CN116871532A - Laser powder bed molten magnesium rare earth alloy high-strength and toughness preparation method based on cryogenic treatment - Google Patents
Laser powder bed molten magnesium rare earth alloy high-strength and toughness preparation method based on cryogenic treatment Download PDFInfo
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- CN116871532A CN116871532A CN202310934020.5A CN202310934020A CN116871532A CN 116871532 A CN116871532 A CN 116871532A CN 202310934020 A CN202310934020 A CN 202310934020A CN 116871532 A CN116871532 A CN 116871532A
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- 239000011777 magnesium Substances 0.000 title claims abstract description 30
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 28
- 239000000956 alloy Substances 0.000 title claims abstract description 28
- 239000000843 powder Substances 0.000 title claims abstract description 23
- 229910052761 rare earth metal Inorganic materials 0.000 title claims abstract description 22
- 229910052749 magnesium Inorganic materials 0.000 title claims abstract description 21
- -1 magnesium rare earth Chemical class 0.000 title claims abstract description 20
- 238000002360 preparation method Methods 0.000 title claims abstract description 8
- 238000000034 method Methods 0.000 claims abstract description 23
- 230000008569 process Effects 0.000 claims abstract description 7
- 238000002844 melting Methods 0.000 claims abstract description 4
- 230000008018 melting Effects 0.000 claims abstract description 4
- 230000002787 reinforcement Effects 0.000 claims abstract description 4
- 238000007499 fusion processing Methods 0.000 claims description 6
- 229910000861 Mg alloy Inorganic materials 0.000 abstract description 28
- 238000004519 manufacturing process Methods 0.000 abstract description 8
- 239000000654 additive Substances 0.000 abstract description 2
- 230000000996 additive effect Effects 0.000 abstract description 2
- 230000035882 stress Effects 0.000 description 16
- 238000001816 cooling Methods 0.000 description 8
- 238000009826 distribution Methods 0.000 description 6
- 230000000694 effects Effects 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 4
- 239000013078 crystal Substances 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- 238000005728 strengthening Methods 0.000 description 4
- 238000004458 analytical method Methods 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 3
- 238000005516 engineering process Methods 0.000 description 3
- 230000006872 improvement Effects 0.000 description 3
- 238000003917 TEM image Methods 0.000 description 2
- 230000032683 aging Effects 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 239000000758 substrate Substances 0.000 description 2
- 229910052727 yttrium Inorganic materials 0.000 description 2
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 1
- 229910000583 Nd alloy Inorganic materials 0.000 description 1
- 238000009825 accumulation Methods 0.000 description 1
- 230000003213 activating effect Effects 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000005540 biological transmission Effects 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 230000015556 catabolic process Effects 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 239000002178 crystalline material Substances 0.000 description 1
- 238000013016 damping Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000010494 dissociation reaction Methods 0.000 description 1
- 230000005593 dissociations Effects 0.000 description 1
- 238000001887 electron backscatter diffraction Methods 0.000 description 1
- 238000001125 extrusion Methods 0.000 description 1
- 230000004927 fusion Effects 0.000 description 1
- 238000009499 grossing Methods 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000007639 printing Methods 0.000 description 1
- 230000002035 prolonged effect Effects 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 230000004044 response Effects 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 238000002791 soaking Methods 0.000 description 1
- 238000003860 storage Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
Classifications
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
- B22F10/20—Direct sintering or melting
- B22F10/28—Powder bed fusion, e.g. selective laser melting [SLM] or electron beam melting [EBM]
-
- 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
- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
- B22F10/60—Treatment of workpieces or articles after build-up
- B22F10/64—Treatment of workpieces or articles after build-up by thermal means
-
- 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
- B33Y40/00—Auxiliary operations or equipment, e.g. for material handling
- B33Y40/20—Post-treatment, e.g. curing, coating or polishing
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- Engineering & Computer Science (AREA)
- Chemical & Material Sciences (AREA)
- Manufacturing & Machinery (AREA)
- Materials Engineering (AREA)
- Physics & Mathematics (AREA)
- Plasma & Fusion (AREA)
- Thermal Sciences (AREA)
- Powder Metallurgy (AREA)
Abstract
The invention relates to the technical field of additive manufacturing engineering, in particular to a laser powder bed molten magnesium rare earth alloy high-strength and toughness preparation method based on cryogenic treatment, which comprises the following steps: step 1) preparing a WE43 magnesium rare earth alloy workpiece by adopting a laser powder bed melting method; step 2) continuing to extract more beta in the WE43 magnesium rare earth alloy workpiece 1 Beta', beta "metastable reinforcement phase; said step 2) is carried out by means of a cryogenic treatment process. The invention solves the problems that the residual stress in the WE43 magnesium alloy formed by the traditional LPBF is uneven and the mechanical strength and toughness degree performance is not the mostThe problem of the figure of merit can greatly improve the mechanical properties.
Description
Technical Field
The invention relates to the technical field of additive manufacturing engineering, in particular to a laser powder bed molten magnesium rare earth alloy high-strength and toughness preparation method based on cryogenic treatment.
Background
Magnesium alloy as the lightest metallic structural material (1.4-2.0 g/cm 3 ) It is considered to be the best green material in the 21 st century due to its excellent biocompatibility, hydrogen storage capacity, and higher specific strength, damping and other physical and chemical properties. The WE43 magnesium alloy has the functions of refining the structure and alloying due to rare earth elements, and has obvious ageing strengthening effect, and the ageing sequence is as follows: beta (Mg) 14 Nd 2 Y)-β 1 (Mg 3 Nd)--β’(Mg 12 NdY)-β”(Mg 3 (Y, nd)) is an important class of high performance magnesium alloys. Where the β "and β' phases are the main strengthening phases, but these phases are metastable, it is difficult to obtain metastable phases with conventional processing, which limits the widespread use of WE43 in production and life.
Laser powder bed fusion technology (LPBF) is an advanced manufacturing technology featuring layer-by-layer build-up and high cooling rates. Compared with the traditional forming and manufacturing technology, the LPBF can obviously change the supersaturation degree, phase formation and element diffusion segregation behavior of the solute of the forming material, thereby influencing the mechanical toughening mechanism of the LPBF, and hopefully improving the performance of the magnesium alloy by forming a metastable phase. However, due to the rapid heating and cooling cycles occurring in the whole manufacturing process, the complicated thermal history causes uneven internal stress distribution of the magnesium alloy, which is very disadvantageous to mechanical properties, and on the other hand, the potential of mechanical toughness of the LPBF molded WE43 magnesium alloy which is not further treated cannot be exerted.
Disclosure of Invention
The invention aims to provide a high-strength and toughness preparation method of laser powder bed molten magnesium rare earth alloy based on cryogenic treatment, which solves the problems that the residual stress in the WE43 magnesium alloy formed by the traditional LPBF is uneven and the mechanical strength and toughness degree performance does not reach the optimal value, and can greatly improve the mechanical property.
The invention provides a laser powder bed molten magnesium rare earth alloy high-strength and toughness preparation method based on cryogenic treatment, which comprises the following steps:
step 1) preparing a WE43 magnesium rare earth alloy workpiece by adopting a laser powder bed melting method;
step 2) continuing to extract more beta in the WE43 magnesium rare earth alloy workpiece 1 Beta', beta "metastable reinforcement phase;
said step 2) is carried out by means of a cryogenic treatment process.
Preferably, the treatment temperature of the cryogenic treatment in step 2) is-196 ℃.
Preferably, the treatment time of the cryogenic treatment in step 2) is 7 hours or more.
Preferably, the treatment time of the cryogenic treatment in step 2) is 9 hours or longer.
Preferably, the treatment time of the cryogenic treatment in step 2) is 9 hours.
Preferably, the thickness of the powder layer of the laser powder bed fusion process in step 1) is 50um.
Preferably, the scanning pitch in step 1) is 0.07mm.
Preferably, the laser power of the laser powder bed fusion process in step 1) is 80W.
Preferably, the scanning speed of the laser powder bed fusion process in step 1) is 800mm/s.
The invention also provides a magnesium rare earth alloy which is prepared by the steps of the method.
The invention has the following beneficial effects
Cryogenic treatment is an effective method for improving mechanical properties of alloys. The lower temperature (-196 ℃) at cryogenic treatment will convert the tensile stress at the edges of the alloy pattern to the same compressive stress as the interior, but due to the unique microstructure of LPBF WE43, including its internal metastable reinforcement phase. The response behavior of these phases with respect to the cryogenic process, as well as the dislocation, texture variations within them, are not apparent. The influence of the cryogenic treatment on the comprehensive performance of the LPBF magnesium alloy is uncertain except that the uneven stress distribution is possibly improved, so that whether the cryogenic treatment can bring about the improvement of mechanical properties for the LPBF WE43 is not predicted.
In the process of producing the invention, the inventor finds that the optimized LPBF process parameters and the cryogenic treatment not only improve the problem of uneven residual stress in the LPBF WE43 magnesium alloy, but also unexpectedly achieve the effects of retaining and improving beta 1 The volume fraction of the metastable strengthening phases of beta 'and beta' has the effects of reducing crystal grains and increasing dislocation. Thereby obtaining the magnesium rare earth alloy with excellent performance and laying an important foundation for the subsequent production and use of the magnesium rare earth alloy.
The invention provides a high-strength and high-toughness preparation method of laser powder bed molten magnesium rare earth alloy based on cryogenic treatment, which is suitable for WE43 magnesium alloy formed by laser powder bed melting. In some preferred embodiments of the present invention, the optimum process parameters of a scan pitch of 0.07mm, a line scan speed of 800mm/s, and a laser power of 80W are combined and a sample of ideal macroscopic morphology is prepared; after cryogenic treatment (-196 ℃ C. Times.9 h), the KAM average value of LPBF WE43 is smaller, which shows that the internal strain of the alloy is reduced and the problem of uneven residual stress is reduced. In addition, the microstructure of the magnesium-rare earth alloy precipitates more beta while retaining a large amount of metastable phase 1 Beta 'and beta' metastable hard-enhanced phases. The low-temperature compressive stress also causes the size crystal grains to be smaller, the grain boundaries are increased, and the strength of the crystal grains is effectively improved. While the dislocation in the crystal increases, including out-of-plane l 1 The increase of the type growth induced stacking fault greatly contributes to the plasticity of the LPBF WE 43. The yield strength is improved from 236MPa to 275MPa, and the increase amplitude is 24%; the tensile strength is improved from 313MPa to 337MPa, and the increase amplitude is 13%; the elongation is improved from 7.6 to 10.5, the increasing amplitude is 58%, and the hardness is increased from 91.6HV to 101.5HV.
Drawings
Specific embodiments of the invention will be more fully understood in conjunction with the following drawings in which:
FIG. 1 is a KAM graph of a WE43 magnesium alloy pattern and a cryogenically processed pattern for LPBF direct forming in an inventive example;
FIG. 2 is a TEM dislocation image of an LPBF direct formed WE43 magnesium alloy pattern and a cryogenically processed pattern in an embodiment of the invention;
FIG. 3 is a TEM micrograph of an LPBF direct formed WE43 magnesium alloy form and a cryogenic treatment form of an embodiment of the invention;
FIG. 4 is a graph comparing stress-strain curves of WE43 magnesium alloys cast, extruded, LPBF and cryogenically processed in examples of the present invention.
Detailed Description
The technical scheme of the invention will be further described in detail below with reference to specific embodiments. It is to be understood that the following examples are illustrative only and are not to be construed as limiting the scope of the invention. All techniques implemented based on the above description of the invention are intended to be included within the scope of the invention.
Comparative example:
(1) The material is WE43 magnesium rare earth alloy, and the powder is filled into a powder feeding cabin of a 3D metal printer of the commercial BLT S210.
(2) The test set the laser power at 80W, the scanning speed at 800mm/s, and the scanning pitch at 0.07mm.
(3) Two sets of 30mm x 400mm samples were printed on the substrate.
Examples:
the sample printing procedure was the same as for the comparative example, followed by cooling the pattern from room temperature to-196 ℃ in ten minutes at an average cooling rate of 21K/min in a closed cabinet, followed by soaking for 9 hours in an environment at-196 ℃.
In fig. 1, electron back scattering diffraction (EBSD, electron Backscattered Diffraction) analysis results of the WE43 magnesium alloy pattern directly formed from LPBF and the pattern subjected to the cryogenic treatment were processed with a gaussian smoothing filter and a third proximity KAM (Kernel average misorientation) to obtain a density analysis diagram of Geometrically Necessary Dislocations (GND) in the crystalline material. Wherein part (a) of FIG. 1 is a KAM chart of the LPBF-formed WE43 magnesium alloy, part (b) of FIG. 1 is a KAM chart of the WE43 magnesium alloy after the cryogenic treatment, and part (c) of FIG. 1 is a KAM value distribution curve comparison.
As can be seen from comparison of the KAM value distribution curve, the maximum distribution value of KAM value of WE43 magnesium alloy after cryogenic treatment (DCT) is changed from 4.43 to 3.46, but the distribution of KAM is more uniform. This is because when the magnesium substrate grain is divided into a plurality of sub-grains, dislocation units inside the grain and internal dislocation lines are eliminated, resulting in a reduction in local stress strain. However, the average value of KAM increased from 0.48 to 0.57, with an increasing trend. Indicating an increase in dislocation density of the alloy after the DCT treatment.
Metallographic phase of WE43 magnesium rare earth alloy patterns prepared in comparative examples and examples was polished to a thickness of 500nm, and then thinned to 300nm by electrolytic polishing. Microscopic tissue analysis was performed in a FEI Talos F200x Transmission Electron Microscope (TEM) and a TEM image was obtained as shown in FIG. 2. In FIG. 2, dislocation conditions inside the pattern are revealed, and in FIG. 2, parts (a, b) are partial dislocation pictures of an LPBF WE43 magnesium alloy workpiece (comparative example) which has not undergone DCT treatment under different observation scales, in which a large amount of dislocation is observed<a>Class and class<c+a>Dislocation-like, these randomly arranged dislocations form dislocation tangles with each other, and where local strain is large, dislocation accumulation forms dislocation walls. Small amount of<c>Dislocations like are also found. Such dislocations are likely to be<c+a>In opposite directions of dislocation-like dissociation<a>The dislocation-like elements ablate away from each other and remain. In addition, out-of-plane I 1 A profile was also observed.
The partial dislocation pictures of the DCT-processed LPBF WE43 magnesium alloy workpiece (example) are shown in parts (c, d) of fig. 2, where the dislocation density is significantly higher than in the pattern without DCT processing, but the out-of-plane I1 type faults are reduced. This reduces the critical breakdown shear stress of the non-basal dislocation structure. The probability that non-basal dislocations are activated increases, such as < c + a > type dislocations. In addition, compressive stress introduced by cryogenic treatment of low temperature conditions causes severe lattice deformation, thereby activating a greater variety of dislocation types. Under very large strains, dislocation structures also promote the formation of nanocrystalline grains, further contributing to the improvement of mechanical properties of the pattern.
As shown in parts (a, b) of FIG. 3, for different sample phasesTEM observation of behavior revealed that the WE43 magnesium alloy directly formed by LPBF contains a partially flocculent phase, which is Y formed by contact of active Y element in WE43 with O 2 O 3 They are dispersed in the matrix. In addition, under TEM field of view, a pattern microstructure was observed as 800nm thick lamellar regions, these lamellar structures being defined by beta 1 -Mg 3 Nd is deposited. The lamellar region contains a plurality of square phases (. Beta.' -Mg) having a width of about 80nm 12 NdY) and a rod-shaped phase (. Beta. -Mg) having a width of 10-20nm and a length of 190-120nm 3 (Y, nd)). The beta' phase will typically have a body-centered structure that will produce less elastic distortion than a base-centered structure. Beta' is thus an important strengthening phase in Mg-Y-Nd alloys. At the same time, the lattice of the β "phase is completely identical to that of the matrix, and the arrangement of atoms in the structure results in the formation of double close-packed hexagonal unit cells (a=2a Mg ,c＝c Mg ) Has great contribution to hardness.
As shown in parts (c, d) of fig. 3, after DCT treatment, RE-based second phase precipitation occurs in WE43 alloy, and the number of metastable compounds increases significantly. Compressive stress caused by cryogenic treatment can move phase boundaries, so that metastable phases are more easily formed in the alloy, and the metastable phases with high volume fractions make a great contribution to the strength and hardness of WE43 magnesium alloy.
The cryogenically processed and non-cryogenically processed WE43 magnesium alloy forms were each processed into standard tensile bars and tensile tested in a universal tester model WDW-100KN at 0.3% strain increment and strain rate of 10-3 s-1. The mechanical properties obtained are shown in the table 1, and the mechanical properties of the patterns with the cryogenic treatment time of 7h and 8h are also included:
table 1 mechanical properties vs. table
As can be seen from the table, after 7 hours of cryogenic treatment, the yield strength of the pattern is better than that of the pattern without cryogenic treatment, but the tensile strength and elongation are reduced; after the deep cooling treatment for 8 hours, the yield strength and the tensile strength of the pattern are improved, but the elongation is reduced; after the deep cooling treatment is carried out for 9 hours, the uniform strength, the tensile strength and the elongation of the sample are all superior to those of the sample which is not subjected to the deep cooling treatment, the yield strength is improved from 236MPa to 275MPa, and the increase range is 24%; the tensile strength is improved from 313MPa to 337MPa, and the increase amplitude is 13%; the elongation is improved from 7.6 to 10.5, the increasing amplitude is 58%, and the hardness is increased from 91.6HV to 101.5HV. According to the trend, the treatment time is continuously prolonged, and better mechanical properties are expected to be obtained.
For comparison with the present invention, fig. 4 shows the drawing results of WE43 magnesium alloy pattern of the conventional manufacturing method (casting, extrusion), LPBF direct forming and cryogenic treatment for 9h. As can be seen from the stress MPa-strain curve in fig. 4, the difference in processing has a large effect on WE43 performance. The performance of the LPBF formed WE43 is significantly better than that of the cast and extruded WE43 magnesium alloy. After the deep cooling treatment, the strength and the plasticity of the WE43 magnesium alloy are further comprehensively improved. On one hand, the compressive stress is introduced into the sample due to the cryogenic treatment in a low-temperature environment, so that the problem of uneven residual stress in the sample is solved. And the dislocation structure in the pattern is changed due to larger compressive stress, various dislocations and faults are increased, and the plasticity is effectively improved. While further generation of the hard metastable phase has a significant effect on the strength. It can be concluded that the strength of the LPBF WE43 magnesium alloy is further enhanced only after the cryogenic treatment.
The embodiments of the present invention have been described above. However, the present invention is not limited to the above embodiment. Any modification, equivalent replacement, improvement, etc. made within the spirit and principle of the present invention should be included in the protection scope of the present invention.
Claims (10)
1. A preparation method of high strength and toughness of molten magnesium rare earth alloy based on a laser powder bed of cryogenic treatment is characterized by comprising the following steps:
step 1) preparing a WE43 magnesium rare earth alloy workpiece by adopting a laser powder bed melting method;
step 2) continuing to extract more beta in the WE43 magnesium rare earth alloy workpiece 1 Beta', beta "metastable reinforcement phase;
said step 2) is carried out by means of a cryogenic treatment process.
2. The method according to claim 1, wherein the treatment temperature of the cryogenic treatment in step 2) is-196 ℃.
3. The method according to claim 1, wherein the treatment time of the cryogenic treatment in step 2) is 7 hours or more.
4. The method according to claim 1, wherein the treatment time of the cryogenic treatment in step 2) is 9 hours or longer.
5. The method according to claim 1, wherein the treatment time of the cryogenic treatment in step 2) is 9 hours.
6. The method according to any one of claims 1, wherein the laser powder bed fusion process of step 1) has a powder bed thickness of 50um.
7. The method according to claim 1, wherein the scanning pitch in step 1) is 0.07mm.
8. The method of claim 1, wherein the laser power of the laser powder bed fusion process in step 1) is 80W.
9. The method according to claim 1, wherein the scanning speed of the laser powder bed fusion process in step 1) is 800mm/s.
10. A magnesium rare earth alloy, characterized in that the alloy is produced by the method steps of any one of claims 1-8.
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Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107574392A (en) * | 2017-08-31 | 2018-01-12 | 中国科学院海洋研究所 | A kind of processing method of raising Mg Y Nd based alloy decay resistances |
| CN110983135A (en) * | 2019-12-10 | 2020-04-10 | 北京科技大学 | High-strength high-plasticity Mg-Ga-Li magnesium alloy capable of being rapidly aged and strengthened and preparation method thereof |
| WO2021173976A1 (en) * | 2020-02-26 | 2021-09-02 | Crs Holdings, Inc. | High fracture toughness, high strength, precipitation hardenable stainless steel |
| CN113427020A (en) * | 2021-06-22 | 2021-09-24 | 清华大学 | Laser powder bed melting additive manufacturing method based on multiple scanning melting |
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- 2023-07-27 CN CN202310934020.5A patent/CN116871532A/en active Pending
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107574392A (en) * | 2017-08-31 | 2018-01-12 | 中国科学院海洋研究所 | A kind of processing method of raising Mg Y Nd based alloy decay resistances |
| CN110983135A (en) * | 2019-12-10 | 2020-04-10 | 北京科技大学 | High-strength high-plasticity Mg-Ga-Li magnesium alloy capable of being rapidly aged and strengthened and preparation method thereof |
| WO2021173976A1 (en) * | 2020-02-26 | 2021-09-02 | Crs Holdings, Inc. | High fracture toughness, high strength, precipitation hardenable stainless steel |
| CN113427020A (en) * | 2021-06-22 | 2021-09-24 | 清华大学 | Laser powder bed melting additive manufacturing method based on multiple scanning melting |
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