Aluminum alloy powder containing in-situ self-generated submicron TiC(N) particles and its application

Abstract

The present invention discloses an aluminum alloy powder containing in-situ self-generated submicron TiC(N) particles and its application. The TiC(N) particles can exist in two forms: nitrogen-doped TiC particles and titanium carbonitride particles. The present invention mainly includes the following steps: nitriding of titanium powder, preparation of mixed powder preforms, preparation of master alloys, preparation of multifunctional aluminum alloy powders, and application of the powders in 3D printing and hot pressing. The powder prepared by the present invention can obtain a high content of submicron TiC(N) particles dispersed on an aluminum matrix. During the rapid solidification process of 3D printing, they can serve as heterogeneous nucleation sites to significantly reduce their thermal cracking tendency and expand the processing window. During the hot pressing process, they can serve as a reinforcement phase to significantly improve the overall performance of sintered components and expand their application range.

Description

Technical Field

[0001] The present invention relates to the field of metal powder preparation and application, and in particular to an aluminum alloy powder containing in-situ self-generated submicron TiC(N) particles and application thereof. Background Art

[0002] Aluminum-based composites, with their excellent properties such as high specific strength, high specific modulus, and low density, have shown broad application prospects in aerospace, automotive, and other fields. As a key component of aluminum-based composites, enhancing the reinforcement's strengthening effect while achieving uniform distribution throughout the aluminum matrix is ​​a pressing issue.

[0003] To ensure uniform distribution of reinforcements, more research is introducing in-situ reaction-generated techniques to prepare reinforcing phases. This technique allows the in-situ nucleation of reinforcements within the metal matrix through chemical reactions between elements or between elements and compounds, thereby generating reinforcements in situ within the metal matrix. Reinforcement phases, such as TiC, have been used in a range of aluminum-based composites. However, studies have shown that TiC lacks chemical stability in aluminum melts and undergoes a series of chemical reactions with the aluminum matrix, generating a brittle and harmful Al4C3 phase that significantly degrades the material's performance.

[0004] 3D printing and hot pressing are common techniques for preparing aluminum-based composites. During 3D printing, some high-strength aluminum alloys experience large solidification ranges, leading to high internal stresses during the forming process, which can cause defects such as thermal cracking, severely impacting the material's mechanical and forming properties. Furthermore, during hot pressing, the reinforcement phases tend to agglomerate, making it difficult to guarantee the overall performance of the material. Summary of the Invention

[0005] The purpose of the present invention is to provide an aluminum alloy powder containing in-situ self-generated submicron TiC (N) particles. The aluminum alloy powder includes an aluminum matrix and TiC (N) particles dispersed on the aluminum matrix. The TiC (N) particles can exist in two forms: one is to form nitrogen-doped TiC particles, which are formed by N atoms occupying the C vacancies in the TiC crystal; the other is to form titanium carbonitride particles, which are formed by N atoms replacing C atoms in the TiC crystal. Both have the same crystal structure as TiC, both of which are NaCl-type structures with face-centered cubic lattices, but their hardness and melt stability are higher than TiC, which can significantly improve the overall strength of the material. During the rotating electrode powder making process, the cooling rate reaches 10 3 -10 5 K / s, the size of TiC(N) particles can be further refined.

[0006] Preferably, the TiC(N) particles in the present invention can be represented by TiCxNy. For nitrogen-doped TiC particles, 0.75 < x < 0.82 and 0.18 < y < 0.25. Titanium carbonitride is also represented by TiCxNy, where 0.3 < x < 0.5 and 0.5 < y < 0.7.

[0007] Preferably, the size of the TiC(N) particles in the present invention is submicron, the average particle size is less than 300 nm, and the mass percentage of TiCN particles is 2 wt.% - 20 wt.%.

[0008] Preferably, in the aluminum alloy powder of the present invention, the content of Ti is 1 wt.% - 16.2 wt.%, the content of C is 0.3 wt.% - 3.4 wt.%, the content of N is 0.2 wt.% - 3.2 wt.%, and the rest is Al and inevitable impurity elements.

[0009] The present invention provides a method for preparing an aluminum alloy powder containing submicron TiC(N) particles, which specifically includes the following steps:

[0010] (1) Nitridation treatment of titanium powder: Place the titanium powder in an atmosphere furnace, introduce nitrogen into the furnace for 10 min, then raise the furnace temperature to 480 - 1020 °C, control the nitrogen flow rate to be 0.1 - 2 L / min, keep warm for 0.5 - 4 h, and then cool to room temperature to obtain nitrogen-doped titanium powder.

[0011] (2) Preparation of a mixed powder preform: Thoroughly mix the titanium powder, graphite powder, and pure aluminum powder obtained in step (1) in a mixer, and then press them into a preform on a briquetting machine.

[0012] (3) Preparation of an intermediate alloy: Melt the pure aluminum ingot, then raise the temperature to 1000 - 1250 °C, add the preform and melt it thoroughly, stir, then press the refining agent into the melt for refining, introduce argon for degassing, skim the slag, and finally cast it into a metal mold to obtain an Al-Ti-C-N cast rod, and further turn it into a Φ30 mm cast rod.

[0013] (4) Preparation of aluminum alloy powder: Perform plasma rotating electrode atomization powder making (PREP) on the cast rod under inert gas conditions. During the atomization process, the oxygen content is less than 100 ppm, and the working speed is 12000 - 25000 rpm to obtain an aluminum alloy powder containing submicron TiC(N) particles.

[0014] Preferably, in step (1) of the present invention, the size of the titanium powder is less than 100 μm, in step (2), the particle size of the pure aluminum powder is less than 100 μm, and the particle size of the graphite powder is less than 50 μm.

[0015] Preferably, in step (2) of the present invention, the mass of pure aluminum powder is m1, the mass of titanium powder is m2, and the mass of graphite powder is m3, and the percentage of aluminum powder in the total weight of the powder is m1 / (m1+m2+m3)=60~85.

[0016] Another object of the present invention is to provide an application of a multifunctional aluminum alloy powder containing submicron TiC(N) particles. When this multifunctional powder is mixed with a common aluminum alloy powder system and then 3D printed, the tendency of thermal cracking during printing can be significantly reduced. Hot pressing and sintering can achieve uniform dispersion of the reinforcement phase, significantly improving the mechanical properties of the composite material. The specific steps include:

[0017] (1) The powder with a particle size range of 15-53 μm was screened for 3D printing, and the powder with a particle size range of 53-106 μm was screened for hot pressing and sintering.

[0018] (2) After mixing the aluminum alloy powder containing submicron TiC(N) particles with aluminum alloy powder of the same particle size in a V-shaped mixer for 1-24 hours, it can be used for 3D printing or powder sintering.

[0019] Preferably, the aluminum alloy powder in step (2) of the present invention can be any one or more of 7075 aluminum alloy powder, 2024 aluminum alloy powder, 6061 aluminum alloy powder, and pure aluminum powder.

[0020] Compared with the prior art, the present invention has the following advantages:

[0021] (1) The present invention can achieve different amounts of nitrogen atoms dissolved in the titanium matrix by adjusting the atmosphere furnace temperature and holding time according to actual needs, thereby forming fine nitrogen-doped titanium carbide and / or titanium carbonitride reinforcement phases during the subsequent in-situ autogenous reaction process. If more N is dissolved, titanium carbonitride is easily formed, and if less N is dissolved, nitrogen-doped titanium carbide is easily formed. The amount of dissolved N is related to the temperature and time of nitriding. The higher the temperature and the longer the time, the more N is dissolved. Both of these reinforcement phases can improve the chemical stability of TiC in aluminum melt.

[0022] (2) The present invention can fully utilize the process advantages of rotating electrode powder making, improve the utilization rate of raw materials, and expand the application range of powder while maintaining the high sphericity of powder. Powder with a particle size of 15-53 μm can be used for 3D printing, and powder with a particle size of 53-106 μm can be used for hot pressing and sintering.

[0023] (3) The present invention can be applied in many aspects of the powder metallurgy field. In the 3D printing process, the tendency of the alloy to thermally crack during the printing process can be reduced. After the powder is mixed with common high-strength aluminum alloy powder, two fine nitrogen-doped titanium carbide or titanium carbonitride reinforcement phases can serve as heterogeneous nucleation sites during the rapid solidification process, significantly refining the coarse columnar crystals, thereby solving the problem that the aluminum alloy cannot be used due to thermal cracking during the 3D printing process and further expanding its processing window; in the hot pressing sintering process, the fine nitrogen-doped titanium carbide or titanium carbonitride reinforcement phases have good wettability with the aluminum matrix, and the evenly dispersed reinforcement phases not only improve the interface bonding strength between the matrix and the aluminum matrix, but also further enhance the comprehensive performance of the composite material. BRIEF DESCRIPTION OF THE DRAWINGS

[0024] Figure 1 This is the SEM morphology of the aluminum alloy powder containing in-situ self-generated submicron TiC(N) particles prepared in the present invention.

[0025] Figure 2 The interface morphology and surface scanning images of the aluminum alloy powder containing in-situ self-generated submicron TiC (N) particles prepared by the present invention show that the submicron TiC (N) particles are uniformly dispersed in the aluminum matrix.

[0026] Figure 3 The invention discloses an application of the aluminum alloy powder containing submicron TiC(N) particles prepared by the present invention in 3D printing. DETAILED DESCRIPTION

[0027] In order to enable those skilled in the art to better understand the technical solutions in this application, the present application will be clearly and completely described below in conjunction with specific embodiments. The described embodiments are only a portion of the embodiments of this application, not all of them. Based on the embodiments in this application, all other embodiments obtained by those skilled in the art without creative work should fall within the scope of protection of this application.

[0028] Example 1

[0029] (1) Prepare the required raw materials according to the following mass percentages: titanium powder (size less than 30 μm) 4.00%, graphite powder (size less than 20 μm) 1.00%, pure aluminum powder (size less than 40 μm) 3.50%, and pure aluminum ingot 91.50%.

[0030] (2) The titanium powder was placed in a tubular atmosphere furnace and argon was introduced for 10 minutes. The furnace temperature was then raised to 600°C, the nitrogen flow rate was controlled at 0.7 L / min, and the temperature was kept for 1.5 hours before cooling to room temperature to obtain N-doped titanium powder.

[0031] (3) The N-doped titanium powder, graphite powder and pure aluminum powder were fully mixed in a V-type mixer and then pressed into a preform on a briquetting machine at a pressure of 50 MPa.

[0032] (4) The pure aluminum ingot weighed in (1) was melted at 720°C, then the temperature was raised to 1000°C, and the prefabricated block was added and fully melted and stirred. Then, a refining agent was pressed into the melt for refining, and argon gas was introduced for degassing and slag removal. Finally, it was cast into a metal mold to obtain Φ32-35 mm Al-Ti-NC cast rods, which were further turned into Φ30 mm cast rods.

[0033] (5) The cast rod is subjected to plasma rotating electrode atomization powdering under argon conditions, the oxygen content during the atomization process is less than 100 ppm, and the operating speed is 15000 rpm; the prepared spherical powder is sieved to screen out aluminum-based nitrogen-doped titanium carbide spherical powder with a particle size of 15-53 μm.

[0034] (6) Select Al-Zn-Mg-Cu spherical powder with the same particle size of 15-53 μm, in which the mass fraction of Zn is 5.4%, the mass fraction of Mg is 2.7%, the mass fraction of Cu is 1.4%, and Al is the balance; use a mechanical mixing method in a V-shaped mixer to mix 1.5 wt.% 15-53 μm aluminum-based nitrogen-doped titanium carbide spherical powder with the same particle size of Al-Zn-Mg-Cu spherical powder for 6 hours at a rotation speed of 50 rpm to obtain the powder used for 3D printing additive manufacturing.

[0035] (7) Before printing, the additive powder needs to be dried in a vacuum drying oven at 80°C for 2 hours, and then 3D printing is performed. The molding parameters are: laser power 350W, scanning speed 1100mm / s, scanning spacing 0.08mm, and layer thickness 0.03mm, and the aluminum-based composite material prepared by 3D printing can be obtained.

[0036] Example 2

[0037] (1) Prepare the required raw materials according to the following mass percentages: titanium powder (size less than 30 μm) 4.00%, graphite powder (size less than 20 μm) 1.00%, pure aluminum powder (size less than 40 μm) 3.50%, and pure aluminum ingot 91.50%.

[0038] (2) The titanium powder was placed in a tubular atmosphere furnace and argon was introduced for 10 minutes. The furnace temperature was then raised to 960°C, the nitrogen flow rate was controlled at 1.3 L / min, and the mixture was kept at this temperature for 2.5 hours and then cooled to room temperature to obtain N-doped titanium powder.

[0039] (3) The N-doped titanium powder, graphite powder and pure aluminum powder were fully mixed in a V-type mixer and then pressed into a preform on a briquetting machine at a pressure of 50 MPa.

[0040] (4) The pure aluminum ingot weighed in (1) was melted at 720°C, then the temperature was raised to 1000°C, and the prefabricated block was added and fully melted and stirred. Then, a refining agent was pressed into the melt for refining, and argon gas was introduced for degassing and slag removal. Finally, it was cast into a metal mold to obtain Φ32-35 mm Al-Ti-NC cast rods, which were further turned into Φ30 mm cast rods.

[0041] (5) The cast rod is subjected to plasma rotating electrode atomization powdering under argon conditions, the oxygen content during the atomization process is less than 100 ppm, and the operating speed is 15000 rpm; the prepared spherical powder is sieved to screen out aluminum-based doped titanium carbonitride spherical powder with a particle size of 15-53 μm.

[0042] (6) The same Al-Zn-Mg-Cu spherical powder as in Example 1 was selected, and 1.5 wt.% of 15-53 μm aluminum-based doped titanium carbonitride spherical powder was mechanically mixed with Al-Zn-Mg-Cu spherical powder of the same particle size in a V-shaped mixer for 6 hours at a rotation speed of 50 rpm to obtain the powder used for 3D printing additive manufacturing.

[0043] (7) Before printing, the additive powder needs to be dried in a vacuum drying oven at 80°C for 2 hours, and then 3D printing is performed. The molding parameters are the same as those in Example 1, and the aluminum-based composite material prepared by 3D printing can be obtained.

[0044] Example 3

[0045] (1) Prepare the required raw materials according to the following mass percentages: titanium powder (size less than 30 μm) 4.00%, graphite powder (size less than 20 μm) 1.00%, pure aluminum powder (size less than 40 μm) 3.50%, and pure aluminum ingot 91.50%.

[0046] (2) The titanium powder was placed in a tubular atmosphere furnace and argon was introduced for 10 minutes. The furnace temperature was then raised to 820°C, the nitrogen flow rate was controlled at 1.8 L / min, and the temperature was kept for 3.5 hours before cooling to room temperature to obtain N-doped titanium powder.

[0047] (3) The N-doped titanium powder, graphite powder and pure aluminum powder were fully mixed in a V-type mixer and then pressed into a preform on a briquetting machine at a pressure of 50 MPa.

[0048] (4) The pure aluminum ingot weighed in (1) was melted at 720°C, then the temperature was raised to 1000°C, and the prefabricated block was added and fully melted and stirred. Then, a refining agent was pressed into the melt for refining, and argon gas was introduced for degassing and slag removal. Finally, it was cast into a metal mold to obtain Φ32-35 mm Al-Ti-NC cast rods, which were further turned into Φ30 mm cast rods.

[0049] (5) The cast rod is subjected to plasma rotating electrode atomization powdering under argon conditions, the oxygen content during the atomization process is less than 100 ppm, and the operating speed is 15000 rpm; the prepared spherical powder is sieved to screen out aluminum-based nitrogen-doped titanium carbide and titanium carbonitride spherical powders with a particle size of 15-53 μm.

[0050] (6) The same Al-Zn-Mg-Cu spherical powder as in Example 1 was selected, and 1.5 wt.% of 15-53 μm aluminum-based nitrogen-doped titanium carbide and titanium carbonitride spherical powder was mixed with Al-Zn-Mg-Cu spherical powder of the same particle size in a V-shaped mixer by mechanical mixing for 6 hours at a rotation speed of 50 rpm to obtain the powder used for 3D printing additives.

[0051] (7) Before printing, the additive powder needs to be dried in a vacuum drying oven at 80°C for 2 hours, and then 3D printing is performed. The molding parameters are the same as those in Example 1, and the aluminum-based composite material prepared by 3D printing can be obtained.

[0052] Comparative Example 1

[0053] (1) Select Al-Zn-Mg-Cu spherical powder with a diameter of 15-53 μm and the same composition as in Example 1.

[0054] (2) Before 3D printing, the powder needs to be dried in a vacuum drying oven at 80°C for 2 hours, and then 3D printing is performed. The molding parameters are: laser power 350W, scanning speed 1100mm / s, scanning spacing 0.08mm, and layer thickness 0.03mm.

[0055] Figure 3 Figure 3 illustrates the application of the aluminum alloy powder containing submicron TiC(N) particles prepared by the present invention in 3D printing. (a) shows the metallographic microstructure of Comparative Example 1; (b) shows the metallographic microstructure of Example 1; (c) shows the metallographic microstructure of Example 2; and (d) shows the metallographic microstructure of Example 3. Comparison reveals that the addition of aluminum alloy powder containing submicron TiC(N) particles reduces the number of pores and cracks in the 7075 aluminum alloy microstructure, demonstrating that the modified 7075 aluminum alloy has achieved full densification, further expanding its 3D printing processing range.

[0056] Example 4

[0057] (1) Prepare the required raw materials according to the following mass percentages: titanium powder (size less than 30 μm) 4.00%, graphite powder (size less than 20 μm) 1.00%, pure aluminum powder (size less than 40 μm) 3.50%, and pure aluminum ingot 91.50%.

[0058] (2) The titanium powder was placed in a tubular atmosphere furnace and argon was introduced for 10 minutes. The furnace temperature was then raised to 600°C, the nitrogen flow rate was controlled at 0.8 L / min, and the temperature was kept for 1.5 hours before cooling to room temperature to obtain nitrided titanium powder.

[0059] (3) The nitrided titanium powder, graphite powder and pure aluminum powder were fully mixed in a V-type mixer and then pressed into a preform on a briquetting machine at a pressure of 50 MPa.

[0060] (4) The pure aluminum ingot weighed in (1) was melted at 720°C, then the temperature was raised to 1000°C, and the prefabricated block was added and fully melted and stirred. Then, a refining agent was pressed into the melt for refining, and argon gas was introduced for degassing and slag removal. Finally, it was cast into a metal mold to obtain Φ32-35 mm Al-Ti-NC cast rods, which were further turned into Φ30 mm cast rods.

[0061] (5) The cast rod was subjected to plasma rotary electrode atomization under argon conditions, with the oxygen content being less than 100 ppm during the atomization process and the operating speed being 15,000 rpm. The prepared spherical powder was sieved to select aluminum-based nitrogen-doped titanium carbide spherical powder with a particle size of 53-106 μm.

[0062] (6) Select pure aluminum powder spherical powder with the same particle size of 53-106 μm, and use a mechanical mixing method in a V-shaped mixer to mix 1.5 wt.% aluminum-based nitrogen-doped titanium carbide spherical powder with a particle size of 15-53 μm with pure aluminum powder at a rotation speed of 50 rpm for 6 hours to obtain the powder used for hot pressing sintering.

[0063] (7) Hot pressing and sintering are performed, wherein the hot pressing and sintering parameters are: sintering temperature 450°C, sintering pressure 100 MPa, and holding time: 90 min, and a dense composite material block can be obtained.

[0064] The room temperature tensile performance test showed that the tensile strength was 145 MPa.

[0065] Example 5

[0066] (1) Prepare the required raw materials according to the following mass percentages: titanium powder (size less than 30 μm) 4.00%, graphite powder (size less than 20 μm) 1.00%, pure aluminum powder (size less than 40 μm) 3.50%, and pure aluminum ingot 91.50%.

[0067] (2) The titanium powder was placed in a tubular atmosphere furnace and argon was introduced for 10 minutes. The furnace temperature was then raised to 960°C, the nitrogen flow rate was controlled at 1.3 L / min, and the temperature was kept for 2.5 hours before cooling to room temperature to obtain nitrided titanium powder.

[0068] (3) The nitrided titanium powder, graphite powder and pure aluminum powder were fully mixed in a V-type mixer and then pressed into a preform on a briquetting machine at a pressure of 50 MPa.

[0069] (4) The pure aluminum ingot weighed in (1) was melted at 720°C, then the temperature was raised to 1000°C, and the prefabricated block was added and fully melted and stirred. Then, a refining agent was pressed into the melt for refining, and argon gas was introduced for degassing and slag removal. Finally, it was cast into a metal mold to obtain Φ32-35 mm Al-Ti-NC cast rods, which were further turned into Φ30 mm cast rods.

[0070] (5) The cast rod was subjected to plasma rotary electrode atomization under argon conditions, with the oxygen content being less than 100 ppm during the atomization process and the operating speed being 15,000 rpm. The prepared spherical powder was sieved to select aluminum-based doped titanium carbonitride spherical powder with a particle size of 53-106 μm.

[0071] (6) Select pure aluminum powder spherical powder with the same particle size of 53-106 μm, and use a mechanical mixing method in a V-shaped mixer to mix 1.5 wt.% of aluminum-based doped titanium carbonitride spherical powder with a particle size of 15-53 μm with pure aluminum powder at a rotation speed of 50 rpm for 6 hours to obtain the powder used for hot pressing sintering.

[0072] (7) Hot pressing and sintering are performed with the same molding parameters as in Example 4 to obtain a dense composite material block.

[0073] The room temperature tensile performance test showed that the tensile strength was 158 MPa.

[0074] Example 6

[0075] (1) Prepare the required raw materials according to the following mass percentages: titanium powder (size less than 30 μm) 4.00%, graphite powder (size less than 20 μm) 1.00%, pure aluminum powder (size less than 40 μm) 3.50%, and pure aluminum ingot 91.50%.

[0076] (2) The titanium powder was placed in a tubular atmosphere furnace and argon was introduced for 10 minutes. The furnace temperature was then raised to 820°C, the nitrogen flow rate was controlled at 1.8 L / min, and the temperature was kept for 3.5 hours before cooling to room temperature to obtain nitrided titanium powder.

[0077] (3) The nitrided titanium powder, graphite powder and pure aluminum powder were fully mixed in a V-type mixer and then pressed into a preform on a briquetting machine at a pressure of 50 MPa.

[0078] (4) The pure aluminum ingot weighed in (1) was melted at 720°C, then the temperature was raised to 1000°C, and the prefabricated block was added and fully melted and stirred. Then, a refining agent was pressed into the melt for refining, and argon gas was introduced for degassing and slag removal. Finally, it was cast into a metal mold to obtain Φ32-35 mm Al-Ti-NC cast rods, which were further turned into Φ30 mm cast rods.

[0079] (5) The cast rod is subjected to plasma rotating electrode atomization powdering under argon conditions, the oxygen content during the atomization process is less than 100 ppm, and the operating speed is 15000 rpm; the prepared spherical powder is sieved to screen out aluminum-based nitrogen-doped titanium carbide and titanium carbonitride spherical powders with a particle size of 53-106 μm.

[0080] (6) Select pure aluminum powder spherical powder with the same particle size of 53-106 μm, and use a mechanical mixing method in a V-shaped mixer to mix 1.5 wt.% of 15-53 μm particle size aluminum-based nitrogen-doped titanium carbide and titanium carbonitride spherical powder with pure aluminum powder for 6 hours at a rotation speed of 50 rpm to obtain the powder used for hot pressing sintering.

[0081] (7) Hot pressing and sintering are performed with the same molding parameters as in Example 4 to obtain a dense composite material block.

[0082] The room temperature tensile performance test showed that the tensile strength was 169 MPa.

[0083] Comparative Example 2

[0084] (1) Select pure aluminum powder with a particle size of 53-106 μm.

[0085] (2) Hot pressing and sintering are performed, and the molding parameters are the same as those in Example 4.

[0086] (3) The room temperature tensile performance test was conducted on the product, and the tensile strength was 97 MPa, which was much lower than that of Examples 4, 5, and 6.

Claims

1. A method for preparing an aluminum alloy powder containing in-situ self-generated TiC(N) particles, characterized in that: The aluminum alloy powder includes an aluminum matrix and TiC(N) particles dispersed on the aluminum matrix. The TiC(N) particles have two forms of existence. One is the formation of nitrogen-doped TiC particles, which are formed by N atoms occupying the C vacancies in the TiC crystal; the other is the formation of titanium carbonitride particles, which are formed by N atoms replacing C atoms in the TiC crystal. Both have the same crystal structure as TiC, and the specific steps are as follows: (1) Nitridation treatment of titanium powder: Place the titanium powder in an atmosphere furnace, introduce nitrogen into the furnace for 10 minutes, then raise the furnace temperature to 480 - 1020 °C, control the nitrogen flow rate to be 0.1 - 2 L / min, keep it warm for 0.5 - 4 h, and then cool it to room temperature to obtain nitrogen atom-doped titanium powder; (2) Preparation of mixed powder preform: Mix the titanium powder, graphite powder, and pure aluminum powder obtained in step (1)充分 in a mixer, and then press them into a preform on a briquetting machine; (3) Preparation of master alloy: Melt the pure aluminum ingot, then raise the temperature to 1000 - 1250 °C, add the preform and melt it充分, stir it, then press the refining agent into the melt for refining, introduce argon for degassing, skim the slag, and finally cast it into a metal mold to obtain an Al-Ti-C-N cast rod, and further turn it into a cast rod; (4) Preparation of aluminum alloy powder: Perform plasma rotating electrode atomization powder making (PREP) on the cast rod under inert gas conditions to obtain a multifunctional aluminum alloy powder containing submicron TiC(N) particles.

2. The method for preparing an aluminum alloy powder containing in-situ self-generated TiC(N) particles according to claim 1, characterized in that: The nitrogen-doped TiC particles are represented by TiCxNy, where 0.75 < x < 0.82 and 0.18 < y < 0.25; the titanium carbonitride particles are also represented by TiCxNy, where 0.3 < x < 0.5 and 0.5 < y < 0.

7.

3. The method for preparing an aluminum alloy powder containing in-situ self-generated TiC(N) particles according to claim 1, characterized in that: The size of the TiC(N) particles is submicron level, the average particle size is less than 300 nm, and the mass percentage of the particles is 2 wt.% - 20 wt.%.

4. The method for preparing an aluminum alloy powder containing in-situ self-generated TiC(N) particles according to claim 1, characterized in that: In the aluminum alloy powder, the content of Ti is 1 wt.% - 16.2 wt.%, the content of C is 0.3 wt.% - 3.4 wt.%, the content of N is 0.2 wt.% - 3.2 wt.%, and the rest is Al and inevitable impurity elements.

5. The method for preparing an aluminum alloy powder containing in-situ self-generated TiC(N) particles according to claim 1, characterized in that: In step (1), the size of the titanium powder is less than 100 µm, in step (2), the particle size of the pure aluminum powder is less than 100 µm, and the particle size of the graphite powder is less than 50 µm.

6. The method for preparing an aluminum alloy powder containing in-situ self-generated TiC(N) particles according to claim 1, characterized in that: In step (2), the mass of the pure aluminum powder is m'1, the mass of the titanium powder is m'2, and the mass of the graphite powder is m'3. The percentage of the aluminum powder in the total powder weight is m'1 / (m'1 + m'2 + m'3) = 60% - 85%.

7. The method for preparing an aluminum alloy powder containing in-situ self-generated TiC(N) particles according to claim 1, characterized in that: During the atomization process in step (4), the oxygen content is less than 100 ppm, and the working speed is 12000 - 25000 rpm.

8. The aluminum alloy powder containing in-situ generated TiC(N) particles prepared by the method described in claim 1.

9. Use of the aluminum alloy powder containing in-situ self-generated TiC(N) particles according to claim 8, characterized in that: Apply the aluminum alloy powder containing in-situ generated TiC(N) particles to 3D printing forming and hot pressing sintering forming.

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