CN114574725B - Al (aluminum) 2 O 3 Preparation and deformation method of/Al high-temperature-resistant aluminum-based composite material - Google Patents
Al (aluminum) 2 O 3 Preparation and deformation method of/Al high-temperature-resistant aluminum-based composite material Download PDFInfo
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- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 title claims abstract description 69
- 229910052782 aluminium Inorganic materials 0.000 title claims abstract description 36
- 239000002131 composite material Substances 0.000 title claims abstract description 34
- 238000000034 method Methods 0.000 title claims abstract description 25
- 238000002360 preparation method Methods 0.000 title claims abstract description 18
- 239000000463 material Substances 0.000 claims abstract description 35
- 238000005245 sintering Methods 0.000 claims abstract description 31
- 238000001125 extrusion Methods 0.000 claims abstract description 25
- 239000011159 matrix material Substances 0.000 claims abstract description 16
- 238000000137 annealing Methods 0.000 claims abstract description 15
- 229910018072 Al 2 O 3 Inorganic materials 0.000 claims abstract description 12
- 230000003647 oxidation Effects 0.000 claims abstract description 7
- 238000007254 oxidation reaction Methods 0.000 claims abstract description 7
- 238000007731 hot pressing Methods 0.000 claims abstract description 6
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 claims description 8
- 238000005096 rolling process Methods 0.000 claims description 8
- 239000002245 particle Substances 0.000 claims description 7
- 238000004663 powder metallurgy Methods 0.000 claims description 7
- 238000000748 compression moulding Methods 0.000 claims description 3
- 238000001513 hot isostatic pressing Methods 0.000 claims description 3
- 238000005516 engineering process Methods 0.000 claims description 2
- 238000010884 ion-beam technique Methods 0.000 claims description 2
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 abstract description 34
- MXRIRQGCELJRSN-UHFFFAOYSA-N O.O.O.[Al] Chemical compound O.O.O.[Al] MXRIRQGCELJRSN-UHFFFAOYSA-N 0.000 abstract description 13
- 230000008569 process Effects 0.000 abstract description 12
- 230000000694 effects Effects 0.000 abstract description 10
- 238000005728 strengthening Methods 0.000 abstract description 6
- 238000002425 crystallisation Methods 0.000 abstract description 4
- 230000008025 crystallization Effects 0.000 abstract description 4
- 230000002195 synergetic effect Effects 0.000 abstract description 4
- 239000002105 nanoparticle Substances 0.000 abstract description 2
- 238000007670 refining Methods 0.000 abstract description 2
- 238000003466 welding Methods 0.000 description 12
- 230000003014 reinforcing effect Effects 0.000 description 11
- 238000003756 stirring Methods 0.000 description 9
- 238000000465 moulding Methods 0.000 description 8
- 230000000052 comparative effect Effects 0.000 description 7
- 238000001192 hot extrusion Methods 0.000 description 7
- 230000009467 reduction Effects 0.000 description 7
- 239000013078 crystal Substances 0.000 description 5
- 239000000203 mixture Substances 0.000 description 4
- 238000003825 pressing Methods 0.000 description 4
- 238000011065 in-situ storage Methods 0.000 description 3
- 229910000838 Al alloy Inorganic materials 0.000 description 2
- 230000009471 action Effects 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 238000003860 storage Methods 0.000 description 2
- 229910001008 7075 aluminium alloy Inorganic materials 0.000 description 1
- 239000011358 absorbing material Substances 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 230000007123 defense Effects 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- 238000010406 interfacial reaction Methods 0.000 description 1
- 239000003562 lightweight material Substances 0.000 description 1
- 238000005551 mechanical alloying Methods 0.000 description 1
- 230000008929 regeneration Effects 0.000 description 1
- 238000011069 regeneration method Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 238000003786 synthesis reaction Methods 0.000 description 1
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- C22C32/001—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 only oxides
- C22C32/0015—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 only oxides with only single oxides as main non-metallic constituents
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Abstract
The invention discloses Al 2 O 3 A preparation and deformation method of a/Al high-temperature resistant aluminum matrix composite belongs to the technical field of aluminum matrix composites. The specific method comprises the following steps: (1) Introducing amorphous alumina by utilizing the natural oxidation of the surface of the superfine aluminum powder; (2) maintaining its amorphous state by controlling the hot pressing process; (3) Obtaining an ultra-fine grain structure by utilizing the grain refining function of the ultra-fine grain structure in the rapid low-temperature extrusion process; (4) High temperature annealing to convert amorphous alumina to stable crystalline alumina; (5) And plastic deformation is carried out to eliminate the holes left in the sintering and extruding processes and formed in the crystallization process and obtain the final required plate. The scheme can simultaneously utilize the grain refinement effect of amorphous alumina and the high thermal stability of crystalline alumina, and the obtained material obtains good high-temperature performance by virtue of the synergistic strengthening effect of nano particles and grain boundaries and has excellent thermal stability and weldability.
Description
Technical Field
The invention relates to the technical field of aluminum-based composite materials, in particular to Al 2 O 3 A method for preparing and deforming a/Al high-temperature-resistant aluminum-based composite material.
Background
The aluminum-based material is an important lightweight material and plays an unremarkable role in the fields of national defense and military industry, aerospace, rail traffic and the like. With the rapid development of the industrial level, especially the replacement of some sophisticated equipment puts higher demands on the relevant materials, wherein the high temperature resistance of the materials is particularly important. However, the high-temperature performance of the existing aluminum alloy can not meet corresponding requirements, and the realization of lightweight of advanced equipment is severely restricted.
The aluminum-based composite material takes pure aluminum as a matrix, and the mechanical property is enhanced by adding a reinforcing phase. Among them, alumina has good compatibility with an aluminum matrix, no interfacial reaction, and excellent high-temperature thermal stability in the matrix, and is considered as an ideal high-temperature strengthening phase. The addition of the reinforcing phase can improve the strength of the material, but also reduce the plasticity of the material. Such as the literature "Effect of nano-size Al 2 O 3 In the regeneration on the mechanical floor of synthesis 7075aluminum alloys by mechanical alloying (Materials Chemistry and Physics 138 (2013) 535-541), the elongation of the material was less than 5% after 5% of alumina was added. Therefore, increasing the reinforcing efficiency of the reinforcing phase to reduce its addition amount is key to making the material have excellent strong plastic matching. Alumina introduced by an in situ manner may have a more superior enhancement efficiency than added alumina introduced by conventional methods. The document "formed HITEMAL Al-based MMCs strained bonded with nanometric thick Al 2 O 3 skeleton”(Materials Science&Engineering A613 (2014) 82-90), the alumina formed on the surface of the aluminum powder in situ can have extremely high enhancing efficiency, and the performance of the material can be obviously improved by adding a small amount of the alumina, so that the material obtains excellent strong plastic matching.
However, among the above materialsAlumina is amorphous and not a high temperature stable phase, and it is transformed into crystalline alumina over a certain period of time under the action of high temperature or under the action of severe mechanical deformation during friction stir welding (B) (the literature "microscopic and mechanical property evaluation of crystallization solid welded 4 C+Al 2 O 3 ) Al compositions designed for neutron absorbing materials "(Science China-technical Sciences, 2020; 63:1256). After the crystallization of the aluminum oxide, the strengthening efficiency is reduced, and holes are generated due to the increase of density, so that the local strength of a heated part is reduced or the strength of a welding joint area is low (the welding strength coefficient is about 70%), deformation is localized when stress is applied, and serious risks are caused. For example, when the amorphous alumina is crystallized during hot pressing, crystalline alumina is obtained, although the performance of the obtained material is stable, the grain refinement capability of the granular crystalline alumina is weak, so that the deformed structure is not a fine-grained structure (as shown in fig. 1), and the enhancement efficiency of the crystalline alumina is low, so that the effective synergistic enhancement of the alumina and the grain boundary is difficult, and the strength of the material is low. Patent application number 201811453938.3' a high-temperature resistant AlN and Al 2 O 3 In the co-reinforced aluminum-based composite material and the preparation method thereof, a large amount of stable crystalline aluminum oxide can be introduced by performing surface pre-oxidation on superfine aluminum powder, but the oxidation process needs to be strictly controlled, and the process flexibility is poor.
In fact, nanoparticles are introduced into the ultra-fine grain structure, and the synergistic strengthening effect of the particles and the grain boundary is a powerful means for improving the high-temperature strength. Therefore, the formation of the ultrafine grain structure is an effective means for obtaining high strength, and the ultrafine grain structure can be obtained by utilizing the grain refinement effect of the amorphous alumina and adopting the process parameters in a specific range. However, the above schemes cannot simultaneously utilize the grain refinement effect of amorphous alumina and the thermal stability of crystalline alumina to obtain a high temperature resistant aluminum-based material having mechanical properties, thermal stability, weldability, and both manufacturability and preparation cost.
Disclosure of Invention
The invention aims to provide Al 2 O 3 Method for preparing and deforming Al high-temperature-resistant aluminum-based composite material by fully utilizing amorphous aluminaThe grain refinement effect and the excellent thermal stability of the crystalline alumina, and the prepared material has good high-temperature mechanical property, thermal stability and weldability, thereby solving the problem of the existing Al 2 O 3 The Al material has poor strong plastic matching or poor high-temperature stability and is difficult to weld, and large-scale industrial production can be carried out.
In order to achieve the purpose, the technical scheme adopted by the invention is as follows:
al 2 O 3 The preparation and deformation method of the Al high-temperature resistant aluminum matrix composite material comprises the following steps:
(1) Carrying out oxidation treatment on the superfine aluminum powder to form an aluminum oxide film on the surface of the superfine aluminum powder;
(2) Carrying out powder metallurgy sintering on the pressed compact obtained after compression molding to obtain Al 2 O 3 Al ingots;
(3) Extruding the billet obtained in the step (2);
(4) Carrying out high-temperature annealing treatment on the material obtained by extrusion in the step (3);
(5) And (4) rolling or extruding the material obtained in the step (4) for the second time to obtain the high-temperature-resistant aluminum-based composite material.
In the step (1), the average grain diameter of the superfine aluminum powder is 0.1-2 μm, so that enough aluminum oxide can be introduced, and the thickness of the aluminum oxide film is 3-12 nm.
In the step (2), the powder metallurgy sintering adopts vacuum hot pressing sintering, hot isostatic pressing or spark ion beam sintering technology under atmosphere or vacuum condition, preferably vacuum hot pressing sintering and hot isostatic pressing, wherein the sintering temperature in the powder metallurgy sintering is 300-540 ℃, and the time is 0.5-6 hours.
In the step (3), the extrusion ratio is 4:1-9:1, extruding the mixture to be in a belt plate or round bar shape at the temperature of 180-480 ℃ and the speed of 50-800 mm/s.
In the step (4), the high-temperature annealing temperature is 580-630 ℃, and the time is 2-12 hours.
In the step (5), the extrusion or rolling temperature is 350-500 ℃, and the deformation ratio is 2:1-12:1, finally deforming to the required shape.
The invention has the following advantages and beneficial effects:
al of the invention 2 O 3 The preparation and deformation method of the Al high-temperature resistant aluminum matrix composite material comprises the following steps: introducing amorphous alumina by utilizing in-situ oxidation of the surface of the superfine aluminum powder, and controlling a hot pressing process to ensure the amorphous state of the superfine aluminum powder; obtaining an ultra-fine grain structure by rapid and low-temperature extrusion and by means of the grain refining effect of the amorphous alumina in the extrusion process; amorphous alumina is converted into high-stability crystalline alumina through high-temperature annealing, and then holes formed in the processes of sintering and extrusion and crystallization are eliminated through plastic deformation, so that the required plate-shaped material is obtained. In the annealing and plastic deformation processes, crystalline alumina can pin the grain boundary to prevent the grains from coarsening, and the high-strength fine-grained structure material is finally obtained by utilizing the synergistic strengthening effect of the grains and the grain boundary.
The prepared material has excellent mechanical properties at high temperature, for example, the strength can reach more than 80MPa at 350 ℃, the strength is more than 50MPa higher than that of aluminum alloy, and the material has excellent plasticity and the elongation is more than 10%. Compared with the composite material with amorphous alumina as the final strengthening phase, the composite material has excellent thermal stability and can realize equal-strength welding through friction stir welding, and the prepared plate is annealed at 600 ℃ for 10 hours without strength reduction. The preparation process is simple, can realize large-scale industrial preparation, has both strong plasticity and good formability and processability.
Drawings
Fig. 1 shows the coarse grains in comparative example 2.
FIG. 2 shows the microstructure of the material of example 1.
Detailed Description
The invention is described in detail below with reference to the figures and examples.
The invention is Al 2 O 3 The preparation and deformation method of the Al high-temperature resistant aluminum matrix composite material comprises the following steps:
(1) Carrying out oxidation treatment on the superfine aluminum powder to form an aluminum oxide film on the surface of the superfine aluminum powder;
(2) Carrying out powder metallurgy sintering on the pressed compact obtained after compression molding to obtain Al 2 O 3 Al billetAn ingot;
(3) Extruding the billet obtained in the step (2);
(4) Carrying out high-temperature annealing treatment on the material obtained by extrusion in the step (3);
(5) And (4) rolling or extruding the material obtained in the step (4) for the second time to obtain the high-temperature-resistant aluminum-based composite material.
By adopting the method, the grain refinement effect of the amorphous alumina and the high-temperature thermal stability of the crystalline alumina can be simultaneously utilized to finally obtain the ultrafine crystal grain structure, thereby obtaining excellent high-temperature thermal stability and weldability.
Example 1
Spherical aluminum powder (the thickness of an alumina film is 3-12 nm) with the average grain diameter of 1.8 mu m is selected, the spherical aluminum powder is formed by cold pressing under 200MPa, the spherical aluminum powder is placed into a vacuum furnace to be sintered for 2 hours at 500 ℃, a sintered billet is subjected to hot extrusion at 400 ℃, the extrusion ratio is 6. The extruded strip was annealed at 580 ℃ for 8 hours and then rolled through 4.
Al produced by the example 2 O 3 The Al high-temperature resistant aluminum-based composite material has a fine crystalline structure, and a reinforcing phase is crystalline alumina with high thermal stability (as shown in figure 2). The yield strength is 75MPa, the tensile strength is 90MPa and the elongation is 14 percent at 350 ℃. The final plate was annealed at 600 ℃ for 10h without strength reduction. After the optimized friction stir welding, the strength coefficient of the joint is 95%.
Example 2
Selecting spherical aluminum powder (the thickness of an alumina film is 3-12 nm) with the average grain diameter of 1.8 μm, cold-pressing and molding under 200MPa, then placing the spherical aluminum powder into a vacuum furnace for sintering for 2 hours at 500 ℃, and hot-extruding a sintering billet at 400 ℃ at an extrusion ratio of 4. The extruded strip was annealed at 580 ℃ for 8 hours and then rolled through 4.
Al produced by this example 2 O 3 The Al high-temperature resistant aluminum-based composite material is a fine-grained structure, and the reinforced phase is crystalline alumina with high thermal stability. The yield strength is 70MPa, the tensile strength is 85MPa and the elongation is 16 percent at 350 ℃. The final plate was annealed at 600 ℃ for 10h without strength reduction. After the optimized stirring friction welding is carried out,the joint strength factor was 96%.
Example 3
Selecting spherical aluminum powder (the thickness of an alumina film is 3-12 nm) with the average particle size of 1.8 mu m, performing cold press molding under 200MPa, then placing the spherical aluminum powder into a vacuum furnace for sintering for 2 hours at 500 ℃, and performing hot extrusion on a sintered billet at 400 ℃ at an extrusion ratio of 9. The extruded strip was annealed at 580 ℃ for 8 hours and then rolled at 4.
Al produced by this example 2 O 3 The Al high-temperature resistant aluminum-based composite material is a fine-grained structure, and a reinforcing phase is crystalline alumina with high thermal stability. The yield strength is 79MPa, the tensile strength is 95MPa and the elongation is 11 percent at 350 ℃. The final plate was annealed at 600 ℃ for 10h without strength reduction. After the optimized friction stir welding, the strength coefficient of the joint is 95%.
Example 4
Spherical aluminum powder (the thickness of an alumina film is 3-12 nm) with the average grain diameter of 1.2 microns is selected, cold pressing molding is carried out under 200MPa, then the spherical aluminum powder is placed into a vacuum furnace for sintering for 2 hours at 500 ℃, a sintering billet is subjected to hot extrusion at 400 ℃, the extrusion ratio is 6. The extruded strip was annealed at 580 ℃ for 8 hours and then rolled at 4.
Al produced by the example 2 O 3 The Al high-temperature resistant aluminum-based composite material is a fine-grained structure, and a reinforcing phase is crystalline alumina with high thermal stability. The yield strength is 81MPa, the tensile strength is 96MPa and the elongation is 12 percent at 350 ℃. The final plate was annealed at 600 ℃ for 10h without strength reduction. After the optimized friction stir welding, the strength coefficient of the joint is 94%.
Example 5
Spherical aluminum powder (the thickness of an alumina film is 3-12 nm) with the average grain diameter of 0.8 mu m is selected, the mixture is cold-pressed and molded under 200MPa, then the mixture is placed into a vacuum furnace to be sintered for 2 hours at the temperature of 520 ℃, a sintered billet is hot-extruded at the temperature of 420 ℃, the extrusion ratio is 6. The extruded strip was annealed at 580 ℃ for 8 hours and then rolled at 4.
Al produced by the example 2 O 3 The Al high-temperature resistant aluminum-based composite material is a fine crystal groupThe reinforcing phase is crystalline alumina with high thermal stability. The yield strength is 95MPa, the tensile strength is 103MPa and the elongation is 10 percent at 350 ℃. The final plate was annealed at 600 ℃ for 10h without strength reduction. After the optimized friction stir welding, the strength coefficient of the joint is 92%.
Example 6
Selecting spherical aluminum powder (the thickness of an alumina film is 3-12 nm) with the average particle size of 1.8 mu m, performing cold press molding under 200MPa, then placing the spherical aluminum powder into a vacuum furnace for sintering for 2 hours at 500 ℃, and performing hot extrusion on a sintered billet at 400 ℃ at an extrusion ratio of 9. Annealing the extruded strip plate at 580 ℃ for 8 hours, and then carrying out 6:1 extruding to obtain the final plate.
Al produced by the example 2 O 3 The Al high-temperature resistant aluminum-based composite material is a fine-grained structure, and a reinforcing phase is crystalline alumina with high thermal stability. The yield strength is 80MPa, the tensile strength is 97MPa and the elongation is 11 percent at 350 ℃. The final plate was annealed at 600 ℃ for 10h without strength reduction. After the optimized friction stir welding, the strength coefficient of the joint is 94%.
Comparative example 1
Selecting spherical aluminum powder with the average particle size of 6 microns, performing cold press molding under 200MPa, sintering in a vacuum furnace at 500 ℃ for 2 hours, and performing hot extrusion on a sintering billet at 450 ℃ at an extrusion ratio of 6. And annealing the extruded strip plate at 580 ℃ for 8 hours, and then rolling to obtain a final plate.
Al produced by this example 2 O 3 The Al material has insufficient alumina content, 45MPa of yield strength at 350 ℃, 56MPa of tensile strength and 16 percent of elongation. The material has low strength and can not meet the dry storage requirement.
Comparative example 2
Selecting spherical aluminum powder with the average grain diameter of 1.8 mu m, cold-pressing and molding under 200MPa, sintering for 2 hours in a vacuum furnace at 630 ℃, and hot-extruding a sintered billet at 450 ℃ to obtain the composite material belt plate.
Al produced by this example 2 O 3 The final crystal grain of Al is thicker (as shown in figure 1), the yield strength at 350 ℃ is 52MPa, the tensile strength is 61MPa, and the elongation is 13 percent. The material has low strength and cannot meet the requirement of drynessThe formula (I) storage requirement.
Comparative example 3
And (2) selecting spherical aluminum powder with the average particle size of 1.8 microns, carrying out cold press molding under 200MPa, then placing the spherical aluminum powder into a vacuum furnace for sintering for 2 hours at 500 ℃, and carrying out hot extrusion on a sintered billet at 450 ℃, wherein the extrusion ratio is 12.
Al produced by this example 2 O 3 The reinforcing phase in the/Al is amorphous alumina. The strength of the final plate is reduced by 30 percent after the final plate is annealed for 24 hours at 500 ℃. And after the extruded sheet is subjected to optimized friction stir welding, the strength coefficient of the joint is only 70%, deformation is concentrated in a weld nugget area, and the elongation of the joint is less than 5%.
Comparative example 4
The method comprises the following steps of selecting spherical aluminum powder with the average particle size of 1.8 mu m, carrying out cold press molding under 200MPa, then placing the spherical aluminum powder into a vacuum furnace for sintering at 500 ℃ for 2 hours, carrying out hot extrusion on a sintered billet at 450 ℃, carrying out an extrusion ratio of 12 to 1, and carrying out annealing at 580 ℃ for 8 hours to convert amorphous alumina into stable crystalline alumina to obtain the final plate.
Al produced by this example 2 O 3 Although the reinforcing phase in the Al is stable crystalline alumina, the composite material plate obtained after the large extrusion ratio has larger size, the composite material plate is difficult to anneal by a conventional annealing furnace, and in the annealing process, holes appear in the material due to the increase of the density of the alumina, and the final uniform elongation of the material is less than 5%.
Comparative example 5
Spherical aluminum powder with the average grain diameter of 1.8 mu m is selected, cold-pressed and molded under 200MPa, and then placed into a vacuum furnace for sintering for 2 hours at 500 ℃, and a sintering billet is hot-extruded at 510 ℃, the extrusion ratio is 6. And annealing the extruded strip plate at 580 ℃ for 8 hours, and then rolling to obtain a final plate.
Al production by Using this example 2 O 3 Al, because the extrusion is too high and is higher than the 480 ℃ specified by the invention, the coarsening of crystal grains is serious, and the performance of the final material is low. The yield strength at 350 ℃ is 60MPa, the tensile strength is 73MPa, which is lower than that of the first embodiment, and the engineering requirements are difficult to meet.
Comparative example 6
Spherical aluminum powder with the average grain diameter of 1.8 mu m is selected, cold-pressed and molded under 200MPa, and then placed into a vacuum furnace for sintering for 2 hours at 500 ℃, and a sintering billet is hot-extruded at 450 ℃, the extrusion ratio is 6. And annealing the extruded strip plate at 580 ℃ for 8 hours, and then rolling to obtain a final plate.
Al production by Using this example 2 O 3 Al, due to the extrusion rate is too low, which is lower than the specification of the invention, the coarsening of crystal grains is serious, and the performance of the final material is low. The yield strength at 350 ℃ is 62MPa, the tensile strength is 74MPa, and the strength is lower than that of the first embodiment, and the engineering requirements are difficult to meet.
The present invention is described in the embodiments, but the embodiments are only for further illustrating the features and advantages of the present invention, and are not to be construed as limiting the claims of the present invention.
Claims (7)
1. Al (aluminum) 2 O 3 The preparation method of the/Al high-temperature resistant aluminum matrix composite material is characterized by comprising the following steps: the preparation method comprises the following steps:
(1) Carrying out oxidation treatment on the superfine aluminum powder, and forming an aluminum oxide film on the surface of the superfine aluminum powder, wherein the average particle size of the superfine aluminum powder is 0.1-2 mu m;
(2) Carrying out powder metallurgy sintering on the pressed compact obtained after compression molding to obtain Al 2 O 3 Al ingots;
(3) Extruding the billet obtained in the step (2) at an extrusion ratio of 4:1-9:1, the temperature is 180-480 ℃, and the speed is 50-800mm/s;
(4) Carrying out high-temperature annealing treatment on the material obtained by extrusion in the step (3), wherein the high-temperature annealing temperature is 580-630 ℃, and the time is 2-12 hours;
(5) And (4) rolling or extruding the material obtained in the step (4) for the second time to obtain the high-temperature-resistant aluminum-based composite material.
2. Al according to claim 1 2 O 3 The preparation method of the/Al high-temperature resistant aluminum matrix composite material is characterized by comprising the following steps: in the step (1), the thickness of the aluminum oxide film is 3-12 nm.
3. The method of claim 1Al 2 O 3 The preparation method of the/Al high-temperature resistant aluminum matrix composite material is characterized by comprising the following steps: in the step (2), the powder metallurgy sintering adopts vacuum hot pressing sintering, hot isostatic pressing or spark ion beam sintering technology under the atmosphere or vacuum condition.
4. Al according to claim 1 or 3 2 O 3 The preparation method of the Al high-temperature resistant aluminum matrix composite material is characterized by comprising the following steps: in the step (2), the sintering temperature in the powder metallurgy sintering is 300-540 ℃, and the time is 0.5-6 hours.
5. Al according to claim 1 2 O 3 The preparation and deformation method of the/Al high-temperature resistant aluminum matrix composite material is characterized in that: and (3) extruding the billet obtained in the step (2) to be in a strip plate or round bar shape.
6. The Al of claim 1 2 O 3 The preparation method of the Al high-temperature resistant aluminum matrix composite material is characterized by comprising the following steps: in the step (5), the extrusion or rolling temperature is 350-500 ℃, and the deformation ratio is 2:1-12:1, finally deforming to the required shape.
7. The Al of claim 1 2 O 3 The preparation method of the/Al high-temperature resistant aluminum matrix composite material is characterized by comprising the following steps: the Al is 2 O 3 The tensile strength of the Al high-temperature resistant aluminum matrix composite material is more than or equal to 80Mpa at 350 ℃, and the elongation is more than 10%.
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