CN111101026A - Preparation method of high-strength high-toughness aluminum-based composite material - Google Patents
Preparation method of high-strength high-toughness aluminum-based composite material Download PDFInfo
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- 229910052782 aluminium Inorganic materials 0.000 title claims abstract description 49
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 title claims abstract description 49
- 239000002131 composite material Substances 0.000 title claims abstract description 43
- 238000002360 preparation method Methods 0.000 title claims abstract description 17
- 239000000956 alloy Substances 0.000 claims abstract description 44
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 43
- 239000002245 particle Substances 0.000 claims abstract description 39
- 229910000838 Al alloy Inorganic materials 0.000 claims abstract description 26
- 239000000843 powder Substances 0.000 claims abstract description 19
- 238000009718 spray deposition Methods 0.000 claims abstract description 18
- 230000032683 aging Effects 0.000 claims abstract description 14
- 238000001125 extrusion Methods 0.000 claims abstract description 14
- 239000006104 solid solution Substances 0.000 claims abstract description 14
- 238000000034 method Methods 0.000 claims abstract description 10
- 238000000889 atomisation Methods 0.000 claims abstract description 9
- 238000006243 chemical reaction Methods 0.000 claims abstract description 9
- 238000005049 combustion synthesis Methods 0.000 claims abstract description 9
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 8
- 239000006229 carbon black Substances 0.000 claims abstract description 7
- 239000002041 carbon nanotube Substances 0.000 claims abstract description 7
- 229910021393 carbon nanotube Inorganic materials 0.000 claims abstract description 7
- 238000005507 spraying Methods 0.000 claims description 18
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 14
- 239000011159 matrix material Substances 0.000 claims description 12
- 238000004321 preservation Methods 0.000 claims description 9
- 238000000498 ball milling Methods 0.000 claims description 8
- 238000000151 deposition Methods 0.000 claims description 8
- 238000010438 heat treatment Methods 0.000 claims description 8
- 229910000831 Steel Inorganic materials 0.000 claims description 7
- 229910052786 argon Inorganic materials 0.000 claims description 7
- 239000000463 material Substances 0.000 claims description 7
- 238000005245 sintering Methods 0.000 claims description 7
- 239000010959 steel Substances 0.000 claims description 7
- 230000006698 induction Effects 0.000 claims description 6
- 238000003825 pressing Methods 0.000 claims description 6
- 238000002844 melting Methods 0.000 claims description 4
- 230000008018 melting Effects 0.000 claims description 4
- 238000007789 sealing Methods 0.000 claims description 4
- 238000002485 combustion reaction Methods 0.000 claims description 3
- 239000011888 foil Substances 0.000 claims description 3
- 229910052742 iron Inorganic materials 0.000 claims description 3
- 229910052748 manganese Inorganic materials 0.000 claims description 3
- 238000002156 mixing Methods 0.000 claims description 3
- 238000003756 stirring Methods 0.000 claims description 3
- 229910052720 vanadium Inorganic materials 0.000 claims description 3
- 229910052725 zinc Inorganic materials 0.000 claims description 3
- 229910052726 zirconium Inorganic materials 0.000 claims description 3
- 229910052802 copper Inorganic materials 0.000 claims description 2
- 239000000203 mixture Substances 0.000 abstract description 3
- 239000000155 melt Substances 0.000 abstract description 2
- 238000004519 manufacturing process Methods 0.000 abstract 1
- 230000000052 comparative effect Effects 0.000 description 7
- 238000012360 testing method Methods 0.000 description 4
- 230000000694 effects Effects 0.000 description 2
- 239000011261 inert gas Substances 0.000 description 2
- 230000003014 reinforcing effect Effects 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 230000000295 complement effect Effects 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 230000007123 defense Effects 0.000 description 1
- 230000008021 deposition Effects 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 238000011031 large-scale manufacturing process Methods 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 239000011156 metal matrix composite Substances 0.000 description 1
- 239000003595 mist Substances 0.000 description 1
- 239000002105 nanoparticle Substances 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
- C22C21/003—Alloys based on aluminium containing at least 2.6% of one or more of the elements: tin, lead, antimony, bismuth, cadmium, and titanium
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- 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
- B22F3/115—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by spraying molten metal, i.e. spray sintering, spray casting
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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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C26/00—Alloys containing diamond or cubic or wurtzitic boron nitride, fullerenes or carbon nanotubes
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- 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
- C22C32/0084—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 carbon or graphite as the main non-metallic constituent
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C26/00—Alloys containing diamond or cubic or wurtzitic boron nitride, fullerenes or carbon nanotubes
- C22C2026/002—Carbon nanotubes
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Abstract
本发明涉及一种高强高韧铝基复合材料的制备方法，先将Ti粉、碳纳米管粉、炭黑与Al粉均匀混合并球磨、放入模具中冷压成预制坯，发生燃烧合成反应，得到微纳混杂Al‑C‑Ti颗粒的中间合金烧结坯，将其与铝合金的熔体在喷射成形设备中混合，雾化后喷射沉积得到微纳混杂Al‑C‑Ti颗粒增强的铝基复合材料坯料，再进行挤压变形、固溶时效处理，最终得到管状或棒状的高强高韧铝基复合材料；本发明方法可同时提高铝合金的强度和延伸率，当微纳混杂Al‑C‑Ti颗粒占铝基复合材料的质量百分含量为0.5％时，抗拉强度提高了23.9％，延伸率提高了33.3％，本发明复合材料的制备方法简单，成本低，可控性强，可用于大规模生产。
The invention relates to a method for preparing a high-strength and high-toughness aluminum-based composite material. First, Ti powder, carbon nanotube powder, carbon black and Al powder are uniformly mixed, ball-milled, put into a mold and cold-pressed to form a preform, and a combustion synthesis reaction occurs. , obtain the sintered master alloy sintered billet of micro-nano hybrid Al-C-Ti particles, mix it with the melt of aluminum alloy in spray forming equipment, spray deposition after atomization to obtain aluminum alloy reinforced with micro-nano hybrid Al-C-Ti particles The base composite material blank is then subjected to extrusion deformation and solid solution aging treatment to finally obtain a tubular or rod-shaped high-strength and high-toughness aluminum-based composite material; the method of the invention can simultaneously improve the strength and elongation of the aluminum alloy. When the C-Ti particles account for 0.5% of the mass percentage of the aluminum-based composite material, the tensile strength is increased by 23.9%, and the elongation is increased by 33.3%. The preparation method of the composite material of the invention is simple, low in cost, and strong in controllability , which can be used for mass production.
Description
Technical Field
The invention relates to the technical field of metal matrix composite materials, in particular to a preparation method of a high-strength high-toughness aluminum matrix composite material.
Background
The aluminum-based composite material has the advantages of low density, high corrosion resistance, excellent electric and heat conductivity, good processability and the like, and has very wide application prospect in the fields of aerospace, automobile industry and the like. The TiC particles have high strength, high modulus and high melting point, are well wetted with an aluminum matrix, and are an ideal reinforcing phase of the aluminum-based alloy. In addition, TiC and aluminum are in face-centered cubic structures, the lattice constants are close, and the TiC and the aluminum can be used as heterogeneous nucleation cores of aluminum melts, so that the grain size is refined.
The aluminum alloy has good comprehensive performance and is applied to the fields of aviation, national defense, civil industry and the like. However, with the development of the advanced fields such as weaponry and new energy, the requirements for the comprehensive properties of the material are higher and higher, and how to simultaneously improve the tensile strength and the elongation of the aluminum alloy is a key point.
Disclosure of Invention
The invention aims to solve the technical problem of improving the tensile strength and the elongation of the aluminum alloy at the same time, thereby providing a preparation method of a high-strength high-toughness aluminum-based composite material. The method can effectively improve the mechanical property of the aluminum alloy material.
In order to achieve the purpose, the invention is realized by the following technical scheme:
a preparation method of a high-strength high-toughness aluminum-based composite material comprises the following steps:
(1) uniformly mixing Ti powder, carbon nanotube powder, carbon black and Al powder, and performing ball milling treatment, and then putting the mixture into a die to perform cold pressing to form a prefabricated blank; carrying out combustion synthesis reaction on the prefabricated blank to obtain a master alloy sintering blank of micro-nano mixed Al-C-Ti particles;
(2) putting the aluminum alloy blank into an induction furnace of a spray forming device, heating to 750-780 ℃ and melting to obtain an aluminum alloy melt; meanwhile, sealing the intermediate alloy sintered blank prepared in the step (1) by using an aluminum foil, heating the intermediate alloy sintered blank to 500 ℃, preserving the heat for 2 hours, taking out the intermediate alloy sintered blank, quickly pressing the intermediate alloy sintered blank into the aluminum alloy melt, and stirring to completely melt the intermediate alloy sintered blank mixed with the micro-nano Al-C-Ti particles into the aluminum alloy melt to obtain a mixed alloy melt;
(3) atomizing the mixed alloy melt obtained in the step (2) in an atomizing chamber of the spray forming equipment to form mixed alloy atomized particles, spraying the mixed alloy atomized particles from a nozzle of the spray forming equipment under the protection of inert gas, and depositing the mixed alloy atomized particles on a depositor of the spray forming equipment to obtain an aluminum-based composite material blank reinforced by micro-nano hybrid Al-C-Ti particles, wherein the micro-nano hybrid Al-C-Ti particles account for 0.5-2% of the aluminum-based composite material blank by mass;
(4) and sequentially carrying out extrusion deformation and solid solution aging treatment on the micro-nano mixed Al-C-Ti particle reinforced aluminum matrix composite blank to finally obtain the high-strength and high-toughness aluminum matrix composite.
Further, the mass ratio of the Ti powder, the carbon nanotube powder, the carbon black and the Al powder in the step (1) is 1:0.9:0.9: 7. Adding carbon nanotube powder and carbon black into an Al-Ti-C system to change the composition and the proportion of a carbon source, thereby obtaining an Al-C-Ti particle intermediate alloy sintered blank with micron and nanometer mixed particles.
Further, in the ball milling treatment process in the step (1), steel balls with the diameter of 5mm are adopted, the steel balls are sealed under the protection of argon according to the ball-to-material ratio of 10:1, and ball milling is carried out for 20 hours at the rotating speed of 400 r/min.
Further, the combustion synthesis reaction in the step (1) is vacuum sintering under the protection of argon, the combustion temperature is 1100-1300 ℃, the pressure is 50MPa, and the heat preservation time is 4 min.
Further, the aluminum alloy blank in the step (2) comprises the following components in percentage by mass: 5.8 to 6.8 percent of Cu5, 0.20 to 0.40 percent of Mn, 0.10 to 0.25 percent of Zr, 0.10 to 0.25 percent of V, less than or equal to 0.20 percent of Si, less than or equal to 0.30 percent of Fe, less than or equal to 0.1 percent of Zn, less than or equal to 0.05 percent of Ti, less than or equal to 0.02 percent of Mg and the balance of Al.
Further, the temperature of the atomization treatment in the step (3) is 750-800 ℃; the spraying pressure sprayed by the nozzle is 0.6MPa to 0.1MPa, the spraying angle is 15 degrees to 40 degrees, and the spraying distance is 400mm to 750 mm; the rotating speed of the depositor is 40 r/min-90 r/min, and the depositing speed is 4 Kg/min-10 Kg/min.
Further, the extrusion deformation temperature in the step (4) is 420-450 ℃, and the extrusion ratio is 6; the temperature of solid solution in the solid solution aging treatment is 520-540 ℃, the temperature is kept for 3h, the temperature of aging is 150-200 ℃, and the temperature is kept for 12 h.
The beneficial technical effects are as follows:
(1) according to the invention, the prepared intermediate alloy sintering blank of the micro-nano mixed Al-C-Ti particles is used as a reinforcing phase, and the mechanical property of the aluminum alloy can be effectively improved by the micro-nano mixed Al-C-Ti particles; compared with an aluminum matrix, when the micro-nano mixed Al-C-Ti particles account for 0.5-2% of the aluminum matrix composite material by mass, the tensile strength of the prepared aluminum matrix composite material is improved by 7.7-23.9%, and the elongation is improved by 6.7-33.3%.
(2) According to the invention, micron and nanometer mixed Al-C-Ti particles are simultaneously introduced into the aluminum alloy matrix, the two particles with different sizes complement each other and generate a synergistic effect, and the spray forming technology is adopted, so that the problem of uneven dispersion of part of nanoparticles is effectively avoided, and the effect of Al-C-Ti particles on enhancing the aluminum alloy is ensured.
(3) The preparation method of the composite material is simple, low in cost and strong in controllability, and can be used for large-scale production.
Drawings
Fig. 1 is a schematic view of the spray forming process in step (3) of the preparation method of the high-strength high-toughness aluminum-based composite material in example 1.
Detailed Description
The invention is further described below with reference to the figures and specific examples, without limiting the scope of the invention.
Example 1
A preparation method of a high-strength high-toughness aluminum-based composite material comprises the following steps:
(1) preparing Ti powder, carbon nanotube powder, carbon black and Al powder according to the mass ratio of 1:0.9:0.9:7, uniformly mixing, carrying out ball milling treatment, putting into a mold, and cold-pressing into a prefabricated blank; carrying out combustion synthesis reaction on the prefabricated blank to obtain a master alloy sintering blank of micro-nano mixed Al-C-Ti particles;
the ball milling process is to adopt steel balls with the diameter of 5mm, seal the steel balls under the protection of argon according to the ball-to-material ratio of 10:1, and ball mill the steel balls for 20 hours at the rotating speed of 400 r/min;
the combustion synthesis reaction is vacuum sintering under the protection of argon, the combustion temperature is 1200 ℃, the pressure is 50MPa, and the heat preservation time is 4 min;
(2) putting the aluminum alloy blank into an induction furnace of a spray forming device, heating to 770 ℃, and melting to obtain an aluminum alloy melt; meanwhile, sealing the intermediate alloy sintered blank prepared in the step (1) by using an aluminum foil, heating the intermediate alloy sintered blank to 500 ℃, preserving the heat for 2 hours, taking out the intermediate alloy sintered blank, quickly pressing the intermediate alloy sintered blank into the aluminum alloy melt, stirring the intermediate alloy sintered blank to completely melt the intermediate alloy sintered blank mixed with the micro-nano Al-C-Ti particles into the aluminum alloy melt to obtain a mixed alloy melt,
the aluminum alloy blank is 2219 type aluminum alloy, and comprises the following components in percentage by mass: 5.8 to 6.8 percent of Cu, 0.20 to 0.40 percent of Mn, 0.10 to 0.25 percent of Zr, 0.10 to 0.25 percent of V, less than or equal to 0.20 percent of Si, less than or equal to 0.30 percent of Fe, less than or equal to 0.1 percent of Zn, less than or equal to 0.05 percent of Ti, less than or equal to 0.02 percent of Mg and the balance of Al;
(3) atomizing the mixed alloy melt obtained in the step (2) in an atomizing chamber of the spray forming equipment to form mixed alloy atomized particles, spraying the mixed alloy atomized particles from a nozzle of the spray forming equipment under the protection of inert gas argon to deposit the mixed alloy atomized particles on a depositor of the spray forming equipment to form a deposition body, and obtaining an aluminum-based composite blank reinforced by micro-nano hybrid Al-C-Ti particles, wherein the micro-nano hybrid Al-C-Ti particles account for 0.5% of the aluminum-based composite blank by mass, and the schematic diagram of the spray forming process in the step (3) is shown in fig. 1; the atomization principle of the atomization chamber is as follows: when the mixed alloy melt enters the atomizing chamber from the induction furnace of the spray forming equipment and is guided onto the rotating disc of the atomizing chamber, the liquid mixed alloy melt is thrown out by the rotating disc which rotates rapidly, and the centrifugal force of the rotating disc exceeds the surface tension and viscous force of the mixed alloy melt, so that the mixed alloy melt becomes unstable and is crushed into mist, and atomization is realized;
the temperature of the atomization treatment is 790 ℃; the spraying pressure sprayed by the nozzle is 0.85MPa, the spraying angle is 30 degrees, and the spraying distance is 675 mm; the rotating speed of the depositor is 75r/min, and the depositing speed is 7 Kg/min;
(4) sequentially carrying out extrusion deformation and solid solution aging treatment on the micro-nano mixed Al-C-Ti particle reinforced aluminum matrix composite blank to finally obtain a tubular or rod-shaped high-strength and high-toughness aluminum matrix composite, wherein the extrusion deformation temperature is 440 ℃, and the extrusion ratio is 6; and the solid solution temperature in the solid solution aging treatment is 535 ℃, the heat preservation time is 3 hours, the aging temperature is 180 ℃, and the heat preservation time is 12 hours, so that the high-strength high-toughness aluminum-based composite material is finally obtained.
Example 2
The preparation method of the high-strength high-toughness aluminum-based composite material is the same as that in the embodiment 1, except that the micro-nano mixed Al-C-Ti particles in the step (3) account for 1% of the aluminum-based composite material blank by mass.
Example 3
The preparation method of the high-strength high-toughness aluminum-based composite material is the same as that in the embodiment 1, except that the micro-nano mixed Al-C-Ti particles in the step (3) account for 2% of the aluminum-based composite material blank by mass.
Example 4
The preparation method of the high-strength high-toughness aluminum-based composite material of the embodiment is the same as that of the embodiment 2, except that the temperature of the combustion synthesis reaction in the step (1) is 1300 ℃; the heating temperature of the induction furnace in the step (2) is 750 ℃; the temperature of the atomization treatment in the step (3) is 750 ℃; the spraying pressure sprayed by the nozzle is 0.1MPa, the spraying angle is 15 degrees, and the spraying distance is 750 mm; the rotating speed of the depositor is 40r/min, and the depositing speed is 4 Kg/min; the extrusion deformation temperature in the step (4) is 450 ℃, and the extrusion ratio is 6; the solid solution temperature in the solid solution aging treatment is 540 ℃, the heat preservation time is 3 hours, the aging temperature is 200 ℃, and the heat preservation time is 12 hours.
Example 5
The preparation method of the high-strength high-toughness aluminum-based composite material of the embodiment is the same as that of the embodiment 3, except that the temperature of the combustion synthesis reaction in the step (1) is 1100 ℃; the heating temperature of the induction furnace in the step (2) is 780 ℃; the temperature of the atomization treatment in the step (3) is 800 ℃; the spraying pressure sprayed by the nozzle is 0.6MPa, the spraying angle is 40 degrees, and the spraying distance is 400 mm; the rotating speed of the depositor is 90r/min, and the depositing speed is 10 Kg/min; the extrusion deformation temperature in the step (4) is 420 ℃, and the extrusion ratio is 6; the solid solution temperature in the solid solution aging treatment is 520 ℃, the heat preservation time is 3 hours, the aging temperature is 150 ℃, and the heat preservation time is 12 hours.
Comparative example 1
The comparative example is the same as the example 1 except that the intermediate alloy sintered compact of micro-nano mixed Al-C-Ti particles of the step (1) is not prepared.
The materials prepared in examples 1-3 and comparative example 1 were subjected to room temperature mechanical property test, the test method was performed according to GB/T228.1-2010 using (CMT-5105) tensile compression testing machine for room temperature mechanical property test, and the tensile rate was 1 × 10- 3m/s. Test results the results are shown in table 1.
TABLE 1 mechanical Properties of the materials prepared in examples 1-3 and comparative example 1
As can be seen from table 1, compared with comparative example 1, the tensile strength, yield strength and elongation of the high-strength high-toughness aluminum-based composite materials prepared in examples 1, 2 and 3 are improved to different degrees, wherein the relevant mechanical properties of example 1 are optimal, the tensile strength is improved by 23.9%, and the elongation is improved by 33.3%; compared with the comparative example 1, the tensile strength of the example 2 is improved by 7.7 percent, and the elongation is improved by 13.3 percent; the tensile strength of the example 3 is improved by 13.2 percent and the elongation is improved by 6.7 percent compared with the tensile strength of the comparative example 1.
Claims (7)
1. The preparation method of the high-strength high-toughness aluminum-based composite material is characterized by comprising the following steps of:
(1) uniformly mixing Ti powder, carbon nanotube powder, carbon black and Al powder, ball-milling, putting into a die, and cold-pressing into a prefabricated blank; carrying out combustion synthesis reaction on the prefabricated blank to obtain a master alloy sintering blank of micro-nano mixed Al-C-Ti particles;
(2) putting the aluminum alloy blank into an induction furnace of a spray forming device, heating to 750-780 ℃ and melting to obtain an aluminum alloy melt; meanwhile, sealing the intermediate alloy sintered blank prepared in the step (1) by using an aluminum foil, heating the intermediate alloy sintered blank to 500 ℃, preserving the heat for 2 hours, taking out the intermediate alloy sintered blank, quickly pressing the intermediate alloy sintered blank into the aluminum alloy melt, and stirring to completely melt the intermediate alloy sintered blank mixed with the micro-nano Al-C-Ti particles into the aluminum alloy melt to obtain a mixed alloy melt;
(3) atomizing the mixed alloy melt obtained in the step (2) in an atomizing chamber of the spray forming equipment to form mixed alloy atomized particles, spraying the mixed alloy atomized particles from a nozzle of the spray forming equipment, and depositing the mixed alloy atomized particles on a depositor of the spray forming equipment to obtain a micro-nano mixed Al-C-Ti particle reinforced aluminum-based composite material blank, wherein the micro-nano mixed Al-C-Ti particles account for 0.5-2% of the aluminum-based composite material blank by mass;
(4) and sequentially carrying out extrusion deformation and solid solution aging treatment on the micro-nano mixed Al-C-Ti particle reinforced aluminum matrix composite blank to finally obtain the tubular or rod-shaped high-strength high-toughness aluminum matrix composite.
2. The preparation method of the high-strength high-toughness aluminum-based composite material as claimed in claim 1, wherein the mass ratio of the Ti powder, the carbon nanotube powder, the carbon black and the Al powder in step (1) is 1:0.9:0.9: 7.
3. The preparation method of the high-strength high-toughness aluminum-based composite material according to claim 1, wherein the ball milling treatment in the step (1) is performed by adopting steel balls with the diameter of 5mm, sealing the steel balls under the protection of argon according to the ball-to-material ratio of 10:1, and ball milling at the rotating speed of 400r/min for 20 hours.
4. The method for preparing the high-strength high-toughness aluminum-based composite material according to claim 1, wherein the combustion synthesis reaction in the step (1) is vacuum sintering under the protection of argon, the combustion temperature is 1100-1300 ℃, the pressure is 50MPa, and the heat preservation time is 4 min.
5. The preparation method of the high-strength high-toughness aluminum-based composite material according to claim 1, wherein the aluminum alloy blank in the step (2) comprises the following components in percentage by mass: 5.8 to 6.8 percent of Cu, 0.20 to 0.40 percent of Mn, 0.10 to 0.25 percent of Zr, 0.10 to 0.25 percent of V, less than or equal to 0.20 percent of Si, less than or equal to 0.30 percent of Fe, less than or equal to 0.1 percent of Zn, less than or equal to 0.05 percent of Ti, less than or equal to 0.02 percent of Mg and the balance of Al.
6. The method for preparing the high-strength high-toughness aluminum-based composite material as claimed in claim 1, wherein the temperature of the atomization treatment in the step (3) is 750 ℃ to 800 ℃; the spraying pressure sprayed by the nozzle is 0.6MPa to 0.1MPa, the spraying angle is 15 degrees to 40 degrees, and the spraying distance is 400mm to 750 mm; the rotating speed of the depositor is 40 r/min-90 r/min, and the depositing speed is 4 Kg/min-10 Kg/min.
7. The method for preparing the high-strength high-toughness aluminum-based composite material according to any one of claims 1 to 6, wherein the extrusion deformation temperature in the step (4) is 420-450 ℃, and the extrusion ratio is 6; the temperature of solid solution in the solid solution aging treatment is 520-540 ℃, the temperature is kept for 3h, the temperature of aging is 150-200 ℃, and the temperature is kept for 12 h.
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| CN201911241394.9A CN111101026A (en) | 2019-12-06 | 2019-12-06 | Preparation method of high-strength high-toughness aluminum-based composite material |
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| CN201911241394.9A CN111101026A (en) | 2019-12-06 | 2019-12-06 | Preparation method of high-strength high-toughness aluminum-based composite material |
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| CN111733357A (en) * | 2020-05-21 | 2020-10-02 | 范语楠 | Preparation method of high-volume-fraction ceramic-reinforced aluminum-based composite material |
| CN112247156A (en) * | 2020-10-21 | 2021-01-22 | 吉林大学 | Titanium alloy powder with endogenous nano-TiC particles and its preparation method and application |
| CN113042748A (en) * | 2021-03-09 | 2021-06-29 | 中北大学 | Method for preparing high-strength high-elongation Al-Cu-Mg alloy by SLM |
| CN113416861A (en) * | 2021-05-17 | 2021-09-21 | 江苏大学 | Preparation method of micro-nano dual-scale TiC particle reinforced aluminum matrix composite material |
| CN113444906A (en) * | 2021-06-10 | 2021-09-28 | 北京科技大学 | Method for preparing carbon nano tube reinforced light aluminum-based alloy |
| CN113462921A (en) * | 2021-06-10 | 2021-10-01 | 北京科技大学 | Method for preparing carbon nano tube reinforced Al-Zn-Mg-Cu ultrahigh-strength aluminum alloy |
| CN113481401A (en) * | 2021-06-10 | 2021-10-08 | 北京科技大学 | Method for preparing Al/CNT composite material |
| CN117026018A (en) * | 2023-07-31 | 2023-11-10 | 中车工业研究院有限公司 | Heat-treatment-free 6N01 aluminum alloy and preparation method and application thereof |
| CN119839306A (en) * | 2025-03-19 | 2025-04-18 | 中国科学院金属研究所 | Carbon nano tube reinforced aluminum-based composite material piece and additive preparation method thereof |
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| CN111733357A (en) * | 2020-05-21 | 2020-10-02 | 范语楠 | Preparation method of high-volume-fraction ceramic-reinforced aluminum-based composite material |
| CN111733357B (en) * | 2020-05-21 | 2022-04-12 | 范语楠 | Preparation method of high-volume-fraction ceramic-reinforced aluminum-based composite material |
| CN112247156A (en) * | 2020-10-21 | 2021-01-22 | 吉林大学 | Titanium alloy powder with endogenous nano-TiC particles and its preparation method and application |
| CN113042748A (en) * | 2021-03-09 | 2021-06-29 | 中北大学 | Method for preparing high-strength high-elongation Al-Cu-Mg alloy by SLM |
| CN113416861A (en) * | 2021-05-17 | 2021-09-21 | 江苏大学 | Preparation method of micro-nano dual-scale TiC particle reinforced aluminum matrix composite material |
| CN113444906A (en) * | 2021-06-10 | 2021-09-28 | 北京科技大学 | Method for preparing carbon nano tube reinforced light aluminum-based alloy |
| CN113462921A (en) * | 2021-06-10 | 2021-10-01 | 北京科技大学 | Method for preparing carbon nano tube reinforced Al-Zn-Mg-Cu ultrahigh-strength aluminum alloy |
| CN113481401A (en) * | 2021-06-10 | 2021-10-08 | 北京科技大学 | Method for preparing Al/CNT composite material |
| CN113481401B (en) * | 2021-06-10 | 2022-04-05 | 北京科技大学 | Method for preparing Al/CNT composite material |
| CN117026018A (en) * | 2023-07-31 | 2023-11-10 | 中车工业研究院有限公司 | Heat-treatment-free 6N01 aluminum alloy and preparation method and application thereof |
| CN119839306A (en) * | 2025-03-19 | 2025-04-18 | 中国科学院金属研究所 | Carbon nano tube reinforced aluminum-based composite material piece and additive preparation method thereof |
| CN119839306B (en) * | 2025-03-19 | 2025-06-06 | 中国科学院金属研究所 | Carbon nano tube reinforced aluminum-based composite material piece and additive preparation method thereof |
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