CN115846689A - Solution treatment method for melting GH3230 alloy by laser powder bed and GH3230 alloy - Google Patents
Solution treatment method for melting GH3230 alloy by laser powder bed and GH3230 alloy Download PDFInfo
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Abstract
The invention relates to a solid solution treatment method for a laser powder bed melting GH3230 alloy and the GH3230 alloy, belonging to the field of high temperature alloyThe technical field of gold. In order to solve the problem that the prior art lacks a solid solution treatment method for melting GH3230 alloy by a laser powder bed, the invention provides a solid solution treatment method for melting GH3230 alloy by a laser powder bed, which comprises the following steps: preparing GH3230 alloy through a laser powder bed melting additive manufacturing system; and then heating the GH3230 alloy to 1130-1280 ℃ for solution treatment, preserving the heat for 1-3 h, and cooling to room temperature. The invention improves M while adapting to the laser powder bed fusion forming technology 6 Volume fraction and morphological distribution of C carbide in the alloy such that M 6 The average size of C is reduced, the stress concentration in the stretching process is reduced, the elongation of the alloy is greatly improved on the premise of ensuring higher strength of the alloy, and the GH3230 alloy with both strength and plasticity is obtained.
Description
Technical Field
The invention belongs to the technical field of high-temperature alloys, and particularly relates to a solution treatment method for melting GH3230 alloy by a laser powder bed and the GH3230 alloy.
Background
The development of high performance aircraft requires an increase in the thrust-to-weight ratio of the engine, which places higher demands on hot end components of the engine, including service with materials having higher high temperature strength, and weight reduction of the integrated structural design. The GH3230 alloy is a solid solution strengthening type Ni-Cr-W-Mo high-temperature alloy, has good durability and creep resistance when used for a long time below 900 ℃, has a short-term working temperature of 1100 ℃, has excellent oxidation resistance and thermal stability when exposed to an environment of 1150 ℃ for a long time, and is widely applied to hot end parts of aero-engines.
The problems of high processing difficulty, long processing period, material waste and the like of a novel topological structure, and the like exist in the process of manufacturing the hot end part of the engine by adopting the traditional material, so that the rapid iteration of the aircraft engine technology is seriously hindered. The laser powder bed fusion process is a non-equilibrium solidification process in which the molten pool undergoes 10 deg.f 7 The GH3230 alloy is melted by the laser powder bed through the ultra-fast fusion of K/s magnitude, so that the GH3230 alloy has an epitaxially grown uneven substructure and dislocation network, and the GH3230 alloy is not suitable for being directly serviced in a deposition state due to low plasticity caused by enrichment of low-melting-point elements such as Cr, B, C and Si in grain boundaries and subgrain boundaries and performance instability caused by tissue transformation in a high-temperature service process.
The invention patent application CN114855030A, ni-Cr-W-based high-temperature alloy suitable for selective laser melting forming and a preparation method thereof, obtains a high-strength sample by increasing the content of precipitated phase to enable the alloy strength to exceed that of a cold-rolled Haynes 230. However, due to the introduction of a large amount of Al, ti, nb, B and Ta elements, the components of the alloy are greatly different from those of GH3230, so that the main strengthening mechanism of the alloy is changed from solid solution strengthening to precipitation strengthening, and the properties of the alloy are changed. And the prepared alloy has a large amount of Laves phases in a deposition state, and the instability of the Laves phases in a long-time high-temperature service process limits the application of the alloy in a combustion chamber.
The solid solution strengthening is an effective means for regulating and controlling the microstructure of the alloy so as to improve the mechanical property of the alloy, and a large amount of granular M inside crystal grains 6 The precipitation of C carbide can effectively improve the strength and creep resistance of the high-temperature alloy, but the coarse M 6 The C particles can become stress concentration points, so that crack initiation critical load is reduced, and the tensile plasticity of the alloy is seriously influenced.
The invention patent application with publication number CN114635059A, ni-Cr-W-based alloy and a preparation method thereof, prepares the Ni-Cr-W-based alloy by smelting, forging, hot rolling, cold rolling and solution heat treatment after the alloy components are changed. The alloy prepared by the method has uniformly grown crystal grains and secondary carbides after regulation and control, and the high-temperature durability of the alloy is improved compared with that of the traditional GH3230 solution treatment. However, the unstable high-temperature environment of the secondary carbide can cause the unstable performance of the alloy in the high-temperature service process, and the plasticity of the alloy after the solution treatment is not improved.
Therefore, the existing solution treatment mode of the Ni-Cr-W alloy is provided for preparing the alloy by traditional casting, forging and rolling, and the problems of uniform regulation of microstructure and high-temperature stable primary carbide size characteristics, strong plasticity comprehensive performance regulation and the like of the GH3230 alloy subjected to melt solution strengthening by a laser powder bed after non-equilibrium solidification and the like are not solved.
Disclosure of Invention
In order to solve the problem that a solution treatment method for melting GH3230 alloy by a laser powder bed is lacked in the prior art, the invention provides a solution treatment method for melting GH3230 alloy by a laser powder bed and GH3230 alloy.
The technical scheme of the invention is as follows:
a solution treatment method for melting GH3230 alloy by a laser powder bed comprises the following steps:
step one, preparing GH3230 alloy:
preparing GH3230 alloy by a laser powder bed melting additive manufacturing system under the protection of inert atmosphere;
step two, solution treatment of GH3230 alloy:
and (3) heating the GH3230 alloy prepared in the step one to 1130-1280 ℃ in a vacuum environment with the pressure not more than 1000Pa for solution treatment, preserving the heat for 1-3 h, and cooling to room temperature.
Further, the GH3230 spherical powder used for preparing the GH3230 alloy in the step one comprises the following components in percentage by mass: c:0.05 to 0.15%, si:0.25 to 0.75%, mn:0.30 to 1%, cr: 20-24%, fe: less than or equal to 3 percent, mo:1 to 3%, co: less than or equal to 5%, W:13 to 15%, al:0.2 to 0.5%, ti: less than or equal to 0.1 percent, cu: less than or equal to 0.5 percent, la:0.005 to 0.05%, B: less than or equal to 0.005 percent and the balance of Ni.
Further, the GH3230 spherical powder used for preparing the GH3230 alloy in the step one comprises the following components in percentage by mass: c:0.07%, si:0.35%, mn:0.5%, cr:21.74%, fe:1.9%, mo:2.8%, co:2.1%, W:14.7%, al:0.45%, ti:0.1%, cu:0.01%, la:0.01%, B:0.001% and the balance of Ni.
Further, the GH3230 spherical powder used for preparing the GH3230 alloy in the first step has a particle size of 15-53 μm.
Further, in the first step, the inert atmosphere is an argon atmosphere, and the oxygen content of the argon atmosphere is lower than 100ppm.
Further, in the first step, a light source in the laser powder bed melting additive manufacturing system is YAG solid laser, the laser power is 120-300W, the spot diameter is 0.087mm, the laser scanning speed is 500-1300 mm/s, the powder spreading thickness is 0.02-0.05 mm, the scanning interval is 0.05-0.12 mm, the scanning strategy is 67 degrees of cross strip scanning, and the substrate preheating temperature is 80-160 ℃.
Furthermore, the temperature of the GH3230 alloy in the second step is raised from room temperature to 1130-1280 ℃ at a speed of 8-10 ℃/min.
Further, the cooling to room temperature in the second step is rapid cooling by using high-pressure argon.
The GH3230 alloy obtained by the solution treatment method for melting the GH3230 alloy by the laser powder bed has a matrix of a fully austenitic structure, and the grain size is controlled within the range of 40-80 mu m.
Further, the precipitated carbide is M 6 C，M 6 The volume fraction of C in the GH3230 alloy is less than 10%, and the original grain boundary position M 6 C average size less than 2 μ M, M in crystal 6 The average size of C is less than 0.3 μm.
The invention has the beneficial effects that:
the GH3230 solution treatment method for laser powder bed melting provided by the invention can eliminate the substructure and dislocation network of a deposition state sample, promote the occurrence of recrystallization and achieve the purposes of improving the structure and optimizing the alloy performance. The invention is suitable for laser powder bed meltingThe primary stable carbide M can be effectively regulated and controlled while the melt forming technology is adopted 6 C is characterized by the fact that 23 C 6 Carbide high temperature stabilization of M 6 C transformation to separate out M in carbide 6 C accounts for more than 90%, and M is improved 6 The volume fraction and the morphological distribution of C carbide in GH3230 alloy are adjusted by adjusting the solid solution temperature to enable M to be in a solid solution state 6 The average size of C is reduced, the stress concentration in the stretching process is reduced, the brittle fracture is inhibited, and the elongation of the GH3230 alloy molten by the laser powder bed is greatly improved on the premise of ensuring higher strength. The ultimate tensile strength of the GH3230 alloy obtained by the solution treatment method can reach more than 70% of that of the deposited GH3230 alloy, and the maximum elongation of the GH3230 alloy is improved by more than 1.5 times compared with that of the deposited GH3230 alloy.
The laser powder bed melting GH3230 solid solution treatment method is simple, the regulation and control effect is obvious, the controllability of the strength and the elongation of the laser powder bed melting GH3230 alloy is realized, and a foundation is laid for the application of the alloy. The GH3230 alloy with strength and plasticity obtained by the solution treatment method is particularly suitable for parts used for a long time in a high-temperature environment of over 900 ℃, such as an aviation turbofan engine combustion chamber, an axial flow wheel and the like.
Drawings
FIG. 1 is a schematic diagram of a forming process for preparing GH3230 alloy by laser powder bed melting additive manufacturing;
FIG. 2 is a microstructure photograph of different parts of a GH3230 alloy forming sample in a deposition state obtained by laser powder bed melting additive manufacturing in example 1;
FIG. 3 is a microstructure photograph and a carbide morphology photograph of GH3230 alloys obtained by different solution treatment methods of examples 1-4;
FIG. 4 is a photograph of grain characteristics of as-deposited GH3230 alloy and GH3230 alloys obtained by different solution treatment methods of examples 1-4;
FIG. 5 is a graph comparing the as-deposited GH3230 alloy with engineering stress-strain curves for GH3230 alloys from examples 1-4 by various solution treatments;
FIG. 6 is a graph comparing tensile strength and elongation of as-deposited GH3230 alloys and GH3230 alloys obtained by different solution treatment methods of examples 1-4.
Detailed Description
The technical solutions of the present invention are further described below with reference to the embodiments, but the present invention is not limited thereto, and any modifications or equivalent substitutions made to the technical solutions of the present invention without departing from the spirit and scope of the technical solutions of the present invention should be covered in the protection scope of the present invention. The process equipment or apparatus not specifically mentioned in the following examples are conventional in the art, and if not specifically mentioned, the raw materials and the like used in the examples of the present invention are commercially available; unless otherwise specified, the technical means used in the examples of the present invention are conventional means well known to those skilled in the art.
Example 1
The embodiment provides a solution treatment method for melting GH3230 alloy by a laser powder bed, which comprises the following steps:
step one, preparing GH3230 alloy through a laser powder bed melting additive manufacturing system under the protection of inert atmosphere.
The components of the GH3230 alloy spherical powder used in the embodiment meet the following requirements in percentage by mass: ni:55.26%, cr:21.74%, W:14.7%, mo:2.8%, fe:1.9%, co:2.1%, mn:0.5%, si:0.35%, al:0.45%, C:0.07%, ti:0.1%, cu:0.01%, la:0.01%, B:0.001 percent.
Placing GH3230 alloy spherical powder with the size of 15-53 mu m into a powder bin, placing a 316L stainless steel substrate into a forming cabin, closing the cabin door, then flushing argon gas to control the oxygen content to be below 100ppm, preheating the substrate to 100 ℃ by a platform resistance heating mode, and starting laser powder bed melting GH3230 alloy processing.
The laser used in this embodiment is a YAG laser, GH3230 powder is uniformly spread on the substrate, GH3230 powder is melted and deposited on the 316L substrate by scanning a galvanometer to swing a laser beam, the platform is lowered, powder is spread and melted again, and the steps are repeated to prepare the required sample.
The process parameters for manufacturing the GH3230 alloy by melting and material increasing of the laser powder bed in the embodiment are as follows: the laser power is 245W, the diameter of a light spot is 0.087mm, the laser scanning speed is 900mm/s, the powder spreading thickness is 0.04mm, the scanning interval is 0.11mm, and the scanning strategy is 67-degree cross strip-shaped scanning; the forming dimension is 71mm × 10mm × 10mm, and the forming process is schematically shown in fig. 1.
The ultimate tensile strength of the formed sample of the GH3230 in a deposition state obtained in the embodiment is 937MPa, the elongation is 15%, the microstructure of the formed sample is shown in FIG. 2, the microstructure of the alloy in a deposition state presents austenite columnar grains, the interior of the grains is columnar dendritic and fine cellular substructure, and a large amount of dislocation network is distributed at the boundary of the substructure.
Step two, solution treatment of GH3230 alloy:
and (3) placing the deposition GH3230 sample prepared in the step one into a vacuum heat treatment furnace, heating the sample to 1130 ℃ at a heating rate of 10 ℃/min in a vacuum environment with the pressure not greater than 1000Pa for solution treatment, keeping the temperature for 2h, and introducing high-pressure argon to rapidly cool to room temperature.
In the embodiment, the ultimate tensile strength of the GH3230 alloy after 1130 ℃ solution treatment is 900MPa, and the elongation is 16.7%.
Example 2
The present example provides a solution treatment method of laser powder bed melting GH3230 alloy, and the solution treatment method of the present example is different from that of example 1 only in that: the specific solid solution temperature and time in step two of this example are:
and (3) placing the deposition GH3230 sample prepared in the step one into a vacuum heat treatment furnace, heating the sample to 1180 ℃ at a heating rate of 10 ℃/min in a vacuum environment with the pressure not greater than 1000Pa for solid solution treatment, keeping the temperature for 2h, and introducing high-pressure argon to rapidly cool the sample to room temperature.
In this example, the ultimate tensile strength of the GH3230 alloy after 1180 ℃ solution treatment was 803MPa, and the elongation was 18%.
Example 3
The embodiment provides a solution treatment method for melting GH3230 alloy by a laser powder bed, and the solution treatment method of the embodiment is only different from that of the embodiment 1 in that: the specific solid solution temperature and time in step two of this example are:
and (3) placing the deposition GH3230 sample prepared in the step one into a vacuum heat treatment furnace, heating the sample to 1230 ℃ at a heating rate of 10 ℃/min in a vacuum environment with the pressure not greater than 1000Pa for solution treatment, keeping the temperature for 2h, and introducing high-pressure argon to rapidly cool to room temperature.
In the embodiment, the ultimate tensile strength of the GH3230 alloy after the solution treatment at 1230 ℃ is 750MPa, and the elongation is 21%.
Example 4
The present example provides a solution treatment method of laser powder bed melting GH3230 alloy, and the solution treatment method of the present example is different from that of example 1 only in that: the specific solid solution temperature and time in step two of this example are:
and (3) placing the deposition GH3230 sample prepared in the step one into a vacuum heat treatment furnace, heating the sample to 1280 ℃ at a heating rate of 10 ℃/min in a vacuum environment with the pressure not greater than 1000Pa for solid solution treatment, preserving heat for 2h, and introducing high-pressure argon to rapidly cool to room temperature.
In the embodiment, the ultimate tensile strength of the GH3230 alloy after solution treatment at 1280 ℃ is 670MPa, and the elongation is 42%.
FIG. 3 is a microstructure photograph and a carbide morphology photograph of GH3230 alloys obtained by different solution treatment methods of examples 1-4; the upper row of photos are micro-structure photos, and the lower row of photos are carbide morphology photos; wherein, a is the microstructure photo of GH3230 alloy obtained in example 1, b is the microstructure photo of GH3230 alloy obtained in example 2, c is the microstructure photo of GH3230 alloy obtained in example 3, and d is the microstructure photo of GH3230 alloy obtained in example 4.
FIG. 4 is a photograph of grain characteristics of as-deposited GH3230 alloy and GH3230 alloys obtained by different solution treatment methods of examples 1-4; fig. a is a photograph of the grain characteristics of the as-deposited GH3230 alloy, b is a photograph of the grain characteristics of the GH3230 alloy obtained in example 1, c is a photograph of the grain characteristics of the GH3230 alloy obtained in example 2, d is a photograph of the grain characteristics of the GH3230 alloy obtained in example 3, and e is a photograph of the grain characteristics of the GH3230 alloy obtained in example 4.
As shown in FIG. 3 and FIG. 4, the austenite grains of GH3230 alloy obtained in example 1 are columnar grains, M 6 C is precipitated in a large amount at the positions of grain boundaries and original subgrain boundaries, and M 6 The grain size of C presents a bimodal distribution, the grain boundary M 6 The size of C particle is 180-2850 nm, and M is in crystal 6 The size of C particles is 40-280 nm, and the volume fraction of carbide is 9.04vt%;
the austenite grains of the GH3230 alloy obtained in example 2 were still columnar, M 6 Growth of C and grain boundary M 6 The size of C particle is 570-3500 nm, and M is in crystal 6 The size of C particles is 60-360 nm, and the volume fraction of carbide is 7.79vt%;
the austenite grains of GH3230 alloy obtained in example 3 recrystallized and transformed to isometric grains, M 6 C is largely dissolved in the matrix and grain boundary M 6 The size of C particle is 320-2080 nm, and M is in crystal 6 The size of C particles is 30-350 nm, and the volume fraction of carbide is 3.74vt%;
the austenite grains of the GH3230 alloy obtained in example 4 underwent complete recrystallization, M 6 C is almost completely dissolved in the matrix, but a small amount of nano precipitated phase still exists.
FIG. 5 is a graph comparing the as-deposited GH3230 alloy with engineering stress-strain curves for GH3230 alloys from examples 1-4 by various solution treatments; FIG. 6 is a graph comparing tensile strength and elongation of as-deposited GH3230 alloys and GH3230 alloys obtained by different solution treatment methods of examples 1-4.
As seen from fig. 5 and 6, as the solid solution temperature increases, the ultimate tensile strength gradually decreases while the elongation rate increases, and the conversion rate of the tensile strength to the elongation rate also increases; in the temperature rising process, due to the micron-sized grain boundary M 6 C is subjected to solid solution to a matrix, so that the stress concentration of a sample is reduced, and the micron-sized grain boundary M of the sample is subjected to solid solution treatment at 1180 DEG C 6 C grows up, which reduces the strength by 13% and improves the elongation by 16%, the conversion efficiency from the strength to the elongation is 1.23, and after the solution treatment at 1280 ℃, the grain boundary is in a micron-sized M 6 C carbide is almost completely eliminated, and the elongation of GH3230 sample melted by laser powder bed isThe tensile strength at room temperature is greatly improved by 1.6 times, the high tensile strength at room temperature is kept (reduced by 28 percent), and the conversion efficiency of the strength to the elongation is 5.71. Therefore, according to the performance requirement of the GH3230 alloy melted by the target laser powder bed, a proper heat treatment method can be selected, so that the controllability of the strength and the plasticity is realized.
Example 5
The present example provides a solution treatment method of laser powder bed melting GH3230 alloy, and the solution treatment method of the present example is different from that of example 1 only in that: the specific solid solution temperature and time in step two of this example are:
and (3) placing the deposition GH3230 sample prepared in the step one into a vacuum heat treatment furnace, heating the sample to 1130 ℃ at a heating rate of 10 ℃/min in a vacuum environment with the pressure not greater than 1000Pa for solution treatment, preserving heat for 1h, and introducing high-pressure argon to rapidly cool to room temperature.
In the embodiment, the ultimate tensile strength of the GH3230 alloy after 1130 ℃ solution treatment is 910MPa, and the elongation is 18.5%.
Example 6
The embodiment provides a solution treatment method for melting GH3230 alloy by a laser powder bed, and the solution treatment method of the embodiment is only different from that of the embodiment 1 in that: the specific solid solution temperature and time in step two of this example are:
and (3) placing the deposition GH3230 sample prepared in the step one into a vacuum heat treatment furnace, heating the sample to 1180 ℃ at a heating rate of 10 ℃/min in a vacuum environment with the pressure not greater than 1000Pa for solution treatment, keeping the temperature for 1h, and introducing high-pressure argon to rapidly cool to room temperature.
In the embodiment, the ultimate tensile strength of the GH3230 alloy after 1180 ℃ solution treatment is 824MPa, and the elongation is 17.3%.
Example 7
The present example provides a solution treatment method of laser powder bed melting GH3230 alloy, and the solution treatment method of the present example is different from that of example 1 only in that: the specific solid solution temperature and time in step two of this example are:
and (3) placing the deposition GH3230 sample prepared in the step one into a vacuum heat treatment furnace, heating the sample to 1230 ℃ at a heating rate of 10 ℃/min in a vacuum environment with the pressure not greater than 1000Pa for solution treatment, keeping the temperature for 1h, and introducing high-pressure argon to rapidly cool to room temperature.
In the embodiment, the ultimate tensile strength of the GH3230 alloy after the solution treatment at 1230 ℃ is 741MPa, and the elongation is 23%.
Example 8
The present example provides a solution treatment method of laser powder bed melting GH3230 alloy, and the solution treatment method of the present example is different from that of example 1 only in that: the specific solid solution temperature and time in step two of this example are:
and (3) placing the deposition GH3230 sample prepared in the step one into a vacuum heat treatment furnace, heating the sample to 1280 ℃ at a heating rate of 10 ℃/min in a vacuum environment with the pressure not greater than 1000Pa for solid solution treatment, preserving heat for 1h, and introducing high-pressure argon to rapidly cool to room temperature.
In the embodiment, the ultimate tensile strength of the GH3230 alloy after solution treatment at 1280 ℃ is 657MPa, and the elongation is 39%.
Claims (10)
1. A solution treatment method for melting GH3230 alloy by a laser powder bed is characterized by comprising the following steps:
step one, preparing GH3230 alloy:
preparing GH3230 alloy by a laser powder bed melting additive manufacturing system under the protection of inert atmosphere;
step two, solution treatment of GH3230 alloy:
and (3) heating the GH3230 alloy prepared in the step one to 1130-1280 ℃ in a vacuum environment with the pressure not more than 1000Pa for solution treatment, preserving the heat for 1-3 h, and cooling to room temperature.
2. The solution treatment method for melting GH3230 alloy by using the laser powder bed as claimed in claim 1, wherein the GH3230 spherical powder used in the first step for preparing the GH3230 alloy has the following components in percentage by mass: c:0.05 to 0.15%, si:0.25 to 0.75%, mn:0.30 to 1%, cr: 20-24%, fe: less than or equal to 3 percent, mo:1 to 3%, co: less than or equal to 5%, W:13 to 15%, al:0.2 to 0.5%, ti: less than or equal to 0.1 percent, cu: less than or equal to 0.5%, la:0.005 to 0.05%, B: less than or equal to 0.005 percent and the balance of Ni.
3. The solution treatment method for melting GH3230 alloy by using the laser powder bed according to claim 1 or 2, wherein the GH3230 spherical powder used in the first step for preparing the GH3230 alloy has the following components in percentage by mass: c:0.07%, si:0.35%, mn:0.5%, cr:21.74%, fe:1.9%, mo:2.8%, co:2.1%, W:14.7%, al:0.45%, ti:0.1%, cu:0.01%, la:0.01%, B:0.001% and the balance of Ni.
4. The solution treatment method for GH3230 alloy by laser powder bed melting in claim 3, wherein GH3230 spherical powder used for preparing GH3230 alloy in the first step has a particle size of 15-53 μm.
5. The solution treatment method of claim 4, wherein in the step one, the inert atmosphere is an argon atmosphere, and the oxygen content of the argon atmosphere is lower than 100ppm.
6. The solution treatment method of claim 5, wherein in the step one, a light source in the laser powder bed melting additive manufacturing system is a YAG solid laser, the laser power is 120-300W, the spot diameter is 0.087mm, the laser scanning rate is 500-1300 mm/s, the powder laying thickness is 0.02-0.05 mm, the scanning interval is 0.05-0.12 mm, the scanning strategy is 67 degrees cross scanning, and the substrate preheating temperature is 80-160 ℃.
7. The solution treatment method for melting GH3230 alloy by using laser powder bed as claimed in claim 6, wherein the temperature rise of GH3230 alloy in the second step is from room temperature to 1130-1280 ℃ at a speed of 8-10 ℃/min.
8. The solution treatment method for melting GH3230 alloy by using laser powder bed as claimed in claim 7, wherein the cooling to room temperature in step two is performed by rapid cooling with high-pressure argon.
9. A solution treatment method for GH3230 alloy by laser powder bed melting of GH3230 alloy according to any of claims 1-8, wherein the matrix of the GH3230 alloy obtained by the treatment is a fully austenitic structure, and the grain size is controlled within the range of 40-80 μm.
10. The solution treatment method of claim 9 for melting GH3230 alloy by laser powder bed, wherein the precipitated carbide is M 6 C，M 6 The volume fraction of C in the GH3230 alloy is less than 10%, and the original grain boundary position M 6 C average size less than 2 μ M, M in crystal 6 The average size of C is less than 0.3 μm.
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Citations (21)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102808113A (en) * | 2012-08-24 | 2012-12-05 | 叶绿均 | Process for preparing nickel-base superalloy |
| CN103240412A (en) * | 2013-05-22 | 2013-08-14 | 北京科技大学 | Method for preparing powder super-alloy by near net shape |
| CN103551573A (en) * | 2013-10-22 | 2014-02-05 | 中国科学院金属研究所 | Previous particle boundary precipitation preventable high-temperature alloy powder hot isostatic pressing process |
| CN103949639A (en) * | 2014-05-19 | 2014-07-30 | 北京航空航天大学 | Method for preparing Nb-Si based superhigh-temperature alloy by SLM (selective laser melting) technology |
| CN104388722A (en) * | 2014-11-07 | 2015-03-04 | 厦门钨业股份有限公司 | Hard alloy with binding phase intensified by virtue of heat treatment and preparation method of hard alloy |
| CN104826969A (en) * | 2015-05-25 | 2015-08-12 | 无锡市派克重型铸锻有限公司 | Method for forging 500-Kg-level GH3230 high-temperature alloy |
| CN105603259A (en) * | 2016-04-11 | 2016-05-25 | 西安欧中材料科技有限公司 | Powder metallurgical method for IN718 alloy |
| CN106312060A (en) * | 2015-06-29 | 2017-01-11 | 中国科学院金属研究所 | Preparation method for high-performance low-modulus medical titanium alloy three-dimensional metal part |
| CN106435270A (en) * | 2016-11-15 | 2017-02-22 | 东北大学 | TC21 titanium alloy powder for laser 3D printing and preparation and using methods |
| CN106563749A (en) * | 2015-10-09 | 2017-04-19 | 北京钢研高纳科技股份有限公司 | Preparation method for controlling organization of GH3230 alloy ring piece to be uniform |
| CN108315598A (en) * | 2018-04-20 | 2018-07-24 | 长沙聚众冶金科技有限公司 | A kind of preparation method of IN713C nickel base superalloys |
| CN109746435A (en) * | 2019-01-30 | 2019-05-14 | 中国科学院过程工程研究所 | A kind of high laser reflectivity metal-powder and 3D printing method that surface is modified |
| CN110218910A (en) * | 2018-11-24 | 2019-09-10 | 西部超导材料科技股份有限公司 | A kind of novel powder high temperature alloy and preparation method thereof |
| CN110666175A (en) * | 2019-10-31 | 2020-01-10 | 西安欧中材料科技有限公司 | Hot isostatic pressing forming method of nickel-based high-temperature alloy powder |
| CN111254317A (en) * | 2020-01-19 | 2020-06-09 | 北京钢研高纳科技股份有限公司 | Nickel-based casting alloy and preparation method thereof |
| CN111500898A (en) * | 2020-06-19 | 2020-08-07 | 北京钢研高纳科技股份有限公司 | Nickel-based superalloy, method for producing same, component and use |
| CN112024870A (en) * | 2020-07-30 | 2020-12-04 | 西安欧中材料科技有限公司 | SMTGH3230 spherical powder for 3D printing and preparation method and application thereof |
| CN113042755A (en) * | 2021-03-12 | 2021-06-29 | 飞而康快速制造科技有限责任公司 | Heat treatment method of GH3536 high-temperature alloy for additive manufacturing |
| CN113061782A (en) * | 2021-03-16 | 2021-07-02 | 山东大学 | GH3230 nickel-based superalloy material, method for eliminating micro-cracks formed by selective laser melting and application thereof |
| CN113481412A (en) * | 2021-05-17 | 2021-10-08 | 东莞材料基因高等理工研究院 | Additive manufacturing nickel-based high-temperature alloy and preparation method and application thereof |
| CN113814413A (en) * | 2021-09-24 | 2021-12-21 | 武汉工程大学 | Preparation method for manufacturing crack-free high-temperature alloy with controllable strength and toughness by laser additive manufacturing |
-
2022
- 2022-11-15 CN CN202211430098.5A patent/CN115846689B/en active Active
Patent Citations (21)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102808113A (en) * | 2012-08-24 | 2012-12-05 | 叶绿均 | Process for preparing nickel-base superalloy |
| CN103240412A (en) * | 2013-05-22 | 2013-08-14 | 北京科技大学 | Method for preparing powder super-alloy by near net shape |
| CN103551573A (en) * | 2013-10-22 | 2014-02-05 | 中国科学院金属研究所 | Previous particle boundary precipitation preventable high-temperature alloy powder hot isostatic pressing process |
| CN103949639A (en) * | 2014-05-19 | 2014-07-30 | 北京航空航天大学 | Method for preparing Nb-Si based superhigh-temperature alloy by SLM (selective laser melting) technology |
| CN104388722A (en) * | 2014-11-07 | 2015-03-04 | 厦门钨业股份有限公司 | Hard alloy with binding phase intensified by virtue of heat treatment and preparation method of hard alloy |
| CN104826969A (en) * | 2015-05-25 | 2015-08-12 | 无锡市派克重型铸锻有限公司 | Method for forging 500-Kg-level GH3230 high-temperature alloy |
| CN106312060A (en) * | 2015-06-29 | 2017-01-11 | 中国科学院金属研究所 | Preparation method for high-performance low-modulus medical titanium alloy three-dimensional metal part |
| CN106563749A (en) * | 2015-10-09 | 2017-04-19 | 北京钢研高纳科技股份有限公司 | Preparation method for controlling organization of GH3230 alloy ring piece to be uniform |
| CN105603259A (en) * | 2016-04-11 | 2016-05-25 | 西安欧中材料科技有限公司 | Powder metallurgical method for IN718 alloy |
| CN106435270A (en) * | 2016-11-15 | 2017-02-22 | 东北大学 | TC21 titanium alloy powder for laser 3D printing and preparation and using methods |
| CN108315598A (en) * | 2018-04-20 | 2018-07-24 | 长沙聚众冶金科技有限公司 | A kind of preparation method of IN713C nickel base superalloys |
| CN110218910A (en) * | 2018-11-24 | 2019-09-10 | 西部超导材料科技股份有限公司 | A kind of novel powder high temperature alloy and preparation method thereof |
| CN109746435A (en) * | 2019-01-30 | 2019-05-14 | 中国科学院过程工程研究所 | A kind of high laser reflectivity metal-powder and 3D printing method that surface is modified |
| CN110666175A (en) * | 2019-10-31 | 2020-01-10 | 西安欧中材料科技有限公司 | Hot isostatic pressing forming method of nickel-based high-temperature alloy powder |
| CN111254317A (en) * | 2020-01-19 | 2020-06-09 | 北京钢研高纳科技股份有限公司 | Nickel-based casting alloy and preparation method thereof |
| CN111500898A (en) * | 2020-06-19 | 2020-08-07 | 北京钢研高纳科技股份有限公司 | Nickel-based superalloy, method for producing same, component and use |
| CN112024870A (en) * | 2020-07-30 | 2020-12-04 | 西安欧中材料科技有限公司 | SMTGH3230 spherical powder for 3D printing and preparation method and application thereof |
| CN113042755A (en) * | 2021-03-12 | 2021-06-29 | 飞而康快速制造科技有限责任公司 | Heat treatment method of GH3536 high-temperature alloy for additive manufacturing |
| CN113061782A (en) * | 2021-03-16 | 2021-07-02 | 山东大学 | GH3230 nickel-based superalloy material, method for eliminating micro-cracks formed by selective laser melting and application thereof |
| CN113481412A (en) * | 2021-05-17 | 2021-10-08 | 东莞材料基因高等理工研究院 | Additive manufacturing nickel-based high-temperature alloy and preparation method and application thereof |
| CN113814413A (en) * | 2021-09-24 | 2021-12-21 | 武汉工程大学 | Preparation method for manufacturing crack-free high-temperature alloy with controllable strength and toughness by laser additive manufacturing |
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