CN111644619A - Preparation method of 3D printing isotropic high-strength aluminum alloy - Google Patents
Preparation method of 3D printing isotropic high-strength aluminum alloy Download PDFInfo
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- CN111644619A CN111644619A CN202010462685.7A CN202010462685A CN111644619A CN 111644619 A CN111644619 A CN 111644619A CN 202010462685 A CN202010462685 A CN 202010462685A CN 111644619 A CN111644619 A CN 111644619A
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- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 37
- 238000010146 3D printing Methods 0.000 title claims abstract description 17
- 238000002360 preparation method Methods 0.000 title claims abstract description 16
- 239000000843 powder Substances 0.000 claims abstract description 45
- 238000005516 engineering process Methods 0.000 claims abstract description 13
- 238000007639 printing Methods 0.000 claims abstract description 13
- 238000000034 method Methods 0.000 claims abstract description 10
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims abstract description 10
- 229910000990 Ni alloy Inorganic materials 0.000 claims abstract description 9
- 238000009689 gas atomisation Methods 0.000 claims abstract description 9
- 229910052796 boron Inorganic materials 0.000 claims abstract description 8
- 230000032683 aging Effects 0.000 claims abstract description 7
- 239000012298 atmosphere Substances 0.000 claims description 4
- 238000007648 laser printing Methods 0.000 claims description 4
- 239000012300 argon atmosphere Substances 0.000 claims description 2
- 238000004321 preservation Methods 0.000 claims description 2
- 238000012216 screening Methods 0.000 claims description 2
- 239000000203 mixture Substances 0.000 claims 1
- 239000000956 alloy Substances 0.000 abstract description 11
- 229910045601 alloy Inorganic materials 0.000 abstract description 9
- 229910052802 copper Inorganic materials 0.000 abstract description 6
- 229910052759 nickel Inorganic materials 0.000 abstract description 6
- 229910052710 silicon Inorganic materials 0.000 abstract description 6
- 229910052726 zirconium Inorganic materials 0.000 abstract description 6
- 238000005728 strengthening Methods 0.000 abstract description 5
- 229910052782 aluminium Inorganic materials 0.000 abstract description 4
- 239000013078 crystal Substances 0.000 abstract description 4
- 239000011812 mixed powder Substances 0.000 abstract description 4
- 229910016459 AlB2 Inorganic materials 0.000 abstract description 3
- 239000002244 precipitate Substances 0.000 abstract description 2
- 239000000654 additive Substances 0.000 abstract 1
- 238000007711 solidification Methods 0.000 abstract 1
- 230000008023 solidification Effects 0.000 abstract 1
- 239000002245 particle Substances 0.000 description 6
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 4
- 229910052786 argon Inorganic materials 0.000 description 2
- 238000001514 detection method Methods 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 238000003892 spreading Methods 0.000 description 2
- 239000000758 substrate Substances 0.000 description 2
- 230000002195 synergetic effect Effects 0.000 description 2
- 239000013585 weight reducing agent Substances 0.000 description 2
- 229910016343 Al2Cu Inorganic materials 0.000 description 1
- 229910003407 AlSi10Mg Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 229910001069 Ti alloy Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 230000017525 heat dissipation Effects 0.000 description 1
- 230000010354 integration Effects 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 239000002667 nucleating agent Substances 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
Classifications
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- B22F1/0003—
-
- 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
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
- B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
- B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B33—ADDITIVE MANUFACTURING TECHNOLOGY
- B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
- B33Y10/00—Processes of additive manufacturing
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B33—ADDITIVE MANUFACTURING TECHNOLOGY
- B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
- B33Y70/00—Materials specially adapted for additive manufacturing
-
- 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
- C22C1/058—Mixtures of metal powder with non-metallic powder by reaction sintering (i.e. gasless reaction starting from a mixture of solid metal compounds)
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/007—Alloys based on nickel or cobalt with a light metal (alkali metal Li, Na, K, Rb, Cs; earth alkali metal Be, Mg, Ca, Sr, Ba, Al Ga, Ge, Ti) or B, Si, Zr, Hf, Sc, Y, lanthanides, actinides, as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
-
- 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
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
- C22C32/0073—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only borides
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Powder Metallurgy (AREA)
Abstract
The invention provides a method for preparing isotropic aluminum alloy by adopting a 3D printing technology, and belongs to the field of aluminum alloy. By adding additives to the aluminiumSi, Cu, Ni, Zr and B elements are respectively prepared into the aluminum alloy powder and the nickel alloy powder by adopting a gas atomization powder preparation technology according to the mass ratio of 98.5%: 1.5 percent of the mixed powder is mixed to obtain mixed powder which can form nano-scale ZrB in the printing process2Phase sum AlB2The phase can obviously eliminate the solidification columnar crystal structure, refine crystal grains, make the alloy isotropic, and precipitate Si and Al through subsequent aging treatment2Cu、Al3The Ni submicron-scale strengthening phase can obviously improve the room temperature strength and the high temperature strength of the aluminum alloy, and simultaneously the alloy keeps high elongation.
Description
Technical Field
The invention belongs to the field of aluminum alloys, and relates to a preparation method of 3D printing isotropic high-strength aluminum alloy.
Background
The metal 3D printing technology has high complexity of forming parts, is particularly suitable for manufacturing precision parts with complex structures (such as heat dissipation devices with inner flow channels or complex grid structures), has wide application prospects in the industrial field, and is widely used for preparing metal materials such as aluminum alloy, titanium alloy, high-temperature alloy, steel and the like. The aluminum alloy material has high specific strength and excellent corrosion resistance, and has wide application in the fields of automobile industry, aerospace and the like. At present, in the aerospace field, the 3D printing technology can solve the processing and manufacturing problems of extremely complex precision components, has inherent advantages on complex structure problems of conformal internal flow channels, complex thin walls, hollow weight reduction, complex inner cavities, multi-component integration and the like, and is an important field for the rapid development of the 3D printing technology. However, in the application of 3D printing aluminum alloy, most of the marks are not suitable for 3D printing due to the forming characteristics of the traditional aluminum alloy. Only a few cast aluminum alloys suitable for 3D printing, including AlSi10Mg, AlSi12 and the like, cannot be applied to large-scale application in the high-end aerospace field due to the limitation of material properties, and are difficult to meet the requirements of high strength and high temperature use, so that the application requirements of 3D printing on weight reduction of aerospace are greatly limited.
Disclosure of Invention
Aiming at the problems of low strength, particularly low high-temperature strength and anisotropy of the existing 3D printing aluminum alloy, the invention designs a new aluminum alloy component, a proper amount of Si, Cu, Ni, Zr and B elements are added into aluminum, so that a plurality of submicron strengthening phases can be generated in the printing process and the subsequent aging process, and the room-temperature strength and the high-temperature strength of the alloy can be greatly improved through the synergistic effect of the strengthening phases, and meanwhile, the printed part has good formability and no cracks or deformation defects.
A preparation method of 3D printing isotropic high-strength aluminum alloy is characterized by comprising the following steps: the preparation steps are as follows: (1) preparing aluminum alloy powder by adopting a gas atomization powder preparation technology, wherein the mass ratio of the powder is Al (5.5-6.0%) Si (1-1.2%) Cu (1.1-1.2%) Zr;
(2) preparing alloy powder with the mass ratio of Ni to (30-35)% B by adopting a gas atomization powder preparation technology;
(3) screening the aluminum alloy powder prepared in the step (1) and the Ni alloy powder prepared in the step (2) respectively, and then, according to the mass ratio of 98.5%: mixing was carried out at a ratio of 1.5%.
(4) Performing laser printing on the part by adopting a powder bed type 3D printer, wherein the atmosphere is argon atmosphere;
(5) and carrying out aging treatment after printing.
Further, the particle size of the aluminum alloy powder in the step (3) is 15-53 microns, and the particle size of the Ni alloy powder is 5-10 microns.
Further, the laser printing laser power in the step (4) is controlled within the range of 200-.
Further, the aging treatment temperature in the step (5) is 500-550 ℃, and the heat preservation time is 60-90 minutes.
The aluminum alloy material prepared by adopting the parameters has the room temperature tensile strength of 580-one-600 MPa, the yield strength of 560-one-580 MPa, the elongation rate of more than 12 percent, the high temperature tensile strength at 250 ℃ of more than 260MPa, the yield strength of more than 190MPa and the elongation rate of more than 10 percent, and can meet the performance requirements of aerospace on aluminum alloy parts.
The invention has the advantages that (1) the aluminum alloy powder and the nickel alloy powder with designed components are mixed to generate the ZrB with the nanometer scale in the process of printing and melting2Phase sum AlB2The two phases are dispersed and distributed in the melt to play the role of nucleating agent, so that the crystal grains can be effectively refined, equiaxed crystals are obtained, and two phases which adopt single ZrB are generated simultaneously2When the phase is subjected to grain refinement, the obtained grains are finer, so that the strength is higher; (2) aging at 550 ℃ can simultaneously precipitate Si and Al2Cu、Al3Ni three submicrometer-scale strengthening phases, and ZrB with nanometer scale2、AlB2The alloy can be subjected to synergistic strengthening, and the alloy has high room temperature strength and high temperature strength.
The specific implementation mode is as follows:
(1) a powder bed type laser printer is adopted to prepare a high-strength aluminum alloy with the components of Al, 5.91 percent of Si, 0.98 percent of Cu, 1.05 percent of Ni, 1.08 percent of Zr and 0.45 percent of B
Firstly, preparing aluminum alloy powder by adopting a gas atomization powder preparation technology, wherein the mass ratio of the powder is Al-6% of Si-1% of Cu-1.1% of Zr; preparing alloy powder with the mass ratio of Ni-30% by adopting a gas atomization powder preparation technology; then, the aluminum alloy powder prepared in the first step and the Ni alloy powder prepared in the second step are respectively sieved, the selected particle size of the former is 15-53 microns, the particle size of the latter is 5-10 microns, and then the mass ratio is 98.5%: 1.5 percent of Al, 5.91 percent of Si, 0.98 percent of Cu, 1.05 percent of Ni, 1.08 percent of Zr and 0.45 percent of B; then the mixed powder is placed in a powder bed type laser printer for printing, argon gas is adopted as printing atmosphere, the laser power is 200W, the scanning speed is 500mm/s, the diameter of a laser spot is 90 mu m, the printing size is 50mm (length) multiplied by 50mm (width) multiplied by 50mm (height), the powder spreading thickness of each layer is 60 mu m, the angle between layers is 60 degrees, and the temperature of the substrate is kept at 100 ℃. After printing, the sample is kept at 500 ℃ for 60 minutes and then cooled to room temperature along with the furnace, and the sample is taken for mechanical property detection, wherein the room temperature tensile strength reaches 590MPa, the yield strength reaches 565MPa, the elongation is 12.5%, the high temperature tensile strength at 250 ℃ is 265MPa, the yield strength is 197MPa, and the elongation is 13.4%, so that the performance requirements of aerospace on aluminum alloy parts can be met.
(2) A powder bed type laser printer is adopted to prepare a high-strength aluminum alloy with the components of Al, 5.4 percent of Si, 0.98 percent of Cu, 0.97 percent of Ni, 1.12 percent of Zr and 0.52 percent of B
Firstly, preparing aluminum alloy powder by adopting a gas atomization powder preparation technology, wherein the mass ratio of the powder is Al-5.5% of Si-1% of Cu-1.2% of Zr; preparing alloy powder with the mass ratio of Ni-35% by adopting a gas atomization powder preparation technology; then, the aluminum alloy powder prepared in the first step and the Ni alloy powder prepared in the second step are respectively sieved, the selected particle size of the former is 15-53 microns, the particle size of the latter is 5-10 microns, and then the mass ratio is 98.5%: 1.5 percent of Al, 5.4 percent of Si, 0.98 percent of Cu, 0.97 percent of Ni, 1.12 percent of Zr and 0.52 percent of B; then the mixed powder is placed in a powder bed type laser printer for printing, argon gas is adopted as printing atmosphere, the laser power is 230W, the scanning speed is 700mm/s, the diameter of a laser spot is 100 mu m, the printing size is 50mm (length) multiplied by 60mm (width) multiplied by 100mm (height), the powder spreading thickness of each layer is 60 mu m, the angle between layers is 60 degrees, and the temperature of the substrate is kept at 100 ℃. After printing, the sample is kept at 550 ℃ for 90 minutes and then cooled to room temperature along with the furnace, and mechanical property detection is carried out on the sample, wherein the room-temperature tensile strength reaches 596MPa, the yield strength reaches 570MPa, the elongation is 12.1%, the high-temperature tensile strength at 250 ℃ is 269MPa, the yield strength is 199MPa, and the elongation is 13.3%, so that the performance requirements of aerospace on aluminum alloy parts can be met.
Claims (4)
1. A preparation method of 3D printing isotropic high-strength aluminum alloy is characterized by comprising the following steps: the preparation steps are as follows:
(1) preparing aluminum alloy powder by adopting a gas atomization powder preparation technology, wherein the mass ratio of the powder is Al (5.5-6%) Si (1-1.2%) Cu (1.1-1.2%) Zr;
(2) preparing nickel alloy powder with the mass ratio of Ni to (30-35)% B by adopting a gas atomization powder preparation technology;
(3) screening the aluminum alloy powder prepared in the step (1) and the nickel alloy powder prepared in the step (2) respectively, and then, according to the mass ratio of 98.5%: 1.5 percent of the mixture is mixed;
(4) performing laser printing on the part by adopting a powder bed type 3D printer, wherein the atmosphere is argon atmosphere;
(5) and carrying out aging treatment after printing.
2. The method for preparing the 3D printing isotropic high-strength aluminum alloy according to claim 1, wherein the method comprises the following steps: the granularity of the aluminum alloy powder in the step (3) is 15-53 microns, and the granularity of the nickel alloy powder is 5-10 microns.
3. The method for preparing the 3D printing isotropic high-strength aluminum alloy according to claim 1, wherein the method comprises the following steps: and (4) controlling the laser printing laser power within the range of 200-.
4. The method for preparing the 3D printing isotropic high-strength aluminum alloy according to claim 1, wherein the method comprises the following steps: the aging treatment temperature in the step (5) is 500-550 ℃, and the heat preservation time is 60-90 minutes.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
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| CN202010462685.7A CN111644619B (en) | 2020-05-27 | 2020-05-27 | Preparation method of 3D printing aluminum alloy |
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| CN202010462685.7A CN111644619B (en) | 2020-05-27 | 2020-05-27 | Preparation method of 3D printing aluminum alloy |
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| CN111644619A true CN111644619A (en) | 2020-09-11 |
| CN111644619B CN111644619B (en) | 2022-04-01 |
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113020585A (en) * | 2021-03-01 | 2021-06-25 | 南京理工大学 | Low-melting-point multi-component alloy additive for laser additive manufacturing of aluminum alloy |
| CN114525428A (en) * | 2020-11-03 | 2022-05-24 | 中国科学院金属研究所 | Titanium alloy system suitable for additive manufacturing process and component manufacturing process |
| CN117600494A (en) * | 2024-01-24 | 2024-02-27 | 安庆瑞迈特科技有限公司 | Printing method for improving corrosion resistance and strength of 3D printing collimator |
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| CN117600494A (en) * | 2024-01-24 | 2024-02-27 | 安庆瑞迈特科技有限公司 | Printing method for improving corrosion resistance and strength of 3D printing collimator |
| CN117600494B (en) * | 2024-01-24 | 2024-04-02 | 安庆瑞迈特科技有限公司 | Printing method for improving corrosion resistance and strength of 3D printing collimator |
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