CN112111667B - Aluminum-based silicon carbide composite material and preparation method thereof - Google Patents
Aluminum-based silicon carbide composite material and preparation method thereof Download PDFInfo
- Publication number
- CN112111667B CN112111667B CN202011006535.1A CN202011006535A CN112111667B CN 112111667 B CN112111667 B CN 112111667B CN 202011006535 A CN202011006535 A CN 202011006535A CN 112111667 B CN112111667 B CN 112111667B
- Authority
- CN
- China
- Prior art keywords
- silicon carbide
- aluminum
- parts
- composite material
- finished product
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/10—Alloys containing non-metals
- C22C1/1036—Alloys containing non-metals starting from a melt
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
- C22C32/0052—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only carbides
- C22C32/0063—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only carbides based on SiC
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacture Of Alloys Or Alloy Compounds (AREA)
Abstract
The application provides an aluminum-based silicon carbide composite material and a preparation method thereof. Wherein the method comprises the following steps: s1, selecting magnesium, silicon, beryllium and aluminum, and sequentially carrying out smelting, hot rolling, cold rolling, solid solution and aging treatment on the magnesium, the silicon, the beryllium and the aluminum to prepare the aluminum alloy; s2, screening silicon carbide particles, mixing and dry-pressing the silicon carbide particles into a green body silicon carbide, and placing the green body silicon carbide into a muffle furnace to pre-oxidize the green body silicon carbide to obtain a silicon carbide primary finished product; s3, performing surface treatment on the silicon carbide primary finished product to form a transition layer on the surface of the silicon carbide primary finished product to obtain a silicon carbide finished product; and S4, mixing the aluminum alloy and the silicon carbide finished product and carrying out pressureless infiltration treatment to obtain the aluminum-based silicon carbide composite material. The preparation method provided by the application can greatly improve the interface bonding force between aluminum and silicon carbide, and further greatly improve the preparation quality of the aluminum-based silicon carbide composite material.
Description
Technical Field
The application relates to the technical field of materials, in particular to an aluminum-based silicon carbide composite material and a preparation method thereof.
Background
The aluminum-based silicon carbide composite material (SiC/Al) is a silicon carbide particle reinforced aluminum-based composite material, has the advantages of low aluminum alloy density, good heat conduction, high cost performance, low silicon carbide specific gravity, high strength, low thermal expansion coefficient and the like, and has very wide application prospect in the fields of aerospace, military, precision instruments, electronic packaging, automobiles, sports goods and the like. In addition, the prefabricated member made of the aluminum-based silicon carbide composite material has stable quality, can greatly reduce the production amount of machining, reduces the investment in time and fund, is expected to be applied in the aspects of electronic packaging of subsequent silicon wafers or GaAs chips and the like, and plays a more positive value.
However, the aluminum-based silicon carbide composite material on the market at present has problems of poor wettability between the reinforcing silicon carbide particles and two phases of the aluminum alloy liquid, generation of a harmful interface reaction, and the like. These problems can seriously affect the performance of aluminum-based silicon carbide composites. Firstly, poor wettability between two phases of the enhanced silicon carbide particles and an aluminum alloy liquid brings a series of problems of increasing holes and pores and the like, so that the mechanical property and the thermal property of the aluminum-based silicon carbide composite material are greatly reduced, and the low quality of a wetting interface is not beneficial to ensuring the thermal conductivity of the material; secondly, if a reaction layer exists at the interface position, the thermal conductivity of the material is reduced, and the possible harmful reaction tends to pulverize the relevant material, so that the material becomes brittle and fails.
At present, the aluminum-based silicon carbide composite material is generally prepared by a powder metallurgy method, an extrusion casting method, a pressure infiltration method or a non-pressure infiltration method. The preparation method of the pressureless infiltration method is rich, the preparation difficulty is low, the preparation cost is low, the subsequent processing operation can be carried out by using the traditional metallurgical equipment, the batch production is easy, and the pressureless infiltration method is most widely used for preparing the aluminum-based silicon carbide composite material. However, because the oxide film on the surface of the aluminum is very compact, the interface wettability of the aluminum alloy and the silicon carbide ceramic framework is poor, the bonding force of the formed interface is weak, and the overall mechanical property of the composite material still cannot reach the optimal state. The problems limit the mass production, popularization and application of the aluminum-based silicon carbide composite material, and are the problems to be solved urgently at present.
Disclosure of Invention
In view of this, embodiments of the present application provide an aluminum-based silicon carbide composite material and a preparation method thereof, so as to solve technical defects in the prior art.
The application provides a preparation method of an aluminum-based silicon carbide composite material, which comprises the following steps:
s1, selecting magnesium, silicon, beryllium and aluminum, and sequentially carrying out smelting, hot rolling, cold rolling, solid solution and aging treatment on the magnesium, the silicon, the beryllium and the aluminum to prepare the aluminum alloy;
s2, screening silicon carbide particles, mixing and dry-pressing the silicon carbide particles into a green body silicon carbide, and placing the green body silicon carbide into a muffle furnace to pre-oxidize the green body silicon carbide to obtain a silicon carbide primary finished product;
s3, performing surface treatment on the silicon carbide primary finished product to form a transition layer on the surface of the silicon carbide primary finished product to obtain a silicon carbide finished product;
and S4, mixing the aluminum alloy and the silicon carbide finished product and carrying out pressureless infiltration treatment to obtain the aluminum-based silicon carbide composite material.
Further, in S1, the addition amount of magnesium is 1-12 parts by mass, the addition amount of silicon is 5-10 parts by mass, the addition amount of beryllium is 0.1-0.25 part by mass, and the addition amount of aluminum is 77.75-93.9 parts by mass.
Further, the S2 includes:
screening silicon carbide particles with the particle size range of 10-100 mu m, mixing the screened silicon carbide particles, dry-pressing the mixture into blank silicon carbide, and carrying out pre-oxidation treatment on the blank silicon carbide to obtain a silicon carbide finished product.
Further, the transition layer is a silicon carbide-titanium-aluminum alloy transition layer.
Further, the S3 includes:
and carrying out surface hot dipping titanium-aluminum alloy treatment on the silicon carbide primary finished product to form a silicon carbide-titanium-aluminum alloy transition layer on the surface of the silicon carbide primary finished product, so as to obtain a silicon carbide finished product.
Further, the titanium-aluminum alloy comprises the following components in parts by weight: 38-42 parts of aluminum, 1.5-2.5 parts of niobium and 55.5-60.5 parts of titanium.
Further, the S4 includes:
and mixing the aluminum alloy and the silicon carbide finished product in the nitrogen atmosphere of 850-1000 ℃ and carrying out pressureless infiltration treatment for 2-4 hours to obtain the aluminum-based silicon carbide composite material.
The application also provides an aluminum-based silicon carbide composite material, which is prepared by the preparation method.
Further, the aluminum-based silicon carbide composite material comprises the following components in parts by weight: 50-60 parts of aluminum alloy, 40-50 parts of silicon carbide and 0.5-3 parts of titanium-aluminum alloy.
The application provides a preparation method of aluminium base silicon carbide composite, through carrying out surface treatment to the silicon carbide primary product and forming the transition layer on the surface of the silicon carbide primary product, obtain the silicon carbide finished product, mix aluminum alloy and silicon carbide finished product and carry out the non-pressure infiltration processing again, obtain aluminium base silicon carbide composite, the transition layer on silicon carbide finished product surface can promote to produce the reaction between aluminium and the silicon carbide, improve the interface cohesion between aluminium and the silicon carbide by a wide margin, and then improve aluminium base silicon carbide composite's preparation quality by a wide margin.
The aluminum-based silicon carbide composite material provided by the application has strong interface bonding force of aluminum and silicon carbide, so that the mechanical property and the impact resistance of the material are extremely excellent.
Drawings
FIG. 1 is a flow chart illustrating steps of a method for preparing an aluminum-based silicon carbide composite according to an embodiment of the present disclosure;
FIG. 2 is a flow chart of a silicon carbide particle fabrication process according to an embodiment of the present disclosure;
FIG. 3 is a cross-sectional view of an aluminum-based silicon carbide composite according to an embodiment of the present application;
FIG. 4 is a line scan of an aluminum-based silicon carbide composite according to an embodiment of the present application;
FIG. 5 is a graph comparing bending strength of an aluminum-based silicon carbide composite according to an embodiment of the present application;
FIG. 6 is a graph comparing fracture toughness for an aluminum-based silicon carbide composite according to an embodiment of the present application.
Detailed Description
The following description of specific embodiments of the present application refers to the accompanying drawings.
In the present invention, unless otherwise specified, scientific and technical terms used herein have the meanings that are commonly understood by those skilled in the art. Also, the reagents, materials and procedures used herein are those that are widely used in the corresponding fields.
Example 1
As shown in fig. 1, the present embodiment provides a method for preparing an aluminum-based silicon carbide composite material, including steps S1 to S4.
S1, selecting magnesium, silicon, beryllium and aluminum, and sequentially carrying out smelting, hot rolling, cold rolling, solid solution and aging treatment to prepare the aluminum alloy.
Wherein, the adding amount of the magnesium is preferably 1 to 12 parts by mass, and specifically can be 2 parts, 4 parts, 5 parts, 6 parts, 8 parts, 10 parts and the like; the adding amount of the silicon is preferably 5-10 parts by mass, and specifically can be 5 parts, 6 parts, 7 parts, 8 parts, 9 parts, 10 parts and the like; the preferable addition amount of beryllium is 0.1-0.25 parts by mass, and specifically may be 0.12 parts, 0.15 parts, 0.18 parts, 0.2 parts, 0.22 parts, 0.25 parts, etc.; the addition amount of aluminum is preferably 77.75-93.9 parts by mass, and specifically may be 80 parts, 82 parts, 85 parts, 88 parts, 90 parts, and the like, which is not limited in the present application.
It should be noted that the content of each component in this embodiment is not arbitrarily defined, but is determined based on a large number of theoretical studies and experimental results, and particularly the content of beryllium in the aluminum alloy, and the content of beryllium has a particularly significant influence on the performance of the alloy. First, alloy strength tends to increase with increasing beryllium content; secondly, the electrical conductivity and the thermal conductivity of the alloy can be reduced along with the increase of the beryllium content; thirdly, beryllium is expensive and toxic, and if the content of beryllium is too high, the production cost can be greatly increased, and the difficulty of the processes of product processing, heat treatment and the like is increased, so that how to find the balance point of alloy performance and beryllium content is particularly important for reducing the beryllium content as much as possible on the basis of improving the alloy performance. And the balance between the alloy performance and the beryllium content can be achieved under the condition that the mass part of the beryllium is 0.1-0.25 percent, namely the beryllium accounts for 0.1-0.25 percent of the aluminum alloy. Low beryllium content, low cost, small process difficulty, high alloy strength, high hardness, high conductivity, high elasticity and excellent performance.
In practical application, the smelting, hot rolling, cold rolling, solid solution and aging treatment processes are as follows:
smelting: adding aluminum into a melting furnace, heating to 650-700 ℃, after the aluminum is completely melted, sequentially adding magnesium, silicon and beryllium, and cooling to obtain an aluminum alloy primary finished product.
Hot rolling: and carrying out hot rolling on the aluminum alloy primary product at the temperature of 300-500 ℃.
Cold rolling: and cooling the hot-rolled aluminum alloy primary product to room temperature and carrying out cold rolling.
Solid solution: the solution heat treatment is carried out on the aluminum alloy primary product after the cold rolling at the temperature of 500-600 ℃ for not less than 1 minute, and then the aluminum alloy primary product is cooled at the speed of more than 10 ℃/min.
Aging: and (3) carrying out aging treatment on the cooled aluminum alloy primary product at the temperature of 100-250 ℃ for not less than 1 hour to obtain the aluminum alloy.
S2, screening silicon carbide particles, mixing and dry-pressing the silicon carbide particles into a blank silicon carbide, and placing the blank silicon carbide into a muffle furnace to pre-oxidize the blank silicon carbide to obtain a silicon carbide primary finished product.
Specifically, the silicon carbide particles selected in this embodiment are preferably prepared by a method of polymer pyrolysis combined reactive sintering, a flow of the preparation process is shown in fig. 2, the preparation process mainly includes several links such as precursor preparation, slurry preparation, dipping, pyrolysis, machining, reactive sintering, and the specific process includes:
(1) mixing silicon carbide powder with high-carbon-yield polymer resin to prepare a material rack;
(2) selecting polyurethane foam with a proper pore diameter, cutting the polyurethane foam into a required shape and size, then immersing the polyurethane foam into slurry, taking out the polyurethane foam, removing redundant slurry in a squeezing mode, a blowing mode and the like to obtain a foam body, and drying and curing the foam body;
(3) carrying out polyurethane removal and resin pyrolysis on the cured foam body in a vacuum or inert gas protection furnace to obtain a foam framework consisting of silicon carbide and pyrolytic carbon, wherein the foam framework has the same shape as the original polyurethane foam;
(4) machining the foam skeleton to the required size and shape, sintering in a sintering furnace through a infiltration reaction, discharging to obtain silicon carbide foam ceramic, and crushing the silicon carbide foam ceramic to obtain silicon carbide particles.
In practical applications, silicon carbide particles with a particle size in the range of 10-100 μm are selected, and silicon carbide particles with a particle size of 10 μm, 20 μm, 30 μm, 40 μm, 50 μm, 60 μm, 70 μm, 80 μm, 90 μm, 100 μm, preferably 10 μm and 100 μm, 10 μm: the particle diameter ratio of the 100 μm silicon carbide particles is preferably 3:7, 10 μm: the weight ratio of the silicon carbide particles with the particle size of 100 mu m is preferably 1:3, the screened silicon carbide particles are mixed and then are dry-pressed into a blank silicon carbide, and the blank silicon carbide is pre-oxidized to obtain a silicon carbide finished product.
S3, performing surface treatment on the silicon carbide primary finished product to form a silicon carbide-titanium aluminum alloy transition layer on the surface of the silicon carbide primary finished product, and obtaining a silicon carbide finished product.
In this embodiment, the transition layer is preferably a silicon carbide-titanium-aluminum alloy transition layer.
In practical application, the silicon carbide primary product may be subjected to surface hot-dip titanium-aluminum alloy (Ti-40Al-2Nb) treatment to form a silicon carbide-titanium-aluminum alloy transition layer on the surface of the silicon carbide primary product, so as to obtain a silicon carbide finished product.
Wherein, the step of hot dipping titanium-aluminum alloy treatment comprises the following steps: (1) heating the titanium-aluminum alloy pot to 1650-1800 ℃ to be in a molten state; (2) and immersing the silicon carbide framework into a titanium-aluminum alloy pot for 10-60s, and taking out.
Specifically, in the process of preparing the aluminum-based silicon carbide composite material, silicon carbide inevitably reacts with various elements in the aluminum alloy, and if different chemical reactions occur, the properties and microstructure of the finally obtained material are changed, and the quality of the material is reduced. And the surface hot dipping titanium-aluminum alloy treatment is carried out on the silicon carbide primary product, a silicon carbide-titanium-aluminum alloy transition layer can be formed on the surface of the porous framework of the silicon carbide primary product, in the process of the action of the aluminum liquid and the silicon carbide, the aluminum and the titanium-aluminum alloy can generate exothermic chemical reaction, the reaction between the aluminum liquid and the silicon carbide is promoted, the interface bonding force between the aluminum and the silicon carbide is greatly improved, and further the excellent metallurgical bonding is formed between the aluminum and the silicon carbide framework.
And S4, mixing the aluminum alloy and the silicon carbide finished product and carrying out pressureless infiltration treatment to obtain the aluminum-based silicon carbide composite material.
In practical application, the aluminum alloy and the silicon carbide finished product are preferably mixed in a nitrogen atmosphere at 850-1000 ℃ and subjected to pressureless infiltration treatment for 2-4 hours to obtain the aluminum-based silicon carbide composite material. The pressureless infiltration process may be performed in a sintering furnace.
As shown in fig. 3, fig. 3 is a cross-sectional view microstructure morphology of the aluminum-based silicon carbide composite material prepared by the method of the present embodiment, and it can be seen from the figure that, when the aluminum-based silicon carbide composite material is prepared by the preparation method provided by the present embodiment, silicon carbide particles are uniformly distributed and well bonded, and the wetting degrees of aluminum liquid and silicon carbide particles are increased, so that the interface recombination of the silicon carbide particles and the aluminum-based silicon carbide composite material is promoted. Despite the enhanced mixing of the particles with the two sizes, the particles are uniformly distributed and no segregation and depletion regions of the particles occur. The densification and the non-porosity of the microstructure prove that the mechanical property of the aluminum-based silicon carbide composite material can be improved by the method provided by the embodiment.
As shown in fig. 4, fig. 4 is a line scan diagram of element distribution between the silicon carbide particles and the aluminum alloy matrix in the aluminum-based silicon carbide composite material prepared by the method of this embodiment, and it can be seen from the line scan diagram that the aluminum element peak is mutated at both sides of the interface where the silicon carbide particles and the aluminum alloy matrix are combined. Aluminum is an alloy matrix element in the aluminum-based silicon carbide composite and is mainly present in the matrix, but line scanning shows that aluminum is also present in the silicon carbide particles, indicating that aluminum has diffused into the silicon carbide particles. The silicon element exists in the aluminum alloy matrix and the silicon carbide particles, but the content of the silicon element in the silicon carbide particles is higher than that in the aluminum alloy matrix, which indicates that the silicon element mainly comes from silicon dioxide formed in the high-temperature oxidation process of the silicon carbide particles. It can also be seen from the line scan results that both magnesium and carbon also showed good diffusion phenomena. The mutual diffusion between the aluminum alloy matrix and the silicon carbide particles in the aluminum-based silicon carbide composite material greatly improves the interface bonding strength between the aluminum alloy matrix and the silicon carbide particles. That is, elements in the aluminum alloy matrix and the silicon carbide particles are diffused into each other, and as a result of the diffusion, the interface bonding is stronger.
In summary, in the method for preparing an aluminum-based silicon carbide composite material provided by this embodiment, a silicon carbide-titanium-aluminum alloy transition layer is formed on the surface of a silicon carbide primary product by performing surface treatment on the silicon carbide primary product, so as to obtain a silicon carbide finished product, and then an aluminum alloy and a silicon carbide finished product are mixed and subjected to non-pressure infiltration treatment, so as to obtain an aluminum-based silicon carbide composite material.
Example 2
The present embodiment provides an aluminum-based silicon carbide composite material prepared by the preparation method of embodiment 1.
Specifically, the aluminum-based silicon carbide composite material comprises the following components in parts by weight: 50-60 parts of aluminum alloy, 50 parts, 52 parts, 54 parts, 56 parts, 58 parts, 60 parts and the like, preferably 55 parts, 40-50 parts of silicon carbide, 40 parts, 42 parts, 44 parts, 46 parts, 48 parts, 50 parts and the like, preferably 45 parts, 0.5-3 parts of titanium aluminum alloy, 0.5 part, 0.8 part, 1 part, 1.2 parts, 1.5 parts, 1.8 parts, 2 parts, 2.2 parts, 2.5 parts, 2.8 parts, 3 parts and the like, which are not limited in the application.
According to the aluminum-based silicon carbide composite material provided by the embodiment, the silicon carbide-titanium-aluminum alloy transition layer is formed between aluminum and silicon carbide in the preparation process, so that the interface bonding force of aluminum and silicon carbide is greatly enhanced by the generation of the silicon carbide-titanium-aluminum alloy transition layer, and the mechanical property and the impact resistance of the aluminum-based silicon carbide composite material are further greatly improved.
Example 3
This example provides a test group and a control group, the aluminum-based silicon carbide composite material of the test group is prepared by the method described in example 1, and the aluminum-based silicon carbide composite material of the control group is prepared by the following method:
(1) selecting magnesium, silicon, beryllium and aluminum to be sequentially subjected to smelting, hot rolling, cold rolling, solid solution and aging treatment to prepare aluminum alloy;
(2) screening silicon carbide particles, mixing and dry-pressing the silicon carbide particles into a green body silicon carbide, and placing the green body silicon carbide into a muffle furnace to pre-oxidize the green body silicon carbide to obtain a silicon carbide primary finished product;
(3) and mixing the aluminum alloy and the silicon carbide primary finished product and carrying out non-pressure infiltration treatment to obtain the aluminum-based silicon carbide composite material.
The bending strength of the aluminum-based silicon carbide composites of the control group and the test group was measured, and the results are shown in fig. 5, in which the horizontal axis of fig. 5 represents the group and the vertical axis of fig. 5 represents the bending strength of the aluminum-based silicon carbide composite, showing that the bending strength of the aluminum-based silicon carbide composite of the test group was improved by 18.2% relative to the control group.
The fracture toughness test of the aluminum-based silicon carbide composite materials of the control group and the test group was performed, and the results are shown in fig. 6, in which the horizontal axis of fig. 6 represents the group and the vertical axis represents the fracture toughness of the aluminum-based silicon carbide composite material, and it can be seen that the fracture toughness of the aluminum-based silicon carbide composite material of the test group is improved by 28.3% compared with the fracture toughness of the control group.
Therefore, the preparation method provided by the application for preparing the aluminum-based silicon carbide composite material can obviously improve the mechanical property and the shock resistance of the aluminum-based silicon carbide composite material, and has the advantages of wide application range and high practical value.
In this document, "upper", "lower", "front", "rear", "left", "right", and the like are used only to indicate relative positional relationships between relevant portions, and do not limit absolute positions of the relevant portions.
In this document, "first", "second", and the like are used only for distinguishing one from another, and do not indicate the degree and order of importance, the premise that each other exists, and the like.
In this context, "equal", "same", etc. are not strictly mathematical and/or geometric limitations, but also include tolerances as would be understood by a person skilled in the art and allowed for manufacturing or use, etc.
Unless otherwise indicated, numerical ranges herein include not only the entire range within its two endpoints, but also several sub-ranges subsumed therein.
The preferred embodiments and examples of the present application have been described in detail with reference to the accompanying drawings, but the present application is not limited to the embodiments and examples described above, and various changes can be made within the knowledge of those skilled in the art without departing from the concept of the present application.
Claims (7)
1. The preparation method of the aluminum-based silicon carbide composite material is characterized by comprising the following steps of:
s1, selecting magnesium, silicon, beryllium and aluminum, and sequentially carrying out smelting, hot rolling, cold rolling, solid solution and aging treatment on the magnesium, the silicon, the beryllium and the aluminum to prepare the aluminum alloy; in S1, the adding amount of magnesium is 1-12 parts by mass, the adding amount of silicon is 5-10 parts by mass, the adding amount of beryllium is 0.1-0.25 part by mass, and the adding amount of aluminum is 77.75-93.9 parts by mass;
s2, screening silicon carbide particles, mixing and dry-pressing the silicon carbide particles into a green body silicon carbide, and placing the green body silicon carbide into a muffle furnace to pre-oxidize the green body silicon carbide to obtain a silicon carbide primary finished product;
s3, performing surface treatment on the silicon carbide primary finished product to form a transition layer on the surface of the silicon carbide primary finished product to obtain a silicon carbide finished product; the transition layer is a silicon carbide-titanium-aluminum alloy transition layer;
and S4, mixing the aluminum alloy and the silicon carbide finished product and carrying out pressureless infiltration treatment to obtain the aluminum-based silicon carbide composite material.
2. The method for preparing an aluminum-based silicon carbide composite material according to claim 1, wherein the S2 includes:
screening silicon carbide particles with the particle size range of 10-100 mu m, mixing the screened silicon carbide particles, dry-pressing the mixture into blank silicon carbide, and carrying out pre-oxidation treatment on the blank silicon carbide to obtain a silicon carbide finished product.
3. The method for preparing an aluminum-based silicon carbide composite material according to claim 1, wherein the S3 comprises:
and carrying out surface hot dipping titanium-aluminum alloy treatment on the silicon carbide primary finished product to form a silicon carbide-titanium-aluminum alloy transition layer on the surface of the silicon carbide primary finished product, so as to obtain a silicon carbide finished product.
4. The method for preparing the aluminum-based silicon carbide composite material according to claim 3, wherein the titanium-aluminum alloy comprises the following components in parts by weight: 38-42 parts of aluminum, 1.5-2.5 parts of niobium and 55.5-60.5 parts of titanium.
5. The method for preparing an aluminum-based silicon carbide composite material according to claim 1, wherein the S4 includes:
and mixing the aluminum alloy and the silicon carbide finished product in the nitrogen atmosphere of 850-1000 ℃ and carrying out pressureless infiltration treatment for 2-4 hours to obtain the aluminum-based silicon carbide composite material.
6. An aluminum-based silicon carbide composite material, characterized in that it is produced by the production method according to any one of claims 1 to 5.
7. The aluminum-based silicon carbide composite material according to claim 6, comprising the following components in parts by weight: 49.5-57 parts of aluminum alloy, 40-50 parts of silicon carbide and 0.5-3 parts of titanium-aluminum alloy.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202011006535.1A CN112111667B (en) | 2020-09-23 | 2020-09-23 | Aluminum-based silicon carbide composite material and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202011006535.1A CN112111667B (en) | 2020-09-23 | 2020-09-23 | Aluminum-based silicon carbide composite material and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN112111667A CN112111667A (en) | 2020-12-22 |
| CN112111667B true CN112111667B (en) | 2022-01-28 |
Family
ID=73800557
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202011006535.1A Active CN112111667B (en) | 2020-09-23 | 2020-09-23 | Aluminum-based silicon carbide composite material and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN112111667B (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113070464B (en) * | 2021-03-19 | 2022-09-06 | 广东省科学院新材料研究所 | Aluminum-based porous composite material, and preparation method and application thereof |
| CN115369291A (en) * | 2022-08-30 | 2022-11-22 | 共享智能装备有限公司 | Metal-based composite material, preparation method and use method thereof |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102806335B (en) * | 2011-05-31 | 2015-07-22 | 比亚迪股份有限公司 | Silicon carbide particle reinforced aluminum matrix composite and preparation method thereof |
| CN102628137A (en) * | 2012-04-24 | 2012-08-08 | 南昌航空大学 | Method for preparing silicon carbide particle reinforced aluminum-based composites |
-
2020
- 2020-09-23 CN CN202011006535.1A patent/CN112111667B/en active Active
Also Published As
| Publication number | Publication date |
|---|---|
| CN112111667A (en) | 2020-12-22 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN112111667B (en) | Aluminum-based silicon carbide composite material and preparation method thereof | |
| KR100768700B1 (en) | Fabrication method of alloy parts by metal injection molding and the alloy parts | |
| CN112267039B (en) | Preparation process of high volume fraction silicon carbide particle reinforced aluminum matrix composite | |
| CN113862540B (en) | MAX phase added molybdenum alloy and preparation method thereof | |
| CN114525424B (en) | Titanium-based composite material and preparation method thereof | |
| CN114525438A (en) | Tungsten-copper composite material and preparation method thereof | |
| CN110358960A (en) | A kind of preparation method of high-strength and high ductility Ti (C, N) based ceramic metal | |
| CN114574732B (en) | Particle reinforced aluminum-based composite material and preparation method thereof | |
| CN111195724B (en) | Ti (C, N) -based cermet nitrogen atmosphere sintering process | |
| CN113798488B (en) | Aluminum-based powder metallurgy material and preparation method thereof | |
| CN112775427B (en) | Preparation method of high-density near-net-shape titanium alloy | |
| CN114438362A (en) | Aluminum-based silicon carbide composite material and preparation method thereof | |
| CN111485141B (en) | SiC particle reinforced aluminum titanium matrix composite material and preparation method thereof | |
| CN111411249B (en) | Preparation method of VNbMoTaW high-entropy alloy | |
| CN107937840A (en) | A kind of titanium-aluminium alloy composite material and preparation method thereof | |
| JP3830733B2 (en) | Particle-dispersed silicon material and manufacturing method thereof | |
| Chen et al. | Electrical, thermal, and mechanical properties of Cu/Ti 3 AlC 2 functional gradient materials prepared by low-temperature spark plasma sintering | |
| CN116144968B (en) | Ti with excellent room temperature plasticity2Preparation method of AlNb-based composite material | |
| CN116987924B (en) | Preparation method of SiC/Al composite material | |
| CN114643359B (en) | Preparation method of high-strength powder metallurgy Ti-W alloy bar | |
| CN115747591B (en) | High-toughness aluminum alloy material and preparation process thereof | |
| CN112919923B (en) | Metal matrix composite material and preparation method and application thereof | |
| CN118106491B (en) | Powder injection molding silicon carbide copper composite material and preparation method thereof | |
| CN113512661B (en) | Diamond @ TiC enhanced high-strength conductive copper-based composite material and preparation method thereof | |
| EP2467223A1 (en) | A process for producing a metal-matrix composite of significant cte between the hard base-metal and the soft matrix |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |