CN114774728A - Wear-resistant aluminum alloy and preparation method thereof - Google Patents
Wear-resistant aluminum alloy and preparation method thereof Download PDFInfo
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- CN114774728A CN114774728A CN202210382682.1A CN202210382682A CN114774728A CN 114774728 A CN114774728 A CN 114774728A CN 202210382682 A CN202210382682 A CN 202210382682A CN 114774728 A CN114774728 A CN 114774728A
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- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 68
- 238000002360 preparation method Methods 0.000 title claims abstract description 18
- 238000009768 microwave sintering Methods 0.000 claims abstract description 21
- 238000005096 rolling process Methods 0.000 claims abstract description 20
- 238000000137 annealing Methods 0.000 claims abstract description 15
- 238000001816 cooling Methods 0.000 claims abstract description 13
- 229910052802 copper Inorganic materials 0.000 claims abstract description 8
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 8
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 8
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 8
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 7
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 7
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 7
- 229910052718 tin Inorganic materials 0.000 claims abstract description 7
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 7
- 238000000713 high-energy ball milling Methods 0.000 claims abstract description 5
- 229910052751 metal Inorganic materials 0.000 claims abstract description 5
- 239000002184 metal Substances 0.000 claims abstract description 5
- 239000000843 powder Substances 0.000 claims description 32
- 238000000498 ball milling Methods 0.000 claims description 31
- 239000000463 material Substances 0.000 claims description 23
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 22
- 239000000956 alloy Substances 0.000 claims description 21
- 229910045601 alloy Inorganic materials 0.000 claims description 20
- 238000000034 method Methods 0.000 claims description 16
- 239000007788 liquid Substances 0.000 claims description 11
- 229910052757 nitrogen Inorganic materials 0.000 claims description 11
- 238000001035 drying Methods 0.000 claims description 10
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical group CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 claims description 8
- MCMNRKCIXSYSNV-UHFFFAOYSA-N Zirconium dioxide Chemical compound O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 claims description 8
- 238000009694 cold isostatic pressing Methods 0.000 claims description 8
- 238000005245 sintering Methods 0.000 claims description 8
- 238000005275 alloying Methods 0.000 claims description 7
- 238000004321 preservation Methods 0.000 claims description 6
- 238000002791 soaking Methods 0.000 claims description 6
- 238000010438 heat treatment Methods 0.000 claims description 5
- 229910052742 iron Inorganic materials 0.000 claims description 5
- 238000004519 manufacturing process Methods 0.000 claims description 5
- 229910052758 niobium Inorganic materials 0.000 claims description 5
- 239000002245 particle Substances 0.000 claims description 5
- 229910052719 titanium Inorganic materials 0.000 claims description 5
- 230000006698 induction Effects 0.000 claims description 4
- 238000005507 spraying Methods 0.000 claims description 4
- 238000001291 vacuum drying Methods 0.000 claims description 4
- 238000005303 weighing Methods 0.000 claims description 4
- 238000002156 mixing Methods 0.000 claims description 2
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 abstract description 15
- 239000010949 copper Substances 0.000 abstract description 11
- 239000011651 chromium Substances 0.000 abstract description 10
- 239000011572 manganese Substances 0.000 abstract description 10
- 239000011135 tin Substances 0.000 abstract description 10
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 abstract description 9
- 239000010936 titanium Substances 0.000 abstract description 8
- 238000005516 engineering process Methods 0.000 abstract description 7
- 239000013078 crystal Substances 0.000 abstract description 6
- 238000005551 mechanical alloying Methods 0.000 abstract description 5
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 abstract description 4
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 abstract description 4
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 abstract description 4
- 239000010703 silicon Substances 0.000 abstract description 4
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 abstract description 3
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 abstract description 3
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 abstract description 3
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 abstract description 3
- 239000011733 molybdenum Substances 0.000 abstract description 3
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 abstract description 3
- 239000006104 solid solution Substances 0.000 abstract description 2
- 150000002739 metals Chemical class 0.000 abstract 1
- 230000002787 reinforcement Effects 0.000 abstract 1
- 239000000126 substance Substances 0.000 abstract 1
- 239000000523 sample Substances 0.000 description 15
- 238000012360 testing method Methods 0.000 description 10
- 230000000052 comparative effect Effects 0.000 description 9
- 239000010955 niobium Substances 0.000 description 7
- 238000005299 abrasion Methods 0.000 description 6
- 238000002474 experimental method Methods 0.000 description 6
- 238000000227 grinding Methods 0.000 description 6
- 229910001008 7075 aluminium alloy Inorganic materials 0.000 description 5
- 230000006872 improvement Effects 0.000 description 5
- 238000002844 melting Methods 0.000 description 5
- 230000008018 melting Effects 0.000 description 5
- 230000008569 process Effects 0.000 description 5
- 229910000831 Steel Inorganic materials 0.000 description 4
- 238000005266 casting Methods 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- 239000010959 steel Substances 0.000 description 4
- 229910052782 aluminium Inorganic materials 0.000 description 3
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 230000007797 corrosion Effects 0.000 description 3
- 230000007547 defect Effects 0.000 description 3
- 238000011056 performance test Methods 0.000 description 3
- 238000007745 plasma electrolytic oxidation reaction Methods 0.000 description 3
- 230000003068 static effect Effects 0.000 description 3
- 230000000694 effects Effects 0.000 description 2
- 238000003912 environmental pollution Methods 0.000 description 2
- 238000011049 filling Methods 0.000 description 2
- 238000004372 laser cladding Methods 0.000 description 2
- 239000000314 lubricant Substances 0.000 description 2
- 238000001755 magnetron sputter deposition Methods 0.000 description 2
- 230000001737 promoting effect Effects 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 239000000758 substrate Substances 0.000 description 2
- 238000004381 surface treatment Methods 0.000 description 2
- 229910000733 Li alloy Inorganic materials 0.000 description 1
- 229910000861 Mg alloy Inorganic materials 0.000 description 1
- 238000003723 Smelting Methods 0.000 description 1
- 229910001069 Ti alloy Inorganic materials 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- KMWBBMXGHHLDKL-UHFFFAOYSA-N [AlH3].[Si] Chemical class [AlH3].[Si] KMWBBMXGHHLDKL-UHFFFAOYSA-N 0.000 description 1
- 239000002253 acid Substances 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 229910052783 alkali metal Inorganic materials 0.000 description 1
- 150000001340 alkali metals Chemical class 0.000 description 1
- JRBRVDCKNXZZGH-UHFFFAOYSA-N alumane;copper Chemical class [AlH3].[Cu] JRBRVDCKNXZZGH-UHFFFAOYSA-N 0.000 description 1
- -1 aluminum-zinc-magnesium-copper series Chemical class 0.000 description 1
- 239000010407 anodic oxide Substances 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 239000012496 blank sample Substances 0.000 description 1
- 238000007664 blowing Methods 0.000 description 1
- 230000015556 catabolic process Effects 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 238000006731 degradation reaction Methods 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000009977 dual effect Effects 0.000 description 1
- 238000010304 firing Methods 0.000 description 1
- 239000003562 lightweight material Substances 0.000 description 1
- 239000001989 lithium alloy Substances 0.000 description 1
- 238000005461 lubrication Methods 0.000 description 1
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 239000012528 membrane Substances 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 239000002159 nanocrystal Substances 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 239000004033 plastic Substances 0.000 description 1
- 229910052761 rare earth metal Inorganic materials 0.000 description 1
- 150000002910 rare earth metals Chemical class 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 229910052712 strontium Inorganic materials 0.000 description 1
- CIOAGBVUUVVLOB-UHFFFAOYSA-N strontium atom Chemical compound [Sr] CIOAGBVUUVVLOB-UHFFFAOYSA-N 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 229910052727 yttrium Inorganic materials 0.000 description 1
- VWQVUPCCIRVNHF-UHFFFAOYSA-N yttrium atom Chemical compound [Y] VWQVUPCCIRVNHF-UHFFFAOYSA-N 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/0408—Light metal alloys
- C22C1/0416—Aluminium-based alloys
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/04—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering with simultaneous application of supersonic waves, magnetic or electric fields
-
- 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
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
-
- 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
- C22F1/02—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working in inert or controlled atmosphere or vacuum
-
- 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
- C22F1/043—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 of alloys with silicon as the next major constituent
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Powder Metallurgy (AREA)
Abstract
The invention relates to a wear-resistant aluminum alloy and a preparation method thereof, belonging to the technical field of nonferrous metals. The aluminum alloy comprises the following chemical components in percentage by mass: 10.4 to 11.8% of Si, 1.5 to 2.5% of Zr, 1.2 to 2.2% of Ti, 0.05 to 0.1% of Cu, 1.2 to 1.7% of Sn, 0.5 to 0.7% of Mn, 1.4 to 2.4% of Nb, 0.07 to 0.2% of Fe, 0.03 to 0.15% of Ni, 0.05 to 0.15% of Cr, 0.14 to 0.22% of V, 0.2 to 0.25% of Mo, and the balance of Al. The preparation method comprises the steps of firstly carrying out mechanical alloying by high-energy ball milling, and then carrying out microwave sintering, low-temperature rolling, vacuum annealing treatment and magnetic field cryogenic treatment. The invention optimizes the contents of elements such as silicon, zirconium, copper, nickel, manganese and the like, adds chromium, vanadium, molybdenum and tin elements, realizes the forced solid solution among atoms of different elements by means of mechanical alloying, and applies a microwave sintering technology, a low-temperature rolling technology and a magnetic field deep cooling technology to refine crystal grains, improve compactness, form deformation stress reinforcement and improve the hardness and wear resistance of the aluminum alloy.
Description
Technical Field
The invention belongs to the field of aluminum alloy materials, and particularly relates to a novel high-wear-resistance aluminum alloy and a preparation method thereof.
Background
The aluminum alloy has low density, high strength close to or exceeding that of high-quality steel, good plasticity, excellent electrical conductivity, thermal conductivity and corrosion resistance, is widely used in industry, and is only second to steel in use amount; however, the wear resistance and hardness of aluminum alloys are generally lower than those of other alloys, which results in a limited range of applications.
With the increasing expansion of energy requirements of countries in the world, materials with low density, high specific strength and high specific stiffness are more and more valued by designers and material science and technology workers; at present, the lightweight materials researched by various countries in the world mainly comprise aluminum alloy, magnesium alloy, lithium alloy, titanium alloy and the like; because the aluminum resource is rich, and the aluminum alloy has the characteristics of small density, large strength-to-weight ratio, strong corrosion resistance, good processability and weldability and the like, the aluminum alloy is widely applied to various fields of aviation, aerospace, automobiles, machinery and the like; the replacement of steel by aluminum can greatly reduce the weight of parts, save energy, reduce cost and reduce environmental pollution.
For aviation and aerospace products, an important link for improving performances of airplanes, missiles and the like is to reduce weight of structural components of the aircraft and the missiles; the aluminum alloy is used as one of main structural materials of aviation products, and is suitable for casting parts with complex shapes, high specific strength requirements and uniform overall performance requirements; in the modern automobile industry, the requirements on the lightweight of automobiles are more and more urgent due to the reasons of energy, environment and safety; aluminum alloy is a preferred material for lightweight automobiles, and has been widely used in chassis, body, engine, steering system, brake and various accessories of automobiles.
However, the aluminum alloy used as a material for mechanical parts has the defects of low hardness, poor wear resistance, high friction coefficient, difficulty in lubrication and the like, which greatly limit the application range of the aluminum alloy; the service life of the workpiece is shortened due to poor wear resistance of the surface of the aluminum alloy; the surface friction coefficient of the aluminum alloy is high, so that the abrasion of the aluminum alloy is accelerated, the energy loss is increased, and the abrasion of a dual material is caused; therefore, improving the tribological properties of the aluminum alloy surface is advantageous for energy saving, cost reduction, productivity improvement and economic efficiency.
In recent years, in order to improve the tribological performance of the surface of the aluminum alloy, a plurality of scholars perform surface treatment on the aluminum alloy, and the surface treatment methods mainly comprise surface spraying, magnetron sputtering, laser cladding, solid lubricant adhesion, anodic oxidation, micro-arc oxidation and the like; although the surface spraying process is simple, the hardness, compactness and membrane-substrate binding force of the obtained membrane layer are generally difficult to achieve ideal effects; magnetron sputtering and laser cladding often need higher treatment temperature, so that the degradation of a matrix is easily caused, and the cost of the two processes is too high; the solid lubricant film layer bonded on the aluminum alloy substrate does not have certain hardness and is not suitable for the heavy-duty working condition application condition; the thickness and the hardness of the anodic oxide film layer are not enough, the pretreatment process is complex, and the temperature requirement of the treatment process is strict; due to the special film forming principle and the film forming process of the micro-arc oxidation, the prepared film layer inevitably has the defects of micropores, microcracks, rough surface, poor acid corrosion resistance of main phases and the like, so that the improvement of the performance of the micro-arc oxidation film layer is limited.
Disclosure of Invention
The invention aims to provide a novel high-wear-resistance aluminum alloy and a preparation method thereof, and solves the problems of poor wear resistance and low hardness of the conventional aluminum alloy.
The purpose of the invention is realized by the following technical scheme:
the preparation method of the wear-resistant aluminum alloy is characterized by comprising the following steps:
weighing aluminum alloy powder: weighing and mixing powders of Si, Zr, Ti, Cu, Sn, Mn, Nb, Fe, Ni, Cr, V and Mo according to the following mass percent, wherein the powders comprise 10.4-11.8% of Si, 1.5-2.5% of Zr, 1.2-2.2% of Ti, 0.05-0.1% of Cu, 1.2-1.7% of Sn, 0.5-0.7% of Mn, 1.4-2.4% of Nb, 0.07-0.2% of Fe, 0.03-0.15% of Ni, 0.05-0.15% of Cr, 0.14-0.22% of V, 0.2-0.25% of Mo and the balance of Al; the particle size of the powder is 100-200 meshes;
step (2) high-energy ball milling alloying: putting the mixed metal powder into a zirconia ball milling tank, vacuumizing the ball milling tank, and carrying out ball milling and drying by adopting a planetary ball mill to obtain alloyed aluminum alloy powder;
and (3) cold isostatic pressing: placing the aluminum alloy powder prepared in the step (2) into a rubber mold for cold isostatic pressing, wherein the static pressure is 400MPa, and the pressure maintaining time is 30min, so as to obtain a green body;
and (4) microwave sintering: placing the green body obtained in the step (3) into a microwave sintering muffle furnace for microwave sintering;
step (5) low-temperature rolling: soaking the microwave sintered sample obtained in the step (4) in liquid nitrogen, and then rolling at low temperature;
step (6) vacuum annealing: carrying out vacuum annealing treatment on the sample rolled at the low temperature in the step (5);
step (7) magnetic field cryogenic treatment: and (4) placing the sample obtained in the step (6) into a magnetic field for cryogenic treatment.
Further, in the step (2), during ball grinding, the ball grinding balls are prepared according to the mass ratio of 1:2:4 of 15mm large balls, 10mm medium balls and 5mm small balls, the ball-material ratio is 5:1, the ball grinding medium is absolute ethyl alcohol, and the ratio of the absolute ethyl alcohol to the powder-material is 3: 5.
Further, the ball milling speed is 320-400 r/min, and the ball milling time is 8-12 hours; and after the ball milling is finished, drying the prepared alloy powder by using a vacuum drying oven at the drying temperature of 70-80 ℃ for 36 hours.
Further, the parameters adopted by the microwave sintering in the step (4) are as follows: the heating rate is 35-50 ℃/min, the sintering temperature is 570-700 ℃, and the sintering time is 60-80 min.
Further, soaking the sample in liquid nitrogen for 10-20 min before rolling in the step (5) to reduce the temperature of the sample to the temperature of the liquid nitrogen; spraying liquid nitrogen on the roller in the rolling process; the rolling deformation is 10-70%.
Further, the vacuum annealing in the step (6) is: and (2) annealing step by step under a vacuum condition, wherein the first step is at 400-500 ℃ for 1-3 h, then air cooling is carried out to room temperature, the second step is at 220-300 ℃, heat preservation is carried out for 20-40 min, and then air cooling is carried out to room temperature.
Further, the magnetic field used in the magnetic field cryogenic treatment in the step (7) is a pulse magnetic field, the magnetic induction intensity is 2.5-3T, and the pulse number is 30 times.
Further, the temperature of the magnetic field cryogenic treatment in the step (7) is-110 ℃ to-196 ℃, and the cryogenic time is 24-48 hours.
The wear-resistant aluminum alloy prepared by the preparation method.
The invention has the beneficial effects that:
1) the invention improves the hardness and the wear resistance of the alloy through multi-element microalloying, and can obviously improve the wear resistance of the aluminum alloy by adding elements such as silicon, zirconium, titanium, copper, tin, manganese, niobium, iron, nickel, chromium, vanadium and molybdenum into the alloy. Compared with the existing aluminum-silicon series casting wear-resistant aluminum alloy, aluminum-zinc-magnesium-copper series and aluminum-copper series high-strength wear-resistant aluminum alloy, rare earth and alkali metal alterants such as yttrium and strontium which are few in resources and high in price are not used, so that the environmental pollution and the cost are reduced; the invention selects the content of elements such as silicon, zirconium, copper, nickel, manganese and the like, and adds elements such as chromium, vanadium, molybdenum and tin, and the elements and aluminum, silicon, zirconium, copper, nickel and manganese are easy to generate high-strength and high-toughness wear-resistant alloy by a mechanical alloying method; the tensile strength of the material is improved to over 800MPa, which is improved by over 30 percent compared with the prior high-strength aluminum alloy, the alloy has high hardness, fine dispersion strengthening phase and obviously improved wear resistance by about 18.09 percent compared with the seven-series wear-resistant aluminum alloy.
2) Compared with the traditional melting preparation method, the mechanical alloying used in the invention is a combination technology which carries out forced solid solution among atoms of different elements by a non-equilibrium means and finally can obtain alloy powder with fine crystal grains and uniform component and tissue distribution; the mechanical alloying has the advantages that the problem of melting point of raw materials is not needed to be considered, the melting temperature is too high or the difference of the melting points is too large, the melting points can be effectively combined together, the obtained alloy has uniform components and no segregation phenomenon, the alloy prepared by the method does not have the problems of shrinkage porosity and shrinkage cavity, the grain size of the alloy is smaller, and the hardness and the wear resistance of the aluminum alloy can be effectively improved.
3) According to the invention, a microwave sintering technology is used, and the microwave sintering technology has the advantages of low-temperature quick firing, so that a uniform fine crystal structure and high compactness can be formed inside the material, and the performance of the material is improved; meanwhile, when the material is heated by microwave sintering, the temperature difference of each part of the material is almost not generated, particles are uniformly distributed in the powder, defects such as segregation and the like are almost not generated, and the performance of the aluminum alloy is greatly improved.
4) According to the invention, liquid nitrogen low-temperature rolling is applied, and along with the improvement of rolling deformation, the strength and plasticity of the material are simultaneously improved, the strength is improved because of the increase of dislocation density caused by plastic deformation, and the plasticity is improved because the high-density pre-existing dislocation starts under the action of stress and forms nano-crystals and sub-crystals.
5) In the invention, the method is used for promoting the generation of twin crystal and sub-crystal tissues, promoting phase change and improving the density of the material, thereby improving the wear resistance of the material.
Detailed Description
In order that those skilled in the art may better understand the technical solutions of the present invention, these examples are only intended to illustrate the present invention, and do not limit the scope of the present invention in any way; in the following examples, various procedures and methods not described in detail are conventional methods well known in the art.
Microhardness experiments of aluminum alloys were performed on a digital microhardness tester; the abrasion experiment of the aluminum alloy is carried out on an MMU-5GA microcomputer controlled high-temperature friction abrasion tester; the test sample size is 4.8mm multiplied by 12.7mm pin test sample, and the grinding material is GCr15 steel processed into D54mm multiplied by 8mm disk test sample; dry sliding friction wear is adopted, the experimental temperature is 25 ℃, the load is 150N, the rotating speed is 50r/min, and the wear time is 20 min; abrasion resistance is expressed in terms of loss of abrasion.
Example 1:
the composition of the wear-resistant aluminum alloy in the embodiment is as follows: 10.4% of Si, 1.5% of Zr, 1.2% of Ti, 0.05% of Cu, 1.2% of Sn, 0.5% of Mn, 1.4% of Nb, 0.07% of Fe, 0.03% of Ni, 0.05% of Cr, 0.14% of V, 0.2% of Mo and the balance of Al.
The preparation method of the wear-resistant aluminum alloy adopts the following steps:
step (1), preparing aluminum alloy powder:
powders of Si, Zr, Ti, Cu, Sn, Mn, Nb, Fe, Ni, Cr, V, Mo are formulated according to the composition in mass percent of claim 1, all of which have a particle size of 100-200 mesh and a purity of 99.9%.
Step (2), high-energy ball milling alloying:
filling the metal powder prepared in the step (1) into a zirconia ball milling tank, vacuumizing the ball milling tank, and carrying out ball milling by adopting a planetary ball mill, wherein the grinding balls are divided into three grades according to the diameter: 15 mm; a middle ball: 10 mm; and (3) small ball: 5mm, the ball milling balls are mixed according to the mass ratio of 1:2:4, the ball-material ratio is 5:1, the ball milling medium is absolute ethyl alcohol, the ratio of the absolute ethyl alcohol to the powder is 3:5, the ball milling rotating speed is 400r/min, and the ball milling time is 10 hours; and after the ball milling is finished, drying the prepared alloy powder by using a vacuum drying oven at the drying temperature of 75 ℃ for 36 hours to obtain the alloy powder.
Step (3), cold isostatic pressing:
and (3) placing the alloying powder prepared in the step (2) into a rubber mold for cold isostatic pressing, wherein the static pressure is 400MPa, and the pressure maintaining time is 30min, so that a green body is obtained.
Step (4), microwave sintering:
and (4) placing the green body obtained in the step (3) into a microwave sintering muffle furnace for microwave sintering, wherein the sintering temperature is 570 ℃, the sintering time is 80min, and the heating rate is 35 ℃/min.
Step (5), low-temperature rolling:
and (5) soaking the microwave sintering sample obtained in the step (4) in liquid nitrogen for 10min, and then performing low-temperature rolling, wherein the rolling deformation is 20%.
Step (6), vacuum annealing:
and (3) carrying out vacuum annealing treatment on the sample rolled at the low temperature in the step (5), carrying out step annealing under a vacuum condition, carrying out heat preservation for 2 hours at 400 ℃ in the first step, then carrying out air cooling to the room temperature, carrying out heat preservation for 30min at 220 ℃ in the second step, and then carrying out air cooling to the room temperature.
Step (7), magnetic field cryogenic treatment:
placing the sample obtained in the step (6) into a magnetic field for cryogenic treatment, wherein the magnetic field is a pulse magnetic field, the magnetic induction intensity is 2.5T, and the pulse number is 30 times; the temperature of the deep cooling treatment is-110 ℃, and the deep cooling time is 24 hours.
The aluminum alloy prepared in example 1 was subjected to a frictional wear test and a microhardness test, and the results of the tests are shown in table 1.
Example 2:
the composition of the wear-resistant aluminum alloy of the embodiment is as follows: 10.9% of Si, 2% of Zr, 1.7% of Ti, 0.07% of Cu, 1.5% of Sn, 0.6% of Mn, 1.. 7% of Nb, 0.15% of Fe, 0.12% of Ni, 0.1% of Cr, 0.19% of V, 0.21% of Mo and the balance of Al.
The preparation method of the wear-resistant aluminum alloy comprises the following steps:
step (1), preparing aluminum alloy powder:
powders of Si, Zr, Ti, Cu, Sn, Mn, Nb, Fe, Ni, Cr, V, Mo, all of which have a particle size of 100-200 mesh and a purity of 99.9% grade, are formulated according to the composition in mass percent of claim 1.
Step (2), high-energy ball milling alloying:
filling the metal powder prepared in the step (1) into a zirconia ball-milling tank, vacuumizing the ball-milling tank, and carrying out ball milling by adopting a planetary ball mill, wherein the grinding balls are divided into three grades according to the diameters: 15 mm; a middle ball: 10 mm; and (3) small ball: 5mm, the ball milling balls are mixed according to the mass ratio of 1:2:4, the ball-material ratio is 5:1, the ball milling medium is absolute ethyl alcohol, the ratio of the absolute ethyl alcohol to the powder is 3:5, the ball milling rotating speed is 400r/min, and the ball milling time is 10 hours; and after the ball milling is finished, drying the prepared alloy powder by using a vacuum drying oven at the drying temperature of 75 ℃ for 36 hours to obtain the alloy powder.
Step (3), cold isostatic pressing:
and (3) putting the alloying powder prepared in the step (2) into a rubber mould for cold isostatic pressing, wherein the static pressure is 400MPa, and the pressure maintaining time is 30min, so that a green body is obtained.
Step (4), microwave sintering:
and (4) placing the green body obtained in the step (3) into a microwave sintering muffle furnace for microwave sintering, wherein the sintering temperature is 620 ℃, the sintering time is 70min, and the heating rate is 40 ℃/min.
Step (5), low-temperature rolling:
and (5) soaking the microwave sintered sample obtained in the step (4) in liquid nitrogen for 15min, and then performing low-temperature rolling, wherein the rolling deformation is 45%.
Step (6), vacuum annealing:
and (3) carrying out vacuum annealing treatment on the sample rolled at the low temperature in the step (5), carrying out step annealing under a vacuum condition, carrying out heat preservation for 1h at 450 ℃ in the first step, then carrying out air cooling to the room temperature, carrying out heat preservation for 20min at 250 ℃ in the second step, and then carrying out air cooling to the room temperature.
Step (7), magnetic field cryogenic treatment:
placing the sample obtained in the step (6) into a magnetic field for cryogenic treatment, wherein the magnetic field is a pulse magnetic field, the magnetic induction intensity is 3T, and the pulse number is 30 times; the temperature of the deep cooling treatment is-196 ℃, and the deep cooling time is 36 h.
The aluminum alloy prepared in example 2 was subjected to a frictional wear test and a microhardness test, and the results of the tests are shown in table 1.
Comparative example 1:
to illustrate the technical effects of the present invention, a commercial 7075 aluminum alloy was selected for performance comparison experiments, and a commercially available 7075 wrought aluminum alloy was used in comparative example 1 for frictional wear tests and microhardness experiments, the method being detailed in the detailed description, and the experimental results being shown in table 1.
Comparative example 2:
the aluminum alloy casting blank is prepared by adopting the aluminum alloy components which are completely the same as those in the embodiment 1 and adopting the traditional method for producing the wear-resistant aluminum alloy, namely, smelting alloying, air blowing refining, semi-continuous casting molding and T6 heat treatment, the casting blank sample is taken to carry out the performance test experiment which is completely the same as that in the embodiment 1, the experimental comparison data of the comparative example 2 are obtained and are summarized in the table 1, and the comparison result shows that the wear resistance and the hardness of the material are obviously improved by adopting the preparation method provided by the invention.
Comparative example 3:
the 7075 aluminum alloy components which are completely the same as those of the 7075 aluminum alloy block in the comparative example 1 are adopted, only the preparation method is adopted, the preparation process is completely the same as that of the 7075 aluminum alloy block in the example 2, the 7075 aluminum alloy block is obtained, the sample in the comparative example 3 is taken to carry out a performance test experiment which is completely the same as that of the example 2, experimental comparison data of the comparative example 3 are obtained and are summarized in a table 1, and the preparation method disclosed by the invention is used for obviously improving the wear resistance and the hardness of the material.
TABLE 1 Friction-wear Properties and microhardness of different aluminium alloys
As can be seen by comparing the performance test results of the examples and the comparative examples in Table 1, the wear-resistant aluminum alloy and the preparation method of the invention have the performance advantages in terms of components and preparation methods compared with the existing commercial wear-resistant aluminum alloy, and the improvement of the invention is reflected, namely, the aluminum alloy with high wear resistance can be prepared according to the invention.
The present invention is not limited to the above-described embodiments, and any obvious improvements, substitutions or modifications can be made by those skilled in the art without departing from the spirit of the present invention.
Claims (10)
1. The method for preparing the wear-resistant aluminum alloy of claim 1, comprising the steps of:
weighing aluminum alloy powder: weighing and mixing powders of Si, Zr, Ti, Cu, Sn, Mn, Nb, Fe, Ni, Cr, V and Mo according to the following mass percent, wherein the powders comprise 10.4-11.8% of Si, 1.5-2.5% of Zr, 1.2-2.2% of Ti, 0.05-0.1% of Cu, 1.2-1.7% of Sn, 0.5-0.7% of Mn, 1.4-2.4% of Nb, 0.07-0.2% of Fe, 0.03-0.15% of Ni, 0.05-0.15% of Cr, 0.14-0.22% of V, 0.2-0.25% of Mo and the balance of Al;
step (2) high-energy ball milling alloying: putting the mixed metal powder into a zirconia ball milling tank, vacuumizing the ball milling tank, and carrying out ball milling and drying by adopting a planetary ball mill to obtain alloyed aluminum alloy powder;
and (3) cold isostatic pressing: putting the aluminum alloy powder prepared in the step (2) into a rubber mold for cold isostatic pressing to prepare a green body;
and (4) microwave sintering: placing the green body obtained in the step (3) into a microwave sintering muffle furnace for microwave sintering;
step (5) low-temperature rolling: soaking the microwave sintering sample obtained in the step (4) in liquid nitrogen, and then rolling at low temperature;
step (6) vacuum annealing: carrying out vacuum annealing treatment on the sample rolled at the low temperature in the step (5);
step (7) magnetic field cryogenic treatment: and (4) placing the sample obtained in the step (6) into a magnetic field for cryogenic treatment.
2. The method of producing a wear-resistant aluminum alloy according to claim 1, wherein: the particle size of the powder in the step (1) is 100-200 meshes.
3. The method of making a wear resistant aluminum alloy of claim 1, wherein: in the step (2), during ball milling, the ball milling balls are prepared according to the mass ratio of 15mm large balls, 10mm medium balls and 5mm small balls of 1:2:4, the ball-material ratio is 5:1, the ball milling medium is absolute ethyl alcohol, and the ratio of the absolute ethyl alcohol to the powder-material ratio is 3: 5.
4. The method of making a wear resistant aluminum alloy of claim 1, wherein: in the step (2), the ball milling speed is 320-400 r/min, and the ball milling time is 8-12 hours; and after the ball milling is finished, drying the prepared alloy powder by using a vacuum drying oven at the drying temperature of 70-80 ℃ for 36 hours.
5. The method of producing a wear-resistant aluminum alloy according to claim 1, wherein: the parameters adopted by the microwave sintering in the step (4) are as follows: the heating rate is 35-50 ℃/min, the sintering temperature is 570-700 ℃, and the sintering time is 60-80 min.
6. The method of making a wear resistant aluminum alloy of claim 1, wherein: soaking the sample in liquid nitrogen for 10-20 min before rolling in the step (5) to reduce the temperature of the sample to the temperature of the liquid nitrogen; spraying liquid nitrogen on the roller in the rolling process; the rolling deformation is 10-70%.
7. The method of producing a wear-resistant aluminum alloy according to claim 1, wherein: the vacuum annealing in the step (6) comprises the following steps: and (2) annealing step by step under a vacuum condition, wherein the first step is at 400-500 ℃ for 1-3 h, then air cooling is carried out to room temperature, the second step is at 220-300 ℃, heat preservation is carried out for 20-40 min, and then air cooling is carried out to room temperature.
8. The method of producing a wear-resistant aluminum alloy according to claim 1, wherein: the magnetic field used in the magnetic field cryogenic treatment in the step (7) is a pulse magnetic field, the magnetic induction intensity is 2.5-3T, and the pulse number is 30 times.
9. The method of making a wear resistant aluminum alloy of claim 1, wherein: the temperature of the magnetic field cryogenic treatment in the step (7) is-110 ℃ to-196 ℃, and the cryogenic time is 24-48 hours.
10. The wear-resistant aluminum alloy prepared by the preparation method of any one of claims 1 to 9.
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Citations (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0147769A2 (en) * | 1983-12-19 | 1985-07-10 | Sumitomo Electric Industries Limited | Dispersion-strengthened heat- and wear-resistant aluminum alloy and process for producing same |
| CA2071503A1 (en) * | 1989-12-11 | 1991-06-12 | Kevin Philip Rogers | Controlled casting of al-si hypereutectic alloys |
| DE4039365A1 (en) * | 1990-12-10 | 1992-06-11 | Bruker Analytische Messtechnik | NMR magnet for highly homogeneous magnetic field - uses at least one superconducting magnetic coil in first chamber of cryostat in deep cooled liquid helium |
| JP2006002148A (en) * | 2005-05-23 | 2006-01-05 | Toshiba Corp | Cryogenic heat storage material, method for producing the cryogenic heat storage material, and method for producing cryogenic heat storage device |
| CN101824585A (en) * | 2010-05-14 | 2010-09-08 | 江苏大学 | Cold treatment method for preparing high-toughness metal-base composite material |
| CN104694792A (en) * | 2015-03-23 | 2015-06-10 | 苏州市神龙门窗有限公司 | Corrosion resistant aluminum alloy material containing hypo eutectic silicon and treatment process thereof |
| CN105331911A (en) * | 2015-11-30 | 2016-02-17 | 江苏大学 | Copious cooling and magnetic field treating method for improving plastic processing performance of magnesium alloy |
| CN108754240A (en) * | 2018-05-31 | 2018-11-06 | 江苏大学 | A kind of magnetism aluminum matrix composite and preparation method thereof |
| CN110523997A (en) * | 2019-08-19 | 2019-12-03 | 江苏大学 | A kind of subzero treatment aluminum matrix composite and preparation method thereof of high-entropy alloy particle enhancing |
| CN110951990A (en) * | 2019-11-22 | 2020-04-03 | 福州大学 | Cu-Ni-Co-Fe-Si-Zr-Zn copper alloy material and preparation method thereof |
-
2022
- 2022-04-13 CN CN202210382682.1A patent/CN114774728B/en active Active
Patent Citations (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0147769A2 (en) * | 1983-12-19 | 1985-07-10 | Sumitomo Electric Industries Limited | Dispersion-strengthened heat- and wear-resistant aluminum alloy and process for producing same |
| CA2071503A1 (en) * | 1989-12-11 | 1991-06-12 | Kevin Philip Rogers | Controlled casting of al-si hypereutectic alloys |
| DE4039365A1 (en) * | 1990-12-10 | 1992-06-11 | Bruker Analytische Messtechnik | NMR magnet for highly homogeneous magnetic field - uses at least one superconducting magnetic coil in first chamber of cryostat in deep cooled liquid helium |
| JP2006002148A (en) * | 2005-05-23 | 2006-01-05 | Toshiba Corp | Cryogenic heat storage material, method for producing the cryogenic heat storage material, and method for producing cryogenic heat storage device |
| CN101824585A (en) * | 2010-05-14 | 2010-09-08 | 江苏大学 | Cold treatment method for preparing high-toughness metal-base composite material |
| CN104694792A (en) * | 2015-03-23 | 2015-06-10 | 苏州市神龙门窗有限公司 | Corrosion resistant aluminum alloy material containing hypo eutectic silicon and treatment process thereof |
| CN105331911A (en) * | 2015-11-30 | 2016-02-17 | 江苏大学 | Copious cooling and magnetic field treating method for improving plastic processing performance of magnesium alloy |
| CN108754240A (en) * | 2018-05-31 | 2018-11-06 | 江苏大学 | A kind of magnetism aluminum matrix composite and preparation method thereof |
| CN110523997A (en) * | 2019-08-19 | 2019-12-03 | 江苏大学 | A kind of subzero treatment aluminum matrix composite and preparation method thereof of high-entropy alloy particle enhancing |
| CN110951990A (en) * | 2019-11-22 | 2020-04-03 | 福州大学 | Cu-Ni-Co-Fe-Si-Zr-Zn copper alloy material and preparation method thereof |
Non-Patent Citations (1)
| Title |
|---|
| 徐晋勇;高清;龙向前;许敏;高原;徐重;: "深冷处理对碳钢表面Mo-Cr合金层摩擦性能的影响" * |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN116949259A (en) * | 2023-08-15 | 2023-10-27 | 华中科技大学 | Preparation method of metal material and metal material |
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