A method for preparing a high-thermal-conductivity silicon carbide particle reinforced aluminum matrix composite

Abstract

The application provides a preparation method of high-thermal-conductivity silicon carbide particle reinforced aluminum matrix composite material, which comprises the following steps: step one, shaping of silicon carbide particles; step two, mechanical mixing; step three, encapsulation; step four, vacuum thermal degassing; and step five, hot isostatic pressing treatment, wherein the ingot blank is placed into a hot isostatic pressing machine for hot isostatic pressing, and then the ingot blank is machined to remove the aluminum sheath to obtain the high-thermal-conductivity silicon carbide particle reinforced aluminum matrix composite material. The preparation method of the high-thermal-conductivity silicon carbide particle reinforced aluminum matrix composite material can optimize the preparation process of the high-thermal-conductivity aluminum matrix composite material, reduce the specific surface area of the particles, reduce the bonding interface area of the composite material, reduce the thermal resistance of the composite material, improve the thermal conductivity of the composite material, and make the stress around the silicon carbide particles more uniform and the mechanical properties better.

Description

Technical Field

[0001] This invention relates to the field of metal matrix composites technology, and more specifically, to a method for preparing a high thermal conductivity silicon carbide particle-reinforced aluminum matrix composite. Background Technology

[0002] In recent years, to meet the development needs of electronic technology, significant progress has been made in the research of high thermal conductivity and low expansion metal matrix composites used as thermal management materials. Particle-reinforced aluminum matrix composites, due to the combined advantages of lightweight aluminum matrix and reinforcing particles, high thermal conductivity, and low expansion, have become an ideal choice for future electronic packaging materials. Among them, silicon carbide particle-reinforced aluminum matrix composites have received widespread attention.

[0003] Currently, silicon carbide particle-reinforced aluminum matrix composites for electronic packaging mainly employ a high volume fraction of reinforcement to achieve high thermal conductivity and a coefficient of thermal expansion matching the chip. However, silicon carbide particles are prone to interfacial reactions with the aluminum matrix, forming rod-shaped or plate-shaped Al4C3 phases. Due to the low thermal conductivity of Al4C3, the composite interface has low thermal conductivity. To address the severe interfacial reaction in Al / SiC, existing patent CN114480942A aims to reduce the interfacial reaction by lowering the material preparation temperature. However, due to the poor wettability of Al and SiC, the composite interface of materials prepared at low temperatures cannot form an effective bond, resulting in poor overall material performance. Another method to reduce the formation of Al4C3 at the interface is to modify the surface of SiC particles by coating them with other materials, such as Ni or Cu. However, these elements also react to form other interfacial phases. Their main purpose is to reduce the formation of the brittle Al4C3 phase and thus improve the mechanical properties of the material, but their effect on reducing interfacial thermal resistance is limited. Patent CN104264000B provides a method for preparing graphene-modified high thermal conductivity aluminum-based composite materials. The method uses graphene nanosheets to modify and coat the reinforcing particles. Although it avoids the generation of interfacial reaction phases, the preparation process is long and the raw material price is high, which seriously limits its application in the field of thermal management.

[0004] To obtain high thermal conductivity silicon carbide-reinforced aluminum matrix composites, reducing the interfacial area to lower interfacial thermal resistance is a feasible method to improve the material's thermal conductivity. However, currently, the SiC particles used in high thermal conductivity aluminum matrix composites are mostly artificially synthesized and then mechanically crushed. Due to the low fracture toughness (high brittleness) of SiC, during the crushing process, SiC often fractures along different crystal planes, resulting in irregular shapes and high particle specific surface areas. This increases the interfacial area of ​​the composite material, significantly reducing its thermal conductivity. Therefore, researching how to reduce the bonding interface and improve the high thermal conductivity of aluminum matrix composites is of great significance. Summary of the Invention

[0005] In view of this, the present invention aims to propose a method for preparing a high thermal conductivity silicon carbide particle-reinforced aluminum matrix composite material, in order to solve the problem of reduced thermal conductivity of composite materials caused by the irregular shape and high specific surface area of ​​SiC particles in the prior art. This method optimizes the preparation process of the high thermal conductivity aluminum matrix composite material, improves the morphology of SiC particles to reduce their specific surface area, reduces the bonding interface area of ​​the composite material, reduces the amount of Al4C3 phase generated at the interface, and reduces the thermal resistance of the composite material; it also improves the thermal conductivity of the composite material; and it makes the stress around the silicon carbide particles more uniform and improves the mechanical properties.

[0006] To achieve the above objectives, the technical solution of the present invention is implemented as follows:

[0007] The present invention relates to a method for preparing a high thermal conductivity silicon carbide particle-reinforced aluminum matrix composite material, comprising the following steps:

[0008] Step 1: Shaping of silicon carbide particles: After grinding silicon carbide micro powder and silicon carbide ceramic balls in a ball mill, the particles are shaped to obtain silicon carbide powder.

[0009] Step 2, Mechanical Mixing: Calculate the volume fraction of silicon carbide particles to obtain the addition ratio of silicon carbide to aluminum; add the shaped silicon carbide powder and aluminum powder to the mixer according to the required addition ratio, and perform mechanical mixing to obtain mixed powder;

[0010] Step 3, Packaging: The mixed powder is loaded into the aluminum sheath, compacted, and then the aluminum sheath is sealed by argon arc welding. An extraction pipe is then welded at the sealing joint.

[0011] Step 4, Vacuum thermal degassing: The sealed aluminum cladding is placed in an electric resistance furnace and heated. Vacuum pumping equipment is used to degas the inside of the aluminum cladding through the pumping pipe. The pumping pipe is then pressed and sealed to obtain a powder ingot containing the aluminum cladding.

[0012] Step 5, Hot Isostatic Pressing: The blank after vacuum degassing is placed in a hot isostatic press for hot isostatic pressing. Then the blank is machined to remove the aluminum cladding, resulting in a high thermal conductivity silicon carbide particle-reinforced aluminum matrix composite material.

[0013] Furthermore, in step three, the diameter of the aluminum sheath is 200mm-500mm.

[0014] Furthermore, in step four, the aluminum cladding is heated in a stepped manner.

[0015] Furthermore, in step four, the heating temperatures for each stage of the aluminum cladding are 100℃, 300℃, and 500℃, respectively.

[0016] Furthermore, in step four, the vacuum level inside the aluminum sheath needs to reach the required range in each temperature range.

[0017] Furthermore, the vacuum level within the aluminum sheath ranges from 10. -3 pa-10 -4 pa.

[0018] Furthermore, in step five, the pressure range for hot isostatic pressing is 180 MPa to 250 MPa.

[0019] Furthermore, the temperature for hot isostatic pressing is 500℃-600℃.

[0020] Furthermore, the hot isostatic pressing time is 3-6 hours.

[0021] Furthermore, step one includes:

[0022] Step S11: Shaping silicon carbide particles: Load silicon carbide micro powder and silicon carbide ceramic balls into a ball mill for grinding;

[0023] Step S12: Sieving: The ground and shaped silicon carbide micro powder is sorted through a sieve to separate silicon carbide particles with qualified particle size.

[0024] Step S13: Purification: The sorted silicon carbide powder is purified by acid washing or alkali washing;

[0025] Step S14: Water washing: Wash the purified silicon carbide powder with water and control the pH value of the water washing within the preset range;

[0026] Step S15: Drying: After the silicon carbide powder is washed with water, it is dried to obtain silicon carbide micro powder for high thermal conductivity aluminum-based composite materials.

[0027] Furthermore, in step S14, the preset range of pH value is 6.5-7.5.

[0028] Furthermore, step four includes:

[0029] Step S41: Vacuum thermal degassing: The sealed aluminum cladding is placed in a resistance furnace and heated, and a vacuum pump is used to degas the inside of the aluminum cladding through the pump pipe; wherein, the aluminum cladding is heated in a stepped manner, first heated to 100℃, held at that temperature, until the vacuum degree reaches 10 -3 pa-10 -4 Pa, then raise the temperature to 300℃.

[0030] Step S42: The aluminum cladding is kept at 300℃ until the vacuum degree reaches 10. -3 pa-10 -4 Pa, then raise the temperature to 500℃.

[0031] Step S43: Insulate the aluminum cladding at 500℃ until the vacuum degree reaches 10.-3 pa-10 -4 pa, then press the suction tube tightly to seal it.

[0032] Compared with existing technologies, the preparation method of a high thermal conductivity silicon carbide particle-reinforced aluminum matrix composite material described in this invention has the following beneficial effects:

[0033] The method described above can optimize the preparation process of high thermal conductivity aluminum-based composite materials, improve the morphology of SiC particles, reduce the specific surface area of ​​particles, reduce the bonding interface area of ​​composite materials, reduce the amount of Al4C3 phase generated at the interface, and reduce the thermal resistance of composite materials; improve the thermal conductivity of composite materials; in addition, the shaping process eliminates stress concentration caused by sharp corners in the particles, and also makes the stress around the silicon carbide particles more uniform and the mechanical properties better. Attached Figure Description

[0034] The accompanying drawings, which constitute a part of this invention, are used to provide a further understanding of the invention. The illustrative embodiments of the invention and their descriptions are used to explain the invention and do not constitute an undue limitation of the invention.

[0035] In the picture:

[0036] Figure 1 This is a schematic diagram of the preparation method process.

[0037] Figure 2 This is a schematic diagram of the SEM image of the silicon carbide particle morphology before shaping.

[0038] Figure 3 This is a schematic diagram of the SEM image of the morphology of the shaped silicon carbide particles. Detailed Implementation

[0039] The inventive concepts of this disclosure will be described below using terminology commonly used by those skilled in the art to communicate the essence of their work to others skilled in the art. However, these inventive concepts may be embodied in many different forms and should not be construed as limited to the embodiments described herein.

[0040] It should be noted that, unless otherwise specified, the embodiments and features described in the present invention can be combined with each other.

[0041] The present invention will now be described in detail with reference to the accompanying drawings and embodiments.

[0042] To address the problem that existing high thermal conductivity aluminum-based composite materials often use SiC particles that are artificially synthesized and then mechanically crushed, resulting in irregular shapes and high particle surface areas, which increases the interfacial area of ​​the composite material and significantly reduces its thermal conductivity, this embodiment proposes a method for preparing a high thermal conductivity silicon carbide particle-reinforced aluminum-based composite material. The method includes the following steps:

[0043] Step 1: Shaping of silicon carbide particles: After grinding silicon carbide micro powder and silicon carbide ceramic balls in a ball mill, the particles are shaped to obtain silicon carbide powder.

[0044] Step 2, Mechanical Mixing: Calculate the volume fraction of silicon carbide particles to obtain the addition ratio of silicon carbide to aluminum; add the shaped silicon carbide powder and aluminum powder to the mixer according to the required addition ratio, and perform mechanical mixing to obtain mixed powder;

[0045] Step 3, Packaging: The mixed powder is loaded into the aluminum sheath, compacted, and then the aluminum sheath is sealed by argon arc welding. An extraction pipe is then welded at the sealing joint.

[0046] Step 4, Vacuum thermal degassing: The sealed aluminum cladding is placed in a resistance furnace and heated. A vacuum pump is used to degas the inside of the aluminum cladding through the pump pipe. The pump pipe is then pressed and sealed to obtain a powder ingot containing the aluminum cladding.

[0047] Step 5, Hot Isostatic Pressing: The blank after vacuum degassing is placed in a hot isostatic press for hot isostatic pressing. Then the blank is machined to remove the aluminum cladding, resulting in a high thermal conductivity silicon carbide particle-reinforced aluminum matrix composite material.

[0048] In step three, the diameter of the aluminum cladding is 200mm-500mm. During compaction, the density of the mixed powder in all locations within the aluminum cladding must remain similar. In step four, the aluminum cladding is heated using a stepped temperature increase. The stepped temperature ranges are 100℃, 300℃, and 500℃. In step four, the vacuum level within the aluminum cladding must reach the required range in each temperature range. During the degassing process in step four, the vacuum level within the aluminum cladding ranges from 10... - 3 pa-10 -4 In step five, the pressure range for hot isostatic pressing is 180 MPa to 250 MPa; the temperature for hot isostatic pressing is 500℃ to 600℃; and the time for hot isostatic pressing is 3 hours to 6 hours.

[0049] Compared to traditional thermal management materials that use unshaped silicon carbide as a reinforcement, this invention utilizes shaped silicon carbide particles as a reinforcement, followed by powder metallurgy to prepare high thermal conductivity aluminum-based composite materials. This optimizes the preparation process, improves the morphology of SiC particles, reduces their specific surface area, decreases the interfacial area of ​​the composite material, reduces the amount of Al4C3 phase generated at the interface, and lowers the thermal resistance of the composite material. It also improves the thermal conductivity of the composite material. Furthermore, the shaping process eliminates stress concentration caused by sharp corners in the particles, resulting in more uniform stress distribution around the silicon carbide particles and improved mechanical properties. This makes it advantageous for applications in electronic packaging.

[0050] Step one includes:

[0051] Step S11: Shaping silicon carbide particles: Load silicon carbide micro powder and silicon carbide ceramic balls into a ball mill for grinding;

[0052] Step S12: Sieving: The ground and shaped silicon carbide micro powder is sorted through a sieve to separate silicon carbide particles with qualified particle size.

[0053] Step S13: Purification: The sorted silicon carbide powder is purified by acid washing or alkali washing;

[0054] Step S14: Water washing: Wash the purified silicon carbide powder with water and control the pH value of the water washing within the preset range;

[0055] Step S15: Drying: After dehydration treatment of the washed silicon carbide powder, it is dried to obtain silicon carbide micro powder with regular and smooth surface for aluminum-based composite materials.

[0056] In step S14, the preset range of pH value is 6.5-7.5.

[0057] The ball milling process in step one shapes irregularly shaped silicon carbide particles, reducing sharp edges and resulting in a more regular particle structure. This leads to a lower specific surface area and a smaller overall interfacial area in the composite material, reducing the amount of Al4C3 phase formed at the interface and thus decreasing the thermal resistance at the composite interface, resulting in higher thermal conductivity. It also eliminates stress concentration caused by sharp corners in the silicon carbide particles, leading to a more uniform stress distribution and improved mechanical properties. Furthermore, controlling the pH value of the washing water helps avoid over-shaping of the silicon carbide, improving the stability of the shaping process.

[0058] Step four includes:

[0059] Step S41: Vacuum thermal degassing: The sealed aluminum cladding is placed in a resistance furnace and heated, and a vacuum pump is used to degas the inside of the aluminum cladding through the pump pipe; wherein, the aluminum cladding is heated in a stepped manner, first heated to 100℃, held at that temperature, until the vacuum degree reaches 10 -3 pa-10 -4 Pa, then raise the temperature to 300℃.

[0060] Step S42: The aluminum cladding is kept at 300℃ until the vacuum degree reaches 10. -3 pa-10 -4 Pa, then raise the temperature to 500℃.

[0061] Step S43: Insulate the aluminum cladding at 500℃ until the vacuum degree reaches 10. -3 pa-10 -4 pa, then press the suction tube tightly to seal it.

[0062] In step S41, whether the evacuation of the aluminum cladding meets the requirements is judged based on whether the vacuum level inside the aluminum cladding is within the required vacuum range. Whether the heating of the aluminum cladding meets the requirements is judged based on whether the temperature inside the resistance furnace reaches the required temperature value.

[0063] By using a stepped heating method to degas the ingot during vacuum thermal degassing, it is possible to effectively prevent the volatile products from reacting with the composite material inside the aluminum cladding during the ingot heating process, reduce the impact of impurities inside the composite material on the density and thermal conductivity of the composite ingot, and effectively improve the thermal conductivity of silicon carbide reinforced aluminum matrix composite material.

[0064] Example 1:

[0065] Step 1: Place silicon carbide micro powder with a purity ≥99.5% and a D50 of 15-20μm, and silicon carbide ceramic balls with a diameter of 2-5mm into a ball mill at a ball-to-material ratio of 1:1 for ball milling. Adjust the ball mill's rotation speed to 600-900r / min and its revolution speed to 300-400r / min. The ball milling time is 12-24h.

[0066] The ball-milled silicon carbide micro powder was sieved using an 1800-mesh sieve to separate silicon carbide particles with a particle size of more than 10 μm.

[0067] Sulfuric acid was added to the sorted silicon carbide powder for acid washing and purification. The amount of sulfuric acid added was 5%-10% of the total weight of the powder. After purification for 2 hours, the powder was filtered.

[0068] The purified silicon carbide powder is washed with deionized water until the pH of the cleaning solution is between 6.5 and 7.5.

[0069] After the powder is washed and dehydrated, it is placed in a drying oven for drying at a temperature of 150-200℃ for 1-3 hours.

[0070] Step 2: Add the dried silicon carbide powder and pure aluminum powder together into a mixer for mechanical mixing. The volume fraction of silicon carbide is 45%, and the mixing time is 8h-24h.

[0071] Step 3: Pack the evenly mixed powder into a pure aluminum sleeve, and vibrate it to ensure that the powder density is similar in all locations. The sleeve should have a diameter of 180mm and a height of 300mm.

[0072] The aluminum sheath is sealed by argon arc welding, and an extraction pipe is welded to the cover.

[0073] Step 4: Place the aluminum-clad sealed powder ingot into the heating furnace, and connect the vacuum pump to the pumping pipe. The heating temperature is 100℃, and vacuuming is performed simultaneously until the vacuum level inside the aluminum cladding reaches 1~2×10⁻⁶. -3 Pa, then raise the temperature to 300℃, and continue to evacuate to 1~2×10 -3 Pa, then raise the temperature to 500℃, and continue to evacuate to 1~2×10 - 3 Pa;

[0074] After vacuum thermal degassing is completed, the extraction pipe is sealed to prevent leakage from the casing.

[0075] Step 5: After hot degassing, the billet is placed in a hot isostatic press at a temperature of 510℃ and a pressure of 150MPa for 4 hours.

[0076] The hot isostatic pressing billet is machined to remove the outer aluminum cladding, resulting in a high thermal conductivity silicon carbide reinforced aluminum matrix composite material.

[0077] Comparative Example 1:

[0078] The difference from Example 1 is that unshaped SiC / Al composite material was used for preparation, resulting in an aluminum-based composite material. The composite materials prepared in Comparative Example 1 and Example 1 were tested, and the relevant performance data of the two composite materials are shown in Table 1.

[0079] Table 1

[0080] Process route Thermal conductivity (W / (m·K)) Bending strength (MPa) Unshaped SiC / Al composite materials 185 408 Shaped SiC / Al composite material 199 468

[0081] The data in Table 1 show that the thermal conductivity of the shaped composite material is about 8% higher than that of the unshaped composite material, and the flexural strength of the shaped composite material is about 15% higher than that of the unshaped composite material. The test results indicate that the various properties of the shaped composite material are significantly improved, effectively reducing the thermal resistance and increasing the thermal conductivity, thus enhancing the mechanical properties of the composite material.

[0082] Example 2:

[0083] Step 1: Place silicon carbide micro powder with a purity ≥99.5% and a D50 of 50-55μm, and silicon carbide ceramic balls with a diameter of 5-10mm into a ball mill at a ball-to-material ratio of 1:1 for ball milling. Adjust the ball mill's rotation speed to 600-900r / min and its revolution speed to 300-400r / min. The ball milling time is 12-24h.

[0084] The ball-milled silicon carbide micro powder was sieved using a 500-mesh sieve to separate silicon carbide particles with a particle size of more than 30μm.

[0085] After sorting, the silicon carbide powder was added to nitric acid for acid washing and purification. The concentration of nitric acid was 4 mol / L. After purification for 5 hours, the powder was filtered.

[0086] The purified silicon carbide powder is washed with deionized water until the pH of the cleaning solution is between 6.5 and 7.5.

[0087] After the powder is washed and dehydrated, it is placed in a drying oven for drying at a temperature of 150-200℃ for 1-3 hours.

[0088] Step 2: Add the dried silicon carbide powder and pure aluminum powder together into a mixer for mechanical mixing. The volume fraction of silicon carbide is 55%, and the mixing time is 8-24 hours.

[0089] Step 3: Pack the evenly mixed powder into a pure aluminum sleeve, and vibrate it to ensure that the powder density is similar in all locations. The sleeve should have a diameter of 300mm and a height of 500mm.

[0090] The aluminum sheath is sealed by argon arc welding, and an extraction pipe is welded to the cover.

[0091] Step 4: Place the aluminum-clad sealed powder ingot into the heating furnace, and connect the vacuum pump to the pumping pipe. The heating temperature is 100℃, and vacuuming is performed simultaneously until the vacuum level inside the aluminum cladding reaches 1~2×10⁻⁶. -3 Pa, then raise the temperature to 300℃, and continue to evacuate to 1~2×10 -3 Pa, then raise the temperature to 500℃, and continue to evacuate to 1~2×10 -3 Pa;

[0092] After vacuum thermal degassing is completed, the extraction pipe is sealed to prevent leakage from the casing.

[0093] Step 5: After hot degassing, the billet is placed in a hot isostatic press at a temperature of 540℃ and a pressure of 140MPa for 6 hours.

[0094] The hot isostatic pressing billet is machined to remove the outer aluminum cladding, resulting in a high thermal conductivity silicon carbide reinforced aluminum matrix composite material.

[0095] Comparative Example 2:

[0096] The difference from Example 2 is that unshaped SiC / Al composite material was used for preparation, resulting in an aluminum-based composite material. The composite materials prepared in Comparative Example 2 and Example 2 were tested, and the relevant performance data of the two composite materials are shown in Table 2.

[0097] Table 2

[0098] Process route Thermal conductivity (W / (m·K)) Bending strength (MPa) Unshaped SiC / Al composite materials 192 379 Shaped SiC / Al composite material 211 431

[0099] The data in Table 2 also show that the thermal conductivity of the shaped composite material is about 10% higher than that of the unshaped composite material, and the flexural strength of the shaped composite material is about 14% higher than that of the unshaped composite material. The test results indicate that the various properties of the shaped composite material are significantly improved, and it can also more effectively reduce the thermal resistance of the composite material, increase its thermal conductivity, and thus improve its mechanical properties.

[0100] The above description is only a preferred embodiment of the present invention and is not intended to limit the present invention. Any modifications, equivalent substitutions, improvements, etc., 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 producing a high thermal conductive silicon carbide particle reinforced aluminum matrix composite material, characterized by, The method comprises the following steps: Step one, shaping of silicon carbide particles: after the silicon carbide powder and the silicon carbide ceramic ball are loaded into a ball mill for grinding, shaping treatment is performed to obtain silicon carbide powder; Step two, mechanical mixing: the volume fraction of the silicon carbide particles is calculated to obtain the addition ratio of the silicon carbide and aluminum; the shaped silicon carbide powder and aluminum powder are added into a mixer according to the required addition ratio, and mechanical mixing is performed to obtain a mixed powder; Step three, packaging: the mixed powder is loaded into an aluminum package, and after being vibrated and compacted, the aluminum package is sealed by argon arc welding, and an air extraction pipe is welded at the sealing opening; Step four, vacuum thermal degassing: the sealed aluminum package is placed in a resistance furnace for heating, and a vacuum air extraction device is used to extract air from the inside of the aluminum package through the air extraction pipe, and then the air extraction pipe is tightly sealed; a powder ingot containing the aluminum package is obtained; Step five, hot isostatic pressing treatment: the ingot after vacuum degassing is placed in a hot isostatic pressing machine for hot isostatic pressing, and then the ingot is machined to remove the aluminum package to obtain a high-thermal-conductivity silicon carbide particle reinforced aluminum matrix composite material; in step five, the pressure of the hot isostatic pressing is in the range of 180 MPa to 250 MPa; In addition, step one comprises: Step S11: shaping of silicon carbide particles: the silicon carbide powder and the silicon carbide ceramic ball are loaded into a ball mill for grinding; Step S12: screening: the ground and shaped silicon carbide powder is sorted by a screen to screen out silicon carbide particles with qualified particle size; Step S13: purification: the sorted silicon carbide powder is pickled or alkali washed for purification; Step S14: water washing: the purified silicon carbide powder is water washed, and the pH value of the water washing is controlled within a preset range; the preset range of the pH value is 6.5-7.5; Step S15: drying: after the water-washed silicon carbide powder is dehydrated, it is dried to obtain high-thermal-conductivity silicon carbide powder special for aluminum matrix composite materials; Step four comprises: Step S41: vacuum heat degassing: after sealing and welding, the aluminum jacket is placed in a resistance furnace for heating, and a vacuum pumping device is used to pump the inside of the aluminum jacket through a pumping pipe; wherein the aluminum jacket is heated in steps, the aluminum jacket is first heated to 100℃, and the temperature is kept constant until the vacuum degree reaches 10 -3 Pa-10 -4 Pa, and then heated to 300℃; Step S42: The aluminum jacket is kept at 300°C until the vacuum degree reaches 10 -3 Pa-10 -4 Pa, and then heated to 500°C; Step S43: The aluminum jacket is kept at 500°C until the vacuum reaches 10 -3 Pa-10 -4 Pa, and the suction pipe is tightly sealed.

2. The method for preparing a high thermal conductivity silicon carbide particle-reinforced aluminum matrix composite material according to claim 1, characterized in that, In step three, the diameter of the aluminum package is 200-500 mm.

3. The method for preparing a high thermal conductivity silicon carbide particle-reinforced aluminum matrix composite material according to claim 1, characterized in that, The temperature of the hot isostatic pressing is 500-600°C.

4. The method for preparing a high thermal conductivity silicon carbide particle-reinforced aluminum matrix composite material according to claim 1, characterized in that, The time of the hot isostatic pressing is 3-6 h.

Images