CN117862530A - Nickel-based superalloy laser additive manufacturing and post-treatment method - Google Patents
Nickel-based superalloy laser additive manufacturing and post-treatment method Download PDFInfo
- Publication number
- CN117862530A CN117862530A CN202410214666.0A CN202410214666A CN117862530A CN 117862530 A CN117862530 A CN 117862530A CN 202410214666 A CN202410214666 A CN 202410214666A CN 117862530 A CN117862530 A CN 117862530A
- Authority
- CN
- China
- Prior art keywords
- laser
- additive manufacturing
- cooling
- post
- treatment
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 238000000034 method Methods 0.000 title claims abstract description 53
- 239000000654 additive Substances 0.000 title claims abstract description 46
- 230000000996 additive effect Effects 0.000 title claims abstract description 46
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 46
- 229910000601 superalloy Inorganic materials 0.000 title claims abstract description 17
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 title claims abstract description 16
- 229910052759 nickel Inorganic materials 0.000 title claims abstract description 8
- 239000000843 powder Substances 0.000 claims abstract description 66
- 230000008569 process Effects 0.000 claims abstract description 23
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 22
- 239000000956 alloy Substances 0.000 claims abstract description 22
- 238000009689 gas atomisation Methods 0.000 claims abstract description 9
- 230000006698 induction Effects 0.000 claims abstract description 9
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 5
- 238000001816 cooling Methods 0.000 claims description 42
- 238000010438 heat treatment Methods 0.000 claims description 38
- 238000002844 melting Methods 0.000 claims description 19
- 230000008018 melting Effects 0.000 claims description 19
- 239000000203 mixture Substances 0.000 claims description 16
- 238000003892 spreading Methods 0.000 claims description 11
- 230000007480 spreading Effects 0.000 claims description 11
- 239000012300 argon atmosphere Substances 0.000 claims description 9
- 230000007547 defect Effects 0.000 claims description 8
- 239000000758 substrate Substances 0.000 claims description 8
- 238000010309 melting process Methods 0.000 claims description 7
- 239000007787 solid Substances 0.000 claims description 4
- 238000009826 distribution Methods 0.000 claims description 3
- 239000002245 particle Substances 0.000 claims description 3
- 239000007789 gas Substances 0.000 claims description 2
- 238000010791 quenching Methods 0.000 claims description 2
- 230000000171 quenching effect Effects 0.000 claims description 2
- 238000012805 post-processing Methods 0.000 claims 3
- 239000006104 solid solution Substances 0.000 abstract description 7
- 229910052751 metal Inorganic materials 0.000 abstract description 6
- 239000002184 metal Substances 0.000 abstract description 6
- 238000001513 hot isostatic pressing Methods 0.000 abstract description 5
- 230000004927 fusion Effects 0.000 abstract description 3
- 239000000243 solution Substances 0.000 description 20
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 14
- 229910052786 argon Inorganic materials 0.000 description 7
- 238000003754 machining Methods 0.000 description 5
- 238000009864 tensile test Methods 0.000 description 5
- 230000009467 reduction Effects 0.000 description 4
- 238000012360 testing method Methods 0.000 description 4
- 238000005336 cracking Methods 0.000 description 3
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 238000000879 optical micrograph Methods 0.000 description 2
- 238000005498 polishing Methods 0.000 description 2
- 229910000838 Al alloy Inorganic materials 0.000 description 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 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
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000007664 blowing Methods 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 238000012993 chemical processing Methods 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 239000011651 chromium Substances 0.000 description 1
- 230000001276 controlling effect Effects 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 239000011572 manganese Substances 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 239000011733 molybdenum Substances 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 238000010583 slow cooling Methods 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 229910001220 stainless steel Inorganic materials 0.000 description 1
- 230000003068 static effect Effects 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 239000011573 trace mineral Substances 0.000 description 1
- 235000013619 trace mineral Nutrition 0.000 description 1
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
- 239000010937 tungsten Substances 0.000 description 1
Landscapes
- Powder Metallurgy (AREA)
Abstract
The invention discloses a nickel-based superalloy laser additive manufacturing and post-treatment method, which belongs to the field of metal additive manufacturing, and is characterized in that GH3536 alloy powder without forming cracks, which is prepared by adopting an electrode induction gas atomization method, is matched with a laser scanning process with a large layer thickness to prepare a laser powder bed fusion forming part without cracks, a hot isostatic pressing process is not needed, the performance requirement of the part is met by solid solution treatment, and the components of the GH3536 alloy powder meet C:0.03 to 0.08 weight percent of Al:0.05 to 0.2 weight percent, mn:0.1 to 0.6 weight percent, W: the invention can greatly reduce the time cost and the economic cost of the additive manufacturing and post-treatment process and improve the production efficiency of the whole process, and the content of other elements is 0.5-1.0 wt% within the national standard range of GH 3536.
Description
Technical Field
The invention belongs to the field of metal additive manufacturing, and particularly relates to a nickel-based superalloy laser additive manufacturing and post-treatment method.
Background
The nickel-based superalloy has excellent high-temperature mechanical properties, oxidation resistance and corrosion resistance, and is widely applied to gas turbine engine parts and chemical processing industries. The GH3536 is a solid solution strengthening alloy rich in nickel, chromium, iron and molybdenum, can be used for a long time at a high temperature of 900 ℃, and becomes an important high-temperature part material in the aerospace field. In the face of the requirements of increasingly complex and precise structural design, particularly for internal hollowed-out shaped components, the traditional forming methods such as casting, forging and the like are long in time consumption and more in working procedures, and the forming quality is difficult to ensure.
Laser powder bed fusion is one of the mainstream metal additive manufacturing techniques, suitable for manufacturing metal parts with complex shapes and internal channels, and has been successfully applied to rapid forming of material parts such as stainless steel, aluminum alloys, titanium alloys, and superalloys. The working principle is that the laser beam is controlled to selectively melt the metal powder along a certain route, so that the metal powder is rapidly metallurgically bonded and is repeated layer by layer, and thus, the solid part is obtained. During the forming process, the extremely rapid cooling rate results in a fine microstructure, and the layer-by-layer remelting promotes the growth of the grains into columnar crystals along a vertical temperature gradient. The formed part has high strength, but has remarkable anisotropism, is easy to generate defects such as cracks, air holes and the like, has poor plasticity and is accompanied by high residual stress. Therefore, for important structural parts, hot isostatic pressing and heat treatment are required after laser additive manufacturing to close cracks, improve compactness, reduce internal stress and regulate microstructure, thereby improving comprehensive mechanical properties. At present, the GH3536 generally adopts a laser powder bed to melt and increase the powder layer thickness of the manufacturing process, which is smaller (less than or equal to 0.04 mm), so that the forming speed is lower, and the formed piece is required to be subjected to hot isostatic pressing treatment and heat treatment, thereby greatly reducing the production efficiency of the whole process and leading to higher production cost.
Disclosure of Invention
The invention aims to provide an efficient nickel-based superalloy laser additive manufacturing and post-treatment method, which is characterized in that GH3536 alloy powder without forming cracks, which is prepared by adopting an electrode induction gas atomization method, is developed to be matched with a laser scanning process with a large layer thickness to obtain a laser powder bed fusion forming part without cracks, and then a heat treatment process without a hot isostatic pressing process is developed to enable the part to meet performance requirements.
The technical scheme adopted by the invention comprises the following specific steps:
s1) performing laser powder bed melting additive manufacturing on GH3536 alloy powder prepared by adopting an electrode induction gas atomization method, and preparing a high-density formed part without crack defects.
S2) carrying out heat treatment on the additive manufacturing forming part so as to regulate and control microstructure, reduce internal stress and reduce anisotropy.
Further, in the step S1, the composition of the GH3536 alloy powder satisfies C:0.03 to 0.08 weight percent of Al:0.05 to 0.2 weight percent, mn:0.1 to 0.6 weight percent, W:0.5 to 1.0 weight percent, and the content of other elements is within the national standard range of GH 3536.
Further, the powder particle size distribution in the step S1 is D10: 19-23 μm, D50: 34-37 mu m, D90: 54-57 μm; the Hall flow rate is 14-17 s/50g, and the sphericity ratio of the powder is not lower than 0.94.
Further, before the laser powder bed melting additive manufacturing of the step S1, the superalloy substrate is subjected to a preheating treatment at 150-180 ℃, and then is subjected to physical printing in an argon atmosphere.
Further, the laser powder bed melting process parameters of step S1 are: the thickness of the powder spreading layer is 0.06-0.08 mm, the laser power is 280-360W, the scanning speed is 800-1000 mm/s, the scanning interval is 0.1mm, and the two adjacent layers rotate 67 degrees by adopting a reciprocating stripe scanning strategy.
Further, the heat treatment process in the step S2 is solution treatment, specifically heating to 600 ℃ at 10 ℃/min, preserving heat for 15 minutes, then heating to 900 ℃ at 10 ℃/min, preserving heat for 15 minutes, and then heating to 1160-1200 ℃ at 6 ℃/min, preserving heat for 1-4 hours.
Further, the solution treatment in step S2 is performed under the protection of an argon atmosphere.
Further, the cooling mode of the solution treatment is to cool to 700 ℃ by cooling at a cooling speed of 35-60 ℃/min; then cooling to 300 ℃ at a cold speed of 20-30 ℃/min; and finally taking out the mixture and air-cooling the mixture to room temperature.
The invention has the following beneficial effects:
1) The GH3536 alloy powder adopted by the invention has extremely low carbon content, greatly reduces the formation of brittle carbide phases, and reduces the hot cracking and solidification cracking tendency in the laser material-increasing process; reducing the aluminum content and increasing the tungsten and manganese content helps to improve the weldability of the alloy, inhibit cracking, and control of the key trace element content allows the GH3536 alloy powder to obtain a crack-free shaped piece within a wider process window (as shown in fig. 1 and 2).
2) Forming rate V according to the forming rate formula b =t (powder spreading layer thickness) ×h (scanning pitch) ×v (scanning speed). The invention adopts a large layer thickness process with the thickness of more than 0.06mmThe forming rate is increased to 20cm 3 And the powder spreading time is reduced by improving the powder spreading layer thickness, the powder spreading waiting time is greatly shortened, and the production efficiency is further improved.
3) The GH3536 formed part has low porosity, no cracks and compactness up to 99.8%, does not need hot isostatic pressing treatment, and can realize static recrystallization of columnar grains (shown in figure 3) through solution treatment under the protection of argon so as to achieve the effect of regulating and controlling microstructure and mechanical properties.
4) The method comprises the steps of blowing argon into the furnace for cooling, then opening the furnace for cooling, and then air cooling to room temperature, so that the test piece is prevented from being oxidized at a high temperature stage, the proper cooling speed at each stage in the cooling process is avoided, the test piece is prevented from generating large quenching stress due to the excessively high cooling speed, and carbide formation due to the excessively slow cooling speed is also avoided, so that the strength and the plasticity of the test piece after heat treatment meet the requirements.
5) The invention can greatly reduce the time cost and the economic cost of the additive manufacturing and post-treatment process and improve the production efficiency of the whole process.
Drawings
Fig. 1 is an optical micrograph of a laser additive manufactured coupon of example 1 after polishing of its longitudinal surface.
Fig. 2 is an optical micrograph of a laser additive manufactured coupon of example 2 after polishing of its longitudinal surface.
FIG. 3 is a photograph of a longitudinal microstructure of a sample of example 3.
FIG. 4 is a photograph of a cross-sectional microstructure of a sample of example 3.
FIG. 5 is an electron back-scattering diffraction photograph of the longitudinal surface of the sample before heat treatment in example 4.
FIG. 6 is an electron back-scattering diffraction photograph of the longitudinal surface of the heat-treated sample of example 4.
Detailed Description
The following embodiments are provided to facilitate a better understanding of the present invention by those skilled in the relevant art in order to make the objects, technical solutions, and advantages of the embodiments of the present invention more apparent.
The composition of the GH3536 alloy powders employed in the various embodiments of the present invention satisfy C:0.03 to 0.08 weight percent of Al:0.05 to 0.2 weight percent, mn:0.1 to 0.6 weight percent, W:0.5 to 1.0 weight percent, and the content of other elements is within the national standard range of GH 3536. The particle size distribution of the powder was D10: 19-23 μm, D50: 34-37 mu m, D90: 54-57 μm; the Hall flow rate is 14-17 s/50g, and the sphericity ratio of the powder is not lower than 0.94.
Example 1
The high-efficiency nickel-base superalloy laser additive manufacturing and post-treatment method comprises the following specific steps:
(1) And performing laser powder bed melting additive manufacturing on GH3536 alloy powder prepared by adopting an electrode induction gas atomization method to prepare a high-density formed part without crack defects.
(2) The additive manufactured form is heat treated.
Further, the step (1) is to perform a preheating treatment at 150 ℃ on the high-temperature alloy substrate before the laser powder bed melting additive manufacturing, and then perform solid printing in an argon environment.
Further, the laser powder bed melting process parameters of the step (1) are as follows: the powder spreading layer has a thickness of 0.06mm, laser power of 280W, scanning speed of 1000mm/s and scanning interval of 0.1mm, and two adjacent layers rotate 67 degrees by adopting a reciprocating stripe scanning strategy.
Further, the heat treatment process in the step (2) is solution treatment, specifically heating to 600 ℃ at 10 ℃/min, preserving heat for 15 minutes, then heating to 900 ℃ at 10 ℃/min, preserving heat for 15 minutes, and then heating to 1160 ℃ at 6 ℃/min, and preserving heat for 4 hours.
Further, the solid solution treatment in the step (2) is performed under the protection of an argon atmosphere.
Further, the cooling mode of the solution treatment is that the solution treatment is cooled to 700 ℃ by cooling at a cooling speed of 35-60 ℃/min; then cooling to 300 ℃ at a cold speed of 20-30 ℃/min; and finally taking out the mixture and air-cooling the mixture to room temperature.
The forming rate of this example was 21.6cm 3 And/h, the density of the formed piece is higher than 99.8%, and the formed piece has no microcrack, as shown in figure 1. A tensile test bar was prepared by machining, and mechanical properties were tested, and the experimental results are shown in the following table. Through laser powder bed melting additive manufacturing and post-treatment, forming partHas good strength and plasticity, and no obvious anisotropism.
| Yield strength of | Tensile strength of | Elongation after break | Area reduction rate | |
| Vertical bar | 301.8MPa | 704.5MPa | 58.1％ | 58.7％ |
| Transverse bar | 312.6MPa | 725.8MPa | 55.5％ | 45.7％ |
Example 2
The high-efficiency nickel-base superalloy laser additive manufacturing and post-treatment method comprises the following specific steps:
(1) And performing laser powder bed melting additive manufacturing on GH3536 alloy powder prepared by adopting an electrode induction gas atomization method to prepare a high-density formed part without crack defects.
(2) The additive manufactured form is heat treated.
Further, the step (1) is to perform a preheating treatment at 150 ℃ on the high-temperature alloy substrate before the laser powder bed melting additive manufacturing, and then perform solid printing in an argon environment.
Further, the laser powder bed melting process parameters of the step (1) are as follows: the powder spreading layer has a thickness of 0.08mm, laser power of 340W, scanning speed of 800mm/s and scanning interval of 0.1mm, and two adjacent layers rotate 67 degrees by adopting a reciprocating stripe scanning strategy.
Further, the heat treatment process in the step (2) is solution treatment, specifically heating to 600 ℃ at 10 ℃/min, preserving heat for 15 minutes, then heating to 900 ℃ at 10 ℃/min, preserving heat for 15 minutes, and then heating to 1160 ℃ at 6 ℃/min, and preserving heat for 4 hours.
Further, the solid solution treatment in the step (2) is performed under the protection of an argon atmosphere.
Further, the cooling mode of the solution treatment is that the solution treatment is cooled to 700 ℃ by cooling at a cooling speed of 35-60 ℃/min; then cooling to 300 ℃ at a cold speed of 20-30 ℃/min; and finally taking out the mixture and air-cooling the mixture to room temperature.
The forming rate of this example was 23.0cm 3 And/h, the density of the formed piece is higher than 99.8%, and the formed piece has no microcrack, as shown in figure 2. A tensile test bar was prepared by machining, and mechanical properties were tested, and the experimental results are shown in the following table. After laser powder bed melting additive manufacturing and post-treatment, the formed part has good strength and plasticity and no obvious anisotropy.
| Yield strength of | Tensile strength of | Elongation after break | Area reduction rate | |
| Vertical bar | 302.3MPa | 715.3MPa | 56.0％ | 58.5％ |
| Transverse bar | 312.9MPa | 732.8MPa | 59.4％ | 55.7％ |
Example 3
The high-efficiency nickel-base superalloy laser additive manufacturing and post-treatment method comprises the following specific steps:
(1) And performing laser powder bed melting additive manufacturing on GH3536 alloy powder prepared by adopting an electrode induction gas atomization method to prepare a high-density formed part without crack defects (shown in fig. 3 and 4).
(2) The additive manufactured form is heat treated.
Further, the step (1) is to perform preheating treatment at 180 ℃ on the high-temperature alloy substrate before laser powder bed melting additive manufacturing, and then to perform entity printing in an argon environment.
Further, the laser powder bed melting process parameters of the step (1) are as follows: the powder spreading layer has a thickness of 0.06mm, laser power of 280W, scanning speed of 1000mm/s and scanning interval of 0.1mm, and two adjacent layers rotate 67 degrees by adopting a reciprocating stripe scanning strategy.
Further, the heat treatment process in the step (2) is solution treatment, specifically heating to 600 ℃ at 10 ℃/min, preserving heat for 15 minutes, then heating to 900 ℃ at 10 ℃/min, preserving heat for 15 minutes, and then heating to 1200 ℃ at 6 ℃/min, and preserving heat for 1 hour.
Further, the solid solution treatment in the step (2) is performed under the protection of an argon atmosphere.
Further, the cooling mode of the solution treatment is that the solution treatment is cooled to 700 ℃ by cooling at a cooling speed of 35-60 ℃/min; then cooling to 300 ℃ at a cold speed of 20-30 ℃/min; and finally taking out the mixture and air-cooling the mixture to room temperature.
The forming rate of this example was 21.6cm 3 And/h, the density of the formed part is higher than 99.8%, and no microcrack exists. A tensile test bar was prepared by machining, and mechanical properties were tested, and the experimental results are shown in the following table. After laser powder bed melting additive manufacturing and post-treatment, the formed part has good strength and plasticity and no obvious anisotropy.
| Yield strength of | Tensile strength of | Elongation after break | Area reduction rate | |
| Vertical bar | 302.8MPa | 709.7MPa | 60.1％ | 57.8％ |
| Transverse bar | 310.6MPa | 726.6MPa | 56.1％ | 51.9％ |
Example 4
The high-efficiency nickel-base superalloy laser additive manufacturing and post-treatment method comprises the following specific steps:
(1) And performing laser powder bed melting additive manufacturing on GH3536 alloy powder prepared by adopting an electrode induction gas atomization method to prepare a high-density formed part without crack defects.
(2) The additive manufactured form is heat treated.
Further, the step (1) is to perform preheating treatment at 180 ℃ on the high-temperature alloy substrate before laser powder bed melting additive manufacturing, and then to perform entity printing in an argon environment.
Further, the laser powder bed melting process parameters of the step (1) are as follows: the powder spreading layer is 0.08mm thick, the laser power is 360W, the scanning speed is 850mm/s, the scanning interval is 0.1mm, and the two adjacent layers rotate 67 degrees by adopting a reciprocating stripe type scanning strategy.
Further, the heat treatment process in the step (2) is solution treatment, specifically heating to 600 ℃ at 10 ℃/min, preserving heat for 15 minutes, then heating to 900 ℃ at 10 ℃/min, preserving heat for 15 minutes, and then heating to 1180 ℃ at 6 ℃/min, and preserving heat for 2 hours.
Further, the solid solution treatment in the step (2) is performed under the protection of an argon atmosphere.
Further, the cooling mode of the solution treatment is that the solution treatment is cooled to 700 ℃ by cooling at a cooling speed of 35-60 ℃/min; then cooling to 300 ℃ at a cold speed of 20-30 ℃/min; and finally taking out the mixture and air-cooling the mixture to room temperature.
The forming rate of this example was 24.5cm 3 And/h, the density of the formed part is higher than 99.8%, and no microcrack exists. A tensile test bar was prepared by machining, and mechanical properties were tested, and the experimental results are shown in the following table. Through laser powder bed melting additive manufacturing and post-treatment, the product is formedThe shape has good strength and plasticity without significant anisotropy (as shown in fig. 5 and 6).
Comparative example
(1) And performing laser powder bed melting additive manufacturing on GH3536 alloy powder prepared by adopting an electrode induction gas atomization method to prepare a high-density formed part without crack defects.
(2) The additive manufactured form is heat treated.
Further, the step (1) is to perform preheating treatment at 180 ℃ on the high-temperature alloy substrate before laser powder bed melting additive manufacturing, and then to perform entity printing in an argon environment.
Further, the laser powder bed melting process parameters of the step (1) are as follows: the powder spreading layer has a thickness of 0.04mm, laser power of 240W, scanning speed of 1000mm/s and scanning interval of 0.1mm, and two adjacent layers rotate 67 degrees by adopting a reciprocating stripe scanning strategy.
Further, the heat treatment process in the step (2) is solution treatment, specifically heating to 600 ℃ at 10 ℃/min, preserving heat for 15 minutes, then heating to 900 ℃ at 10 ℃/min, preserving heat for 15 minutes, and then heating to 1180 ℃ at 6 ℃/min, and preserving heat for 2 hours.
Further, the solid solution treatment in the step (2) is performed under the protection of an argon atmosphere.
Further, the cooling mode of the solution treatment is that the solution treatment is cooled to 700 ℃ by cooling at a cooling speed of 35-60 ℃/min; then cooling to 300 ℃ at a cold speed of 20-30 ℃/min; and finally taking out the mixture and air-cooling the mixture to room temperature.
The forming rate of this comparative example was only 14.4cm 3 And/h, the density of the formed part is higher than 99.8%, and no microcrack exists. The tensile test bar is prepared by machining, and the mechanical property test is carried out, and the experimental result is as followsAnd (3) a table. After laser powder bed melting additive manufacturing and post-treatment, the formed part has good strength and plasticity and no obvious anisotropy.
| Yield strength of | Tensile strength of | Elongation after break | Area reduction rate | |
| Vertical bar | 309.2MPa | 708.4MPa | 50.1％ | 51.5％ |
| Transverse bar | 313.0MPa | 726.3MPa | 47.5％ | 49.0％ |
Examples 1 and 2 differ in the thickness of the powder layer, laser power and scanning speed, and examples 1 and 3 differ in the substrate heating temperature and the heat treatment process.
While the foregoing embodiments have been described in some detail for purposes of clarity of understanding, it will be understood that the foregoing embodiments are merely illustrative of the invention and are not intended to limit the invention, and that any modifications, equivalents, improvements, etc. that fall within the spirit and principles of the present disclosure are intended to be included within the scope of the present disclosure.
Claims (8)
1. The method for manufacturing and post-processing the nickel-based superalloy laser additive is characterized by comprising the following steps of:
s1) performing laser powder bed melting additive manufacturing on GH3536 alloy powder prepared by adopting an electrode induction gas atomization method to prepare a high-density formed part without crack defects, wherein the components of the GH3536 alloy powder meet the conditions of C:0.03 to 0.08 weight percent of Al:0.05 to 0.2 weight percent, mn:0.1 to 0.6 weight percent, W:0.5 to 1.0 weight percent, and the content of other elements is within the national standard range of GH 3536;
s2) carrying out heat treatment on the additive manufacturing forming part so as to regulate and control microstructure, reduce internal stress and reduce anisotropy.
2. The method of claim 1, wherein the powder particle size distribution in step S1 is D10: 19-23 μm, D50: 34-37 mu m, D90: 54-57 μm; the Hall flow rate is 14-17 s/50g, and the sphericity ratio of the powder is not lower than 0.94.
3. The method according to claim 1, wherein the pre-heating treatment is performed at 150-180 ℃ on the superalloy substrate before the laser powder bed melting additive manufacturing of step S1, and then the solid printing is performed in an argon atmosphere.
4. The method for manufacturing and post-processing the nickel-base superalloy laser additive according to claim 1, wherein the laser powder bed melting process parameters of step S1 are: the thickness of the powder spreading layer is 0.06-0.08 mm, the laser power is 280-360W, the scanning speed is 800-1000 mm/s, the scanning interval is 0.1mm, and the two adjacent layers rotate 67 degrees by adopting a reciprocating stripe scanning strategy.
5. The method according to claim 1, wherein the heat treatment process of step S2 is solution treatment, specifically heating to 600 ℃ at 10 ℃/min, maintaining for 15 minutes, heating to 900 ℃ at 10 ℃/min, maintaining for 15 minutes, heating to 1160-1200 ℃ at 6 ℃/min, and maintaining for 1-4 hours.
6. The method according to claim 5, wherein the solution treatment in step S2 is performed under the protection of argon atmosphere.
7. The method for manufacturing and post-processing the nickel-base superalloy laser additive according to claim 6, wherein the cooling mode of solution treatment is cooling to 700 ℃ by cooling rate gas quenching of 35-60 ℃/min; then cooling to 300 ℃ at a cold speed of 20-30 ℃/min; and finally taking out the mixture and air-cooling the mixture to room temperature.
8. Nickel-base superalloy, characterized in that it is produced by a method according to any of claims 1-7.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202410214666.0A CN117862530A (en) | 2024-02-27 | 2024-02-27 | Nickel-based superalloy laser additive manufacturing and post-treatment method |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202410214666.0A CN117862530A (en) | 2024-02-27 | 2024-02-27 | Nickel-based superalloy laser additive manufacturing and post-treatment method |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN117862530A true CN117862530A (en) | 2024-04-12 |
Family
ID=90577779
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202410214666.0A Pending CN117862530A (en) | 2024-02-27 | 2024-02-27 | Nickel-based superalloy laser additive manufacturing and post-treatment method |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN117862530A (en) |
-
2024
- 2024-02-27 CN CN202410214666.0A patent/CN117862530A/en active Pending
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| WO2022042204A1 (en) | Method for preventing selective laser melting nickel-based superalloy from cracking | |
| CN112589115B (en) | Selective laser melting forming process for GH4099 nickel-based alloy component | |
| CN112605395B (en) | Laser deposition forming process method of GH4099 nickel-based alloy component | |
| WO2022174766A1 (en) | Titanium alloy powder for selective laser melting 3d printing, and selective laser melting titanium alloy and preparation thereof | |
| CN102605263A (en) | Ultrahigh-hardness high-toughness malleable spray-formed high-speed steel and preparation method thereof | |
| CN108315598A (en) | A kind of preparation method of IN713C nickel base superalloys | |
| CN114939654B (en) | High-entropy alloy powder for laser additive manufacturing and preparation method and application thereof | |
| CN113020598A (en) | Selective laser melting formed nickel-based high-temperature alloy and preparation method thereof | |
| CN112008079A (en) | Method for improving mechanical property of 3D printing nickel-based superalloy through in-situ heat treatment | |
| CN112958784A (en) | Method for actively controlling uniform distribution and growth direction of reinforcing phase in particle-reinforced titanium-based composite material | |
| CN108274000A (en) | A kind of process of laser gain material manufacture CrNiV series low-alloy steel | |
| CN117862530A (en) | Nickel-based superalloy laser additive manufacturing and post-treatment method | |
| CN114559054A (en) | Forming process for preparing GH99 nickel-based alloy by melting of laser powder bed | |
| CN114934211B (en) | Nickel-base superalloy, nickel-base superalloy powder, and nickel-base superalloy component | |
| CN114959508B (en) | Stainless steel and preparation method thereof | |
| CN114855092B (en) | High-strength and high-toughness stainless steel manufactured by additive manufacturing and preparation process thereof | |
| CN114737083A (en) | GH3536 raw material powder for laser additive manufacturing, preparation method of GH3536 raw material powder and preparation method of GH3536 alloy | |
| CN113732280A (en) | Graphene reinforced nickel-based high-temperature alloy powder for selective laser melting and preparation method thereof | |
| CN114134368B (en) | High-temperature alloy for laser cutting nozzle and preparation method thereof | |
| CN115287501B (en) | GH3536 high-temperature alloy powder for laser additive manufacturing and preparation method thereof | |
| CN114472896B (en) | Method for reinforcing hardness of brazing tool blank | |
| CN117230347B (en) | Nickel-based superalloy with reduced additive manufacturing cracks and preparation method thereof | |
| CN114561600B (en) | High-speed steel through intermetallic compound and carbide composite strong hardening and preparation method thereof | |
| CN113909496B (en) | Preparation method of titanium alloy printed part, titanium alloy printed part and aircraft | |
| CN112322987B (en) | Ultrahigh-strength steel wire for electric arc additive manufacturing and preparation method |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination |