CN113957297B - Silicon carbide particle reinforced aluminum matrix composite material, and preparation method and application thereof - Google Patents
Silicon carbide particle reinforced aluminum matrix composite material, and preparation method and application thereof Download PDFInfo
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- CN113957297B CN113957297B CN202111228846.7A CN202111228846A CN113957297B CN 113957297 B CN113957297 B CN 113957297B CN 202111228846 A CN202111228846 A CN 202111228846A CN 113957297 B CN113957297 B CN 113957297B
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- HBMJWWWQQXIZIP-UHFFFAOYSA-N silicon carbide Chemical compound [Si+]#[C-] HBMJWWWQQXIZIP-UHFFFAOYSA-N 0.000 title claims abstract description 74
- 229910010271 silicon carbide Inorganic materials 0.000 title claims abstract description 73
- 239000002245 particle Substances 0.000 title claims abstract description 67
- 239000002131 composite material Substances 0.000 title claims abstract description 49
- 239000011159 matrix material Substances 0.000 title claims abstract description 47
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 title claims abstract description 44
- 229910052782 aluminium Inorganic materials 0.000 title claims abstract description 38
- 238000002360 preparation method Methods 0.000 title claims abstract description 10
- 239000000843 powder Substances 0.000 claims abstract description 75
- 238000000034 method Methods 0.000 claims abstract description 32
- 239000002994 raw material Substances 0.000 claims abstract description 27
- 238000005242 forging Methods 0.000 claims abstract description 20
- 238000005245 sintering Methods 0.000 claims abstract description 19
- 229910002482 Cu–Ni Inorganic materials 0.000 claims abstract description 18
- 238000002156 mixing Methods 0.000 claims abstract description 16
- 238000010438 heat treatment Methods 0.000 claims description 30
- 229910052720 vanadium Inorganic materials 0.000 claims description 13
- 239000000203 mixture Substances 0.000 claims description 12
- 238000007723 die pressing method Methods 0.000 claims description 10
- 238000003825 pressing Methods 0.000 claims description 8
- 239000012298 atmosphere Substances 0.000 claims description 4
- 150000001875 compounds Chemical class 0.000 claims description 4
- 239000006104 solid solution Substances 0.000 claims description 4
- 230000001681 protective effect Effects 0.000 claims description 3
- 239000004411 aluminium Substances 0.000 claims 1
- 230000008569 process Effects 0.000 abstract description 19
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- 239000012071 phase Substances 0.000 description 20
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- 238000001816 cooling Methods 0.000 description 4
- 238000000280 densification Methods 0.000 description 4
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- 229910016343 Al2Cu Inorganic materials 0.000 description 2
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
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- 229910018173 Al—Al Inorganic materials 0.000 description 1
- 229910018182 Al—Cu Inorganic materials 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical group [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 1
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- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- XOOUIPVCVHRTMJ-UHFFFAOYSA-L zinc stearate Chemical compound [Zn+2].CCCCCCCCCCCCCCCCCC([O-])=O.CCCCCCCCCCCCCCCCCC([O-])=O XOOUIPVCVHRTMJ-UHFFFAOYSA-L 0.000 description 1
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- 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/02—Compacting only
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/10—Sintering only
- B22F3/1003—Use of special medium during sintering, e.g. sintering aid
- B22F3/1007—Atmosphere
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/10—Sintering only
- B22F3/1017—Multiple heating or additional steps
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/10—Sintering only
- B22F3/1035—Liquid phase sintering
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/17—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by forging
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- 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
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/05—Mixtures of metal powder with non-metallic powder
-
- 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
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16D—COUPLINGS FOR TRANSMITTING ROTATION; CLUTCHES; BRAKES
- F16D69/00—Friction linings; Attachment thereof; Selection of coacting friction substances or surfaces
- F16D69/02—Composition of linings ; Methods of manufacturing
- F16D69/027—Compositions based on metals or inorganic oxides
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16D—COUPLINGS FOR TRANSMITTING ROTATION; CLUTCHES; BRAKES
- F16D2200/00—Materials; Production methods therefor
- F16D2200/0004—Materials; Production methods therefor metallic
- F16D2200/0026—Non-ferro
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16D—COUPLINGS FOR TRANSMITTING ROTATION; CLUTCHES; BRAKES
- F16D2200/00—Materials; Production methods therefor
- F16D2200/0004—Materials; Production methods therefor metallic
- F16D2200/0026—Non-ferro
- F16D2200/003—Light metals, e.g. aluminium
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16D—COUPLINGS FOR TRANSMITTING ROTATION; CLUTCHES; BRAKES
- F16D2200/00—Materials; Production methods therefor
- F16D2200/006—Materials; Production methods therefor containing fibres or particles
- F16D2200/0065—Inorganic, e.g. non-asbestos mineral fibres
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16D—COUPLINGS FOR TRANSMITTING ROTATION; CLUTCHES; BRAKES
- F16D2200/00—Materials; Production methods therefor
- F16D2200/0082—Production methods therefor
- F16D2200/0086—Moulding materials together by application of heat and pressure
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16D—COUPLINGS FOR TRANSMITTING ROTATION; CLUTCHES; BRAKES
- F16D2250/00—Manufacturing; Assembly
- F16D2250/0023—Shaping by pressure
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- Engineering & Computer Science (AREA)
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- Manufacturing & Machinery (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- General Engineering & Computer Science (AREA)
- Inorganic Chemistry (AREA)
- Powder Metallurgy (AREA)
- Manufacture Of Alloys Or Alloy Compounds (AREA)
Abstract
The application relates to a silicon carbide particle reinforced aluminum matrix composite material, a preparation method and application thereof. The composite material is prepared by taking SiC particles, Al-12Fe-2V-3Si powder, Cu-Ni powder and Al powder as raw materials through mixing, die forming, sintering and hot forging, has good wear resistance and high-temperature strength, can avoid material softening caused by high temperature in the braking process when applied to a brake disc, has good heat conductivity, and can effectively reduce the temperature rise of a friction surface.
Description
Technical Field
The invention relates to the technical field of composite materials, in particular to a silicon carbide particle reinforced aluminum matrix composite material, and a preparation method and application thereof.
Background
The light weight is one of the most effective means for realizing energy conservation and consumption reduction of automobiles and other traffic vehicles. The high-performance light metal material is adopted to replace steel materials to be applied to key moving parts such as an engine, a brake disc and the like of the traffic equipment, so that the weight of the whole vehicle can be reduced, the momentum of high-speed moving parts of the traffic equipment can be reduced, the power performance of the traffic equipment can be remarkably improved, and the energy consumption can be reduced.
The silicon carbide particle reinforced aluminum matrix composite has low density, high specific strength and specific stiffness, high thermal conductivity, excellent wear resistance, wear resistance and corrosion resistance, and wide application prospect in the field of lightweight structural members, and the silicon carbide particle reinforced aluminum matrix composite is adopted to replace the traditional brake disc material and also becomes the main research direction of the lightweight of the current traffic vehicles, however, the application of the silicon carbide particle reinforced aluminum matrix composite on the traffic vehicle brake disc is not optimistic, which is mainly caused by the following two problems: firstly, the plasticity and toughness of the traditional silicon carbide particle reinforced aluminum matrix composite are low, and thermal fatigue cracks are easy to be generated on the surface of a brake disc; secondly, the traditional silicon carbide particle reinforced aluminum matrix composite material has poor temperature resistance, and the strength of the material is obviously reduced when the temperature exceeds 400 ℃. Therefore, it is urgent to find a new silicon carbide particle reinforced aluminum matrix composite material with better mechanical property and temperature resistance.
Disclosure of Invention
Based on this, there is a need to provide a silicon carbide particle reinforced aluminum matrix composite material with better mechanical properties and temperature resistance.
A preparation method of silicon carbide particle reinforced aluminum matrix composite material comprises the following steps:
providing the following raw materials: silicon carbide particles, Al-12Fe-2V-3Si powder, Cu-Ni powder and aluminum powder, wherein the mass content of Ni in the Cu-Ni powder is 0-20%;
and after uniformly mixing the raw materials, sequentially carrying out die pressing forming, sintering and hot forging to obtain the silicon carbide particle reinforced aluminum matrix composite.
In one embodiment, the raw materials comprise the following components in percentage by mass:
in one embodiment, the raw materials comprise the following components in percentage by mass:
in one embodiment, the silicon carbide particles have a particle size of 20 μm to 50 μm; the granularity of the Al-12Fe-2V-3Si powder is-200 meshes; the granularity Dv50 of the Cu-Ni powder is 10-20 mu m; the granularity of the aluminum powder is 10-15 mu m.
In one embodiment, the Al-12Fe-2V-3Si powder consists essentially of an alpha-Al solid solution and Al13(Fe,V)3And a Si compound.
In one embodiment, the unit pressing pressure of the die pressing forming is 350MPa to 450MPa, and the dwell time is 3s to 8 s.
In one embodiment, the sintering conditions are: in the protective gas atmosphere, the temperature is raised to 200-300 ℃ at the heating rate of 5-15 ℃/min, the temperature is preserved for 30-60 min, then the temperature is raised to 500-540 ℃, the temperature is preserved for 45-90 min, finally the temperature is raised to 550-570 ℃ at the heating rate of 3-10 ℃/min, and the temperature is preserved for 60-120 min.
In one embodiment, the temperature of the hot forging is 420-540 ℃, the pressure is 350-500 MPa, and the pressure is maintained for 3-8 s.
In addition, the application also provides the silicon carbide particle reinforced aluminum matrix composite prepared by the preparation method and the application of the composite on a brake disc.
The preparation method of the silicon carbide particle reinforced aluminum matrix composite takes SiC particles, Al-12Fe-2V-3Si powder, Cu-Ni powder and Al powder as raw materials, and Al powder and Cu-Ni powder react to generate Al-Al powder in the sintering process2Cu eutectic phase, forming transient liquid phase sintering, Al contained in Al-12Fe-2V-3Si powder due to short high temperature retention time13(Fe,V)3Si metastable phase does not undergo significant transformation, while Al13(Fe,V)3The metastable phase heat stability temperature of Si is up to more than 500 ℃, and the temperature resistance of the material can be obviously improved; meanwhile, in the processes of die forming and hot forging, Al powder is subjected to plastic deformation, so that pores among the powder can be effectively filled, the density of the material is remarkably improved, and full compactness is achieved.
The silicon carbide particle reinforced aluminum matrix composite material prepared by the method has good wear resistance and high-temperature strength, can be applied to a brake disc to avoid material softening caused by high temperature in the braking process, has good heat conductivity, and can effectively reduce the temperature rise of a friction surface.
Drawings
FIG. 1 is an X-ray diffraction pattern of Al-12Fe-2V-3Si powder;
FIG. 2 is an X-ray diffraction pattern of a sample obtained by subjecting the SiC particle-reinforced Al-based composite prepared in example 2 to different heat treatment processes;
FIG. 3 is a scanning electron microscope image of the SiC particle-reinforced Al matrix composite prepared in example 2 after different heat treatment processes;
fig. 4 is a high-power scanning electron microscope image of the silicon carbide particle reinforced aluminum matrix composite prepared in example 2 after different heat treatment processes.
Detailed Description
In order that the invention may be more fully understood, a more particular description of the invention will now be rendered by reference to specific embodiments thereof that are illustrated in the appended drawings. This invention may, however, be embodied in many different forms and should not be construed as limited to the embodiments set forth herein. Rather, these embodiments are provided so that this disclosure will be thorough and complete.
Unless defined otherwise, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this invention belongs. The terminology used in the description of the invention herein is for the purpose of describing particular embodiments only and is not intended to be limiting of the invention. As used herein, the term "and/or" includes any and all combinations of one or more of the associated listed items.
The method for preparing a silicon carbide particle-reinforced aluminum matrix composite according to an embodiment includes the following steps S110 to S150:
s110, providing the following raw materials: silicon carbide (SiC) particles, Al-12Fe-2V-3Si powder, Cu-Ni powder and aluminum (Al) powder.
Wherein the mass content of Ni in the Cu-Ni powder is 0-20%. It is understood that when the mass content of Ni in the Cu — Ni powder is 0, it is copper (Cu) powder.
Further, the particle size of the SiC particles is 20 to 50 μm. The granularity of the Al-12Fe-2V-3Si powder is-200 meshes. The particle size Dv50 of the Cu-Ni powder is 10-20 μm. The granularity of the aluminum powder is 10-15 mu m.
The SiC particles are too fine and are easy to agglomerate in the composite material, and when the SiC particles are applied to a brake disc, the SiC particles are easy to separate from a matrix during braking, so that the abrasion of the surface of the brake disc is aggravated, and the service life of the brake disc is influenced; if the SiC particles are too coarse, the hardening effect of the SiC particles on the matrix can be reduced, the matrix is easy to generate plastic deformation and viscous flow during braking, the abrasion of the brake disc can be aggravated, and the service life of the brake disc is influenced. In the present application, Al is contained in Al-12Fe-2V-3Si powder13(Fe,V)3The Si compound particles can inhibit the plastic deformation and high-temperature viscous flow of the matrix, so that the SiC particles are controlled to be 30-50 mu m, and the heat conduction performance and the wear resistance of the composite material are improved.
Specifically, in the present embodiment, the SiC particles are formed by mixing-320 mesh silicon carbide particles and-500 mesh silicon carbide particles at an equal mass ratio.
By selecting raw materials with proper particle size, soft powder (such as Al powder, Cu powder or Cu-Ni powder) which is easy to plastically deform can be fully dispersed around powder (such as Al-12Fe-2V-3Si powder and SiC particles) which is difficult to deform or filled in gaps of the powder at the initial stage of die filling and pressing, so that high density and strong hardness can be obtained; meanwhile, the matrix can better fix SiC particles so as to avoid the shedding of the SiC particles in the later use process; in addition, Cu-Ni powder with Dv50 of 10-20 μm is also favorable for alloying.
Further, Al-12Fe-2V-3Si powder is prepared by an air atomization process, and the rapid solidification of molten drops and the addition of Si element in the air atomization process can ensure that the needle-shaped Al powder is acicular3Al with Fe equilibrium phase transition to spherical form13(Fe,V)3Metastable phase of Si, so its phase composition is mainly alpha-Al solid solution and Al13(Fe,V)3Si compound (shown in figure 1). Al (aluminum)13(Fe,V)3The Si metastable phase has high thermal stability, and the thermal stability temperature is up to more than 500 ℃.
And S120, uniformly mixing the raw materials to obtain a mixture.
Specifically, the raw materials are uniformly mixed according to the following mass ratio:
further, this application adopts the compounding jar of nylon material to overturn the mixture to above-mentioned raw materials to avoid the compounding in-process to introduce other impurity pollution raw materials. The adoption of the turnover mixing is beneficial to the uniform distribution of SiC particles, the rotation speed of the turnover mixing tank is 60 r/min-90 r/min, and the mixing time is 8 hours-12 hours. (it can be understood that when the mixing tank is large in size, the mixing efficiency is high, the rotating speed and the time can be shortened), and in order to better disperse easily agglomerated SiC particles and Al powder, hard alloy balls with the diameters of 6mm and 8mm are added into the mixing tank respectively (the mass ratio of the two grinding balls is about 1: 1).
The SiC particles, the Al-12Fe-2V-3Si powder, the Cu-Ni powder and the Al powder are used as raw materials, the SiC particles are dispersed around the Al-12Fe-2V-3Si powder in the mixing process and are not obviously aggregated, the SiC particles are not embedded into the Al-12Fe-2V-3Si powder, the fine Al powder and the Cu-Ni powder are fully dispersed around the SiC particles and the Al-12Fe-2V-3Si powder, and the distribution is favorable for full densification of the composite material in the subsequent die forming and hot forging processes of the raw materials.
And S130, carrying out die pressing forming on the mixture to obtain a compact.
Wherein the unit pressing pressure of the die pressing forming is 350 MPa-450 MPa, and the pressure maintaining time is 3 s-8 s.
Furthermore, in order to facilitate the demoulding of the pressed compact after the compression molding, the mixed solution of zinc stearate and absolute ethyl alcohol is needed to lubricate the surface of the punch and the inner wall of the female die before the pressing.
And S140, sintering the green compact to obtain a sintered body.
In the present embodiment, the conditions for sintering are: in a protective gas atmosphere (such as nitrogen), the temperature is raised to 200-300 ℃ at a heating rate of 5-15 ℃/min, the temperature is preserved for 30-60 min, then the temperature is raised to 500-540 ℃, the temperature is preserved for 45-90 min, finally the temperature is raised to 550-570 ℃ at a heating rate of 3-10 ℃/min, and the temperature is preserved for 60-120 min.
The method is characterized in that the temperature is kept at 200-300 ℃ for 30-60 min, the method is mainly used for removing air physically adsorbed on the surface of powder, the temperature is kept at 500-540 ℃ for 45-90 min, the method is mainly used for carrying out homogenization reaction on Cu-Ni powder, aluminum powder and aluminum alloy powder, and the temperature is kept at 550-570 ℃ for 60-120 min, and the method is mainly used for sintering an aluminum alloy matrix.
Under the sintering condition of the application, Al powder in the green compact can react with Cu-Ni powder to generate Al-Al2Cu two-phase eutectic to form transient liquid phase sintering, and Al contained in Al-12Fe-2V-3Si powder due to short high-temperature retention time13(Fe,V)3The metastable phase of Si does not have obvious transformation, so that the material has high thermal stability.
In addition, the instantaneous liquid phase sintering can prevent Al from being separated out, and the mechanical property of the material is effectively improved.
And S150, carrying out hot forging on the sintered body to obtain the silicon carbide particle reinforced aluminum matrix composite.
Wherein the temperature of hot forging is 420-540 ℃, the pressure is 350-500 MPa, and the pressure is maintained for 3-8 s.
Specifically, hot forging is performed in a die, and the die and the above sintered body need to be preheated in consideration of a rapid temperature drop at the time of forging operation. In the present application, the preheating temperature of the mold is 500. + -. 10 ℃ and the preheating temperature of the sintered body is 520. + -. 10 ℃.
It is to be noted that the Al-12Fe-2V-3Si powder contains Al with higher volume fraction and dispersion distribution13(Fe,V)3The Si phase has higher powder hardness and poorer compression deformation performance, the raw materials contain certain porosity after being pressed and sintered, and the density can be greatly improved through hot forging to achieve full compactness.
The silicon carbide particle reinforced aluminum matrix composite material prepared by the method has good wear resistance and high-temperature strength, can avoid material softening caused by high temperature in the braking process when applied to a brake disc, has good heat conductivity, and can effectively reduce the temperature rise of a friction surface.
The following are specific examples.
The raw material compositions of example 1 and example 2 are shown in table 1.
TABLE 1
| Raw material ratio | Example 1 | Example 2 |
| -320 mesh SiC particles (wt.%) | 9.0 | 9.0 |
| -500 mesh SiC particles (wt.%) | 9.0 | 9.0 |
| Al-12Fe-2V-3Si powder (wt.%) | 41.0 | 54.0 |
| Cu-20Ni powder (wt.%) | 4.1 | 4.1 |
| Al powder (wt.%) | 36.9 | 23.9 |
The preparation of example 1 and example 2 is as follows:
(1) the raw materials are uniformly mixed to obtain a mixture, the rotation speed of the mixing tank is 90r/min, and the mixing time is 12 hours.
(2) And carrying out die pressing on the mixture to obtain a pressed compact, wherein the unit pressing pressure of the die pressing is 400MPa, and the pressure maintaining time is 5 s.
(3) Sintering the green compact to obtain a sintered body, wherein the sintering conditions are as follows: heating to 300 deg.C at a heating rate of 10 deg.C/min in nitrogen atmosphere, maintaining for 60min, heating to 510 deg.C, maintaining for 60min, heating to 565 deg.C at 3 deg.C/min, maintaining for 120min, and furnace cooling.
(4) And carrying out hot forging on the sintered body to obtain the silicon carbide particle reinforced aluminum matrix composite, wherein the hot forging temperature is 520 ℃, the pressure is 400-450 MPa, and the pressure maintaining time is 5 s.
The silicon carbide particle reinforced aluminum matrix composite prepared in example 1 can be expressed as: 18SiC- (Al-6Fe-1V-1.5Si-4Cu-1 Ni)); the silicon carbide particle reinforced aluminum matrix composite prepared in example 2 can be expressed as: 18SiC- (Al-8Fe-1.3V-2Si-4Cu-1 Ni). The relative density data are shown in table 2.
TABLE 2
| Example 1 | Example 2 | |
| Green density (g/cm)3) | 2.57 | 2.50 |
| Relative density of green compact (%) | 86.4 | 83.0 |
| Density of forged blank (g/cm)3) | 2.96 | 2.98 |
| Relative density (%) of the forged billet | 99.5 | 99.0 |
As can be seen from Table 2, the average density of the compacts of example 1 after press molding was 2.57g/cm3The theoretical density is 2.947g/cm calculated by a component weighted average method386.4% of; example 2 the average density of the compacts was 2.50g/cm3Is aTheoretical density 3.012g/cm calculated by component weighted average method383.0% of. This indicates that the relative density of the green compact decreases as the content of Al-12Fe-2V-3Si powder in the raw material increases, due to the high volume fraction, dispersed Al content in the Al-12Fe-2V-3Si powder13(Fe,V)3Si phase, high strength and hardness of the powder body, and poor compression set properties. After hot forging, the densities of the silicon carbide particle reinforced aluminum matrix composites prepared in examples 1 and 2 were greatly increased, and sufficient densification was achieved. It is also shown that the relative density of the forged billet decreases as the content of Al-12Fe-2V-3Si powder in the raw material increases.
The samples obtained by subjecting the silicon carbide particle-reinforced aluminum matrix composite prepared in example 2 to different heat treatment processes were subjected to X-ray diffraction, and the results are shown in fig. 2. Wherein T4 represents a state of being naturally aged to a substantially stable state after solution treatment; t6 represents that the solution treatment is added with the complete artificial aging, the artificial aging is directly carried out in the atmosphere (the treatment is the same as that of T8 and T9), the temperature is heated to 165 ℃, the heat is preserved for 8 hours, and the furnace is cooled; t8 represents the steps of after solution treatment, annealing, softening and heating to 280 ℃, preserving heat for 4 hours, and furnace cooling; t9 represents cyclic softening treatment, heating to 450 deg.C, maintaining the temperature for 15min, taking out sample, cooling at room temperature for 15min, and repeating the above steps for 15 times. The solid solution treatment is carried out by adopting a vacuum sintering furnace, firstly, the forged sample is placed in a burning boat, the vacuum is pumped to below 0.1Pa, then the heating function is started, the temperature is heated to 300 ℃, and the heat preservation is carried out for 1 h. Then heating to 525 ℃ and preserving the temperature for 7 h. Taking out the sample, and quickly quenching the sample into warm water at the temperature of 50-80 ℃.
As can be seen from FIG. 2, after the SiC particle-reinforced Al matrix composite prepared in example 2 is subjected to different heat treatment processes, the phase composition in the sample mainly comprises SiC phase and Al phase, and a small amount of Al phase13(Fe,V)3Si and Al2Cu, almost no metastable Al-Cu phase observed and possible Al3(Ni, Cu) and the like. It is explained that the sintering temperature and the hot forging temperature of the present invention both exceed 500 ℃, but Al is formed due to a short residence time at high temperature13(Fe,V)3No obvious transformation of Si metastable phase occurs, and Al appears3An equilibrium phase of Fe.
FIG. 3 is a scanning electron microscope image of the SiC particle-reinforced Al matrix composite prepared in example 2 after the heat treatment of T4, T6, T8 and T9. As can be seen from fig. 3, no significant voids were present in the sample, consistent with the density measurements. In addition, the original Al-12Fe-2V-3Si powder in the composite material still remained nearly spherical, which indicates that densification during pressing and forging was mainly achieved by plastic deformation of the Al powder of the raw material. SiC particles (black) and Al are uniformly distributed around the larger aluminum alloy powder particles2Cu phase (bright color).
Fig. 4 is a high-power scanning electron microscope image of the silicon carbide particle-reinforced aluminum matrix composite prepared in example 2 after the heat treatment of the above T4, T6, T8 and T9. As can be seen from FIG. 4, the SiC particles were dispersed around the original Al-12Fe-2V-3Si powder without significant aggregation and without being embedded into the original Al-12Fe-2V-3Si powder. SiC particles coated with an alloy matrix or Al2The Cu phase is separated. This indicates that the fine Al powder and Cu-20Ni powder are more fully dispersed around the SiC particles during the mixing process, and the distribution is beneficial to the press forming of the blank and the full densification of the composite material during the forging process.
Table 3 shows the room temperature mechanical properties of the silicon carbide particle-reinforced aluminum matrix composites prepared in examples 1 and 2 after different heat treatment processes.
TABLE 3
Table 4 shows the high temperature strength tables of the SiC particle-reinforced Al matrix composites prepared in examples 1 and 2 at 250 deg.C, 300 deg.C, 350 deg.C, 400 deg.C, and 450 deg.C, respectively, after different heat treatment processes.
TABLE 4
Table 5 shows the thermal conductivity at 25 ℃, 200 ℃ and 300 ℃ of the silicon carbide particle-reinforced aluminum matrix composite prepared in example 1 and example 2 respectively after different heat treatment processes.
TABLE 5
The raw material compositions of examples 3 to 5 are shown in table 6.
TABLE 6
Examples 3 to 5 were prepared as follows:
(1) the raw materials are uniformly mixed to obtain a mixture, the rotation speed of the mixing tank is 60 r/min-90 r/min, and the mixing time is 8 h-12 h.
(2) And carrying out die pressing on the mixture to obtain a pressed blank, wherein the unit pressing pressure of the die pressing is 350-450 MPa, and the pressure maintaining time is 3-8 s.
(3) Sintering the green compact to obtain a sintered body, wherein the sintering conditions are as follows: heating to 200-300 ℃ at a heating rate of 5-15 ℃/min in a nitrogen atmosphere, preserving heat for 30-60 min, then raising the temperature to 500-540 ℃, preserving heat for 45-90 min, finally heating to 550-570 ℃ at 3-10 ℃/min, preserving heat for 60-120 min, and furnace cooling.
(4) And carrying out hot forging on the sintered body to obtain the silicon carbide particle reinforced aluminum matrix composite, wherein the hot forging temperature is 420-540 ℃, the pressure is 350-500 MPa, and the pressure maintaining time is 3-8 s.
The above-mentioned embodiments only express several embodiments of the present invention, and the description thereof is more specific and detailed, but not construed as limiting the scope of the present invention. It should be noted that, for a person skilled in the art, several variations and modifications can be made without departing from the inventive concept, which falls within the scope of the present invention. Therefore, the protection scope of the present patent shall be subject to the appended claims.
Claims (5)
1. A preparation method of silicon carbide particle reinforced aluminum matrix composite is characterized by comprising the following steps:
providing the following raw materials: silicon carbide particles, Al-12Fe-2V-3Si powder, Cu-Ni powder and aluminum powder, wherein the mass content of Ni in the Cu-Ni powder is 0-20%, and the Al-12Fe-2V-3Si powder mainly comprises alpha-Al solid solution and Al13(Fe,V)3Si compound composition; the raw materials comprise the following components in percentage by mass:
after uniformly mixing the raw materials, sequentially carrying out die pressing forming, sintering and hot forging to obtain the silicon carbide particle reinforced aluminum matrix composite;
the unit pressing pressure of the die pressing forming is 350 MPa-450 MPa, and the pressure maintaining time is 3 s-8 s;
the sintering conditions are as follows: in a protective gas atmosphere, firstly heating to 200-300 ℃ at a heating rate of 5-15 ℃/min, preserving heat for 30-60 min, then heating to 500-540 ℃, preserving heat for 45-90 min, finally heating to 550-570 ℃ at a heating rate of 3-10 ℃/min, and preserving heat for 60-120 min;
the temperature of the hot forging is 420-540 ℃, the pressure is 350-500 MPa, and the pressure maintaining time is 3-8 s.
2. The method for preparing silicon carbide particle-reinforced aluminum matrix composite according to claim 1, wherein the silicon carbide particle-reinforced aluminum matrix composite comprises the following raw materials in percentage by mass:
3. the method for preparing a silicon carbide particle-reinforced aluminum matrix composite as claimed in claim 1 or 2, wherein the silicon carbide particles have a particle size of 20 to 50 μm; the granularity of the Al-12Fe-2V-3Si powder is-200 meshes; the granularity Dv50 of the Cu-Ni powder is 10-20 mu m; the granularity of the aluminum powder is 10-15 mu m.
4. A silicon carbide particle reinforced aluminum matrix composite material prepared by the preparation method of any one of claims 1 to 3.
5. Use of a silicon carbide particle reinforced aluminium matrix composite according to claim 4 in a brake disc.
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