A method for preparing a horizontal continuous casting copper-aluminum composite material

Abstract

This invention belongs to the field of metal matrix composite technology, specifically relating to a method for preparing a horizontally continuously cast copper-aluminum composite material. The preparation method includes the following steps: continuously forming a copper plate; controlling the temperature of the copper plate to be no lower than 900°C between the output copper plate and the aluminum melt inlet; using an inert gas, cold-spraying nano-aluminum nitride and micron-sized copper composite particles onto the copper plate strip; then cold-spraying nano-titanium and micron-sized aluminum composite particles to form a composite coating on the copper plate; the aluminum melt flows out onto the composite coating, and after cooling, the aluminum melt solidifies on the copper plate and forms a metallurgical bond with the copper plate; rolling is then performed to obtain the copper-aluminum composite material. The preparation method of this invention can suppress the formation of brittle phases at the copper-aluminum composite interface and improve the interface stability during processing.

Description

Technical Field

[0001] This invention belongs to the field of metal matrix composite materials technology, specifically relating to a method for preparing a horizontally continuously cast copper-aluminum composite material. Background Technology

[0002] Copper-aluminum bimetallic composite plates combine the advantages of both copper and aluminum, exhibiting high electrical conductivity, good corrosion resistance, low density, and ease of bonding. They can replace pure copper plates in various fields such as electronics and communications, petrochemicals, transportation, decorative building materials, aerospace, and national defense. Conventional methods for preparing copper-aluminum bimetallic composite plates include explosive bonding, rolling bonding, extrusion-rolling bonding, and casting-rolling bonding. However, these methods all suffer from drawbacks such as long process flows, high production costs, significant environmental impact, and low yield. Horizontal continuous casting has been widely used in the preparation of copper-clad aluminum bimetallic composite materials, offering advantages such as a short process flow, high production efficiency, and metallurgical bonding at the composite interface.

[0003] However, horizontal continuous casting still presents challenges in controlling the casting temperature and time when preparing composite plates. At low casting temperatures, the molten aluminum freezes in the crystallizer, preventing the copper-aluminum composite slab from forming. At high temperatures, the composite reaction time is too long, resulting in a large as-cast interface layer on the copper-aluminum composite slab, severely impacting its processing and forming performance. Furthermore, the copper-aluminum composite slab has an asymmetrical layered structure. Due to the differences in heat transfer properties between copper and aluminum, the solidification process of the composite slab is asymmetrical, leading to asymmetrical heat transfer and solidification behavior during continuous casting. This is especially problematic when the width is large, making precise control of the solidification behavior and interface layer size extremely difficult under these asymmetrical solidification characteristics. In contrast, copper-clad aluminum involves pouring molten aluminum into a copper tube, a structure different from that of copper-aluminum composite plates. Furthermore, due to the significant difference in deformation properties between copper and aluminum, the asymmetric layered copper-aluminum composite sheet exhibits asymmetric deformation characteristics. During deformation processing, this easily leads to a large difference in deformation rates between copper and aluminum, causing the copper-aluminum composite sheet to bend towards the copper side. This difference in deformation rates generates significant stress at the composite interface. When the stress at the interface exceeds the interfacial bonding strength, the copper-aluminum composite sheet will fail due to cracking, delamination, and other failure behaviors. Further in-depth research is needed on how to apply horizontal continuous casting to the preparation of copper-aluminum composite sheets to overcome the problems arising from solidification and bonding. Summary of the Invention

[0004] To address the problem of insufficient interfacial bonding strength in existing copper-aluminum bimetallic composite plates, which easily leads to cracking and delamination during rolling and other processing, this invention mainly provides a horizontal continuous casting method that can suppress the formation of brittle phases at the copper-aluminum composite interface. The technical solution is as follows: A method for preparing a horizontally continuously cast copper-aluminum composite material includes the following steps: continuously forming a copper plate; controlling the temperature of the copper plate to be no less than 900°C between the output copper plate and the aluminum melt inlet; using an inert gas, cold spraying nano-aluminum nitride and micron-sized copper composite particles onto the copper plate strip; then cold spraying nano-titanium and micron-sized aluminum composite particles to form a composite coating on the copper plate; the aluminum melt flows out onto the composite coating, and after cooling, the aluminum melt solidifies on the copper plate and forms a metallurgical bond with the copper plate; rolling is then performed to obtain the copper-aluminum composite material.

[0005] Furthermore, the temperature is 900~1050℃.

[0006] Furthermore, the mass ratio of the nano-aluminum nitride to the micron-sized copper is 1:2~6; the mass ratio of the nano-titanium to the micron-sized aluminum is 1:1~2.

[0007] Furthermore, the main gas pressure of the cold-sprayed aluminum nitride and micron copper composite particles is 1~2MPa, the main gas heating temperature is 500~700℃, the spraying distance is 10~20mm, the relative moving speed of the substrate is 100~250mm / min, and the powder feeding speed is 4~10g / min.

[0008] Furthermore, the main gas pressure of the cold-sprayed nano-titanium and micron-sized aluminum composite particles is 0.8~1.5MPa, the main gas heating temperature is 300~400℃, the spraying distance is 15~25mm, the relative moving speed of the substrate is 100~250mm / min, and the powder feeding speed is 2~5g / min.

[0009] Furthermore, the nano-aluminum nitride and micron-sized copper composite particles are prepared by ball milling and mixing, respectively.

[0010] Furthermore, the ball milling mixing step includes: mixing the raw materials at a ball-to-material ratio of 5 to 10:1, and ball milling the mixture at a speed of 200 to 300 r / min for 1.5 to 3 hours under a protective atmosphere.

[0011] Furthermore, this includes the following steps: a. The copper is melted, and the molten copper is poured into a mold, where it is cast into a copper plate under the action of a traction device; b. Between the copper liquid outlet and the aluminum liquid inlet, inert gas is used to cold spray nano-aluminum nitride and micron-sized copper composite particles onto the copper plate; then nano-titanium and micron-sized aluminum composite particles are cold sprayed, and the excess gas is discharged to form a composite coating. c. The molten aluminum flows onto the composite coating, and through the crystallizer and cooling water, the molten aluminum solidifies and forms a metallurgical bond with the copper plate to obtain the billet; d. Roll the billet to the target thickness at 20~350℃ with a deformation of 35~80% per pass.

[0012] Furthermore, the time interval between the cold spraying of nano-titanium and micron-sized aluminum composite particles and the injection into the molten aluminum is 3 to 10 seconds.

[0013] Furthermore, the temperature of the molten aluminum is 780~850℃. By adopting the above scheme, the method of the present invention has the following advantages: 1. The method of the present invention can suppress the diffusion between copper and aluminum atoms at the copper-aluminum composite interface, suppress the formation and growth of brittle intermetallic compounds such as CuAl2 that have a significant impact on the interfacial bonding strength, reduce the thickness of the brittle layer, and thus improve the performance of the interface.

[0014] 2. The method of the present invention involves cold spraying nano-aluminum nitride and micron-sized copper composite particles onto a copper strip. The high temperature of the copper strip causes the aluminum nitride and the secondary sprayed titanium to form a titanium nitride barrier layer, reducing the penetration and diffusion of aluminum into the copper strip, thereby reducing the formation of brittle phases.

[0015] 3. In the method of the present invention, nanomaterials are combined with micromaterials to reduce the agglomeration of nanomaterials. Through the use of micromaterials with large particle size, nano-aluminum nitride is evenly distributed on the surface of the metal plate, thereby uniformly combining with nano-titanium.

[0016] 4. This invention controls the thickness of the titanium nitride barrier layer by controlling the content of aluminum nitride and titanium, so that the barrier layer can form a good barrier effect and also has a low thickness. In subsequent processing, it can be successfully fragmented to form dispersed particles, so that the copper and aluminum on both sides can form a further metallurgical bond.

[0017] 5. In this invention, the nanomaterials used for the reaction are respectively wrapped around copper particles and aluminum particles. While utilizing the micron-sized particle size, the reactants are directly combined and reacted, which protects the copper below and avoids direct contact between titanium and copper, thus reducing the generation of side reactions.

[0018] 6. In the method of this invention, combining micron-sized particles with nano-sized particles facilitates the filling of gaps between particles by the nano-sized particles, reduces coating defects, increases deposition efficiency, and reduces coating thickness. 7. The method of the present invention only requires adding a cold spraying step to the existing horizontal continuous casting process to achieve the preparation of copper-aluminum bimetallic composite materials with high bonding strength and good processing performance. The improvement cost and difficulty of equipment and process are low, and it can be quickly promoted to industrial applications. Attached Figure Description

[0019] Figure 1 These are comparison diagrams of the copper layer shapes in the copper-aluminum composite materials of various embodiments; Detailed Implementation

[0020] The technical solutions in the embodiments of the present invention will be clearly and completely described below. 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.

[0021] Example 1: (1) The copper is melted and the molten copper liquid enters the mold. Under the casting action of the traction device at 150 mm / min, a copper plate with a width of 150 mm and a thickness of 3 mm is formed. (2) Under an argon atmosphere, nano-aluminum nitride and micron-sized copper were mixed at a mass ratio of 1:4 and a ball-to-material ratio of 8:1. The mixture was ball-milled at a speed of 250 r / min for 2.5 h to obtain composite particles of aluminum nitride and micron-sized copper. Nano-titanium and micron-sized aluminum were mixed at a mass ratio of 1:1.5 and ball-milled according to the above method to obtain composite particles of nano-titanium and micron-sized aluminum. (3) At a position of 950°C between the copper liquid outlet and the aluminum liquid inlet, a first cold spray nozzle is set up. Argon gas is used, with the main gas pressure set to 1.5MPa, the main gas heating temperature set to 600°C, the spraying distance set to 15mm, and the powder feeding speed set to 7g / min. Nano aluminum nitride and micro copper composite particles are cold sprayed onto the copper plate through the first cold spray nozzle. A second cold spray nozzle is set up between the first cold spray nozzle and the aluminum liquid inlet. After the nano aluminum nitride and micro copper composite particles are sprayed, nano titanium and micro aluminum composite particles are cold sprayed through the second cold spray nozzle with the main gas pressure set to 1.2MPa, the main gas heating temperature set to 350°C, the spraying distance set to 20mm, and the powder feeding speed set to 3g / min. The residual gas is then discharged to form a composite coating. (4) After the cold spraying is completed, the copper plate continues to move forward; after an interval of 3~10s, the aluminum liquid at 800℃ flows onto the composite coating on the surface of the copper plate. Through the crystallizer and cooling water, the aluminum liquid solidifies and forms a metallurgical bond with the copper plate to obtain a 12mm thick billet. (5) The billet is rolled in two passes at room temperature with a deformation of 50%, and then rolled with a small deformation to form a 2mm thick plate.

[0022] Example 2: The difference from Example 1 is as follows: (2) Under an argon atmosphere, nano-aluminum nitride and micron-sized copper were mixed at a mass ratio of 1:2 and a ball-to-material ratio of 8:1. The mixture was ball-milled at a speed of 250 r / min for 2.5 h to obtain composite particles of aluminum nitride and micron-sized copper. Nano-titanium and micron-sized aluminum were mixed at a mass ratio of 1:1.5 and ball-milled according to the above method to obtain composite particles of nano-titanium and micron-sized aluminum.

[0023] Example 3: The difference from Example 1 is as follows: (2) Under an argon atmosphere, nano-aluminum nitride and micron-sized copper were mixed at a mass ratio of 1:6 and a ball-to-material ratio of 8:1. The mixture was ball-milled at a speed of 250 r / min for 2.5 h to obtain composite particles of aluminum nitride and micron-sized copper. Nano-titanium and micron-sized aluminum were mixed at a mass ratio of 1:1.5 and ball-milled according to the above method to obtain composite particles of nano-titanium and micron-sized aluminum.

[0024] Example 4: The difference from Example 1 is as follows: (2) Under an argon atmosphere, nano-aluminum nitride and micron-sized copper were mixed at a mass ratio of 1:4 and a ball-to-material ratio of 8:1. The mixture was ball-milled at a speed of 250 r / min for 2.5 h to obtain composite particles of aluminum nitride and micron-sized copper. Nano-titanium and micron-sized aluminum were mixed at a mass ratio of 1:1 and ball-milled according to the above method to obtain composite particles of nano-titanium and micron-sized aluminum.

[0025] Example 5: The difference from Example 1 is as follows: (2) Under an argon atmosphere, nano-aluminum nitride and micron-sized copper were mixed at a mass ratio of 1:4 and a ball-to-material ratio of 8:1. The mixture was ball-milled at a speed of 250 r / min for 2.5 h to obtain composite particles of aluminum nitride and micron-sized copper. Nano-titanium and micron-sized aluminum were mixed at a mass ratio of 1:2 and ball-milled according to the above method to obtain composite particles of nano-titanium and micron-sized aluminum.

[0026] Example 6: The difference from Example 1 is as follows: (3) A first cold spray nozzle is set at a position of 950°C between the copper liquid outlet and the aluminum liquid inlet. Argon gas is used, with the main gas pressure set at 1.5MPa, the main gas heating temperature at 500°C, the spraying distance at 15mm, and the powder feeding speed at 7g / min. Nano-aluminum nitride and micron copper composite particles are cold sprayed onto the copper plate through the first cold spray nozzle. A second cold spray nozzle is set between the first cold spray nozzle and the aluminum liquid inlet. After the nano-aluminum nitride and micron copper composite particles are sprayed, nano-titanium and micron aluminum composite particles are cold sprayed through the second cold spray nozzle at a main gas pressure of 1.2MPa, a main gas heating temperature of 350°C, a spraying distance of 20mm, and a powder feeding speed of 3g / min. The residual gas is discharged to form a composite coating.

[0027] Example 7: The difference from Example 1 is as follows: (3) A first cold spray nozzle is set at a position of 950°C between the copper liquid outlet and the aluminum liquid inlet. Argon gas is used, with the main gas pressure set at 1.5MPa, the main gas heating temperature at 700°C, the spraying distance at 15mm, and the powder feeding speed at 7g / min. Nano-aluminum nitride and micron copper composite particles are cold sprayed onto the copper plate through the first cold spray nozzle. A second cold spray nozzle is set between the first cold spray nozzle and the aluminum liquid inlet. After the nano-aluminum nitride and micron copper composite particles are sprayed, nano-titanium and micron aluminum composite particles are cold sprayed through the second cold spray nozzle at a main gas pressure of 1.2MPa, a main gas heating temperature of 350°C, a spraying distance of 20mm, and a powder feeding speed of 3g / min. The residual gas is discharged to form a composite coating.

[0028] Example 8: The difference from Example 1 is as follows: (3) A first cold spray nozzle is set at a position of 950°C between the copper liquid outlet and the aluminum liquid inlet. Argon gas is used, with the main gas pressure set at 1.5MPa, the main gas heating temperature at 600°C, the spraying distance at 10mm, and the powder feeding speed at 10g / min. Nano aluminum nitride and micro copper composite particles are cold sprayed onto the copper plate through the first cold spray nozzle. A second cold spray nozzle is set between the first cold spray nozzle and the aluminum liquid inlet. After the nano aluminum nitride and micro copper composite particles are sprayed, nano titanium and micro aluminum composite particles are cold sprayed through the second cold spray nozzle at a main gas pressure of 1.2MPa, a main gas heating temperature of 350°C, a spraying distance of 20mm, and a powder feeding speed of 3g / min. The residual gas is discharged to form a composite coating.

[0029] Example 9: The difference from Example 1 is as follows: (3) A first cold spray nozzle is set at a position of 950°C between the copper liquid outlet and the aluminum liquid inlet. Argon gas is used, with the main gas pressure set at 1.5MPa, the main gas heating temperature at 600°C, the spraying distance at 15mm, and the powder feeding speed at 7g / min. Nano aluminum nitride and micro copper composite particles are cold sprayed onto the copper plate through the first cold spray nozzle. A second cold spray nozzle is set between the first cold spray nozzle and the aluminum liquid inlet. After the nano aluminum nitride and micro copper composite particles are sprayed, nano titanium and micro aluminum composite particles are cold sprayed through the second cold spray nozzle at a main gas pressure of 1.5MPa, a main gas heating temperature of 350°C, a spraying distance of 20mm, and a powder feeding speed of 3g / min. The residual gas is discharged to form a composite coating.

[0030] Example 10: The difference from Example 1 is as follows: (3) A first cold spray nozzle is set at a position of 950°C between the copper liquid outlet and the aluminum liquid inlet. Argon gas is used, with the main gas pressure set at 1.5MPa, the main gas heating temperature at 600°C, the spraying distance at 15mm, and the powder feeding speed at 7g / min. Nano aluminum nitride and micro copper composite particles are cold sprayed onto the copper plate through the first cold spray nozzle. A second cold spray nozzle is set between the first cold spray nozzle and the aluminum liquid inlet. After the nano aluminum nitride and micro copper composite particles are sprayed, nano titanium and micro aluminum composite particles are cold sprayed through the second cold spray nozzle at a main gas pressure of 1.2MPa, a main gas heating temperature of 350°C, a spraying distance of 15mm, and a powder feeding speed of 3g / min. The residual gas is discharged to form a composite coating.

[0031] Comparative Example 1: The difference from Example 1 is that: (3) At a position of 950°C between the copper liquid outlet and the aluminum liquid inlet, a first cold spray nozzle is set up. Argon gas is used, with the main gas pressure set to 1.5MPa, the main gas heating temperature set to 600°C, the spraying distance set to 15mm, and the powder feeding speed set to 15g / min. Nano aluminum nitride and micro copper composite particles are cold sprayed onto the copper plate through the first cold spray nozzle. A second cold spray nozzle is set up between the first cold spray nozzle and the aluminum liquid inlet. After the nano aluminum nitride and micro copper composite particles are sprayed, nano titanium and micro aluminum composite particles are cold sprayed through the second cold spray nozzle with the main gas pressure set to 1.2MPa, the main gas heating temperature set to 350°C, the spraying distance set to 20mm, and the powder feeding speed set to 6g / min. The residual gas is then discharged to form a composite coating. (4) After the cold spraying is completed, the copper plate continues to move forward; after an interval of 3~10s, the aluminum liquid at 800℃ flows onto the composite coating on the surface of the copper plate. Through the crystallizer and cooling water, the aluminum liquid solidifies and forms a metallurgical bond with the copper plate to obtain a 12mm thick billet. (5) The billet is rolled at room temperature with a deformation of 50% in the first pass. When it is rolled in the second pass with a deformation of 50%, it cracks and cannot be made into a composite material.

[0032] Comparative Example 2: (1) Copper was melted and the molten copper liquid was poured into a mold and formed into a copper plate with a width of 150 mm and a thickness of 3 mm under the casting action of the traction device at 150 mm / min; (2) The copper plate continues to move forward and when it reaches the aluminum liquid outlet, the aluminum liquid at 800°C flows onto the surface of the copper plate. Then, through the crystallizer and cooling water, the aluminum liquid solidifies and forms a metallurgical bond with the copper plate to obtain a 12mm thick billet. (3) The billet was rolled at room temperature with a deformation of 50% in the first pass. The material cracked and could not be rolled in the next step.

[0033] Example Sample Testing: Because the barrier layer formed in Comparative Example 1 was too thick, while Comparative Example 2 did not have a barrier layer, neither Comparative Example 1 nor Comparative Example 2 could be rolled into a composite material of the target thickness. Therefore, samples from each comparative example were not used for further experiments.

[0034] The interface shapes of the copper-aluminum composite materials prepared in each embodiment were compared to evaluate the uniformity of the copper layer thickness. The results are as follows: Figure 1 As shown. By Figure 1 It can be seen that the copper layer interfaces in all embodiments are relatively smooth, with Example 1 exhibiting the best uniformity. This indicates that the copper-aluminum composite material obtained by rolling at room temperature with low deformation using the method of the present invention has good uniformity, good interfacial bonding, and is not prone to splitting. The method of the present invention eliminates the need for large deformation rolling in the first pass, allowing for a wider range of product specifications, less wear and tear on machinery, lower costs, and higher controllability.

[0035] Tensile and tensile shear tests were conducted on the rolled copper-aluminum composite materials of each embodiment using a 200kN universal testing machine to evaluate tensile strength, bond strength, and elongation. The tensile speed was 3 mm / min, the total length of the tensile specimen was 60 mm, and the nominal length was 15 mm. Tensile shear tests were conducted on a 10kN universal testing machine at a tensile speed of 0.5 mm / min. Each experiment was performed in triplicate, and the results were averaged. The results are shown in the table below.

[0036]

[0037] As shown in the table above, compared to Example 1, the tensile strength, bond strength, and elongation of Examples 2 and 4, which have lower micron particle content, all decreased. This indicates that the ratio of nanoparticles to micron particles directly affects the mechanical properties of the material. An increase in the relative content of nanoparticles affects the cold spraying effect and the uniformity of the barrier layer. In Example 3, the elongation did not change significantly, but the tensile strength and bond strength decreased more noticeably. This suggests that an increase in the micron copper content affects the integrity of the aluminum nitride nanoparticle coating on the copper particles, increasing the chance of subsequent titanium contact with copper and increasing the probability of the formation of brittle copper-titanium compounds, thus having a greater impact on the interfacial strength of the material. In Example 5, the relative content of micron aluminum increased while the relative content of nano titanium decreased, resulting in a significant decrease in the tensile strength and bond strength of the material. This indicates that a decrease in titanium content directly affects the formation of the barrier layer and reduces the barrier effect on the brittle phase.

[0038] Compared to Example 1, the temperature change during the cold spraying of nano-aluminum nitride and micron-sized copper composite particles in Examples 6 and 7 resulted in a decrease in material strength. Example 6, with its lower temperature and larger temperature difference with the copper plate, caused significant disturbance to the copper plate surface environment, even leading to localized hardening and affecting the uniformity of adhesion of the nano-aluminum nitride and micron-sized copper composite particles. While Example 7, with its higher temperature and smaller temperature difference, still experienced a higher spraying speed, making it easier for the nano-aluminum nitride and micron-sized copper composite particles to embed into the copper plate, affecting the integrity of the surface coverage. Therefore, the strength decrease was more pronounced in Example 7. Changes in other cold spraying parameters in Examples 8-10 all adversely affected the tensile strength, bond strength, and elongation of the composite material, indicating that the formed barrier layer directly influences the properties of the composite material. Optimal performance can only be guaranteed within the aforementioned parameter ranges; any change in any parameter will affect the interfacial bond strength of the composite material.

[0039] For those skilled in the art, various other corresponding changes and modifications can be made based on the technical solutions and concepts described above, and all such changes and modifications should fall within the protection scope of the claims of this invention.

Claims

1. A method for preparing a horizontally continuously cast copper-aluminum composite material, characterized in that, Includes the following steps: A continuous copper plate is formed. Between the output copper plate and the aluminum melt inlet, the temperature of the copper plate is controlled to be no less than 900°C. Using an inert gas, nano-aluminum nitride and micron-sized copper composite particles are cold-sprayed onto the copper plate strip. Then, nano-titanium and micron-sized aluminum composite particles are cold-sprayed to form a composite coating on the copper plate. The aluminum melt flows out onto the composite coating. After cooling, the aluminum melt solidifies on the copper plate and forms a metallurgical bond with the copper plate. Rolling is then performed to obtain a copper-aluminum composite material.

2. The method for preparing horizontally continuously cast copper-aluminum composite materials according to claim 1, characterized in that, The temperature is 900~1050℃.

3. The method for preparing horizontally continuously cast copper-aluminum composite materials according to claim 1, characterized in that, The mass ratio of nano-aluminum nitride to micron-sized copper is 1:2~6; the mass ratio of nano-titanium to micron-sized aluminum is 1:1~2.

4. The method for preparing horizontally continuously cast copper-aluminum composite materials according to claim 1, characterized in that, The main gas pressure of the cold-sprayed aluminum nitride and micron copper composite particles is 1~2MPa, the main gas heating temperature is 500~700℃, the spraying distance is 10~20mm, the relative moving speed of the substrate is 100~250mm / min, and the powder feeding speed is 4~10g / min.

5. The method for preparing horizontally continuously cast copper-aluminum composite materials according to claim 1, characterized in that, The main gas pressure of the cold-sprayed nano-titanium and micron-sized aluminum composite particles is 0.8~1.5MPa, the main gas heating temperature is 300~400℃, the spraying distance is 15~25mm, the relative moving speed of the substrate is 100~250mm / min, and the powder feeding speed is 2~5g / min.

6. The method for preparing horizontally continuously cast copper-aluminum composite materials according to claim 1, characterized in that, The nano-aluminum nitride and micron-copper composite particles were prepared by ball milling.

7. The method for preparing horizontally continuously cast copper-aluminum composite materials according to claim 6, characterized in that, The ball milling mixing step includes: mixing the raw materials at a ball-to-material ratio of 5 to 10:1, and ball milling them at a speed of 200 to 300 r / min for 1.5 to 3 hours under a protective atmosphere.

8. The method for preparing horizontally continuously cast copper-aluminum composite material according to claim 1, characterized in that, Includes the following steps: a. The copper is melted, and the molten copper is poured into a mold, where it is cast into a copper plate under the action of a traction device; b. Between the copper liquid outlet and the aluminum liquid inlet, inert gas is used to cold spray nano-aluminum nitride and micron-sized copper composite particles onto the copper plate; then nano-titanium and micron-sized aluminum composite particles are cold sprayed, and the excess gas is discharged to form a composite coating. c. The molten aluminum flows onto the composite coating, and through the crystallizer and cooling water, the molten aluminum solidifies and forms a metallurgical bond with the copper plate to obtain the billet; d. Roll the billet to the target thickness at 20~350℃ with a deformation of 35~80% per pass.

9. The method for preparing horizontally continuously cast copper-aluminum composite materials according to claim 8, characterized in that, The time interval between the cold spraying of nano-titanium and micron-sized aluminum composite particles and the injection into the molten aluminum is 3 to 10 seconds.

10. The method for preparing horizontally continuously cast copper-aluminum composite material according to claim 8, characterized in that, The temperature of the molten aluminum is 780~850℃.

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