In-situ synthesis molybdenum carbide dispersion reinforced molybdenum alloy and preparation method thereof
By generating the Mo2C enhanced phase in situ in molybdenum alloy, the problem of insufficient mechanical properties of molybdenum alloy is solved, and its room temperature yield strength, elongation and hardness are significantly improved.
Patent Information
- Application Number
- CN202411722085.4
- Authority / Receiving Office
- CN · China
- Patent Type
- Applications(China)
- Current Assignee / Owner
- Filing Date
- 2024-11-28
- Publication Date
- 2025-03-04
AI Technical Summary
The lack of mechanical properties of molybdenum alloys, especially poor room temperature ductility, limits its industrial applications.
By mixing the MoO3 powder with carbon powder, a carbon coated MoO3 powder was generated and sintered in an inert gas atmosphere to obtain a Mo2C enhanced phase. Subsequently, the mixed powder was wet mixing, molding and hydrogen sintering to prepare an in-situ self-generating molybdenum carbide diffusion-enhanced molybdenum alloy with Mo2C reinforced phase.
The mechanical properties of molybdenum alloys have been improved, the room temperature yield strength has been increased by more than 300%, and the elongation and hardness have also been significantly improved, solving the problem that the strength and toughness of molybdenum alloys are difficult to simultaneously improve.
Smart Images
Figure CN119553160A_ABST
Abstract
Description
Technical Field
[0001] The present disclosure relates to the technical field of powder metallurgy, and in particular to a preparation method of an in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy and an in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy. Background Art
[0002] Molybdenum (Mo) is one of the most widely used refractory metal materials in industry. Molybdenum has high melting point, high density, high elastic modulus, low linear thermal expansion coefficient, high wear resistance, good electrical and thermal conductivity, good acid and alkali resistance and liquid metal corrosion resistance. Therefore, molybdenum and its alloys have broad application prospects as high-temperature resistant structural materials and functional materials in various industrial fields such as steel, metallurgy, machinery, chemical industry, nuclear energy, electronics, aerospace, etc.
[0003] Although molybdenum alloys have many performance advantages, their mechanical properties are not sufficient to meet the demand for structural materials in the rapid development of science and technology. In particular, their low room temperature ductility leads to poor machinability, which seriously limits their industrial applications.
[0004] It should be noted that the information disclosed in the above background technology section is only used to enhance the understanding of the background of the present disclosure, and therefore may include information that does not constitute the prior art known to ordinary technicians in the field. Summary of the invention
[0005] The purpose of the present disclosure is to provide a method for preparing an in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy and an in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy, thereby overcoming the problem of insufficient mechanical properties of molybdenum alloys at least to a certain extent.
[0006] According to a first aspect of the present disclosure, a method for preparing an in-situ self-generated molybdenum carbide dispersion reinforced molybdenum alloy is provided, comprising: mixing MoO3 powder with carbon powder to obtain carbon-coated MoO3 powder; sintering the carbon-coated MoO3 powder in an inert gas atmosphere to obtain a first mixed powder, the first mixed powder comprising Mo2C powder and molybdenum powder; adding the first mixed powder and a solvent into a ball mill for wet mixing, and drying the mixture under vacuum to obtain a second mixed powder; molding the second mixed powder to obtain a blank, and sintering the blank in a hydrogen atmosphere to obtain an in-situ self-generated molybdenum carbide dispersion reinforced molybdenum alloy with a Mo2C reinforcement phase.
[0007] Optionally, mixing MoO3 powder with carbon powder to obtain carbon-coated MoO3 powder includes: mixing MoO3 powder with carbon powder by ball milling to obtain carbon-coated MoO3 powder.
[0008] Optionally, for the process of preparing carbon-coated MoO3 powder, the ball-to-material ratio is 1:1 to 5:1, the rotation speed is 300r / min to 500r / min, and the ball milling mixing time is 6h to 12h.
[0009] Optionally, the mass ratio of MoO3 powder to carbon powder is 5:1 to 6:1, the particle size of MoO3 powder is 1 μm to 3 μm, and the particle size of carbon powder is 5 nm to 40 nm.
[0010] Optionally, sintering the carbon-coated MoO3 powder in an inert gas atmosphere to obtain a first mixed powder includes: sintering the carbon-coated MoO3 powder at a temperature of 800°C to 1500°C in an inert gas atmosphere for 1h to 4h to obtain the first mixed powder.
[0011] Optionally, in the process of preparing the second mixed powder from the first mixed powder, the ball-to-material ratio is 1:1 to 5:1, and the rotation speed is 300 r / min to 500 r / min.
[0012] Optionally, the second mixed powder is molded to obtain a blank, including: using a tablet press and a cold isostatic press to mold the second mixed powder to obtain the blank.
[0013] Optionally, the pressure for preparing the blank is 100 MPa to 300 MPa, and the holding time is 5 min to 10 min.
[0014] Optionally, the blank is sintered in a hydrogen atmosphere to obtain an in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy with a Mo2C reinforcement phase, comprising: sintering the blank at a temperature of 1000°C to 1500°C in a hydrogen atmosphere for 1h to 2h to obtain an in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy with a Mo2C reinforcement phase.
[0015] According to a second aspect of the present disclosure, an in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy is provided. The in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy is prepared by any of the above-mentioned methods for preparing the in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy.
[0016] In the scheme of the exemplary embodiment of the present disclosure, carbon powder is used as a reducing agent to react with MoO3 powder to obtain a molybdenum matrix, and a Mo2C reinforcing phase is generated at the same time. The Mo2C reinforcing phase not only has few impurities at the interface between the Mo2C and the Mo2C matrix and is well bonded, so that the interface can be prevented from cracking under a large stress, but also the in-situ generated Mo2C reinforcing phase is evenly dispersed and not easy to agglomerate in the Mo2C matrix, so that the mechanical properties of the Mo2C alloy are better improved.
[0017] It is to be understood that the foregoing general description and the following detailed description are exemplary and explanatory only and are not restrictive of the present disclosure. BRIEF DESCRIPTION OF THE DRAWINGS
[0018] The accompanying drawings herein are incorporated into the specification and constitute a part of the specification, illustrate embodiments consistent with the present disclosure, and together with the specification are used to explain the principles of the present disclosure. Obviously, the accompanying drawings described below are only some embodiments of the present disclosure, and for ordinary technicians in this field, other accompanying drawings can be obtained based on these accompanying drawings without creative work.
[0019] Figure 1 The flowchart of the method for preparing the in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy according to an exemplary embodiment of the present disclosure is schematically shown.
[0020] Figure 2 The scanning electron microscope (SEM) image of the carbon powder used in the embodiment of the present disclosure is shown.
[0021] Figure 3 The SEM image of MoO3 powder used in the examples of the present disclosure is shown.
[0022] Figure 4 The SEM image of the fracture of the in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy prepared in Example 1 of the present disclosure is shown.
[0023] Figure 5 The SEM image of the fracture of the in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy prepared in Example 2 of the present disclosure is shown.
[0024] Figure 6 The SEM image of the fracture surface of the in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy prepared in Example 3 of the present disclosure is shown.
[0025] Figure 7 The yield strength curves of the in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloys prepared in Examples 1, 2 and 3 of the present disclosure are shown. DETAILED DESCRIPTION
[0026] Example embodiments will now be described more fully with reference to the accompanying drawings. However, example embodiments can be implemented in a variety of forms and should not be construed as being limited to the examples set forth herein; on the contrary, these embodiments are provided so that the present disclosure will be more comprehensive and complete, and the concepts of the example embodiments are fully conveyed to those skilled in the art. The described features, structures, or characteristics may be combined in any suitable manner in one or more embodiments. In the following description, many specific details are provided to provide a full understanding of the embodiments of the present disclosure. However, those skilled in the art will appreciate that the technical solutions of the present disclosure may be practiced while omitting one or more of the specific details, or other methods, processes, steps, etc. may be adopted. In other cases, known technical solutions are not shown or described in detail to avoid obscuring various aspects of the present disclosure.
[0027] In addition, the accompanying drawings are only schematic illustrations of the present disclosure and are not necessarily drawn to scale. The same reference numerals in the figures represent the same or similar parts, and thus their repeated descriptions will be omitted. The flowcharts shown in the accompanying drawings are only exemplary illustrations and do not necessarily include all the steps. For example, some steps can also be decomposed, while some steps can be combined or partially combined, so the actual execution order may change according to actual conditions. In addition, all the terms "first", "second", etc. below are only for the purpose of distinction and should not be used as limitations of the present disclosure.
[0028] At present, in order to give full play to the potential of molybdenum as a high-temperature structural material and further realize and expand its application, it is necessary to solve the bottleneck problem of room temperature brittleness and simultaneously achieve the strengthening of molybdenum alloys at room temperature and high temperature. However, the contradictory relationship between ductility and strength has always been an important scientific problem in the field of materials, and is also a key issue currently faced by the research of molybdenum-based materials.
[0029] The strengthening and toughening of molybdenum alloys usually involves dispersing second-phase particles such as oxides or carbides as hard points in the molybdenum matrix. Whether distributed at the grain boundary or within the grain, they will hinder the dislocation slip in the molybdenum matrix, thereby strengthening the alloy. However, in some schemes, when the amount of second-phase reinforcing particles added is large, nano- or sub-micron-sized particles tend to agglomerate in the molybdenum matrix and even form a continuous reinforcing phase, which deteriorates the strengthening effect and even reduces the mechanical properties of the alloy. In addition, when the amount of second-phase reinforcing particles added is small, the strengthening effect of the molybdenum alloy is not obvious.
[0030] In order to solve the above problems to a certain extent, the embodiments of the present disclosure provide a new in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy and a preparation method thereof.
[0031] Figure 1The flowchart of the method for preparing the in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy according to an exemplary embodiment of the present disclosure is schematically shown. Figure 1 The method for preparing the in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy according to the embodiment of the present disclosure may include the following steps:
[0032] S12. Mixing MoO3 powder and carbon powder to obtain carbon-coated MoO3 powder.
[0033] In an exemplary embodiment of the present disclosure, the mass ratio of MoO3 powder to carbon powder is 5:1 to 6:1. The particle size of MoO3 powder is 1 μm to 3 μm. The particle size of carbon powder is 5 nm to 40 nm, and the BET specific surface area of carbon powder can be greater than 80 m 2 , specifically, it can be 90m 2 Up to 110m 2 .
[0034] Figure 2 The SEM image of the carbon powder used in the embodiments of the present disclosure is shown. Figure 3 The SEM image of MoO3 powder used in the examples of the present disclosure is shown.
[0035] MoO3 powder and carbon powder can be mixed by ball milling to obtain carbon-coated MoO3 powder. Specifically, in this process, the ball-to-material ratio is 1:1 to 5:1, the rotation speed is 300 r / min to 500 r / min, and the ball milling mixing time is 6 h to 12 h.
[0036] S14. Sintering the carbon-coated MoO3 powder in an inert gas atmosphere to obtain a first mixed powder, wherein the first mixed powder includes Mo2C powder and molybdenum powder.
[0037] Specifically, the carbon-coated MoO3 powder obtained in step S12 can be sintered at 800° C. to 1500° C. in an inert gas atmosphere for 1 h to 4 h to obtain a first mixed powder, that is, a molybdenum powder with an in-situ reaction enhanced phase Mo2C.
[0038] S16. Add the first mixed powder and the solvent into a ball mill for wet mixing, and dry the mixture under vacuum to obtain a second mixed powder.
[0039] In this process, the ball-to-material ratio is 1:1 to 5:1, and the rotation speed is 300 r / min to 500 r / min. The balls in the ball milling jar in the ball milling process adopted in the present disclosure may be zirconia balls, which is not limited in the present disclosure.
[0040] The solvent used for wet mixing may be, for example, ethanol or deionized water, which is not limited in the present disclosure.
[0041] It should be understood that, through the wet mixing ball milling process in step S16, the in-situ reaction enhancement phase Mo2C can be uniformly dispersed in the molybdenum powder.
[0042] S18. The second mixed powder is molded to obtain a blank, and the blank is sintered in a hydrogen atmosphere to obtain an in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy with a Mo2C reinforcement phase.
[0043] According to some embodiments of the present disclosure, the second mixed powder may be molded using a tablet press and a cold isostatic press to obtain a blank, wherein the pressure for preparing the blank is 100 MPa to 300 MPa, and the holding time is 5 min to 10 min.
[0044] After the blank is obtained, the blank can be sintered at a temperature of 1000° C. to 1500° C. in a hydrogen atmosphere for 1 h to 2 h to obtain an in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy with a Mo2C reinforcement phase.
[0045] The room temperature yield strength of the obtained in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy by the preparation method of step S12 to step S18 can be 480 to 1289 MPa, and the elongation can be 10 to 40%. In some embodiments, the molybdenum alloy composite material can have a yield strength of more than 1300 MPa and an elongation of more than 30% due to the uniform distribution of the grain refinement of the reinforcement phase and the pinning of the grain boundaries.
[0046] The disclosed embodiment uses Mo2C as a reinforcing phase of the Mo matrix, and combines the in-situ reaction of Mo and C to make Mo2C uniformly distributed in the Mo matrix, causing deflection during crack propagation, effectively reducing the crack propagation ability, so that it has better strength and toughness than pure Mo, thereby solving the problem that the strength and toughness of molybdenum alloys are difficult to improve simultaneously.
[0047] In the preparation method of an in-situ self-generated molybdenum carbide dispersion reinforced molybdenum alloy provided by the present disclosure, C is added to MoO3, and after powder mixing, powder reduction, reinforcement phase dispersion, and press sintering, a uniformly distributed Mo2C reinforcement phase is generated in the molybdenum matrix, which not only makes the grains of the molybdenum alloy sintering process significantly refined, but also improves the strength and toughness of the molybdenum alloy. Compared with pure molybdenum, the yield strength of the present disclosure at room temperature is increased by more than 300%, the elongation is increased by more than 300%, and the hardness is increased by more than 200%.
[0048] In addition, ball milling can not only effectively mix MoO3 and C evenly, but also evenly mix the reinforcing phase Mo2C generated in situ after reduction with Mo powder. This is not only beneficial to reducing the grain size of the molybdenum alloy after sintering, improving the surface energy of the mixed powder, and promoting the subsequent in-situ reaction, but also beneficial to the uniform distribution of the in-situ generated reinforcing phase Mo2C in the Mo matrix, thereby improving the strength and toughness of the molybdenum alloy.
[0049] In the above-mentioned preparation scheme, on the one hand, the uniform mixing of MoO3 powder and carbon powder is achieved by ball milling. On the other hand, the mixed powder of MoO3 powder and carbon powder is sintered to achieve the in-situ generation of Mo2C and the reduction of MoO3. On the other hand, the reduced Mo and the in-situ generated phase Mo2C are subjected to high-energy ball milling again to achieve the uniform dispersion of the reinforcing phase Mo2C in the Mo matrix. On the other hand, the present disclosure can achieve the in-situ enhancement of molybdenum alloy by regulating the ratio of MoO3 powder to carbon powder, and then regulating the content of Mo2C in the Mo matrix. In addition, the strengthening and toughening scheme of molybdenum alloy disclosed in the present disclosure can also be applied to other metals, such as W, Ta, Nb, Ti, Zr, Hf, etc., and the present disclosure does not limit this.
[0050] The above-mentioned preparation process of the present disclosure is described below through examples.
[0051] Example 1
[0052] Firstly, MoO3 powder and carbon powder were mixed by ball milling at a mass ratio of 5.4:1, a ball-to-material ratio of 5:1, a ball milling speed of 400 r / min, ball milling for 10 h, and then dried to obtain carbon-coated MoO3 powder.
[0053] Next, the carbon-coated MoO3 powder was sintered in an argon atmosphere at 1000°C for 1 hour to obtain a first mixed powder. The first mixed powder was wet-milled in an argon atmosphere at a speed of 300 r / min, a ball-to-material ratio of 5:1, and ball milled for 3 hours. After drying under vacuum, the in-situ generated Mo2C was evenly dispersed in the molybdenum powder to obtain a second mixed powder.
[0054] Subsequently, the second mixed powder was molded at a pressure of 180 MPa with a holding time of 5 min. After molding, the green body was placed in a cold isostatic press for pressing at a pressure of 300 MPa with a holding time of 5 min to obtain a green body.
[0055] Then, the blank is sintered in a hydrogen atmosphere at a sintering temperature of 1500° C. for 2 hours to obtain an in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy with a Mo2C reinforcement phase.
[0056] Figure 4The SEM image of the fracture of the in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy prepared in Example 1 of the present disclosure is shown.
[0057] Example 2
[0058] Firstly, MoO3 powder and carbon powder were mixed by ball milling at a mass ratio of 5.2:1, a ball-to-material ratio of 5:1, a ball milling speed of 500 r / min, ball milling for 12 h, and then dried to obtain carbon-coated MoO3 powder.
[0059] Next, the carbon-coated MoO3 powder was sintered in an argon atmosphere at 1000°C for 1 hour to obtain a first mixed powder. The first mixed powder was wet-milled in an argon atmosphere at a rotation speed of 350 r / min, a ball-to-powder ratio of 5:1, and ball milled for 4 hours. After drying under vacuum, the in-situ generated Mo2C was evenly dispersed in the molybdenum powder to obtain a second mixed powder.
[0060] Subsequently, the second mixed powder was molded at a pressure of 180 MPa with a holding time of 5 min. After molding, the green body was placed in a cold isostatic press for pressing at a pressure of 300 MPa with a holding time of 5 min to obtain a green body.
[0061] Then, the blank is sintered in a hydrogen atmosphere at a sintering temperature of 1500° C. for 2 hours to obtain an in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy with a Mo2C reinforcement phase.
[0062] Figure 5 The SEM image of the fracture of the in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy prepared in Example 2 of the present disclosure is shown.
[0063] Example 3
[0064] Firstly, MoO3 powder and carbon powder were mixed by ball milling at a mass ratio of 5:1, a ball-to-material ratio of 5:1, a ball milling speed of 500 r / min, ball milling for 12 h, and then dried to obtain carbon-coated MoO3 powder.
[0065] Next, the carbon-coated MoO3 powder was sintered in an argon atmosphere at 1000°C for 1.5 hours to obtain a first mixed powder. The first mixed powder was wet-milled in an argon atmosphere at a rotation speed of 400 r / min, a ball-to-powder ratio of 5:1, and ball milled for 4 hours. After drying under vacuum, the in-situ generated Mo2C was evenly dispersed in the molybdenum powder to obtain a second mixed powder.
[0066] Subsequently, the second mixed powder was molded at a pressure of 180 MPa with a holding time of 5 min. After molding, the green body was placed in a cold isostatic press for pressing at a pressure of 300 MPa with a holding time of 5 min to obtain a green body.
[0067] Then, the blank is sintered in a hydrogen atmosphere at a sintering temperature of 1500° C. for 2 hours to obtain an in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy with a Mo2C reinforcement phase.
[0068] Figure 6 The SEM image of the fracture surface of the in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy prepared in Example 3 of the present disclosure is shown.
[0069] In addition, for the in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloys prepared in Example 1, Example 2 and Example 3, the molybdenum alloy hardness was tested using a Vickers hardness tester, and a room temperature compression test was performed to obtain the micro-Vickers hardness and room temperature compressive yield strength of the in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloys prepared in Example 1, Example 2 and Example 3, respectively. Figure 7 The yield strength curves of the in-situ self-generated molybdenum carbide dispersion-enhanced molybdenum alloys prepared in Examples 1, 2 and 3 of the present disclosure are shown. The specific results are shown in Table 1:
[0070] Table 1
[0071]
[0072] As can be seen from Table 1, the present disclosure uses in-situ generated Mo2C as a reinforcing phase of Mo alloy, which can effectively solve the problem that the strength and toughness of molybdenum alloys are difficult to improve simultaneously. When different proportions of MoO3 and C are used, after the above preparation process, a Mo-based alloy with an in-situ generated Mo2C reinforcing phase is obtained, and its yield strength can reach 515-1328MPa, the elongation can reach 12%-36%, and the hardness can reach 244HV-579HV.
[0073] Furthermore, the embodiments of the present disclosure also provide an in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy, which is prepared by the above-mentioned method for preparing the in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy.
[0074] It should be noted that although the steps of the method in the present disclosure are described in a specific order in the drawings, this does not require or imply that the steps must be performed in this specific order, or that all the steps shown must be performed to achieve the desired results. Additionally or alternatively, some steps may be omitted, multiple steps may be combined into one step, and / or one step may be decomposed into multiple steps, etc.
[0075] In addition, the above-mentioned figures are only schematic illustrations of the processes included in the method according to the exemplary embodiments of the present disclosure, and are not intended to be limiting. It is easy to understand that the processes shown in the above-mentioned figures do not indicate or limit the time sequence of these processes. In addition, it is also easy to understand that these processes can be performed synchronously or asynchronously, for example, in multiple modules.
[0076] Those skilled in the art will readily appreciate other embodiments of the present disclosure after considering the specification and practicing what is disclosed herein. This application is intended to cover any variations, uses, or adaptations of the present disclosure that follow the general principles of the present disclosure and include common knowledge or customary technical means in the art that are not disclosed in the present disclosure. The specification and embodiments are to be considered merely as exemplary, and the true scope and spirit of the present disclosure are indicated by the claims.
[0077] It should be understood that the present disclosure is not limited to the exact structures that have been described above and shown in the drawings, and that various modifications and changes may be made without departing from the scope thereof. The scope of the present disclosure is limited only by the appended claims.
Claims
1. A method for preparing an in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy, characterized in that: include: Mixing MoO3 powder with carbon powder to obtain carbon-coated MoO3 powder; Sintering the carbon-coated MoO3 powder in an inert gas atmosphere to obtain a first mixed powder, wherein the first mixed powder includes Mo2C powder and molybdenum powder; Adding the first mixed powder and the solvent into a ball mill for wet mixing, and drying the mixture under vacuum to obtain a second mixed powder; The second mixed powder is molded to obtain a blank, and the blank is sintered in a hydrogen atmosphere to obtain an in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy with a Mo2C reinforcement phase.
2. The preparation method according to claim 1, characterized in that: MoO3 powder is mixed with carbon powder to obtain carbon-coated MoO3 powder, comprising: MoO3 powder and carbon powder are mixed by ball milling to obtain carbon-coated MoO3 powder.
3. The preparation method according to claim 2, characterized in that: For the process of preparing the carbon-coated MoO3 powder, the ball-to-material ratio is 1:1 to 5:1, the rotation speed is 300r / min to 500r / min, and the ball milling mixing time is 6h to 12h.
4. The preparation method according to any one of claims 1 to 3, characterized in that The mass ratio of the MoO3 powder to the carbon powder is 5:1 to 6:1, the particle size of the MoO3 powder is 1 μm to 3 μm, and the particle size of the carbon powder is 5 nm to 40 nm.
5. The preparation method according to claim 1, characterized in that: The carbon-coated MoO3 powder is sintered in an inert gas atmosphere to obtain a first mixed powder, comprising: The carbon-coated MoO3 powder is sintered at 800°C to 1500°C in an inert gas atmosphere for 1 hour to 4 hours to obtain a first mixed powder.
6. The preparation method according to claim 1, characterized in that: In the process of preparing the second mixed powder from the first mixed powder, the ball-to-material ratio is 1:1 to 5:1, and the rotation speed is 300 r / min to 500 r / min.
7. The preparation method according to claim 1, characterized in that: The second mixed powder is molded to obtain a blank, comprising: The second mixed powder is molded by using a tablet press and a cold isostatic press to obtain a blank.
8. The preparation method according to claim 1 or 7, characterized in that: The pressure for preparing the blank is 100 MPa to 300 MPa, and the holding time is 5 min to 10 min.
9. The preparation method according to claim 1, characterized in that: The blank is sintered in a hydrogen atmosphere to obtain an in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy with a Mo2C reinforcement phase, comprising: The blank is sintered at 1000° C. to 1500° C. in a hydrogen atmosphere for 1 to 2 hours to obtain an in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy with a Mo2C reinforcement phase.
10. An in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy, characterized in that: The in-situ self-generated molybdenum carbide dispersion-reinforced molybdenum alloy is prepared by the preparation method of any one of claims 1 to 9.