CN112853168A - AlSi10Mg powder and selective laser melting manufacturing process - Google Patents
AlSi10Mg powder and selective laser melting manufacturing process Download PDFInfo
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- 229910003407 AlSi10Mg Inorganic materials 0.000 title claims abstract description 87
- 239000000843 powder Substances 0.000 title claims abstract description 70
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 25
- 238000002844 melting Methods 0.000 title claims abstract description 15
- 230000008018 melting Effects 0.000 title claims abstract description 15
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 39
- 229910052691 Erbium Inorganic materials 0.000 claims description 39
- 238000000034 method Methods 0.000 claims description 11
- 239000002245 particle Substances 0.000 claims description 10
- 230000008569 process Effects 0.000 claims description 8
- 239000000758 substrate Substances 0.000 claims description 7
- 229910052782 aluminium Inorganic materials 0.000 claims description 6
- 238000005275 alloying Methods 0.000 claims description 5
- 239000011261 inert gas Substances 0.000 claims description 5
- 238000010309 melting process Methods 0.000 claims description 5
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 4
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 3
- 229910052802 copper Inorganic materials 0.000 claims description 3
- 238000005520 cutting process Methods 0.000 claims description 3
- 238000011065 in-situ storage Methods 0.000 claims description 3
- 229910052742 iron Inorganic materials 0.000 claims description 3
- 229910052748 manganese Inorganic materials 0.000 claims description 3
- 239000001301 oxygen Substances 0.000 claims description 3
- 229910052760 oxygen Inorganic materials 0.000 claims description 3
- 238000003892 spreading Methods 0.000 claims description 3
- 230000007480 spreading Effects 0.000 claims description 3
- 239000000956 alloy Substances 0.000 abstract description 48
- 229910045601 alloy Inorganic materials 0.000 abstract description 47
- 238000005516 engineering process Methods 0.000 abstract description 8
- 239000000654 additive Substances 0.000 abstract description 5
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- 229910033181 TiB2 Inorganic materials 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
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
-
- B22F1/0003—
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- 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
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- 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
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- 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
- B33Y80/00—Products made by additive manufacturing
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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
- C22C1/0408—Light metal alloys
- C22C1/0416—Aluminium-based alloys
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- 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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Abstract
The invention belongs to the technical field of additive manufacturing, and particularly relates to AlSi10Mg powder and a selective laser melting manufacturing process. The AlSi10Mg powder contains Er of 0.02-0.2 at% and Zr of 0.02-0.08 at% in terms of atomic percentage. The AlSi10Mg powder is prepared into a novel AlSi10Mg alloy by adopting an SLM technology, the relative density of an SLM forming sample reaches more than 99%, the microhardness is 156 +/-7 HV, the tensile strength is 461 +/-7 MPa, and the yield strength is 304 +/-4 MPa. In addition, the tensile strength of the AlSi10Mg alloy manufactured by the novel SLM after annealing heat treatment is 411MPa, the yield strength is 272MPa, and the alloy has better thermal stability compared with the conventional AlSi10Mg alloy, and has important engineering application value in the fields of aerospace, automobile manufacturing and the like.
Description
Technical Field
The invention belongs to the technical field of additive manufacturing, and particularly relates to AlSi10Mg powder and a selective laser melting manufacturing process.
Background
Since the 20 th century 80 times of the invention of the additive manufacturing (AM, also called 3D printing) technology, research and development have been conducted for over thirty years, and since a high-performance and high-precision complex precision part can be directly prepared from a three-dimensional computer aided design model, compared with the conventional manufacturing technology, the additive manufacturing (AM, also called 3D printing) technology has many advantages of short period, no mold, no limitation of part structure, and the like. The Selective Laser Melting (SLM) technology was first developed in 1995 by the german Fraunhofer research institute, and is an emerging technology that is based on the discrete-stacking principle and is comprehensively applied by combining multiple fields of disciplines such as machinery, computers, numerical control, analog simulation, materials and the like. The SLM technology is one of the most rapidly developed high-precision metal AM technologies in the last decade, and has an extremely high cooling speed (10)5～108K/s), short crystal grain forming time, fine crystal grains, high size precision, good surface quality, excellent performance of formed parts and the like. Has been applied to aerospace, medical research and medical appliances to a certain extent, and has important application prospect in national economy and national security core fields such as transportation, automobile industry, national defense security and the like.
The AlSi10Mg alloy has small density, high specific strength and good corrosion resistance, and has wide engineering application requirements in aerospace and automobile lightweight manufacturing. Compared with other aluminum alloys, the AlSi10Mg alloy manufactured by the SLM at present has good SLM formability, mature forming process, relative density of a material additive piece of over 99.0 percent, generally obtained tensile strength of 300-420 MPa, yield strength of 150-270 MPa and elongation of 1.5-6.0 percent, and has mechanical properties of being good compared with the AlSi10Mg alloy cast traditionallyThe improvement is remarkable. However, the aerospace field has higher strength requirements on the aluminum alloy, and the current SLM manufactured AlSi10Mg alloy is difficult to meet the requirements on the high-strength aluminum alloy. In order to further improve the mechanical properties of AlSi10Mg alloy manufactured by SLM, researchers at home and abroad carry out more research and research. The composite powder was obtained by mixing ceramic particles with AlSi10Mg powder, as by means of mechanical mixing of the powders, the reported added ceramic particles being: TiB2The composite powder is subjected to SLM forming, the mechanical property is improved to a certain degree, the tensile strength can reach 400MPa, and the yield strength is more than 300 MPa. However, the method needs secondary processing of the powder, and certain influence is generated on the shape of the powder in the processing process, so that the sphericity and the particle size of the powder are damaged, the SLM forming manufacturability is difficult, a compact and crack-free formed part is difficult to prepare, and the SLM forming conditions are very harsh.
In addition, there is a report on improvement of strength of SLM-formed aluminum alloy by adding a rare earth element. Most typically, with addition of Sc as a rare earth element
The alloy, after heat treatment,
the tensile strength of the alloy can reach 520MPa, the yield strength is 480MPa, and the elongation is 13%. However, Sc is very expensive and not suitable for large-scale production and application, so that the rare earth elements which have similar strengthening effect to Sc and are low in price are required to realize strengthening of the SLM-made aluminum alloy, so that the method has important application value. The strengthening effect of the rare earth element Er in the aluminum alloy is already carried out by Nie 31066of Beijing university of industry, and the Keren team carries out research for many years, and the Er and Sc are proved to have similar strengthening effects in the aluminum alloy. This is because Er and Al form stable L1 during the solidification of Al alloy2Structural Al3And the Er phase becomes heterogeneous nucleation, and the heterogeneous nucleation is rented, so that the crystal grains of the aluminum alloy are refined. Further, Al3Er particles can alsoThe dislocation and the subgrain boundary can be pinned, so that the strength and the recrystallization temperature of the aluminum alloy are improved.
Disclosure of Invention
The invention aims to provide AlSi10Mg powder and a selective laser melting manufacturing process, which can obtain an SLM manufacturing AlSi10Mg aluminum alloy with excellent SLM forming quality. The activity is reduced mutually by adding Er and Zr in a compounding way and by means of the composite microalloying effect of the Er and the Zr, the solid solubility is increased, and Al is formed3The (Er, Zr) phase improves the mechanical property of the aluminum alloy, effectively inhibits recrystallization, improves the recrystallization temperature and further enhances the corrosion resistance, the shaping property and the weldability of the alloy.
Specifically, the invention provides the following technical scheme:
the AlSi10Mg powder comprises, by atomic percent, 0.02-0.2 at% Er and 0.02-0.08 at% Zr in the AlSi10Mg powder.
Preferably, the AlSi10Mg powder contains Er in an amount of 0.02 to 0.06 at% and Zr in an amount of 0.02 to 0.06 at% in terms of atomic percentage.
Preferably, in the AlSi10Mg powder, the AlSi10Mg powder contains the following main alloying elements in mass%: 7.50-11.50% of Si, 0.20-0.55% of Mg and the balance of aluminum; further preferably, the AlSi10Mg powder contains the following main alloying elements in mass%: 8.50-9.50% of Si, 0.20-0.40% of Mg and the balance of aluminum.
Preferably, in the AlSi10Mg powder, the AlSi10Mg powder further includes, in mass%: 0.50% or less Mn, 0.10% or less Cu, 0.15% or less Fe, and more preferably, the AlSi10Mg powder further contains, in mass%: 0.25-0.50% of Mn, less than or equal to 0.05% of Cu and 0.08-0.15% of Fe.
Preferably, in the AlSi10Mg powder, the AlSi10Mg powder has a particle size of 20 to 53 μm.
Preferably, in the AlSi10Mg powder, the AlSi10Mg powder is in-situ Er/Zr alloyed powder.
The invention also provides a selective laser melting manufacturing process by using the AlSi10Mg powder, which comprises the following steps:
(1) laying the AlSi10Mg powder on a substrate to obtain a powder layer;
(2) under the protection of inert gas, scanning the powder layer in the step (1) by using laser, and carrying out selective laser melting and forming;
(3) and (3) removing the formed part in the step (2) from the substrate by wire cutting (such as machining modes of wire electrical discharge machining, diamond wire cutting, laser cutting and the like).
Preferably, in the selective laser melting manufacturing process, the AlSi10Mg powder is vacuum-dried at 80-110 ℃ for 1-8 hours before powder spreading.
Preferably, in the selective laser melting manufacturing process, in the step (1), the thickness of the powder layer is 20 to 50 μm.
Preferably, in the selective laser melting manufacturing process, in step (2), the parameters of laser scanning include: the laser power is 90-110W, the spot diameter is 40-60 μm, the scanning distance is 30-50 μm, and the scanning speed is 900-1900 mm/s.
Preferably, in the selective laser melting manufacturing process, in the step (2), the energy density is controlled to be 52-60J/mm3. (the laser volume energy density formula is:
where ρ is the laser volume energy density, P is the laser power, h is the scanning distance, v is the scanning speed, and d is the layer thickness. )
Preferably, in the selective laser melting process, in the step (2), under the protection of inert gas, the oxygen content is 100 to 1000 ppm.
Preferably, in the selective laser melting manufacturing process, the preheating temperature of the substrate is 80-120 ℃, and the scanning paths of the adjacent two layers of lasers rotate anticlockwise by 67.7 degrees.
The principle that the SLM can be effectively strengthened to manufacture the AlSi10Mg alloy has the following aspects:
firstly, Er and Zr are added into the AlSi10Mg alloy in a compounding way, so that the activity of the Er and the Zr can be reduced, the solid solubility can be increased, and the solid solution strengthening of the Er and the Zr in the AlSi10Mg is facilitated;
second, Er and Al matrix form stable L12Structural Al3The Er phase is dispersed in the matrix and forms a coherent relationship with the matrix. These dispersed Al3The Er phase can obviously improve the mechanical property of the alloy;
third, removing Al3Outside the Er phase, Er and Zr can form ternary composite particles Al with the Al matrix3(ZrxEr1-x) The particles have better thermal stability, have pinning effect on grain boundary movement, can effectively improve the recrystallization temperature of the alloy and inhibit the growth of recrystallized grains;
fourth, Al described above3Er and Al3(ZrxEr1-x) The two phases can be used as heterogeneous nucleation particles in the SLM forming process, the nucleation number of the alloy in the SLM forming process is increased, the size of alloy grains is refined, and therefore a stable fine grain strengthening effect is obtained;
fifth, Al described above3Er and Al3(ZrxEr1-x) The pinning effect of two relative dislocations and the grain boundary can improve the opening energy required by the plastic deformation of the alloy, thereby improving the mechanical property of the alloy.
The invention has the following beneficial effects:
the novel AlSi10Mg powder provided by the invention is prepared into a sample by adopting an SLM printer, the relative density of the formed sample reaches more than 99%, the microhardness is 156 +/-7 HV, the tensile strength is 461 +/-7 MPa, the yield strength is 304 +/-4 MPa, and the elongation is 2.3 +/-0.4%. In addition, the tensile strength of the AlSi10Mg alloy manufactured by the novel SLM after annealing heat treatment is 411MPa, the yield strength is 272MPa, and the alloy has better thermal stability compared with the conventional AlSi10Mg alloy, and has important engineering application value in the fields of aerospace, automobile manufacturing and the like.
Drawings
FIG. 1 is a three-dimensional gold phase diagram of tensile specimens of the novel Er, Zr composite microalloyed AlSi10Mg alloy prepared in example 1, wherein, (a) the three-dimensional gold phase diagram, (b) X-Y plane, (c) Y-Z plane, (d) X-Z plane; (b) the scales in (c) and (d) are all 20 μm in size.
FIG. 2 is an EBSD antipodal map of tensile specimens of the novel Er, Zr composite microalloyed AlSi10Mg alloy prepared in example 1, wherein (a) is the X-Y plane and (b) is the X-Z plane; (a) the sizes of the scales in (a) and (b) are both 20 μm.
FIG. 3 is a graph comparing the room temperature mechanical properties perpendicular to the printing direction of tensile specimens of the AlSi10Mg alloy prepared in example 1 and conventional AlSi10Mg alloy, wherein AlSi10Mg represents a conventional AlSi10Mg alloy tensile specimen without Er or Zr elements, and AlSi10Mg-Er-Zr represents a novel Er and Zr composite microalloyed AlSi10Mg alloy tensile specimen.
Detailed Description
The present invention will be described in further detail with reference to specific examples, but the scope of the present invention is not limited thereto.
The experimental procedures used in the following examples are conventional unless otherwise specified. The experimental raw materials and the related equipments used in the following examples are commercially available unless otherwise specified.
Example 1
This example provides a novel AlSi10Mg powder and SLM manufacturing process.
The chemical composition of the novel AlSi10Mg powder is as follows:
si: 9.11 wt%, Mg 0.30 wt%, Cu not more than 0.05 wt%, Fe: 0.11 wt%, Mn: 0.37 wt%, Er: 0.04 at%, Zr: 0.04 at%, and the balance Al.
The novel AlSi10Mg powder containing the components is prepared by gas atomization powder preparation and in-situ alloying, and meanwhile, the powder is dried for 8 hours in a vacuum drying oven at 80 ℃ before SLM manufacturing.
In this example, an EOS M100 metal 3D printer manufactured by EOS of Germany was used to prepare an experimental sample. After the dried novel AlSi10Mg powder is loaded into a powder bin, the height of a substrate is adjusted, and technological parameters are set, wherein the laser scanning power is 92W; the diameter of a laser scanning spot is 40 mu m; the laser scanning interval is 50 μm; the thickness of the powder spreading layer is 30 mu m; the laser scanning speed is 1600 mm/s; under the protection of high-purity inert gas argon, the oxygen content is 1000 ppm; the preheating temperature of the substrate is 80 ℃; the laser scanning paths of two adjacent layers rotate anticlockwise by 67 degrees. Novel Er and Zr composite microalloyed AlSi10Mg alloy tensile specimens and 5 × 5mm microstructure analysis test blocks were printed. Using the same equipment, a conventional AlSi10Mg alloy tensile specimen without addition of Er and Zr elements and a microstructure analysis coupon of 5 × 5mm (only no Er and Zr were added to the AlSi10Mg powder compared to the Er and Zr composite microalloyed AlSi10Mg alloy tensile specimen prepared in example 1) were printed under the same environment and using the same process.
The relative density of the novel Er and Zr composite microalloyed AlSi10Mg alloy tensile sample measured by a metallographic method is 99.17%, and the three-dimensional structure morphology is shown in figure 1, wherein an X-Z surface and a Y-Z surface show the typical fish-scale micro molten pool morphology, and the X-Y surface shows the rail-like micro molten pool morphology and is consistent with the structure morphology of a conventional AlSi10Mg alloy tensile sample without Er and Zr elements. The Vickers microhardness measurement shows that the microhardness distribution of the SLM forming sample is uniform without obvious deviation, and the microhardness of the novel Er and Zr composite microalloyed AlSi10Mg alloy tensile sample is 156 +/-7 HV and is higher than the microhardness of 124 +/-4 HV of a conventional AlSi10Mg alloy tensile sample without Er and Zr.
FIG. 2 is an EBSD antipodal map of tensile specimens of the novel Er, Zr composite microalloyed AlSi10Mg alloy prepared in example 1, wherein (a) is the X-Y plane and (b) is the X-Z plane. As can be seen from FIG. 2, the average size of the alpha-Al matrix in the novel Er and Zr composite microalloyed AlSi10Mg alloy tensile sample is 0.59 μm, the average grain size is 1.27 μm, and the alpha-Al matrix is respectively reduced by 18.27% and 45.96% compared with the conventional AlSi10Mg alloy tensile sample without Er and Zr, so that the addition of Er and Zr elements can form Al with the Al matrix2Er and Al3The (Er, Zr) phase is preferentially precipitated during the solidification process of the molten pool, enriches the grain boundary and serves as heterogeneous nucleation particles to increase the nucleation quantity in unit time, and the (Er, Zr) phase also hinders the movement of the grain boundary during the grain growth process, thereby obtaining the effect of refining grains.
The tensile strength, yield strength, microhardness and elongation after fracture of the novel Er and Zr composite microalloyed AlSi10Mg alloy tensile sample are 461 +/-7 MPa, 304 +/-4 MPa, 156 +/-7 HV and 2.3 +/-0.4 percent respectively measured according to the national standard GB/T228.1-2010, and are shown in figure 3. Compared with the tensile strength, yield strength and microhardness of a conventional AlSi10Mg alloy without Er and Zr, the tensile strength, yield strength and microhardness of the alloy are respectively improved by 22.6%, 26.7% and 25.8%.
After the two are annealed at 300 ℃ for 2 hours, the tensile strength of the novel Er and Zr composite microalloyed AlSi10Mg alloy tensile sample is reduced from 461MPa to 411MPa, the yield strength is reduced from 304MPa to 272MPa, while the tensile strength of the conventional AlSi10Mg alloy tensile sample without the Er and Zr is reduced from 376MPa to 292MPa, and the yield strength is reduced from 240MPa to 184MPa, and the result shows that the novel Er and Zr composite microalloyed AlSi10Mg alloy tensile sample has better thermal stability.
Example 2
This example provides a novel AlSi10Mg powder and SLM manufacturing process.
The chemical composition of the novel AlSi10Mg powder is as follows:
si: 7.75 wt%, Mg: 0.31 wt%, Cu is less than or equal to 0.05 wt%, Fe: 0.11 wt%, Mn: 0.33 wt%, Er: 0.04 at%, Zr: 0.04 at%, and the balance Al.
The same preparation process as that of example 1 is adopted, and the result shows that the Er and Zr composite microalloyed AlSi10Mg alloy tensile sample formed by SLM of the powder provided by example 2 has the relative density of 99.07%, no macrocracks and pores, the average microhardness value of 134.6 +/-1 HV, the tensile strength of 378 +/-3 MPa and the yield strength of 245 +/-3 MPa. Compared with the forming sample without Er and Zr (compared with the Er and Zr composite microalloyed AlSi10Mg alloy tensile sample prepared in the example 2, only Er and Zr are not added into the AlSi10Mg powder), the microhardness is improved by 8HV, the tensile strength is improved by 11MPa, and the yield strength is improved by 23 MPa.
Although the invention has been described in detail hereinabove by way of general description, specific embodiments and experiments, it will be apparent to those skilled in the art that many modifications and improvements can be made thereto based on the invention. Accordingly, such modifications and improvements are intended to be within the scope of the invention as claimed.
Claims (10)
1. An AlSi10Mg powder, characterized in that the AlSi10Mg powder contains 0.02-0.2 at% Er and 0.02-0.08 at% Zr in atomic percentage.
2. The AlSi10Mg powder according to claim 1, wherein the AlSi10Mg powder contains Er 0.02-0.06 at% and Zr 0.02-0.06 at%.
3. The AlSi10Mg powder according to claim 1 or 2, wherein the AlSi10Mg powder comprises the following main alloying elements in mass%: 7.50-11.50% of Si, 0.20-0.55% of Mg and the balance of aluminum; preferably, the AlSi10Mg powder comprises the following main alloying elements in mass%: 8.50-9.50% of Si, 0.20-0.40% of Mg and the balance of aluminum.
4. The AlSi10Mg powder according to any of claims 1-3, wherein the AlSi10Mg powder further comprises, in mass%: 0.50% Mn, 0.10% Cu and 0.15% Fe, preferably, the AlSi10Mg powder contains, in mass%: 0.25-0.50% of Mn, less than or equal to 0.05% of Cu and 0.08-0.15% of Fe.
5. The AlSi10Mg powder according to any one of claims 1-4, wherein the AlSi10Mg powder has a particle size of 20-53 μm, and preferably the AlSi10Mg powder is Er, Zr in-situ alloyed powder.
6. A process for the selective laser melting manufacturing using AlSi10Mg powder according to any of claims 1-5, comprising the steps of:
(1) laying the AlSi10Mg powder on a substrate to obtain a powder layer;
(2) under the protection of inert gas, scanning the powder layer in the step (1) by using laser, and carrying out selective laser melting and forming;
(3) and (3) removing the formed part obtained in the step (2) from the substrate through wire cutting.
7. The selective laser melting process according to claim 6, wherein the AlSi10Mg powder is vacuum dried at 80-110 ℃ for 1-8 hours before powder spreading.
8. The selective laser melting process according to claim 6 or 7, wherein in the step (1), the thickness of the powder layer is 20-50 μm.
9. The selective laser melting process according to any one of claims 6 to 8, wherein in step (2), the parameters of the laser scanning include: the laser power is 90-110W, the spot diameter is 40-60 μm, the scanning distance is 30-50 μm, and the scanning speed is 900-1900 mm/s.
10. The selective laser melting process as claimed in any one of claims 6 to 9, wherein in the step (2), the energy density of the energy is controlled to be 52 to 60J/mm3；
And/or in the step (2), under the protection of inert gas, the oxygen content is 100-1000 ppm.
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| CN202011623507.4A CN112853168A (en) | 2020-12-31 | 2020-12-31 | AlSi10Mg powder and selective laser melting manufacturing process |
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Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113787198A (en) * | 2021-09-16 | 2021-12-14 | 中国工程物理研究院机械制造工艺研究所 | Printing process for improving mechanical property of AlSi9Mg1ScZr formed by SLM |
| CN114395742A (en) * | 2021-12-10 | 2022-04-26 | 中国商用飞机有限责任公司 | Heat treatment method for selective laser melting of AlSi10Mg alloy |
| CN114959519A (en) * | 2022-06-10 | 2022-08-30 | 中国航发北京航空材料研究院 | AlSi for reducing selective laser melting 10 Method for residual stress of Mg alloy |
| CN115141989A (en) * | 2022-06-17 | 2022-10-04 | 中国航发北京航空材料研究院 | Method for improving strength of AlSi10Mg alloy melted in laser selected area |
| CN116117165A (en) * | 2023-02-27 | 2023-05-16 | 常州钢研极光增材制造有限公司 | Manufacturing method for improving comprehensive performance of AlSi10Mg aluminum alloy workpiece |
| CN116900306A (en) * | 2023-09-14 | 2023-10-20 | 内蒙古工业大学 | AlSi10Mg/ZrO 2 Composite metal powder and forming process thereof |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108396203A (en) * | 2018-05-04 | 2018-08-14 | 上海康速金属材料有限公司 | Rare earth er element enhances the special AlSi10Mg Al alloy powders of SLM and its application |
| CN110172620A (en) * | 2019-06-13 | 2019-08-27 | 江苏科技大学 | Selective laser melting process Al-Si-Mg alloy and its product preparation method |
-
2020
- 2020-12-31 CN CN202011623507.4A patent/CN112853168A/en active Pending
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108396203A (en) * | 2018-05-04 | 2018-08-14 | 上海康速金属材料有限公司 | Rare earth er element enhances the special AlSi10Mg Al alloy powders of SLM and its application |
| CN110172620A (en) * | 2019-06-13 | 2019-08-27 | 江苏科技大学 | Selective laser melting process Al-Si-Mg alloy and its product preparation method |
Non-Patent Citations (1)
| Title |
|---|
| 杨天野等: "激光选区熔化AlSi10Mg-0.6Er-0.4Zr成形组织及性能研究", 《第二十四次全国焊接学术会议"计算机辅助焊接工程"分会场》 * |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113787198A (en) * | 2021-09-16 | 2021-12-14 | 中国工程物理研究院机械制造工艺研究所 | Printing process for improving mechanical property of AlSi9Mg1ScZr formed by SLM |
| CN114395742A (en) * | 2021-12-10 | 2022-04-26 | 中国商用飞机有限责任公司 | Heat treatment method for selective laser melting of AlSi10Mg alloy |
| CN114395742B (en) * | 2021-12-10 | 2022-10-14 | 中国商用飞机有限责任公司 | Heat treatment method for selective laser melting of AlSi10Mg alloy |
| CN114959519A (en) * | 2022-06-10 | 2022-08-30 | 中国航发北京航空材料研究院 | AlSi for reducing selective laser melting 10 Method for residual stress of Mg alloy |
| CN115141989A (en) * | 2022-06-17 | 2022-10-04 | 中国航发北京航空材料研究院 | Method for improving strength of AlSi10Mg alloy melted in laser selected area |
| CN116117165A (en) * | 2023-02-27 | 2023-05-16 | 常州钢研极光增材制造有限公司 | Manufacturing method for improving comprehensive performance of AlSi10Mg aluminum alloy workpiece |
| CN116900306A (en) * | 2023-09-14 | 2023-10-20 | 内蒙古工业大学 | AlSi10Mg/ZrO 2 Composite metal powder and forming process thereof |
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