High-modulus magnesium-based composite material as well as preparation method and application thereof

Abstract

The invention discloses a high-modulus magnesium-based composite material as well as a preparation method and application thereof, and belongs to the technical field of magnesium alloy materials. The preparation raw materials of the magnesium-based composite material comprise micron Ti particles coated with nano Al and magnesium-aluminum-zinc alloy powder; the mass of the micron Ti particles accounts for 10 wt%-15 wt% of the magnesium-aluminum-zinc alloy powder, and the mass of the nano Al powder accounts for 5 wt%-9 wt% of the magnesium-aluminum-zinc alloy powder; the magnesium-aluminum-zinc alloy powder contains 1wt%-9wt% of Al, 0.5 wt%-1.5 wt% of Zn and the balance of Mg; the magnesium-aluminum-zinc alloy powder forms a matrix of the magnesium-based composite material; the nano Al powder and Mg in the matrix form an Al2O3 composite MgO nano layer with a semi-coherent orientation relationship in situ at an interface; segregation of the Al element exists at the grain boundary of the matrix. The magnesium-based composite material has excellent strength, plasticity and elasticity modulus, and can meet the requirements of 3C electronic product structural members.

Description

Technical Field

[0001] The present invention relates to the technical field of magnesium alloy materials, and in particular to a high-modulus magnesium-based composite material and a preparation method and application thereof. Background Art

[0002] As consumer electronics (3C) products evolve toward thinner, lighter, and higher-performance designs, the application of lightweight materials has become a key industry trend. High-modulus magnesium-based composites, with their superior specific strength, specific stiffness, electromagnetic shielding properties, and excellent heat dissipation, have become ideal structural materials for high-end 3C products such as laptops, smartphones, tablets, and wearable devices.

[0003] Traditional 3C product shells and internal support structures are mostly made of aluminum alloy or engineering plastics, but the density of aluminum alloy is relatively high (about 2.7g / cm 3 ), while engineering plastics lack the stiffness and strength. In contrast, the density of magnesium-based composites is only 1.7g / cm 3 ~2.0g / cm 3 By introducing a high-modulus reinforcement phase, its elastic modulus can be increased to over 60 GPa while maintaining excellent impact resistance and dimensional stability. However, the elastic modulus of pure magnesium and traditional magnesium alloys is relatively low (usually 40 GPa to 45 GPa), which limits their application in load-bearing structural parts. Currently, the main methods to improve the elastic modulus of magnesium-based composites include alloying (such as adding rare earth elements) and compositeization (such as introducing ceramic particles such as SiO2, Al2O3, and ZrO2). However, composites prepared by traditional mechanical mixing methods are prone to problems such as uneven distribution of the reinforcement phase and poor interface wettability, resulting in unstable mechanical properties of the composites. In addition, the thermal expansion coefficients of the reinforcement phase and the magnesium matrix are quite different, which easily generates residual stress during thermal processing, affecting the mechanical properties and dimensional stability of the material.

[0004] In view of this, the present invention is proposed. Summary of the Invention

[0005] The object of the present invention is to provide a high modulus magnesium-based composite material and a preparation method and application thereof, so as to solve or improve the above technical problems.

[0006] The present invention can be implemented like this: In a first aspect, the present invention provides a high modulus magnesium-based composite material, wherein the raw materials for preparing the high modulus magnesium-based composite material include micron Ti particles coated with nano-Al powder and magnesium-aluminum-zinc alloy powder; The nano-Al powder-coated micronized Ti particles are obtained by coating micronized Ti particles with nano-Al powder, wherein the mass of the micronized Ti particles is 10 wt% to 15 wt% of the magnesium-aluminum-zinc alloy powder, and the mass of the nano-Al powder is 5 wt% to 9 wt% of the magnesium-aluminum-zinc alloy powder; the magnesium-aluminum-zinc alloy powder contains 1 wt% to 9 wt% of Al and 0.5 wt% to 1.5 wt% of Zn, with the balance being Mg; The magnesium-aluminum-zinc alloy powder forms a matrix of a high modulus magnesium-based composite material; Al elements are segregated at the grain boundaries of the matrix; The nano-Al in the micron Ti particles coated with nano-Al powder and the Mg in the matrix in situ form an Al2O3 composite MgO nano-layer at the interface. The Al2O3 composite MgO nano-layer includes an inner MgO layer and an outer Al2O3 layer. The thickness of the inner MgO layer is 10nm~30nm, and the thickness of the outer Al2O3 layer is 10nm~60nm.

[0007] In an optional embodiment, the high modulus magnesium-based composite material has at least one of the following characteristics: Feature 1: The average particle size of the magnesium-aluminum-zinc alloy powder is 50μm~100μm; Feature 2: The average particle size of nano-Al powder is 5nm~50nm; Feature 3: The average particle size of micron Ti particles is 5μm~15μm; Feature 4: In the micron Ti particles coated with nano-Al powder, the nano-Al powder is evenly coated on the surface of the micron Ti particles; Feature 5: The coating thickness of nano-Al powder is 10nm~100nm; Feature 6: The Al element present at the grain boundaries of the matrix accounts for 6wt%~9wt% of the matrix mass; Feature 7: The grains of high modulus magnesium-based composites are mainly in an equiaxed state after recrystallization and have no obvious texture orientation; Feature 8: The average grain size of the high modulus magnesium-based composite material is 1.0μm~2.5μm; Feature 9: The tensile strength of the high modulus magnesium-based composite material is not less than 360 MPa; Feature 10: The yield strength of the high modulus magnesium-based composite material is not less than 250 MPa; Feature 11: The elastic modulus of the high modulus magnesium-based composite material is 60GPa~100GPa.

[0008] In a second aspect, the present invention provides a method for preparing a high modulus magnesium-based composite material as described in the aforementioned embodiment, comprising the following steps: ball milling micronized Ti particles coated with nano-Al powder and magnesium-aluminum-zinc alloy powder, followed by spark plasma sintering, homogenization treatment and hot extrusion.

[0009] In an optional embodiment, the preparation of the micron Ti particles coated with nano-Al powder includes: coating the nano-Al powder on the surface of the micron Ti particles by magnetron sputtering; Among them, the process parameters of magnetron sputtering are sputtering power of 80W~200W, working pressure range of 0.5Pa~2Pa, and sputtering time of 20min~60min.

[0010] In an optional embodiment, the ball milling includes: a ball-to-material ratio of 20:1 to 30:1, a ball milling time of 1 hour to 2 hours, and a ball milling speed of 200 rpm to 250 rpm.

[0011] In an optional embodiment, the spark plasma sintering temperature is 500° C. to 550° C., the spark plasma sintering pressure is 30 MPa to 40 MPa, the spark plasma sintering time is 3 min to 6 min, and air cooling is performed after the spark plasma sintering.

[0012] In an optional embodiment, the temperature of the homogenization treatment is 300° C. to 400° C., and the time of the homogenization treatment is 1 hour to 2 hours.

[0013] In an optional embodiment, the temperature of the hot extrusion is 300° C. to 350° C., and the rate of the hot extrusion is 0.1 mm / s to 0.5 mm / s.

[0014] In a third aspect, the present invention provides an application of a high modulus magnesium-based composite material as described in the aforementioned embodiment, wherein the high modulus magnesium-based composite material is used to prepare 3C product structural parts.

[0015] In a fourth aspect, the present invention provides a 3C product structural part, wherein the raw materials for preparing the 3C product structural part include the high modulus magnesium-based composite material of the aforementioned embodiment.

[0016] The beneficial effects of the present invention include: The high modulus magnesium-based composite material provided by the present invention is prepared from micron Ti particles coated with nano-Al powder and magnesium-aluminum-zinc alloy powder in a specific ratio, wherein the nano-Al powder uniformly coated on the surface of the Ti particles forms an Al2O3 composite MgO nanolayer in situ at the interface. Since the Al2O3 layer is extremely thin, it can present an amorphous or nanocrystalline structure and has a high interfacial energy, which is conducive to enhancing interfacial bonding. Moreover, Al2O3 is a typical high-hardness, high-melting-point oxide with excellent chemical stability in the magnesium matrix, which can effectively hinder the diffusion of elements at the interface and maintain interfacial stability. It is worth noting that there is lattice matching between the Al2O3 layer and the MgO layer, and between the MgO layer and the magnesium matrix, forming an interface with a low-energy semi-coherent structure, reducing stress concentration and significantly improving interfacial bonding. Moreover, the Al2O3 composite MgO layer forms a thermal expansion coefficient gradient transition structure, and the thermal expansion coefficients of Al2O3, MgO and Mg are 8×10 -6 / K, 13.5×10 -6 / K, 25×10 -6 / K, that is, the Al2O3 / MgO / Mg structure can relieve the residual stress caused by the mismatch of thermal expansion coefficient at the interface and improve the interface bonding strength.

[0017] The present invention specifically controls the mass of the nano-Al powder coated on the surface of the Ti particles to 5wt% to 9wt% of the magnesium-aluminum-zinc alloy powder. This is because as the Al content increases, the thickness of the Al2O3 layer generated by the composite material's interface reaction increases. As the thickness increases, the bulk phase gradually dominates, tending to form thermodynamically stable α-Al2O3. Due to its high hardness and poor plasticity, it exhibits typical ceramic particle characteristics and significantly weakens the composite material's interface structure. If the coated nano-Al powder is too little, it cannot promote the interface auto-oxidation reaction to form the Al2O3-composite MgO nanolayer.

[0018] Magnetron sputtering technology uses plasma to bombard an aluminum target, causing Al atoms to sputter in a high-energy state and deposit uniformly on the surface of Ti particles, enabling controlled coating of nanoscale Al coatings. In the initial stages of magnetron sputtering deposition, when Al atoms reach the Ti particle surface, the nucleation and growth behavior of individual Al particles can be directly influenced by regulating parameters such as sputtering power, operating pressure, and deposition distance, forming discrete Al nanoparticles. As deposition continues, these initial nanoparticles contact and merge with each other through surface diffusion, ultimately forming a continuous Al coating. The thickness of the coating is affected by parameters such as sputtering power, operating pressure, and deposition time. Therefore, by adjusting the deposition process parameters, the thickness of the Al coating and the Al powder particle size can be precisely controlled, while achieving a higher coating density and bonding strength.

[0019] Therefore, the use of magnetron sputtering to uniformly coat the surface of micronized Ti particles with an appropriate amount of nano-Al powder as a reinforcement phase to strengthen the magnesium-aluminum-zinc alloy helps improve the mechanical properties of the magnesium-based composite, especially the elastic modulus, and further expands the application potential of magnesium-based composites. In addition, the presence of Al enriched at the grain boundaries of the matrix of the magnesium-based composite helps to inhibit the formation of large-sized oxide inclusions at the interface and improve grain boundary bonding. At the same time, Al hinders the movement of grain boundaries through the solute drag effect, significantly inhibiting grain growth.

[0020] The magnesium-based composite material provided by the present invention has high yield strength, tensile strength and elastic modulus, and can meet the requirements of 3C electronic product structural parts. BRIEF DESCRIPTION OF THE DRAWINGS

[0021] In order to more clearly illustrate the technical solutions of the embodiments of the present invention, the following briefly introduces the drawings required for use in the embodiments. It should be understood that the following drawings only illustrate certain embodiments of the present invention and therefore should not be regarded as limiting the scope. For ordinary technicians in this field, other relevant drawings can be obtained based on these drawings without paying any creative work.

[0022] Figure 1 This is the SEM image of the micron Ti particles coated with nano-Al powder in Example 1; Figure 2 This is the EDS image of the micron Ti particles coated with nano-Al powder in Example 1; Figure 3 This is a longitudinal cross-sectional SEM image of the high modulus magnesium-based composite material in Example 1; Figure 4 TEM image of the microstructure of the Al2O3 composite MgO nanolayer of the high modulus magnesium-based composite material in Example 1; Figure 5 TEM image of the semi-coherent interface structure of Al2O3 / MgO / Mg of the high modulus magnesium-based composite material in Example 1; Figure 6 This is a line scan of the energy spectrum of Al element segregation at the grain boundaries of the high modulus magnesium-based composite material in Example 1; Figure 7 This is a grain size diagram of the high modulus magnesium-based composite material prepared in Example 1. DETAILED DESCRIPTION

[0023] To make the purpose, technical solutions and advantages of the embodiments of the present invention clearer, the technical solutions in the embodiments of the present invention are described clearly and completely below. Where specific conditions are not specified in the embodiments, conventional conditions or conditions recommended by the manufacturer are used. Where the manufacturer of the reagents or instruments is not specified, all are conventional products that can be purchased commercially.

[0024] The high modulus magnesium-based composite material provided by the present invention, its preparation method and application are described in detail below.

[0025] The raw materials for preparing the high-modulus magnesium-based composite material provided by the invention include micron Ti particles coated with nanometer Al powder and magnesium-aluminum-zinc alloy powder.

[0026] In the present invention, the mass of the micronized Ti particles is 10wt% to 15wt% of the magnesium-aluminum-zinc alloy powder, such as 10wt%, 10.5wt%, 11wt%, 11.5wt%, 12wt%, 12.5wt%, 13wt%, 13.5wt%, 14wt%, 14.5wt%, or 15wt%, and may also be other values ​​within the range of 10wt% to 15wt%. If the amount of micronized Ti particles is too small, it is not conducive to improving the strength of the magnesium-based composite material. If the amount of micronized Ti particles is too large, the number of interfaces between the micronized Ti particles and the matrix is ​​too large, which is not conducive to improving the plasticity of the magnesium-based composite material.

[0027] The quality of nanometer Al powder is 5wt%~9wt% of magnesium-aluminum-zinc alloy powder, as 5wt%, 5.5wt%, 6wt%, 6.5wt%, 7wt%, 7.5wt%, 8wt%, 8.5wt% or 9wt% etc., can also be other values ​​within the scope of 5wt%~9wt%.If the amount of nanometer Al powder is too little, can cause the coating area of ​​micron Ti particles to be less, be unfavorable for Al generation auto-oxidation reaction at interface, can not effectively improve the mechanical property situation of interface bonding and magnesium-based composite material.If the amount of nanometer Al powder is too much, be unfavorable for forming uniformly dispersed coating on the surface of micron Ti particles.And, if the content of nanometer Al powder is too much, easily excessive generation auto-oxidation reaction at interface forms thicker Al2O3 layer, be unfavorable for strong interface bonding, also be unfavorable for the grain refinement of magnesium-based composite material and the improvement of mechanical property.

[0028] By controlling the mass of nano-Al powder coated on the Ti particles to 5-9wt% of the magnesium-aluminum-zinc alloy powder, the thickness of the Al2O3 layer generated by the composite's interfacial reaction increases with increasing nano-Al powder mass. With increasing thickness, the bulk phase gradually dominates, favoring the formation of thermodynamically stable α-Al2O3. Due to its inherent hardness and poor plasticity, it exhibits typical ceramic particle characteristics, significantly weakening the composite's interfacial structure. Too little nano-Al powder coating fails to promote the interfacial auto-oxidation reaction to form the Al2O3-composite MgO nanolayer. Therefore, selecting an appropriate amount of nano-Al powder to coat micronized Ti particles reinforced with magnesium-aluminum-zinc alloys can improve the mechanical properties, particularly the elastic modulus, of magnesium-based composites, broadening their application prospects. Furthermore, Al enrichment at the grain boundaries in the matrix of the magnesium-based composite inhibits the formation of large oxide inclusions at the interface and improves grain boundary bonding. Furthermore, Al segregation at the grain boundaries of the magnesium matrix can hinder grain boundary movement, significantly refining the composite's grain size. As mentioned above, by adjusting the mass of the nano-Al powder coated on the surface of the micron Ti particles within the above-mentioned range provided by the present invention, the thickness of the interface composite nanolayer of the magnesium-based composite material can be more accurately designed, the grain size can be refined, and the strength, plasticity, and especially the elastic modulus of the high-modulus magnesium-based composite material can be effectively controlled.

[0029] In the present invention, the magnesium-aluminum-zinc alloy powder contains 1 wt% to 9 wt% Al and 0.5 wt% to 1.5 wt% Zn, with the balance being Mg. The mass of Al contained in the magnesium-aluminum-zinc alloy powder may be 1 wt%, 1.5 wt%, 2 wt%, 2.5 wt%, 3 wt%, 3.5 wt%, 4 wt%, 4.5 wt%, 5 wt%, 5.5 wt%, 6 wt%, 6.5 wt%, 7 wt%, 7.5 wt%, 8 wt%, 8.5 wt%, or 9 wt%, or other values ​​within the range of 1 wt% to 9 wt%. The mass of Zn contained in the magnesium-aluminum-zinc alloy powder may be 0.5 wt%, 0.6 wt%, 0.7 wt%, 0.8 wt%, 0.9 wt%, 1.0 wt%, 1.1 wt%, 1.2 wt%, 1.3 wt%, 1.4 wt%, or 1.5 wt%, or other values ​​within the range of 0.5 wt% to 1.5 wt%.

[0030] In the present invention, the nano-Al in the micronized Ti particles coated with nano-Al powder and the Mg in the matrix form an in-situ Al2O3-composite MgO nanolayer at the interface. The Al2O3-composite MgO nanolayer comprises an inner MgO layer and an outer Al2O3 layer. The inner MgO layer has a thickness of 10 nm to 30 nm (preferably 10 nm to 20 nm), such as 10 nm, 15 nm, 20 nm, 25 nm, or 30 nm, or other values ​​within the range. The outer Al2O3 layer has a thickness of 10 nm to 60 nm (preferably 15 nm to 35 nm), such as 10 nm, 15 nm, 20 nm, 25 nm, 30 nm, 35 nm, 40 nm, 45 nm, 50 nm, 55 nm, or 60 nm, or other values ​​within the range.

[0031] Magnesium-aluminum-zinc alloy powder forms the matrix of the high-modulus magnesium-based composite, with Al segregation at the grain boundaries of the matrix. This Al segregation helps suppress the formation of excessive oxide inclusions at the grain boundaries, thereby improving the interfacial bonding strength of the magnesium-based composite. It also hinders grain boundary movement through the Al solute drag effect, refining the grain size of the magnesium-based composite.

[0032] It should be noted that the Al2O3 composite MgO nano-layer in the present invention can play a role in contributing to the continuous transmission of load at the interface, improves the effect of interface bonding.Wherein, MgO self elastic modulus is 250GPa, significantly higher than magnesium matrix and Ti particles, can significantly improve the elastic modulus of composite material, if the MgO layer is thinner, the improvement effect on elastic modulus is weaker, if the MgO layer thickness is thicker, tissue is relatively loose, there is hole inside, easily produces stress concentration deterioration interface bonding strength when bearing load.Al2O3 self elastic modulus reaches 380GPa, so Al2O3 outer layer can play the effect of further improving composite material elastic modulus, while Al2O3 layer inside is relatively dense, is relatively evenly distributed in thin bands, can significantly hinder the element diffusion between MgO inner layer and magnesium matrix, the thickness of controllable regulation MgO inner layer. If the thickness of the Al2O3 outer layer is too thin, it is not conducive to the improvement of the elastic modulus, and the effect of hindering the diffusion of elements is relatively weak, resulting in the MgO inner layer being too thick and easily causing stress concentration; if the thickness of the Al2O3 outer layer is too thick, since Al2O3 is a ceramic phase with high hardness, the thicker Al2O3 layer has poor plastic deformation ability, which is not conducive to the coordinated plastic deformation of the interface, and the mechanical properties of the composite material are reduced.

[0033] In some optional embodiments, the average particle size of the magnesium-aluminum-zinc alloy powder is 50 μm to 100 μm, such as 50 μm, 55 μm, 60 μm, 65 μm, 70 μm, 75 μm, 80 μm, 85 μm, 90 μm, 95 μm or 100 μm, etc., and can also be other values ​​within the range of 50 μm to 100 μm.

[0034] If the average particle size of the magnesium-aluminum-zinc alloy powder is less than 50 μm, the magnesium alloy powder is relatively active, which is not conducive to ensuring safety during the hot sintering and hot extrusion preparation process; if the average particle size of the magnesium-zinc-zinc alloy powder is greater than 100 μm, it will lead to larger pores between the powders, which is not conducive to obtaining a magnesium-based composite material with dense sintering and fine grain size.

[0035] In some optional embodiments, the average particle size of the nano-Al powder is 5 nm to 50 nm, such as 5 nm, 10 nm, 15 nm, 20 nm, 25 nm, 30 nm, 35 nm, 40 nm, 45 nm or 50 nm, or other values ​​within the range of 5 nm to 50 nm.

[0036] If the average particle size of the nano-Al powder is less than 5nm, the specific surface area is large and it is easy to agglomerate, which is not conducive to uniform coating on the surface of micron Ti particles, and the effect of improving the interface is significantly reduced; if the average particle size of the nano-Al powder is greater than 50nm, the effect of coating micron Ti particles is significantly reduced, and the coarse Al2O3 phase formed by the interface reaction is not conducive to further refinement of the grain size, and the thicker interface layer thickness will also significantly reduce the interface bonding strength.

[0037] In some optional embodiments, the average particle size of the micron Ti particles can be 5 μm to 15 μm, such as 5 μm, 6 μm, 7 μm, 8 μm, 9 μm, 10 μm, 11 μm, 12 μm, 13 μm, 14 μm or 15 μm, or other values ​​within the range of 5 μm to 15 μm.

[0038] If the average particle size of the micron Ti particles is greater than 15 μm, the pores between the powders are too large, which is not conducive to the sintering density of the composite material. If the average particle size of the micron Ti particles is less than 5 μm, they are prone to agglomeration and difficult to disperse evenly.

[0039] In some optional embodiments, in the micron Ti particles coated with nano-Al powder, the nano-Al powder is uniformly coated on the surface of the micron Ti particles, and the coating thickness of the nano-Al powder is 10 nm to 100 nm, such as 10 nm, 30 nm, 50 nm, 80 nm or 100 nm, etc., and can also be other values ​​within the range of 10 nm to 100 nm.

[0040] If the coating thickness of the nano-Al powder is too thin, it is not conducive to the self-reaction to form a dense Al2O3 layer at the interface of the composite material, which has a negative impact on hindering the diffusion of elements at the interface and the controllable regulation of the thickness of the MgO inner layer, and the effect on improving the elastic modulus of the magnesium-based composite material is not significant; if the coating thickness of the nano-Al powder is too thick, it is not conducive to the uniform dispersion of nano-Al on the surface of the micron Ti particles, and a thin strip-shaped Al2O3 layer cannot be formed at the interface of the magnesium-based composite material after the self-oxidation reaction. The thicker Al2O3 layer is not conducive to the coordinated deformation with the magnesium matrix, resulting in a significant decrease in the interface bonding strength.

[0041] In some optional embodiments, the Al element segregated at the grain boundaries of the matrix accounts for 6wt%~9wt% of the matrix mass, such as 6wt%, 6.5wt%, 7wt%, 7.5wt%, 8wt%, 8.5wt% or 9wt%, etc., and can also be other values ​​within the range of 6wt%~9wt%.

[0042] If the Al element is too little at the matrix grain boundary, it cannot significantly inhibit the grain growth; if the Al element is too much at the matrix grain boundary, it will promote the formation of brittle intermetallic compound Mg 17 Al 12 The precipitation of excess Mg 17 Al 12 The phase is easily distributed in a continuous network, which destroys the continuity of the matrix and is not conducive to improving the mechanical properties of the composite material.

[0043] In some optional embodiments, the grains of the high modulus magnesium-based composite material are mainly in an equiaxed state after recrystallization and have no obvious texture orientation.

[0044] In some optional embodiments, the average grain size of the high modulus magnesium-based composite material may be 1.0 μm to 2.5 μm (eg, 1.0 μm, 1.5 μm, 2 μm, or 2.5 μm, etc.).

[0045] In some optional embodiments, the tensile strength of the high modulus magnesium-based composite material is not less than 360 MPa.

[0046] In some optional embodiments, the yield strength of the high modulus magnesium-based composite material is not less than 250 MPa.

[0047] In some optional embodiments, the elastic modulus of the high modulus magnesium-based composite material is 60 GPa to 100 GPa.

[0048] Continuing from the above, the high modulus magnesium-based composite material provided by the present invention is prepared by micron Ti particles coated with nano-Al powder and magnesium-aluminum-zinc alloy powder in a specific ratio, wherein the nano-Al powder uniformly coated on the surface of the Ti particles forms an Al2O3 composite MgO nanolayer in situ at the interface of the composite material. Since the Al2O3 layer is extremely thin, it may present an amorphous or nanocrystalline structure, with a high interfacial energy, which is conducive to enhancing the interfacial bonding strength. Moreover, Al2O3 is a typical high-hardness, high-melting-point oxide with excellent chemical stability in the magnesium matrix, which can effectively hinder the diffusion of elements at the interface and maintain interfacial stability. It is worth noting that there is lattice matching between the Al2O3 layer and the MgO layer, and between the MgO layer and the magnesium matrix, forming a low-energy semi-coherent interface structure, which reduces stress concentration. The Al2O3 composite MgO nanolayer forms a thermal expansion coefficient gradient transition structure, namely Al2O3 / MgO / Mg, which can alleviate the residual stress caused by the thermal expansion coefficient mismatch and improve the interfacial bonding strength.

[0049] The magnesium-based composite material provided by the present invention has high yield strength, tensile strength and elastic modulus. Among them, the high elastic modulus can improve the structural stability of 3C electronic products, prevent large deformation during actual application, enhance durability, and achieve lightweight products.

[0050] Accordingly, the present invention also provides a method for preparing the above-mentioned high modulus magnesium-based composite material, comprising the following steps: ball milling micron Ti particles coated with nano-Al powder and magnesium-aluminum-zinc alloy powder, followed by spark plasma sintering, homogenization treatment and hot extrusion.

[0051] In some optional embodiments, the preparation of the micron Ti particles coated with nano-Al powder may include: coating the nano-Al powder on the surface of the micron Ti particles by magnetron sputtering.

[0052] In situ generation of a ceramic phase in magnesium-based composites through interface design not only achieves a uniform distribution of the reinforcement phase but also significantly improves the elastic modulus of the material. Powder metallurgy offers advantages over traditional casting methods by precisely controlling the extent of interfacial reactions and product content during solid-phase sintering. Surface modification of the reinforcement particles is one of the most effective means of interface manipulation. Compared to the coating inhomogeneity associated with electric explosion deposition and the solution contamination issues associated with electroplating, magnetron sputtering offers significant advantages. Its vacuum environment prevents oxidation, and its low temperature prevents thermal damage to the Ti particles. Magnetron sputtering utilizes Ar plasma to bombard an Al target, depositing sputtered Al atoms and nanoclusters onto the Ti particle surface to form a controllable coating. Al particle size is controlled by the sputtering power (high sputtering power leads to agglomeration of Al nanoparticles) and the operating pressure (high pressure increases collisions and reduces particle size), while sputtering time directly influences the coating thickness. This precise control of the Al layer size and thickness optimizes the thermodynamic driving force and diffusion kinetics of subsequent interfacial reactions, effectively improving the composite's strength, toughness, and elastic modulus. The process parameters of magnetron sputtering are sputtering power of 80W~200W, working pressure of 0.5Pa~2Pa, and sputtering time of 20min~60min.

[0053] The sputtering power may be 80W, 100W, 120W, 140W, 160W, 180W or 200W, or other values ​​within the range of 80W to 200W.

[0054] During magnetron sputtering deposition, sputtering power significantly affects the particle size of Al particles. Increasing the sputtering power can significantly increase the sputtering yield of Al atoms and significantly improve the deposition rate. Higher sputtering power significantly promotes the surface migration of Al particles and grain fusion, resulting in the formation of coarse Al particles. Lower power, on the other hand, is conducive to obtaining small and dispersed nanoscale Al particles, but may result in loose bonding between particles.

[0055] The working pressure may be 0.5Pa, 1Pa, 1.5Pa, 2Pa, etc., or other values ​​within the range of 0.5Pa~2Pa.

[0056] During magnetron sputtering, operating pressure significantly affects the particle size of deposited Al. High pressure slows the deposition rate due to particle scattering. When the operating pressure is too high, frequent collisions between sputtered particles and gas molecules reduce the kinetic energy of the Al atoms, resulting in insufficient surface migration and a loose structure with coarse particles. However, too low a pressure keeps the Al atoms at a high energy level, promoting surface diffusion and forming fine nanoparticles.

[0057] The sputtering time may be 20 min, 30 min, 40 min, 50 min or 60 min, or other values ​​within the range of 20 min to 60 min.

[0058] During magnetron sputtering deposition, sputtering time plays a key role in regulating the thickness of the Al coating. As the sputtering time increases, the initially deposited Al nanoparticles undergo continuous atomic deposition and surface diffusion. The particles continuously merge and grow through Ostwald ripening and grain boundary migration, ultimately forming a stable grain structure. While extended sputtering time can significantly increase the thickness of the Al layer, excessive deposition time can lead to the formation of coarse columnar crystals and excessively thick interface layers, causing significant stress accumulation. Therefore, controlling the sputtering time within an appropriate range is crucial to achieve an Al coating of ideal thickness, ensuring both good density and interfacial bonding strength.

[0059] It should be noted that if nano-Al powder and micron-Ti particles are simply mechanically mixed, rather than being prepared in a form where the nano-Al powder coats the micron-Ti particles, Ti-Al intermetallic compounds will form after mechanical ball milling, weakening the strengthening effect of the Ti particles themselves. Furthermore, during the subsequent preparation process, Al element segregation at the matrix grain boundaries will not occur, increasing the grain boundary bonding strength and significantly reducing the effect of weakening the grain size. The magnetron sputtering method of the present invention can evenly coat the surface of the micron-Ti particles with nano-Al powder, facilitating the formation of a thin ribbon-like Al2O3 layer and a MgO layer of suitable thickness in the composite material.

[0060] In some optional embodiments, the ball milling includes: a ball-to-material ratio of 20:1 to 30:1, a ball milling time of 1 hour to 2 hours, and a ball milling speed of 200 rpm to 250 rpm.

[0061] Among them, in terms of mass ratio, the ball-to-material ratio can be 20:1, 25:1 or 30:1, etc., or other values ​​within the range of 20:1 to 30:1.

[0062] The ball milling time can be 1 h, 1.5 h or 2 h, etc., or other values ​​within the range of 1 h to 2 h.

[0063] The ball milling speed may be 200 rpm, 210 rpm, 220 rpm, 230 rpm, 240 rpm or 250 rpm, or other values ​​within the range of 200 rpm to 250 rpm.

[0064] The above-mentioned ball milling speed will directly affect the thickness of the Al2O3 composite MgO thin layer. If the ball milling speed is too low, it is not conducive to the formation of thin strip-like Al2O3 phase, and the interface is mainly composed of MgO layer; if the ball milling speed is too high, it is easy to destroy the structure of the composite material Al2O3 phase composite MgO layer, and the structural advantages of the composite pattern cannot be fully utilized.

[0065] In some optional embodiments, the spark plasma sintering temperature is 500° C. to 550° C., the spark plasma sintering pressure is 30 MPa to 40 MPa, the spark plasma sintering time is 3 min to 6 min, and air cooling is performed after the spark plasma sintering.

[0066] The pressure of spark plasma sintering may be 30 MPa, 32 MPa, 35 MPa, 38 MPa, or 40 MPa, or other values ​​within the range of 30 MPa to 40 MPa.

[0067] The spark plasma sintering time may be 3 min, 3.5 min, 4 min, 4.5 min, 5 min, 5.5 min or 6 min, or other values ​​within the range of 3 min to 6 min.

[0068] The spark plasma sintering time mentioned above will directly affect the thickness of the Al2O3 composite MgO thin layer. If the spark plasma sintering time is too short, it will be unfavorable for the formation of the nano-scale Al2O3 thin strip layer; if the spark plasma sintering time is too long, it will easily cause the thickness of the Al2O3 composite MgO layer to exceed 1μm, significantly deteriorating the interface bonding strength.

[0069] In some optional embodiments, the temperature of the homogenization treatment is 300° C. to 400° C., and the time of the homogenization treatment is 1 hour to 2 hours.

[0070] The temperature of the homogenization treatment may be 300° C., 320° C., 350° C., 380° C., or 400° C., or other values ​​within the range of 300° C. to 400° C.

[0071] The homogenization treatment time can be 1 hour, 1.5 hours or 2 hours, etc., or other values ​​within the range of 1 hour to 2 hours.

[0072] In some optional embodiments, the temperature of the hot extrusion is 300° C. to 350° C., and the rate of the hot extrusion is 0.1 mm / s to 0.5 mm / s.

[0073] The temperature of hot extrusion may be 300°C, 310°C, 320°C, 330°C, 340°C or 350°C, or other values ​​within the range of 300°C to 350°C.

[0074] The hot extrusion rate may be 0.1 mm / s, 0.2 mm / s, 0.3 mm / s, 0.4 mm / s or 0.5 mm / s, or other values ​​within the range of 0.1 mm / s to 0.5 mm / s.

[0075] The above hot extrusion rate will directly affect the shape of Al2O3 and the density of MgO. If the hot extrusion rate is too slow, Al will diffuse into the Mg matrix and form MgO at the interface. 17 Al 12 Brittle phase replaces part of the Al2O3 / MgO layer, causing excessive growth of the MgO layer and reducing the interface bonding strength. 17 Al 12 The brittle phase can easily become a crack propagation path, causing the mechanical properties of the composite material to deteriorate. If the hot extrusion rate is too fast, the plastic deformation is severe, and the local temperature rise is high, it may lead to: abnormal thickening of the Al2O3 layer, because the high temperature promotes the diffusion of Al, which reacts with residual oxygen to generate more Al2O3, but the distribution is uneven. At the same time, rapid deformation causes stress concentration at the interface between the Mg matrix and Ti particles, and the MgO layer may break. Ultimately, the interface cracks and unbonded areas become sources of stress concentration, leading to early fracture.

[0076] As mentioned above, the preparation method provided by the present invention is simple to operate, can effectively obtain an Al2O3 composite MgO nanolayer with controllable thickness, and is conducive to obtaining a magnesium-based composite material with excellent strength, plasticity and elastic modulus.

[0077] In addition, the present invention also provides an application of the above-mentioned high modulus magnesium-based composite material. For example, the high modulus magnesium-based composite material can be used to prepare 3C product structural parts.

[0078] Correspondingly, the present invention also provides a 3C product structural part, the raw materials for preparing the 3C product structural part include the above-mentioned high modulus magnesium-based composite material.

[0079] Illustratively, the 3C product structural component may be a shell of the 3C product.

[0080] The features and performance of the present invention are further described in detail below with reference to the embodiments.

[0081] Example 1 This embodiment provides a high modulus magnesium-based composite material, the preparation method of which includes: S1: Preparation of micronized Ti particles coated with nano-Al powder.

[0082] The magnetron sputtering method was used to obtain micron Ti particles coated with nano-Al powder. The process parameters were sputtering power of 80 W, working pressure of 0.5 Pa, and sputtering time of 20 min.

[0083] The average particle size of the nano-Al powder is 5 nm, and the mass of the nano-Al powder is 5 wt % of the magnesium-aluminum-zinc alloy powder.

[0084] The SEM image of the nano-Al coated micron Ti particles is as follows: Figure 1 As shown by Figure 1 It can be seen that the nano-Al powder is successfully coated on the surface of the micron Ti particles. The coating thickness of the nano-Al powder is 10nm. The EDS image of the nano-Al coated micron Ti particles is as follows Figure 2 As shown by Figure 2 It can be seen that the Al element distribution on the surface of micron Ti particles is relatively uniform, proving the effectiveness of the magnetron sputtering method.

[0085] S2: ball milling the micronized Ti particles coated with nano-Al powder and magnesium-aluminum-zinc alloy powder.

[0086] The magnesium-aluminum-zinc alloy powder contains 9wt% Al and 1wt% Zn, with the remainder being Mg; the average particle size of the magnesium-aluminum-zinc alloy powder is 80μm, the average particle size of the micron Ti particles is 10μm, and the mass of the micron Ti particles accounts for 10wt% of the magnesium-aluminum-zinc alloy powder.

[0087] The ball-to-material ratio was 25:1, the ball milling time was 1.5 h, and the ball milling speed was 220 rpm.

[0088] S3: The material obtained by ball milling is subjected to spark plasma sintering.

[0089] The spark plasma sintering temperature is 500° C., the spark plasma sintering pressure is 35 MPa, the spark plasma sintering time is 5 min, and the spark plasma sintering is followed by air cooling.

[0090] S4: homogenizing the material after spark plasma sintering.

[0091] The temperature of the homogenization treatment is 350° C., and the time of the homogenization treatment is 1.5 h.

[0092] S5: hot extruding the homogenized material.

[0093] The hot extrusion temperature was 350° C., and the hot extrusion rate was 0.1 mm / s.

[0094] The longitudinal section SEM image of the high modulus magnesium-based composite material prepared in this embodiment is as follows: Figure 3 As shown by Figure 3 It can be seen that the Ti particles are evenly distributed inside the composite material, and a composite ceramic layer is formed at the interface. The combination is relatively dense, and no defects such as voids are found at the interface. The TEM image of the nanoscale Al2O3 composite MgO nanolayer in the high modulus magnesium-based composite material is as follows: Figure 4 As shown by Figure 4It can be seen that a composite layer is formed at the interface, and the outer layer is a nano-thin ribbon. The thickness of the MgO inner layer is 30nm, and the thickness of the Al2O3 outer layer is 10nm. The TEM image of the Mg / Al2O3 / MgO semi-coherent structure is shown in Figure 2. Figure 5 As shown by Figure 5 It can be seen that the (102) crystal plane spacing of the Mg phase is 0.19nm, the (113) crystal plane spacing of the Al2O3 phase is 0.20nm, and the (222) crystal plane spacing of the MgO phase is 0.21nm. The Al2O3 / Mg interface presents a semi-coherent orientation relationship, and the Al2O3 / MgO interface also presents a semi-coherent orientation relationship, with a mismatch of about 5%. The segregation energy spectrum line scan of the Al element at the grain boundary of the matrix in this high modulus magnesium-based composite material is shown in the figure. Figure 6 As shown by Figure 6 It can be seen that the Al element is obviously segregated at the matrix grain boundaries, and the Al element at the matrix grain boundaries accounts for 6wt% of the matrix mass. The grain size diagram of the high modulus magnesium-based composite material is shown in Figure 2. Figure 7 As shown by Figure 7 It can be seen that the grains are mainly equiaxed after recrystallization, and the grain size is relatively small.

[0095] Example 2 This embodiment provides a high modulus magnesium-based composite material, the preparation method of which includes: S1: Preparation of micronized Ti particles coated with nano-Al powder.

[0096] The magnetron sputtering method was used to obtain micron Ti particles coated with nano-Al powder. The process parameters were sputtering power of 140 W, working pressure of 1.25 Pa, and sputtering time of 40 min.

[0097] The average particle size of the nano-Al powder is 30 nm, the mass of the nano-Al powder is 7 wt % of the magnesium-aluminum-zinc alloy powder, and the coating thickness of the nano-Al powder is 60 nm.

[0098] S2: ball milling the micronized Ti particles coated with nano-Al powder and magnesium-aluminum-zinc alloy powder.

[0099] Among them, the magnesium-aluminum-zinc alloy powder contains 7wt% Al and 0.5wt% Zn, with the balance being Mg; the average particle size of the magnesium-aluminum-zinc alloy powder is 50μm, the average particle size of the micron Ti particles is 5μm, and the mass of the micron Ti particles accounts for 12wt% of the magnesium-aluminum-zinc alloy powder.

[0100] The ball-to-material ratio was 20:1, the ball milling time was 2 h, and the ball milling speed was 200 rpm.

[0101] S3: The material obtained by ball milling is subjected to spark plasma sintering.

[0102] The spark plasma sintering temperature is 500° C., the spark plasma sintering pressure is 30 MPa, the spark plasma sintering time is 6 min, and the spark plasma sintering is followed by air cooling.

[0103] S4: homogenizing the material after spark plasma sintering.

[0104] The temperature of the homogenization treatment is 300°C, and the time of the homogenization treatment is 2 hours.

[0105] S5: hot extruding the homogenized material.

[0106] The temperature of hot extrusion is 300°C, and the rate of hot extrusion is 0.1 mm / s.

[0107] In this embodiment, the thickness of the MgO inner layer is 21 nm, and the thickness of the Al2O3 outer layer is 28 nm. The Al element present at the grain boundaries of the matrix accounts for 7.5 wt% of the matrix mass.

[0108] Example 3 This embodiment provides a high modulus magnesium-based composite material, the preparation method of which includes: S1: Preparation of micronized Ti particles coated with nano-Al powder.

[0109] The magnetron sputtering method was used to obtain micron Ti particles coated with nano-Al powder. The process parameters were sputtering power of 200 W, working pressure of 2 Pa, and sputtering time of 60 min.

[0110] The average particle size of the nano-Al powder is 50 nm, and the mass of the nano-Al powder is 9 wt % of the magnesium-aluminum-zinc alloy powder. The coating thickness of the nano-Al powder is 100 nm.

[0111] S2: ball milling the micronized Ti particles coated with nano-Al powder and magnesium-aluminum-zinc alloy powder.

[0112] The magnesium-aluminum-zinc alloy powder contains 1 wt% Al and 1.0 wt% Zn, with the remainder being Mg. The average particle size of the magnesium-aluminum-zinc alloy powder is 100 μm, the average particle size of the micronized Ti particles is 15 μm, and the mass of the micronized Ti particles accounts for 15 wt% of the magnesium-aluminum-zinc alloy powder.

[0113] The ball-to-material ratio was 30:1, the ball milling time was 1 h, and the ball milling speed was 250 rpm.

[0114] S3: The material obtained by ball milling is subjected to spark plasma sintering.

[0115] The spark plasma sintering temperature is 550° C., the spark plasma sintering pressure is 40 MPa, the spark plasma sintering time is 3 min, and air cooling is performed after the spark plasma sintering.

[0116] S4: homogenizing the material after spark plasma sintering.

[0117] The temperature of the homogenization treatment is 400° C., and the time of the homogenization treatment is 1 h.

[0118] S5: hot extruding the homogenized material.

[0119] The hot extrusion temperature was 350° C., and the hot extrusion rate was 0.5 mm / s.

[0120] In this embodiment, the thickness of the MgO inner layer is 10 nm, and the thickness of the Al2O3 outer layer is 50 nm. The Al element present at the grain boundaries of the matrix accounts for 9 wt% of the matrix mass.

[0121] Comparative Example 1 The difference between this comparative example and Example 1 is that the mass of the micronized Ti particles is 20 wt % of the magnesium-aluminum-zinc alloy powder.

[0122] Comparative Example 2 The difference between this comparative example and Example 1 is that the average particle size of the micron Ti particles is 20 μm.

[0123] Comparative Example 3 The difference between this comparative example and Example 1 is that the average particle size of the magnesium-aluminum-zinc alloy powder is 20 μm.

[0124] Comparative Example 4 The difference between this comparative example and Example 1 is that the average particle size of the magnesium-aluminum-zinc alloy powder is 120 μm.

[0125] Comparative Example 5 The difference between this comparative example and Example 1 is that the power of the magnetron sputtering is 250W.

[0126] Comparative Example 6 The difference between this comparative example and Example 1 is that the power of the magnetron sputtering is 50W.

[0127] Comparative Example 7 The difference between this comparative example and Example 1 is that the operating voltage of the magnetron sputtering is 5 Pa.

[0128] Comparative Example 8 The difference between this comparative example and Example 1 is that the operating voltage of the magnetron sputtering is 0.1 Pa.

[0129] Comparative Example 9 The difference between this comparative example and Example 1 is that the deposition time of magnetron sputtering is 2 hours.

[0130] Comparative Example 10 The difference between this comparative example and Example 1 is that the deposition time of magnetron sputtering is 10 minutes.

[0131] Comparative Example 11 The difference between this comparative example and Example 1 is that the micron Ti particles coated with nano-Al powder are directly replaced with micron Ti particles.

[0132] Comparative Example 12 The difference between this comparative example and Example 1 is that the micron Ti particles coated with nano-Al powder are directly replaced by a mixture obtained by mechanically mixing micron Ti particles and nano-Al powder.

[0133] Test example Some of the results of Examples 1 to 3 and Comparative Examples 1 to 12 were statistically compared, and the results are shown in Table 1. The average grain size, yield strength, tensile strength, and elastic modulus of the high modulus magnesium-based composite materials prepared in Examples 1 to 3 and Comparative Examples 1 to 12 were compared, and the results are shown in Table 2. The average grain size was tested in accordance with GB / T 38532-2020 "Determination of the average grain size by electron backscatter diffraction using microbeam analysis," the yield strength and tensile strength were tested in accordance with GB / T 228.1-2010 "Tension test of metallic materials - Part 1: Test method at room temperature," and the elastic modulus was tested in accordance with GB / T 38897-2020 "Ultrasonic measurement of elastic modulus and Poisson's ratio for non-destructive testing."

[0134] Table 1 Comparison of microstructures of magnesium-based composites

[0135] Table 2 Test results of mechanical properties

[0136] It can be seen from Table 2 that the high modulus magnesium-based composite materials obtained in Examples 1 to 3 of the present invention have higher yield strength, tensile strength and elastic modulus than the magnesium-based composite materials obtained in Comparative Examples 1 to 12.

[0137] Comparing Example 1 with Comparative Examples 1-12 demonstrates that a thin, ribbon-like Al2O3 nanolayer of appropriate thickness effectively regulates the thickness of the inner MgO layer. A suitably thick Al2O3-composite MgO layer facilitates continuous load transfer at the interface, synergistically improving the strength and toughness of the composite material. Furthermore, the high-modulus Al2O3 phase, the high-mass fraction of Ti particles, and the interfacial strengthening effect ultimately contribute to an elastic modulus exceeding 60 GPa for the composite material.

[0138] In summary, the high modulus magnesium-based composite material provided by the present invention has high yield strength, tensile strength and high elastic modulus, and can meet the requirements of 3C electronic product structural parts.

[0139] The foregoing description is merely a preferred embodiment of the present invention and is not intended to limit the present invention. Those skilled in the art will readily appreciate that various modifications and variations of the present invention are possible. Any modifications, equivalent substitutions, or improvements made within the spirit and principles of the present invention are intended to be within the scope of protection of the present invention.

Claims

1. A high modulus magnesium-based composite material, characterized in that: The raw materials for preparing the high modulus magnesium-based composite material include micron Ti particles coated with nano-Al powder and magnesium-aluminum-zinc alloy powder; The nano-Al powder-coated micron Ti particles are obtained by coating micron Ti particles with nano-Al powder, wherein the mass of the micron Ti particles is 10wt% to 15wt% of the magnesium-aluminum-zinc alloy powder, and the mass of the nano-Al powder is 5wt% to 9wt% of the magnesium-aluminum-zinc alloy powder; the magnesium-aluminum-zinc alloy powder contains 1wt% to 9wt% Al and 0.5wt% to 1.5wt% Zn, with the balance being Mg; The magnesium-aluminum-zinc alloy powder forms the matrix of the high modulus magnesium-based composite material; Al elements are segregated at the grain boundaries of the matrix; The nano-Al in the micron Ti particles coated with the nano-Al powder and the Mg in the matrix form an Al2O3 composite MgO nano-layer in situ at the interface. The Al2O3 composite MgO nano-layer includes an inner MgO layer and an outer Al2O3 layer. The thickness of the inner MgO layer is 10nm~30nm, and the thickness of the Al2O3 outer layer is 10nm~60nm.

2. The high modulus magnesium-based composite material according to claim 1, characterized in that The high modulus magnesium-based composite material has at least one of the following characteristics: Feature 1: The average particle size of the magnesium-aluminum-zinc alloy powder is 50 μm to 100 μm; Feature 2: The average particle size of the nano-Al powder is 5nm~50nm; Feature 3: The average particle size of the micron Ti particles is 5μm~15μm; Feature 4: In the micron Ti particles coated with nano-Al powder, the nano-Al powder is evenly coated on the surface of the micron Ti particles; Feature 5: The coating thickness of the nano-Al powder is 10nm~100nm; Feature 6: The Al element present at the grain boundaries of the matrix accounts for 6wt% to 9wt% of the matrix mass; Feature 7: The grains of the high modulus magnesium-based composite material are mainly in an equiaxed state after recrystallization and have no obvious texture orientation; Feature 8: The average grain size of the high modulus magnesium-based composite material is 1.0 μm to 2.5 μm; Feature 9: The tensile strength of the high modulus magnesium-based composite material is not less than 360 MPa; Feature 10: The yield strength of the high modulus magnesium-based composite material is not less than 250 MPa; Feature 11: The elastic modulus of the high modulus magnesium-based composite material is 60 GPa~100 GPa.

3. A method for preparing a high modulus magnesium-based composite material according to claim 1 or 2, characterized in that: The following steps are involved: The micronized Ti particles coated with nano-Al powder are mixed with magnesium-aluminum-zinc alloy powder by ball milling, and then spark plasma sintering, homogenization treatment and hot extrusion are performed.

4. The preparation method according to claim 3, characterized in that The preparation of the nano-Al powder-coated micron Ti particles comprises: coating the nano-Al powder on the surface of the micron Ti particles by magnetron sputtering; wherein the process parameters of the magnetron sputtering are sputtering power of 80W to 200W, working pressure range of 0.5Pa to 2Pa, and sputtering time of 20min to 60min.

5. The preparation method according to claim 3, characterized in that Ball mill includes: balls The material ratio is 20:1 to 30:1, the ball milling time is 1h~2h, and the ball milling speed is 200rpm~250rpm.

6. The preparation method according to claim 3, characterized in that The temperature of spark plasma sintering is 500°C~550°C, the pressure of spark plasma sintering is 30MPa~40MPa, the time of spark plasma sintering is 3min~6min, and air cooling is performed after spark plasma sintering.

7. The preparation method according to claim 3, characterized in that The temperature of the homogenization treatment is 300°C~400°C, and the time of the homogenization treatment is 1h~2h.

8. The preparation method according to claim 3, characterized in that The temperature of hot extrusion is 300℃~350℃, and the rate of hot extrusion is 0.1mm / s~0.5mm / s.

9. Use of the high modulus magnesium-based composite material according to claim 1 or 2, characterized in that: The high modulus magnesium-based composite material is used to prepare 3C product structural parts.

10. A 3C product structural part, characterized in that: The raw materials for preparing the 3C product structural parts include the high modulus magnesium-based composite material according to claim 1 or 2.

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