalent substitutions, improvements, etc., made within the spirit and principles of the present invention should be included within the scope of protection of the present invention.

Claims

1. A type of amplitude-modulated decomposition carbide powder with in-situ precipitation of nano-WC, characterized in that, The amplitude-modulated decomposition carbide powder has the chemical formula (Ti) 0.5-x Zr 0.5-x W 2x The ceramic material is composed of C, wherein 0.05≤x≤0.075, and the ceramic material contains nanoscale WC particles and amplitude modulation decomposition structure, wherein the microstructure of the amplitude modulation decomposition structure is striped. The preparation steps of the amplitude-modulated decomposition carbide powder include: S1. Mix commercial TiO2, ZrO2, WO3 and graphite powder, and perform briquetting operation. After sintering, the green body is crushed to obtain (Ti, Zr, W)C ceramic powder. S2. The ceramic powder obtained in step S1 is subjected to aging treatment to obtain the final product.

2. The method for preparing in-situ precipitated nano-WC amplitude-modulated decomposition carbide powder according to claim 1, characterized in that, The preparation steps include the following: S1. Mix commercial TiO2, ZrO2, WO3 and graphite powder, and perform briquetting operation. After sintering, the green body is crushed to obtain (Ti, Zr, W)C ceramic powder. S2. The ceramic powder obtained in step S1 is subjected to aging treatment to obtain the final product.

3. The preparation method according to claim 2, characterized in that, The molar ratio of TiO2, ZrO2, WO3 and graphite powder is 0.425~0.45:0.425~0.45:0.1~0.15:0.

9.

4. The preparation method according to claim 2, characterized in that, In step S1, the average particle size of the TiO2, ZrO2, WO3 and graphite powder is 0.5-2 μm; the purity of the TiO2, ZrO2, WO3 and graphite powder raw materials is not less than 99%; and the oxygen content of the (Ti, Zr, W)C ceramic powder is not greater than 1.0 wt%.

5. The preparation method according to claim 4, characterized in that, The average particle size is 0.8-1 μm.

6. The preparation method according to claim 4, characterized in that, The purity of the raw materials is not less than 99.5%.

7. The preparation method according to claim 4, characterized in that, In step S1, after mixing commercial TiO2, ZrO2, WO3 and graphite powder, the mixture is sequentially ground, dried, sieved and briquetteed; the grinding refers to obtaining a mixed slurry by ball milling after adding grinding media. The ball-to-material ratio of the ball mill is 5:1-10:1; the rotation speed of the ball mill is 200-250 rpm; and the milling time is 12-48 hours. The grinding media are selected from one or more of anhydrous ethanol and acetone.

8. The preparation method according to claim 7, characterized in that, The drying method is vacuum drying; after drying, the material is ground and passed through a 200-mesh sieve.

9. The preparation method according to claim 7, characterized in that, The drying temperature is 80~100℃, and the drying time is 12~24 h.

10. The preparation method according to claim 7, characterized in that, The pressing operation refers to loading the mixed powder into a mold and pressing it into blocks; the pressing pressure is 280~320 MPa and the time is 8~15 min.

11. The preparation method according to claim 7, characterized in that, The ball-to-material ratio in the ball mill is 5:1; the rotation speed of the ball mill is 200 rpm; and the milling time is 40 h. The grinding medium is selected from anhydrous ethanol, and the amount added per gram of material is 2 mL; The drying temperature is 80℃, and the drying time is 18 hours. The pressure of the pressing block is 300 MPa, and the time is 10 min.

12. The preparation method according to claim 2, characterized in that, In step S1, the sintering process is pressureless sintering; The sintering process is carried out under an inert atmosphere. The sintering process involves first heating the temperature to 1200-1300℃ at a rate of 15-20℃ / min, then heating it to 1800-2000℃ at a rate of 8-10℃ / min, and finally heating it to 2200℃ at a rate of 3-5℃ / min, with a holding time of 1.5-2.5 h.

13. The preparation method according to claim 12, characterized in that, The inert atmosphere is argon, helium, or a mixture of hydrogen and argon.

14. The preparation method according to claim 12, characterized in that, The sintering process involves first heating to 1200℃ at a rate of 20℃ / min, then heating to 2000℃ at a rate of 10℃ / min, and finally heating to 2200℃ at a rate of 5℃ / min, with a holding time of 2 hours.

15. The preparation method according to claim 12, characterized in that, After the sintering process, the powder obtained by crushing should have a particle size of less than 200 mesh.

16. The preparation method according to claim 2, characterized in that, In step S2, the aging treatment involves heating the temperature to 1200-1500℃ at a rate of 5-10℃ / min for 1-3 hours.

17. The preparation method according to claim 16, characterized in that, The aging treatment involves heating to 1500℃ at a rate of 5℃ / min for 2 hours.

18. The application of the in-situ precipitated nano-WC amplitude-modulated decomposition carbide powder according to claim 1 in carbide wear-resistant ceramics.

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