A method for preparing two-dimensional nano-Ti3C2 reinforced aluminum matrix composites

Abstract

This invention relates to a method for preparing a two-dimensional nano-Ti3C2 reinforced aluminum matrix composite material. First, aluminum sheets coated with polydiallyldimethylammonium chloride (PDDA) are prepared. Then, Ti3C2 / Al layered composite powder is electrostatically self-assembled and heated to 550–600°C at a certain rate, held at 10–100 MPa for 10–30 min, while simultaneously undergoing plasma vacuum sintering to obtain the composite material. The sintered body is heated to 400–500°C at a certain rate and held for 1–2 h, then biaxially compressed by 10%–40%. After furnace cooling, it is placed in a holding furnace and heated to 400–480°C, held for 1–1.5 h, and then water-cooled; this cycle is repeated 1–10 times. The composite material is then biaxially cold-compressed by 5%–35%, heated to 450–600°C and held for 5 min–3 h, and water-cooled to obtain the two-dimensional nano-Ti3C2 reinforced aluminum matrix composite material. This invention is characterized by ease of operation, safety, effectiveness, low cost, and controllable quality.

Description

Technical Field

[0001] This invention belongs to the field of metal material preparation, and specifically relates to a method for preparing a two-dimensional nano-Ti3C2 reinforced aluminum matrix composite material. Background Technology

[0002] Compared to traditional alloys, metal matrix composites exhibit superior comprehensive mechanical properties, such as high specific strength, excellent creep resistance, good wear resistance, and high fatigue resistance, and are widely used in aerospace, vehicle manufacturing, rail transportation, electronic information and other fields.

[0003] Two-dimensional materials, such as graphene, boron nitride, and MXene, are widely used to reinforce metallic materials. Their high-temperature resistance, high strength, high toughness, and high rigidity make them ideal as reinforcements for matrix alloys. Notably, the arrangement of individual flakes in a composite material can significantly influence its reinforcing effect, thus attracting considerable attention. However, due to their high surface energy, high specific area, and strong van der Waals forces, they are more difficult to disperse uniformly than nanoparticles or fibers.

[0004] Currently, methods such as mechanical stirring, electromagnetic stirring, in-situ synthesis, powder metallurgy, surface metallization, and molecular-level mixing are used to address the dispersion problem of reinforcements. In CN108251679A, a method for preparing graphene-reinforced magnesium-based composite materials solves the dispersion problem of graphene in magnesium metal through ball milling pre-dispersion, electromagnetic stirring, and semi-solid casting. However, the uniform distribution of graphene at the microscale remains unresolved. Patent CN113667858A discloses a method for preparing nano-alumina-reinforced aluminum-based composite materials with in-situ spinel coating. By generating spinel in-situ on the surface of nano-alumina, its distribution in the molten metal is improved and grain refinement is achieved, solving the problems of reinforcement dispersion and grain size controllability. However, the uniform distribution of nano-reinforcement at the microscale still has significant potential, and the spatial structure of the composite material remains uncontrollable. In CN117026001A, a method for preparing graphene-aluminum-based composite materials is disclosed, in which graphene surface metallization is used to improve wettability with the metal melt, and electromagnetic stirring is used to uniformly disperse graphene in the metal melt. Due to the large density difference, large specific surface area, and nanometer thickness of graphene and aluminum, there is still room for improvement in the distribution of graphene in a small size range.

[0005] The theoretically calculated elastic modulus of monolayer Ti3C2 reaches 300 GPa, which is lower than that of graphene but higher than that of most oxides and layered clays. Furthermore, Ti3C2 nanosheets can be bent into diameters less than 20 nm without breaking, exhibiting good strength and toughness; their bending stiffness is significantly higher than that of graphene, and at 200 kV, Ti3C2 sheets are more stable than graphene sheets. These properties provide a solid foundation for its application in composite materials. However, due to the high surface energy, high specific area, and strong van der Waals forces of Ti3C2 nanosheets, they are prone to agglomeration when mixed with metals.

[0006] Besides dispersion issues, the spatial distribution of two-dimensional nanosheets plays a crucial role in material properties. Arbitrary arrangement of two-dimensional nanosheets within the matrix only results in a simple mixing effect, offering limited reinforcement to the composite material. However, the strengthening effect of ordered, layered distribution of two-dimensional nanosheets within the matrix far surpasses that of simple mixing. In CN116798875A, a method for preparing a layered composite material of two-dimensional layered carbonitrides and copper was described. Surface modification, electroplating, and hot rolling were used to prepare a copper-based composite material with high electrical and thermal conductivity and low thermal expansion, solving the dispersion problem of layered carbonitrides in the copper matrix. However, the orientation of the two-dimensional nanosheets is arbitrary and uncontrollable. Furthermore, the interfacial bonding between the nanosheets and the matrix metal, and the compactness of the composite material, still require further solutions.

[0007] In CN116607039A, a method for preparing graphene-reinforced TC4 titanium-based composite materials was disclosed. This method employed chemical vapor deposition, spark plasma sintering, and hot extrusion to prepare the composite material, solving the problems of graphene dispersion and material density. However, the graphene coating and matrix structure are difficult to control, and safety issues also exist. It is important to note that while the problems of dispersion, spatial distribution, interfacial bonding, and density of the nanosheet reinforcement are resolved, the trade-off between strength and toughness in the composite material remains.

[0008] Therefore, in summary, an effective method for preparing two-dimensional nanosheet-reinforced aluminum-based composite materials is still lacking. In view of this, this application is hereby submitted. Summary of the Invention

[0009] The present invention provides a method for preparing two-dimensional nano-Ti3C2 reinforced aluminum matrix composites, in order to solve the problem that there is still a lack of an effective method for preparing two-dimensional nanosheet reinforced aluminum matrix composites.

[0010] The embodiments of the present invention are implemented as follows: A method for preparing a two-dimensional nano-Ti3C2 reinforced aluminum matrix composite material includes the following steps: Step S1: Place spherical aluminum powder and stearic acid into a container and ball mill them under argon atmosphere to obtain aluminum sheet powder; Step S2: Add anhydrous ethanol to a 0.1-0.4 wt% polydiallyldimethylammonium chloride (PDDA) solution to prepare a mixture of deionized water, ethanol and PDDA; Step S3: Add the aluminum sheet powder obtained in step S1 to the mixture obtained in step S2, and stir with positive and negative magnetic force for 30 to 60 minutes with an interval of 1 to 2 seconds to obtain an aluminum sheet suspension. Step S4: Add 5-20 mg / ml of Ti3C2 aqueous solution to the aluminum sheet suspension obtained in step S3, wherein the amount of Ti3C2 added is 1.0 wt% of the aluminum powder, and apply positive and negative magnetic stirring and mechanical stirring at the same time. After the addition is complete, continue stirring for 2-4 hours, wherein the mechanical stirring rate is 300-400 rpm, to obtain a composite powder suspension. Step S5: Wash the composite powder suspension obtained in step S4 in distilled water and vacuum filter it, repeating the process 3 to 5 times to obtain the powder. Step S6: Place the powder obtained in step S5 in a vacuum furnace, let it stand for 8 to 12 hours, then heat it to 60 to 80°C and hold it for 12 to 24 hours. Cool it with the furnace to obtain Ti3C2 / Al layered composite powder. Step S7: Place the Ti3C2 / Al layered composite powder obtained in step S6 into a graphite mold, heat it to a temperature of 550-600℃ at a heating rate of 10-50℃ / min, hold it at a pressure of 10-100MPa for 10-30min, and simultaneously perform plasma vacuum sintering. After holding at the temperature, maintain the pressure and allow it to cool naturally to obtain a plasma sintered body. Step S8: The plasma sintered body obtained in step S7 is heated to 400-500°C at a rate of 3-10°C / min, held for 1-2 hours, and then bidirectionally compressed by 10%-40% at a deformation rate of 0.1-2 mm / min. It is then cooled in the furnace to obtain deformed body a. Step S9: Place the deformed body a obtained in step S8 into a heat preservation furnace, heat it to 400-480°C at a rate of 10-20°C / min, keep it at that temperature for 1-1.5 hours, and then water cool it. Step S10: Repeat steps S8 and S9 1 to 10 times to obtain the composite material; Step S11: The composite material obtained in step S10 is subjected to cold compression deformation, and bidirectional compression of 5% to 35% is performed at a deformation rate of 0.1 to 10 mm / min to obtain deformed body b; Step S12: The deformed body b obtained in step S11 is heated to 450-600°C at a rate of 10-20°C / min, held at that temperature for 5 min-3 h, and then water-cooled to obtain a two-dimensional nano-Ti3C2 reinforced aluminum matrix composite material.

[0011] Furthermore, the spherical aluminum powder in step S1 has a size of 10–100 μm.

[0012] Further, in step S1, the mass ratio of the spherical aluminum powder to the stearic acid is 40:1 to 100:1.

[0013] Furthermore, in step S1, the diameter of the grinding ball is 3 to 10 mm.

[0014] Further, in step S1, the spherical aluminum powder and the stearic acid are ball-milled at a rate of 300-600 rpm for 2-5 hours, then cooled for 24-48 hours, and ball-milled again for 2-5 hours. After the process is completed, the mixture is cooled for 24-48 hours. The mass ratio of the ball milling balls to the aluminum powder is 10:1 to 20:1.

[0015] Furthermore, in step S2, the volume ratio of anhydrous ethanol to polydiallyldimethylammonium chloride (PDDA) solution is 1:1.5 to 1:1.

[0016] Furthermore, the concentration of the aluminum sheet powder in the mixture in step S3 is 0.05–0.5 g / ml.

[0017] Furthermore, the dripping rate of the Ti3C2 aqueous solution in step S4 is 1–5 ml / min.

[0018] Furthermore, step S4 is carried out under an inert atmosphere.

[0019] Furthermore, in step S5, the vacuum filtration uses an organic filter membrane with a pore size of 1.2–2.0 μm.

[0020] The beneficial effects of the embodiments of the present invention are: (1) The preparation method provided by the present invention has a simple operation process and a relatively low working temperature, which not only improves the safety of operation but also reduces energy consumption. At the same time, due to the use of environmentally friendly raw materials and processes, the entire preparation process is pollution-free, simple to operate, low working temperature, safe and reliable, and pollution-free.

[0021] (2) This method improves the affinity of aluminum sheet powder with Ti3C2 nanosheets by modifying the surface of the aluminum sheet powder with polydiallyldimethylammonium chloride (PDDA). At the same time, Ti3C2 nanosheets are uniformly coated on the surface of the aluminum sheet powder by positive and negative magnetic stirring and mechanical stirring to form Ti3C2 / Al layered composite powder. This method also achieves the compactness of the structure, the ordered layered distribution of nano-reinforcing sheets in the matrix metal, and the grain refinement and microstructure control of the matrix metal through processes such as plasma vacuum sintering, hot compression deformation, heat treatment, and thermomechanical treatment. This method can effectively avoid problems such as agglomeration, sedimentation, and oxidation of nano-reinforcing sheets, and ensure the uniformity and stability of the composite material. This method can realize the spatial dispersion and distribution of nano-reinforcing sheets and the control of matrix metal structure, and can realize mass production.

[0022] (3) This method improves the affinity between aluminum sheet powder and Ti3C2 nanosheets by modifying the surface of the aluminum sheet powder with PDDA, and at the same time, atomic diffusion occurs between Ti3C2 nanosheets and aluminum matrix through plasma vacuum sintering, thereby realizing the atomic-level bonding between nanosheets and metal, improving the interface strength and interface transfer efficiency, and resulting in high interface strength.

[0023] (4) This method achieves controllable control over the grain boundary microstructure characteristics of composite materials through processes such as hot compression deformation, heat treatment, and thermomechanical treatment, including the number of grain boundaries, grain boundary type, grain boundary angle, and grain boundary width. By adjusting parameters such as deformation temperature, deformation rate, deformation degree, and holding time, the grain boundary microstructure characteristics of composite materials can be optimized, achieving controllable grain boundary microstructure characteristics and thus improving the mechanical properties of composite materials.

[0024] (5) This method strengthens and toughens the composite material by introducing two-dimensional nano-Ti3C2 reinforcing sheets into the aluminum matrix. The two-dimensional nano-Ti3C2 reinforcing sheets possess high elastic modulus, toughness, and stability, effectively improving the strength, hardness, wear resistance, and creep resistance of the composite material. Simultaneously, the layered distribution of the two-dimensional nano-Ti3C2 reinforcing sheets within the matrix metal effectively prevents crack propagation and increases the toughness, ductility, and fatigue resistance of the composite material. Therefore, this method achieves synergistic improvement in strength and plasticity, enhancing the overall performance of the composite material. Attached Figure Description

[0025] Figure 1 EBSD microstructure diagram of the Ti3C2 / Al composite material prepared in Example 2; Figure 2 The image shows the EDS analysis spectrum of Ti3C2 in the interlayer of the aluminum sheet prepared in Example 2. Detailed Implementation

[0026] The technical solutions of the embodiments of the present invention will be clearly and completely described below with reference to the accompanying drawings. Obviously, the described embodiments are only some embodiments of the present invention, and not all embodiments. Based on the embodiments of the present invention, all other embodiments obtained by those skilled in the art without creative effort are within the scope of protection of the present invention.

[0027] It should be understood that the terms "first," "second," etc., are used in this invention to describe various types of information, but these terms are not limited to them; they are only used to distinguish information of the same type from one another. For example, without departing from the scope of this invention, "first" information may also be referred to as "second" information, and similarly, "second" information may also be referred to as "first" information.

[0028] This invention provides a method for preparing a two-dimensional nano-Ti3C2 reinforced aluminum matrix composite material. Utilizing the abundant functional groups and high specific surface area of ​​the two-dimensional nano-Ti3C2 surface, it achieves self-assembly with metal sheets rich in cations to form a nanolayered structure. To improve the bonding state of the Ti3C2 / Al interface, the plasma sintering and subsequent deformation and annealing processes can be controlled to achieve atomic-scale bonding between Ti3C2 and Al while preventing the formation of brittle TiAl phases at the interface that would damage the interface strength, thereby improving the interface. Furthermore, the design and control of the nanolayered structure can be achieved by controlling ball milling, assembly, and subsequent processes. Grain boundary characteristic control is implemented on the Ti3C2 / Al nanolayered aluminum matrix composite material to improve the overall mechanical properties of the composite material. Example

[0029] 20 μm spherical pure aluminum powder and stearic acid were placed in a container, with a mass ratio of 40:1. The diameter of the ball milling balls was 8 mm. The mixture was ball milled at 500 rpm for 4 hours under argon atmosphere, then cooled for 48 hours, and ball milled again for 4 hours, followed by cooling for 48 hours. The mass ratio of ball milling balls to powder was 10:1, yielding aluminum flake powder. Anhydrous ethanol was added to a 0.1 wt% polydiallyldimethylammonium chloride (PDDA) solution to prepare a mixture of deionized water, ethanol, and PDDA, with a volume ratio of 1:1.5. The aluminum flake powder obtained above was added to the mixture, and the mixture was stirred magnetically for 30 minutes with 2-second intervals, resulting in a concentration of 0.1 g / ml of aluminum flake powder in the solution. 5 mg / ml of the mixture was then added dropwise. An aqueous solution of Ti3C2 was added to the aluminum sheet suspension obtained above, with a dropping rate of 1 ml / min, while applying both positive and negative magnetic stirring and mechanical stirring. After the addition was complete, stirring continued for 2 hours, with the mechanical stirring rate at 300 rpm, under an inert atmosphere. The amount of Ti3C2 added was 1.0 wt% of the aluminum powder. The resulting composite powder suspension was washed in distilled water and vacuum filtered, repeated three times, using an organic filter membrane with a pore size of 1.2 μm. The resulting powder was placed in a vacuum furnace, allowed to stand for 8 hours, then heated to 80°C and held for 24 hours, followed by furnace cooling to obtain Ti3C2 / Al layered composite powder. The obtained layered composite powder was placed in a graphite mold and heated to 550°C at a heating rate of 40°C / min. The plasma sintered body was held at 50 MPa pressure for 10 min while undergoing plasma vacuum sintering. After holding at 50 MPa, it was naturally cooled under pressure. The plasma sintered body was then heated to 480°C at a rate of 3°C / min and held for 1 h. It was then bidirectionally compressed by 10% at a deformation rate of 0.5 mm / min and cooled in the furnace. The deformed body was then placed in a holding furnace and heated to 400°C at a rate of 15°C / min. After holding at 400°C for 1.5 h, it was water-cooled. The bidirectional compression and high-temperature holding followed by water cooling were repeated twice. The resulting composite material was then subjected to cold compression deformation at a deformation rate of 1.0 mm / min and bidirectionally compressed by 10%. The deformed body was then heated to 450°C at a rate of 15°C / min and held for 2 h before water cooling, yielding a two-dimensional nano-Ti3C2 reinforced aluminum matrix composite material. Example

[0030] 40μm spherical 5083 aluminum powder and stearic acid were placed in a container, with a mass ratio of spherical aluminum powder to stearic acid of 40:1. The diameter of the ball milling balls was 8mm. The mixture was ball milled at 500rpm for 4 hours under argon atmosphere, then cooled for 48 hours, and ball milled again for 4 hours, followed by cooling for 48 hours. The mass ratio of ball milling balls to powder was 10:1, yielding aluminum flake powder. Anhydrous ethanol was added to a 0.4wt% polydiallyldimethylammonium chloride (PDDA) solution to prepare a mixture of deionized water, ethanol, and PDDA, with a volume ratio of anhydrous ethanol to PDDA solution of 1:1.5. The aluminum flake powder obtained above was added to the mixture, and the mixture was stirred magnetically for 30 minutes with 2s intervals, resulting in a concentration of 0.05g / ml of aluminum flake powder in the solution. 10mg / ml of the mixture was then added dropwise. An aqueous solution of Ti3C2 was added to the aluminum sheet suspension obtained above, with a dropping rate of 1 ml / min, while applying both positive and negative magnetic stirring and mechanical stirring. After the addition was complete, stirring continued for 3 hours, with the mechanical stirring rate at 300 rpm, under an inert atmosphere. The amount of Ti3C2 added was 1.5 wt% of the aluminum powder. The resulting composite powder suspension was washed in distilled water and vacuum filtered, repeated four times, using an organic filter membrane with a pore size of 2.0 μm. The resulting powder was placed in a vacuum furnace, allowed to stand for 12 hours, then heated to 80°C and held for 24 hours, followed by furnace cooling to obtain Ti3C2 / Al layered composite powder. The obtained layered composite powder was placed in a graphite mold and heated to 580°C at a heating rate of 50°C / min. The plasma sintered body was held at 50 MPa pressure for 10 min while undergoing plasma vacuum sintering. After holding at 50 MPa, it was naturally cooled under pressure. The plasma sintered body was then heated to 430°C at a rate of 3°C / min and held for 1 h. It was then bidirectionally compressed by 20% at a deformation rate of 1.0 mm / min and cooled in the furnace. The deformed body was then placed in a holding furnace and heated to 450°C at a rate of 15°C / min. After holding at 450°C for 1 h, it was water-cooled. The bidirectional compression and high-temperature holding followed by water cooling were repeated once. The resulting composite material was then subjected to cold compression deformation at a deformation rate of 1.0 mm / min and bidirectionally compressed by 30%. The deformed body was then heated to 450°C at a rate of 20°C / min and held for 1.0 h before water cooling to obtain a two-dimensional nano-Ti3C2 reinforced aluminum matrix composite material. Example

[0031] 50μm spherical 7075 aluminum powder and stearic acid were placed in a container, with a mass ratio of spherical aluminum powder to stearic acid of 40:1. The diameter of the ball milling balls was 6mm. The mixture was ball milled at 550rpm for 5 hours under argon atmosphere, then cooled for 48 hours, and ball milled again for 3 hours, followed by cooling for 48 hours. The mass ratio of ball milling balls to powder was 20:1, yielding aluminum flake powder. Anhydrous ethanol was added to a 0.2wt% polydiallyldimethylammonium chloride (PDDA) solution to prepare a mixture of deionized water, ethanol, and PDDA, with a volume ratio of anhydrous ethanol to PDDA solution of 1:1.5. The aluminum flake powder obtained above was added to the mixture, and the mixture was stirred magnetically for 60 minutes with 2s intervals, resulting in a concentration of 0.5g / ml of aluminum flake powder in the solution. 10mg / ml of the mixture was then added dropwise. An aqueous solution of Ti3C2 was added to the aluminum sheet suspension obtained above, wherein the Ti3C2 aqueous solution was added at a dropping rate of 4.0 ml / min, while applying both positive and negative magnetic stirring and mechanical stirring. After the addition was complete, stirring was continued for 3 hours, wherein the mechanical stirring rate was 400 rpm, under an inert atmosphere, and the amount of Ti3C2 added was 1.0 wt% of the aluminum powder. The composite powder suspension obtained above was washed in distilled water and vacuum filtered, repeated 3 times, wherein the vacuum filtration used an organic filter membrane with a pore size of 2.0 μm. The powder obtained above was placed in a vacuum furnace, allowed to stand for 12 hours, then heated to 80°C and held for 24 hours, and cooled with the furnace to obtain Ti3C2 / Al layered composite powder. The layered composite powder obtained above was placed in a graphite mold and heated to a temperature of 580°C at a heating rate of 30°C / min. The plasma-sintered material was heated to 450°C at a pressure of 45 MPa for 20 min, and then subjected to plasma vacuum sintering. After holding at the pressure, it was naturally cooled. The plasma-sintered material was heated to 450°C at a rate of 5°C / min and held for 2 h. Then, it was biaxially compressed by 20% at a deformation rate of 0.5 mm / min and cooled in the furnace. The deformed material was placed in a holding furnace and heated to 480°C at a rate of 20°C / min. After holding at the temperature for 1 h, it was water-cooled. The biaxial compression and holding at the high temperature were repeated 4 times. The composite material was cold-compressed and deformed at a deformation rate of 1.0 mm / min, and then biaxially compressed by 25%. The deformed material was heated to 600°C at a rate of 15°C / min and held for 25 min before being water-cooled to obtain a two-dimensional nano-Ti3C2 reinforced aluminum matrix composite material.

[0032] The above are merely preferred embodiments of the present invention and are not intended to limit the present invention. Any modifications, equivalent substitutions, and improvements made within the spirit and principles of the present invention should be included within the protection scope of the present invention.

Claims

1. A method for preparing a two-dimensional nano-Ti3C2 reinforced aluminum matrix composite material, Its features are, Includes the following steps: Step S1: Place spherical aluminum powder and stearic acid into a container and ball mill them under argon atmosphere to obtain aluminum sheet powder; Step S2: Add anhydrous ethanol to a 0.1-0.4 wt% polydiallyldimethylammonium chloride (PDDA) solution to prepare a mixture of deionized water, ethanol and PDDA; Step S3: Add the aluminum sheet powder obtained in step S1 to the mixture obtained in step S2, and stir with positive and negative magnetic force for 30 to 60 minutes with an interval of 1 to 2 seconds to obtain an aluminum sheet suspension. Step S4: Add 5-20 mg / ml of Ti3C2 aqueous solution to the aluminum sheet suspension obtained in step S3, wherein the amount of Ti3C2 added is 1.0 wt% of the aluminum powder, and apply positive and negative magnetic stirring and mechanical stirring at the same time. After the addition is complete, continue stirring for 2-4 hours, wherein the mechanical stirring rate is 300-400 rpm, to obtain a composite powder suspension. Step S5: Wash the composite powder suspension obtained in step S4 in distilled water and vacuum filter it, repeating the process 3 to 5 times to obtain the powder. Step S6: Place the powder obtained in step S5 in a vacuum furnace, let it stand for 8 to 12 hours, then heat it to 60 to 80°C and hold it for 12 to 24 hours. Cool it with the furnace to obtain Ti3C2 / Al layered composite powder. Step S7: Place the Ti3C2 / Al layered composite powder obtained in step S6 into a graphite mold, heat it to a temperature of 550-600℃ at a heating rate of 10-50℃ / min, hold it at a pressure of 10-100MPa for 10-30min, and simultaneously perform plasma vacuum sintering. After holding at the temperature, maintain the pressure and allow it to cool naturally to obtain a plasma sintered body. Step S8: The plasma sintered body obtained in step S7 is heated to 400-500°C at a rate of 3-10°C / min, held for 1-2 hours, and then bidirectionally compressed by 10%-40% at a deformation rate of 0.1-2 mm / min. It is then cooled in the furnace to obtain deformed body a. Step S9: Place the deformed body a obtained in step S8 into a heat preservation furnace, heat it to 400-480°C at a rate of 10-20°C / min, keep it at that temperature for 1-1.5 hours, and then water cool it. Step S10: Repeat steps S8 and S9 1 to 10 times to obtain the composite material; Step S11: The composite material obtained in step S10 is subjected to cold compression deformation, and bidirectional compression of 5% to 35% is performed at a deformation rate of 0.1 to 10 mm / min to obtain deformed body b; Step S12: The deformed body b obtained in step S11 is heated to 450-600°C at a rate of 10-20°C / min, held at that temperature for 5 min-3 h, and then water-cooled to obtain a two-dimensional nano-Ti3C2 reinforced aluminum matrix composite material.

2. The method for preparing the two-dimensional nano-Ti3C2 reinforced aluminum matrix composite material according to claim 1, characterized in that: The spherical aluminum powder in step S1 has a size of 10 to 100 μm.

3. The method for preparing two-dimensional nano-Ti3C2 reinforced aluminum matrix composite material according to claim 1, characterized in that: The mass ratio of the spherical aluminum powder to the stearic acid in step S1 is 40:1 to 100:

1.

4. The method for preparing the two-dimensional nano-Ti3C2 reinforced aluminum matrix composite material according to claim 1, characterized in that: In step S1, the diameter of the grinding ball is 3-10 mm.

5. The method for preparing two-dimensional nano-Ti3C2 reinforced aluminum matrix composite material according to claim 1, characterized in that: In step S1, the spherical aluminum powder and the stearic acid are ball-milled at a rate of 300-600 rpm for 2-5 hours, then cooled for 24-48 hours, and then ball-milled for another 2-5 hours. After the process is completed, the mixture is cooled for 24-48 hours. The mass ratio of the ball milling balls to the aluminum powder is 10:1 to 20:

1.

6. The method for preparing the two-dimensional nano-Ti3C2 reinforced aluminum matrix composite material according to claim 1, characterized in that: In step S2, the volume ratio of anhydrous ethanol to polydiallyldimethylammonium chloride (PDDA) solution is 1:1.5 to 1:

1.

7. The method for preparing two-dimensional nano-Ti3C2 reinforced aluminum matrix composite material according to claim 1, characterized in that: The concentration of the aluminum sheet powder in the mixture in step S3 is 0.05–0.5 g / ml.

8. The method for preparing two-dimensional nano-Ti3C2 reinforced aluminum matrix composite material according to claim 1, characterized in that: The dripping rate of the Ti3C2 aqueous solution in step S4 is 1-5 ml / min.

9. The method for preparing two-dimensional nano-Ti3C2 reinforced aluminum matrix composite material according to claim 1, characterized in that: Step S4 is carried out under an inert atmosphere.

10. The method for preparing two-dimensional nano-Ti3C2 reinforced aluminum matrix composite material according to claim 1, characterized in that: In step S5, vacuum filtration uses an organic filter membrane with a pore size of 1.2–2.0 μm.

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