CN113927044A - Solid solution treatment method for laser additive manufacturing of high-temperature alloy - Google Patents
Solid solution treatment method for laser additive manufacturing of high-temperature alloy Download PDFInfo
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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
- B22F10/60—Treatment of workpieces or articles after build-up
- B22F10/64—Treatment of workpieces or articles after build-up by thermal means
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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
- B22F10/25—Direct deposition of metal particles, e.g. direct metal deposition [DMD] or laser engineered net shaping [LENS]
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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
- 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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- 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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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/055—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 20% but less than 30%
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C30/00—Alloys containing less than 50% by weight of each constituent
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
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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
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Abstract
The invention relates to a solution treatment method for laser additive manufacturing of a high-temperature alloy, which comprises the following steps: preparing GH3536 alloy on an I n718 alloy substrate through a synchronous powder feeding laser additive manufacturing system in an inert atmosphere protection environment; and (3) heating the manufactured sample to 1075-1225 ℃ for solution treatment, keeping the temperature for 1 hour, and cooling the sample to room temperature by water. The invention has the beneficial effects that: the shape of the Laves phase can be effectively controlled, the Laves phase is changed into dispersed particles from a continuous strip shape in a deposition state, and the volume fraction of the Laves phase is gradually reduced along with the increase of the solid solution temperature, so that the plasticity of the material is greatly improved while certain strength is maintained, the controllability of the strength and the elongation of the GH3536 alloy manufactured by laser additive manufacturing is realized, and a foundation is provided for the application of the GH3536 alloy.
Description
Technical Field
The invention relates to the field of metal material preparation and heat treatment thereof, in particular to a solid solution treatment method for laser additive manufacturing of a high-temperature alloy.
Background
The GH3536 alloy is a solid solution strengthening type nickel-based high-temperature alloy, has good durability and creep property after being used for a long time at the temperature of below 900 ℃, has a short-term working temperature of 1080 ℃, also has excellent oxidation resistance and corrosion resistance, and is widely applied to manufacturing of hot end parts of aero-engines. With the development of high-performance aircraft engines, the requirements of light weight and integration are provided for the structure of the aircraft engine, and the problems of high design difficulty, long processing period, material waste and the like exist in the traditional manufacturing technology, so that the innovative development of the aircraft engine technology is restricted.
The laser additive manufacturing can realize the near-net-shape free manufacturing of high-performance metal parts with complex structures, and gradually becomes an important way for manufacturing key parts of aerospace. As a representative laser additive manufacturing technology, the synchronous powder feeding laser additive manufacturing technology (laser three-dimensional forming) has the advantages of high deposition efficiency, good forming performance, high-performance accurate repair of metal parts and the like, and is widely applied to manufacturing and repairing high-performance complex metal parts such as high-temperature alloy, titanium alloy, high-strength steel and the like.
Because the synchronous powder feeding laser additive manufacturing is a non-equilibrium near-rapid solidification process, a molten pool is subjected to rapid melting and solidification in the forming process, and the laser three-dimensional forming nickel-based superalloy has an uneven structure of epitaxial growth. In addition, in the nickel-based superalloy with high Nb and Mo contents, the Nb and Mo elements which are refractory at the end of solidification are easily concentrated in the liquid phase, and harmful Laves phases are generated. The formation of Laves consumes a large amount of Nb and Mo elements in the matrix, so that the solid solution strengthening effect of the matrix is reduced, and the Laves phase as a hard and brittle topological closely-packed phase (TCP) can seriously affect the tensile plasticity, fracture toughness, fatigue and creep property of the alloy and is also easy to become a crack nucleation base point and an expansion channel.
Therefore, the solidification structure of the nickel-based superalloy manufactured by synchronous powder feeding laser additive manufacturing is different from that of the traditional cast and forged piece, so that the thermal stability of the deposited nickel-based superalloy sample is different from that of the traditional cast and forged piece. Therefore, for the GH3536 alloy manufactured by simultaneous powder feeding and laser additive manufacturing, the plasticity of a deposited sample is low, and a more reasonable heat treatment schedule needs to be newly established to improve the structure and the mechanical property of the GH3536 alloy manufactured by laser additive manufacturing.
Disclosure of Invention
Based on the above deficiencies of the prior art, the present invention provides a solution treatment method for laser additive manufacturing of high temperature alloy, which reduces the volume fraction of Laves phase in the deposition zone, changes the form distribution, and improves the strength and plasticity of the additive manufacturing high temperature alloy.
The technical scheme for solving the technical problems is as follows: a solution treatment method for laser additive manufacturing of a high-temperature alloy comprises the following steps:
s100, preparing GH3536 alloy on a substrate through a synchronous powder feeding laser additive manufacturing system in an inert atmosphere protection environment;
and S200, heating the manufactured sample to 1075-1225 ℃, carrying out solution treatment, keeping the temperature for 1 hour, and then cooling the sample to room temperature by water.
On the basis of the technical scheme, the invention can be further improved as follows.
Further, the substrate is In718 high-temperature alloy or GH3536 forgings.
Further, a light source in the synchronous powder feeding laser additive manufacturing system is a semiconductor laser, the laser power is 1500W-3000W, the diameter of a light spot is 3 mm-5 mm, the laser scanning speed is 6 mm/s-12 mm/s, the powder feeding amount is 6 g/min-20 g/min, the constrained gas flow is 5L/min-12L/min, the Z-axis single-layer lifting amount is 0.2 mm-1 mm, and the lap joint rate is 40% -60%.
Furthermore, the size of GH3536 spherical powder is 50-150 μm;
the raw material powder comprises the following components in percentage by mass:
cr: 20 wt% -23 wt%, Fe: 17 wt% -20 wt%, Mo: 8 wt% -10 wt%, Co: 0.5 wt% to 2.5 wt%, W: 0.2 wt% -1.5 wt%, Al: 0.3 wt% -0.5 wt%, C: 0.05 wt% -0.2 wt%, Si: 0.05 wt% -0.5 wt%, Mn: 0.05 wt% -0.5 wt%, and the balance of Ni.
Further, the GH3536 alloy comprises the following raw material powder components in percentage by mass:
cr: 22.23 wt%, Fe: 17.22 wt%, Mo: 9.71 wt%, Co: 1.63 wt%, W: 0.56 wt%, Al: 0.32 wt%, C: 0.85 wt%, Si: 0.087 wt%, Mn: 0.072 wt% and the balance of Ni.
Further, the inert atmosphere is argon and the oxygen content is less than 200 ppm.
Furthermore, a heating furnace is adopted for heating the sample, the temperature control precision is +/-1 ℃, and the temperature rise rate is 10 ℃/min.
Further, the heating furnace is a box-type resistance furnace.
Further, step S200 is:
the prepared sample was heated to 1200 ℃ for solution treatment, and after heat preservation for 1 hour, it was cooled to room temperature by water cooling.
In an environment with argon atmosphere protection, laser emitted by a laser source is gathered on an In718 substrate to be locally melted to form a molten pool, meanwhile, powder is synchronously fed into the molten pool through a powder feeding device through airflow restriction, the powder is rapidly melted after entering the molten pool, meanwhile, a laser beam continuously moves to continuously generate a new molten pool, and due to loss of the heat source, the molten pool on a sweeping path is rapidly solidified on the surfaces of a relatively large base material and a test piece, and the steps are repeated In such a circulating way, and are gradually stacked layer by layer according to two-dimensional profile information from point to line, from line to surface and from surface to body to obtain a GH3536 alloy sample for laser material increase manufacturing of a three-dimensional entity;
the GH3536 deposition state sample prepared by the method is typically thick columnar crystals growing along the deposition direction, the width of the columnar crystals is about 35-400 mu m, the interior of the columnar crystals is mainly of a columnar dendritic crystal structure, the distance between primary dendritic crystal arms is about 8-12 mu m, and the growth direction of the dendritic crystals does not strictly grow along the deposition direction but forms a certain included angle with the deposition direction; the deposited sample structure also has an obvious zonal structure, the dendrite on the upper part of the zonal boundary is smaller, the secondary dendrite arm is not developed, the dendrite on the lower part of the zonal boundary is coarser, the secondary dendrite arm is more developed, and the top of the deposited sample is an equiaxed dendrite structure; obvious micro segregation exists among dendrites of the GH3536 alloy manufactured by laser additive manufacturing, and a chain-shaped white Laves phase is precipitated among the dendrites; the Laves phase is generally considered as a brittle phase which seriously influences various mechanical properties of the alloy; as for the In718 alloy, solution treatment is usually carried out at 1100 ℃ to eliminate the Laves phase, the research finds that the Laves phase is difficult to eliminate by adopting the conventional solution treatment, the solution treatment is carried out at a higher temperature to convert the continuous Laves phase into dispersed particles, and meanwhile, the content of the Laves phase can be controlled to ensure that part of the Laves phase is dissolved In a matrix, so that a proper heat treatment process can be selected according to the performance requirement of laser additive manufacturing high-temperature alloy, and the controllability of the strength and the elongation of the laser additive manufacturing high-temperature alloy is realized.
After the solid solution treatment, the microstructure of the high-temperature alloy manufactured by the laser additive shows that columnar crystals are recrystallized and transformed into fine isometric crystals, and the dendrite segregation basically disappears;
after the solution treatment, the microstructure of the high-temperature alloy manufactured by the laser additive shows that the strip-shaped Laves phase is gradually dissolved into the matrix and is in discontinuous granular shape, and the quantity of the brittle Laves phase is obviously reduced.
The process has the advantages that:
1. according to the solid solution treatment method for laser additive manufacturing of the high-temperature alloy, provided by the invention, the heat preservation is carried out for 1h at 1075-1225 ℃, so that coarse columnar crystals of a deposition-state sample are dissolved, the sample is recrystallized, the crystal grain form is converted into isometric crystals, a large amount of annealing twin crystals are generated inside, the crystal grains are further refined, and the purposes of improving the structure and optimizing the alloy performance are achieved;
2. according to the invention, appropriate heat energy is input into the laser additive manufacturing high-temperature alloy to melt the Laves phase back into the matrix, and the shape is changed from a continuous strip shape to a dispersed particle shape, so that the stress concentration in the stretching process is reduced, and the plasticity of the alloy is greatly improved;
3. the solid solution treatment method is simple and low in cost, and is an efficient method for improving the mechanical property of the laser additive manufactured high-temperature alloy.
Drawings
Fig. 1 is a schematic diagram of a laser additive manufacturing GH3536 process and scan path;
fig. 2 is a laser additive manufacturing GH3536 as-deposited structure;
fig. 3 is a laser additive manufacturing GH3536 as deposited Laves phase morphology;
fig. 4 shows Laves phase morphology under different solution treatments for laser additive manufacturing of GH 3536: (a)1075 deg.C; (b)1125 deg.C; (c)1175 deg.C; (d)1200 ℃;
fig. 5 shows room temperature tensile properties of laser additive manufactured GH3536 at different solution treatments: (a) engineering stress-strain curves; (b) tensile strength and elongation.
Detailed Description
The principles and features of this invention are described below in conjunction with the following drawings, which are set forth by way of illustration only and are not intended to limit the scope of the invention.
Example 1
The solution treatment method for laser additive manufacturing of the high-temperature alloy takes GH3536 alloy with alloy components shown in Table 1 as an example, and the treatment method of the invention is described in detail as follows:
TABLE 1 alloy composition (wt%) of materials used in examples of the present invention
| Ni | Cr | Fe | Mo | Co | W | Al | C | Si | Mn |
| 48.086 | 22.23 | 17.22 | 9.71 | 1.63 | 0.56 | 0.32 | 0.085 | 0.087 | 0.072 |
Placing GH3536 alloy spherical powder with the size of 50-150 mu m into a powder feeder;
putting an In718 high-temperature alloy substrate into a processing chamber filled with argon atmosphere, fixing the processing chamber on a workbench, controlling the oxygen content to be below 200ppm through argon replacement, and starting synchronous powder feeding laser additive manufacturing to obtain the high-temperature alloy with the forming size of 65mm multiplied by 60mm multiplied by 15 mm;
the laser is a semiconductor laser, GH3536 powder is fused and deposited on an In718 substrate on a 6kW laser additive manufacturing system provided with a five-axis linkage numerical control machine tool, a required sample is prepared, and the forming process is shown In figure 1;
the laser additive manufacturing process parameters are as follows: the laser power is 2000W, the diameter of a light spot is 5mm, the laser scanning speed is 8mm/s, the powder feeding amount is about 8.5g/min, the restricted gas flow is 8L/min, the Z-axis single-layer lifting amount is 0.2-0.3 mm, and the overlapping rate is 50%. In the forming process, high-purity argon gas with the purity of 99.99 percent is used as protective gas and powder conveying gas to protect a molten pool, and a powder conveying nozzle is adopted in the powder conveying process;
the tensile strength of the obtained GH3536 deposition alloy manufactured by the laser additive is 652MPa, the elongation is 30%, the microstructure of the alloy is shown in figure 2, coarse austenite columnar grains are presented, and fine dendrites are arranged inside the grains;
the embodiment provides the processing method as follows:
firstly, before heat treatment, sand paper with the models of 240#, 400#, 600#, 800#, 1000#, 1200#, 1500# and 2000# is adopted to successively polish the surfaces of the laser additive manufacturing high-temperature alloy samples until the surfaces of the alloys are smooth;
then carrying out solid solution treatment on the polished sample: placing the first sample in a box-type resistance furnace, heating to 1075 ℃ at a heating rate of 10 ℃/min, preserving the heat for 1h, and then cooling to room temperature by water, wherein the microstructure of the sample is shown in figure 4(a), and a strip-shaped continuous Laves phase just begins to dissolve;
putting the second sample in a box-type resistance furnace, heating to 1125 ℃ at the heating rate of 10 ℃/min, preserving the temperature for 1h, then cooling to room temperature by water, wherein the microstructure of the second sample is shown in figure 4(b), and the continuous Laves phase is further dissolved to be in a chain shape;
putting the third sample in a box-type resistance furnace, heating to 1175 ℃ at the heating rate of 10 ℃/min, preserving the temperature for 1h, and then cooling to room temperature by water, wherein the microstructure is shown in figure 4(c), and the chain-shaped Laves phase is dissolved into spherical particles;
putting the fourth sample in a box-type resistance furnace, heating to 1225 ℃ at a heating rate of 10 ℃/min, preserving the temperature for 1h, and then cooling to room temperature by water, wherein the microstructure of the fourth sample is shown in figure 4(e), and only a small amount of Laves phase particles exist; austenite grains are recrystallized and present as equiaxed grains;
putting the fifth sample in a box-type resistance furnace, heating to 1200 ℃ at the heating rate of 10 ℃/min, preserving the heat for 1h, and then cooling to room temperature by water, wherein the microstructure is shown in figure 4(d), the number of the granular Laves phases is reduced compared with that of the granular Laves phases at 1175 ℃, and austenite grains are recrystallized and appear as isometric grains;
the room-temperature tensile strength, elongation and stress-strain curves of the laser additive manufactured GH3536 alloy after solution treatment at different temperatures in the embodiment are shown in FIG. 5;
the curves at the tail end in the left diagram of fig. 5 refer to: as-deposited, 1075 ℃, 1125 ℃, 1175 ℃, 1200 ℃, 1225 ℃;
on the same abscissa in the right-hand diagram of fig. 5, the left column denotes the Ultimate orientation strand, and the right column denotes the Elongation.
It can be seen that with the increase of the solid solution temperature, the tensile strength is increased and then decreased, and reaches the maximum value at 1200 ℃, in the temperature increasing process, as the Laves phase is melted back into the matrix, the quantity of the brittle Laves phase is obviously reduced, and simultaneously the residual stress of the sample and the stress concentration in the stretching process are reduced, so that the plasticity is gradually increased, and the strength and the elongation of the laser additive manufacturing high-temperature alloy after the solid solution treatment are greatly improved compared with those of the deposition state sample, therefore, a proper heat treatment method can be selected according to the performance requirements of the target laser additive manufacturing high-temperature alloy, so that the controllability of the strength and the plasticity is realized.
Example 2
Placing GH3536 alloy spherical powder with the size of 50-150 mu m into a powder feeder;
putting an In718 high-temperature alloy substrate into a processing chamber filled with argon atmosphere, fixing the processing chamber on a workbench, controlling the oxygen content to be below 200ppm through argon replacement, and starting synchronous powder feeding laser additive manufacturing to obtain the high-temperature alloy with the forming size of 65mm multiplied by 10 mm;
the method comprises the following steps that the laser is a semiconductor laser, GH3536 powder is fused and deposited on an In718 substrate on a 6kW laser additive manufacturing system provided with a five-axis linkage numerical control machine tool, and a required sample is prepared;
the laser additive manufacturing process parameters are as follows: the laser power is 1800W, the diameter of a light spot is 5mm, the laser scanning speed is 6mm/s, the powder feeding amount is about 8.5g/min, the flow of a constrained gas is 8L/min, the Z-axis single-layer lifting amount is 0.2-0.3 mm, the lap joint rate is 50%, 99.99% of high-purity argon is used as a shielding gas and a powder conveying gas in the forming process to protect a molten pool, and a powder feeding nozzle is used in the powder feeding process;
the obtained GH3536 deposition alloy manufactured by laser additive manufacturing presents coarse austenite columnar grains, and fine dendrites are arranged in the grains;
the embodiment provides the processing method as follows:
firstly, before heat treatment, sand paper with the models of 240#, 400#, 600#, 800#, 1000#, 1200#, 1500# and 2000# is adopted to successively polish the surfaces of the laser additive manufacturing high-temperature alloy samples until the surfaces of the alloys are smooth;
then carrying out solid solution treatment on the polished sample: and (3) putting the first sample in a box-type resistance furnace, heating to 1200 ℃ at the heating rate of 10 ℃/min, preserving the temperature for 1h, and then cooling to room temperature by water.
The alloy in the embodiment has 721MPa of tensile strength and 46% of elongation after solution treatment.
Example 3
Placing GH3536 alloy spherical powder with the size of 50-150 μm into a powder feeder.
Putting an In718 high-temperature alloy substrate into a processing chamber filled with argon atmosphere, fixing the processing chamber on a workbench, controlling the oxygen content to be below 200ppm through argon replacement, and starting synchronous powder feeding laser additive manufacturing to obtain the high-temperature alloy with the forming size of 50mm multiplied by 10 mm;
the method comprises the following steps that the laser is a semiconductor laser, GH3536 powder is fused and deposited on an In718 substrate on a 6kW laser additive manufacturing system provided with a five-axis linkage numerical control machine tool, and a required sample is prepared;
the laser additive manufacturing process parameters are as follows: the laser power is 2500W, the diameter of a light spot is 5mm, the laser scanning speed is 10mm/s, the powder feeding amount is about 10g/min, the flow rate of a restraint gas is 8L/min, the Z-axis single-layer lifting amount is 0.2-0.3 mm, the lap joint rate is 50%, 99.99% of high-purity argon gas is used as a protective gas and a powder conveying gas in the forming process to protect a molten pool, and a powder feeding nozzle is used in the powder feeding process;
the embodiment provides the processing method as follows:
firstly, before heat treatment, sand paper with the models of 240#, 400#, 600#, 800#, 1000#, 1200#, 1500# and 2000# is adopted to successively polish the surfaces of the laser additive manufacturing high-temperature alloy samples until the surfaces of the alloys are smooth;
then carrying out solid solution treatment on the polished sample: and (3) putting the first sample in a box-type resistance furnace, heating to 1200 ℃ at the heating rate of 10 ℃/min, preserving the temperature for 1h, and then cooling to room temperature by water.
The alloy in this example was solution treated to have a tensile strength of 732MPa and an elongation of 45%.
Although embodiments of the present invention have been shown and described above, it is understood that the above embodiments are exemplary and should not be construed as limiting the present invention, and that variations, modifications, substitutions and alterations can be made to the above embodiments by those of ordinary skill in the art within the scope of the present invention.
Claims (9)
1. A solution treatment method for laser additive manufacturing of a high-temperature alloy is characterized by comprising the following steps:
s100, preparing GH3536 alloy on a substrate through a synchronous powder feeding laser additive manufacturing system in an inert atmosphere protection environment;
and S200, heating the manufactured sample to 1075-1225 ℃, carrying out solution treatment, keeping the temperature for 1 hour, and then cooling the sample to room temperature by water.
2. The solution treatment method for laser additive manufacturing of superalloy according to claim 1, wherein the substrate is In718 superalloy or GH3536 forging.
3. The solution treatment method for laser additive manufacturing of high-temperature alloy according to claim 2, wherein a light source in the synchronous powder feeding laser additive manufacturing system is a semiconductor laser, a laser power is 1500W-3000W, a spot diameter is 3 mm-5 mm, a laser scanning rate is 6 mm/s-12 mm/s, a powder feeding amount is 6 g/min-20 g/min, a constrained gas flow is 5L/min-12L/min, a Z-axis single-layer lifting amount is 0.2 mm-1 mm, and an overlapping rate is 40% -60%.
4. The solution treatment method for laser additive manufacturing of superalloy according to claim 1, 2 or 3, wherein the GH3536 spherical powder size is 50 μ ι η to 150 μ ι η;
the raw material powder comprises the following components in percentage by mass:
cr: 20 wt% -23 wt%, Fe: 17 wt% -20 wt%, Mo: 8 wt% -10 wt%, Co: 0.5 wt% to 2.5 wt%, W: 0.2 wt% -1.5 wt%, Al: 0.3 wt% -0.5 wt%, C: 0.05 wt% -0.2 wt%, Si: 0.05 wt% -0.5 wt%, Mn: 0.05 wt% -0.5 wt%, and the balance of Ni.
5. The solution treatment method for laser additive manufacturing of high-temperature alloy according to claim 1, 2, 3 or 4, wherein the GH3536 alloy comprises the following raw powder components by mass:
cr: 22.23 wt%, Fe: 17.22 wt%, Mo: 9.71 wt%, Co: 1.63 wt%, W: 0.56 wt%, Al: 0.32 wt%, C: 0.85 wt%, Si: 0.087 wt%, Mn: 0.072 wt% and the balance of Ni.
6. The solution treatment method for laser additive manufacturing of superalloy according to claim 1, wherein the inert atmosphere is argon and the oxygen content is less than 200 ppm.
7. The solution treatment method for laser additive manufacturing of superalloy according to claim 1, wherein the sample is heated by a heating furnace with a temperature control accuracy of ± 1 ℃ and a temperature rise rate of 10 ℃/min.
8. The solution treatment method for laser additive manufacturing of superalloy according to claim 7, wherein the heating furnace is a box-type resistance furnace.
9. The solution treatment method for laser additive manufacturing of superalloy according to claim 1, wherein step S200 is:
the prepared sample was heated to 1200 ℃ for solution treatment, and after heat preservation for 1 hour, it was cooled to room temperature by water cooling.
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