CN114559054A - Forming process for preparing GH99 nickel-based alloy by melting of laser powder bed - Google Patents
Forming process for preparing GH99 nickel-based alloy by melting of laser powder bed Download PDFInfo
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- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
- B22F10/20—Direct sintering or melting
- B22F10/28—Powder bed fusion, e.g. selective laser melting [SLM] or electron beam melting [EBM]
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- B22—CASTING; POWDER METALLURGY
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- 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
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- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/14—Making metallic powder or suspensions thereof using physical processes using electric discharge
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B33—ADDITIVE MANUFACTURING TECHNOLOGY
- B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
- B33Y10/00—Processes of additive manufacturing
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B33—ADDITIVE MANUFACTURING TECHNOLOGY
- B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
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- B33Y40/20—Post-treatment, e.g. curing, coating or polishing
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- B—PERFORMING OPERATIONS; TRANSPORTING
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- 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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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- 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
- C22C19/056—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 10% but less than 20%
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- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
Abstract
A forming process for preparing GH99 nickel-based alloy by melting a laser powder bed belongs to the field of metal additive manufacturing, and is characterized in that a powder material is prepared into a rotary electrode, the rotating speed is 20000-45000r/min, the current is 850-1500A, the feeding speed is 1.5-3.0mm/s, the argon atmosphere is adopted, and the cooling temperature is 23-25 ℃. S2) carrying out laser powder bed melting process molding on the powder obtained in S1) to prepare a high-density defect-free sample. The heat treatment process is a combined mode of solid solution and aging heat treatment, widens the forming mode of the GH99 alloy, prepares the alloy with high compactness, no defects such as cracks and excellent mechanical properties, effectively solves the defects caused by casting, forging, welding and machining, greatly improves the design freedom degree and the forming efficiency of the GH99 alloy, and provides technical reference for engineering application of the GH99 alloy in the fields of aerospace and the like.
Description
Technical Field
The invention belongs to the field of metal additive manufacturing, and particularly relates to a forming process for preparing GH99 nickel-based alloy by melting a laser powder bed.
Background
GH99(GH4099) is based on nickel element and on Gamma prime phase Ni3(Al, Ti) is a precipitation strengthening type nickel-base superalloy with a main strengthening phase. The GH99 alloy component can be used at the temperature of over 900 ℃ and can break through 1000 ℃ at most, so the GH99 alloy component is widely applied to high-temperature components such as an aircraft engine combustion chamber, a hot end component of a gas turbine and the like. In recent years, with the development of the aerospace field, the demand of parts made of GH99 alloy is increasing, and the requirements on the structural design and performance of the alloy are increasing.
The forming method of the GH99 alloy member mainly comprises forging, casting, welding, machining and other methods. However, GH99 alloy has a large number of constituent elements, low metal melt fluidity and poor castability. GH99 contains cemented carbide elements such as W, Co, Cr, etc., resulting in poor forgeability and severe tool wear and difficulty in machining. And for forging, casting, welding and machining: on one hand, the forming period is large, a large amount of manpower and material resources are wasted, the environment is polluted, and the low-carbon environmental protection and carbon neutralization concepts are not met; on the other hand, the process has low design freedom degree, and is difficult to form complex geometric structures such as an inner runner, a honeycomb structure, a small curved surface turbine and the like. Therefore, it is very important to find a process with high forming efficiency, low carbon, environmental protection and high forming freedom.
Laser Powder Bed Fusion (LPBF) is a typical process in metal additive manufacturing (commonly known as 3D printing), the LPBF process uses a high-energy Laser Gaussian beam as an energy source, layer-by-layer scanning is carried out on a metal powder bed according to a scanning path planned in a three-dimensional Computer Aided Drawing (CAD) slicing model, scanned metal powder is a rapid non-equilibrium solidification process, and the metal powder is rapidly melted and solidified under the action of Laser energy, so that powder materials are metallurgically combined, and a designed three-dimensional entity is finally obtained. Compared with the traditional forming processes such as casting, forging, welding and the like, the LPBF process has certain unique advantages, such as large forming freedom degree, simple forming process, high efficiency, low carbon, environmental protection, economy and the like. By virtue of the unique advantages of the LPBF process, the LPBF process is applied to metal materials such as titanium alloy, high-temperature alloy, steel, copper alloy and the like.
The LPBF process has the advantages of just solving the defects of the traditional process of the GH99 alloy, and greatly expanding the forming mode and the design freedom of the GH99 alloy. After the LPBF alloy is formed, the mechanical property also needs to be improved, a reasonable heat treatment method is designed, and the mechanical property which is higher than that of the conventional forming mode of the alloy is extremely important. Aiming at the defects of the GH99 alloy component at present, the invention innovatively adopts an LPBF process and optimizes an optimal heat treatment method, and aims to better widen the engineering application of the GH99 component.
Disclosure of Invention
Aiming at the existing problems, the invention provides a forming process for preparing GH99 by melting a laser powder bed, and GH99 alloy prepared by the forming process has the advantages of high density, no defects such as cracks and the like and excellent mechanical properties.
In order to achieve the above purpose, the technical scheme of the invention is as follows: a forming process for preparing GH99 through laser powder bed melting comprises the following specific steps:
s1) preparing GH99 nickel-based high-temperature alloy powder by SS-PREP, preheating the prepared powder in a drying box for 4-6 hours at 80-120 ℃, and cooling for later use.
S2) carrying out laser powder bed melting process forming by using the powder obtained in S1), and preparing a high-density defect-free sample through process optimization.
S3) carrying out solid solution and aging heat treatment on the alloy obtained in S2), and obtaining the alloy with excellent mechanical property after selecting the optimal heat treatment process.
Further, in the step S1), the powder material is prepared into a rotating electrode with the rotating speed of 20000-45000r/min, the current of 850-1500A, the feeding speed of 1.5-3.0mm/S, the argon atmosphere and the cooling temperature of 23-25 ℃.
Furthermore, the particle size distribution of the powder meets the requirements that D10 is 16-25 μm, D50 is 34-42 μm, and D90 is 50-55 μm; other test results meet the requirements that the Hall flow rate is not more than 13.1s/50g and the apparent density is not more than 4.92g/cm3Tap density of not more than 5.21g/cm3The powder sphericity ratio is not less than 0.98.
Further, the GH99 powder comprises the following elements in percentage by mass: 17.0-21.2% of Cr, 5.0-8.0% of Co, 5.5-7.0% of W, 3.5-4.2% of Mo, 1.7-2.4% of Al, 1.0-1.5% of Ti, no more than 1.0% of Fe, no more than 0.055% of C, no more than 0.035% of Mn, less than 0.003% of Si, B, Ce, P and S, and the balance of Ni.
Further, step S2) includes the steps of:
s2.1) drawing a three-dimensional solid model required by printing in Magic 14.0 software, slicing after setting printing parameters, and importing the three-dimensional solid model into printing equipment;
s2.2) selecting a stainless steel substrate, preheating to 180-200 ℃, and then carrying out entity printing in an argon environment;
and S2.3) after printing is finished, taking out the substrate after the substrate is cooled to room temperature, and separating the sample from the substrate by linear cutting after the substrate is taken out.
Further, the LPBF process parameters in step S2.1) are: the laser power (280W-320W), the laser scanning speed (900 mm/s-1010 mm/s), the scanning interval (0.11 mm-0.13 mm) and the powder layer thickness are 0.04mm, and the rotation angles of two adjacent layers are 67 degrees by adopting a strips scanning strategy.
Further, the heat treatment process of step S3) is a combination of solution treatment and aging heat treatment, and specifically includes the following steps:
s3.1) solution heat treatment: preserving heat at 1100-1200 ℃ for 1-2 h, air-cooling to room temperature, and then carrying out S3.2) step;
s3.2) aging heat treatment: preserving heat for 5-10 h at 900-980 ℃, and cooling to room temperature along with the furnace.
Further, the mechanical properties of the as-formed sample (without heat treatment) were: the tensile strength is more than or equal to 940MPa, the yield strength is more than or equal to 680, and the elongation is more than or equal to 38%.
Further, the mechanical properties of the heat-treated sample are as follows: the tensile strength is more than or equal to 1100MPa, the yield strength is more than or equal to 700MPa, and the elongation is more than or equal to 40%.
The invention has the beneficial effects that: thanks to the technical scheme, the forming mode of the GH99 alloy is widened, the alloy with high compactness, no defects such as cracks and excellent mechanical property is prepared, the defects caused by casting, forging, welding and machining are effectively overcome, the design freedom degree and the forming efficiency of the GH99 alloy are greatly improved, and important technical reference is provided for engineering application of the GH99 alloy in the fields of aerospace and the like.
Drawings
FIG. 1 is an SEM image of a powder prepared by the SS-PREP process of the present invention.
FIG. 2 is a diagram of the gold phase of the alloy under different magnification factors under the optimal parameters (laser power is 300W, laser scanning speed is 950mm/s, scanning interval is 0.12mm, and powder layer thickness is 0.04 mm).
FIG. 3 is a graph of stress strain curves for the present invention in its as-formed and heat treated state.
Detailed Description
To make the purpose, technical solution and advantages of the embodiments of the present invention more obvious, the following embodiments of the present invention will help those skilled in the relevant art to better understand the present invention, and it is obvious that the embodiments are only some embodiments, and not all embodiments. It should be noted that those skilled in the relevant art can make appropriate modifications without departing from the basic idea of the invention. All of which are within the scope of the invention.
Example 1
A forming process for preparing GH99 through laser powder bed melting comprises the following specific steps:
(1) preparing GH99 nickel-based superalloy powder by using SS-PREP, wherein the prepared powder is shown in figure 1, preheating the prepared powder in a drying oven at 90 ℃ for 4 hours, and cooling the powder for later use.
(2) And (3) carrying out laser powder bed melting process forming on the powder obtained in the step (1), and preparing a high-density defect-free sample through process optimization, as shown in FIG. 2.
(3) And (3) carrying out solid solution and aging heat treatment on the alloy (2), and obtaining the alloy with excellent mechanical properties after selecting an optimal heat treatment process.
In the step (1), the powder material is prepared into a rotating electrode, the rotating speed of the rotating electrode is 25000r/min, the current is 900A, the feeding speed is 1.5mm/s, the argon atmosphere is adopted, and the cooling temperature is 23 ℃.
The particle size distribution of the powder meets the requirements that D10 is 16-25 mu m, D50 is 34-42 mu m, and D90 is 50-55 mu m; other test results meet the requirements that the Hall flow rate is 13.1s/50g and the apparent density is 4.92g/cm3Tap density of 5.21g/cm3The powder sphericity ratio was 0.98.
The GH99 powder comprises the following elements in percentage by mass: 17.0-21.2% of Cr, 5.0-8.0% of Co, 5.5-7.0% of W, 3.5-4.2% of Mo, 1.7-2.4% of Al, 1.0-1.5% of Ti, no more than 1.0% of Fe, no more than 0.055% of C, no more than 0.035% of Mn, less than 0.003% of Si, B, Ce, P and S, and the balance of Ni.
The step (2) comprises the following steps:
(2.1) drawing a three-dimensional solid model required by printing in Magic 14.0 software, slicing after setting printing parameters, and importing the three-dimensional solid model into printing equipment;
(2.2) selecting a stainless steel substrate, preheating to 180 ℃, and then carrying out entity printing in an argon environment;
and (2.3) after printing is finished, taking out the substrate after the substrate is cooled to room temperature, and separating the sample from the substrate by using wire cutting after the substrate is taken out.
Further, the LPBF process parameters in step S2.1) are: the laser power (300W), the laser scanning speed (900mm/s), the scanning interval (0.11mm) and the powder coating thickness are 0.04mm, and the rotation angle of two adjacent layers is 67 degrees by adopting a strips scanning strategy.
The heat treatment process in the step (3) is a combination of solid solution and aging heat treatment, and specifically comprises the following steps:
(3.1) solution Heat treatment: keeping the temperature at 1100 ℃ for 2h, air-cooling to room temperature, and then carrying out the step (3.2);
(3.2) aging heat treatment: preserving the heat for 10 hours at 900 ℃, and cooling to room temperature along with the furnace.
The mechanical properties of the formed sample (without heat treatment) are as follows: tensile strength 950MPa, yield strength 680MPa, and elongation 38%, as shown in FIG. 3.
Mechanical properties of the heat-treated sample: the tensile strength was 1100MPa, the yield strength was 700MPa, and the elongation was 40%, as shown in FIG. 3.
Example 2
A forming process for preparing GH99 through laser powder bed melting comprises the following specific steps:
(1) preparing GH99 nickel-based superalloy powder by SS-PREP, preheating the prepared powder in a drying oven at 100 ℃ for 5 hours, and cooling for later use.
(2) And (3) carrying out laser powder bed melting process forming on the powder obtained in the step (1), and preparing a high-density defect-free sample through process optimization.
(3) And (3) carrying out solid solution and aging heat treatment on the alloy (2), and obtaining the alloy with excellent mechanical properties after selecting an optimal heat treatment process.
In the step (1), the powder material is prepared into a rotating electrode, the rotating speed of the rotating electrode is 30000r/min, the current is 950A, the feeding speed is 2mm/s, the argon atmosphere is achieved, and the cooling temperature is 24 ℃.
The particle size distribution of the powder meets the requirements that D10 is 16-25 mu m, D50 is 34-42 mu m, and D90 is 50-55 mu m; other test results satisfy the Hall flow rate of 12.8/50g and the apparent density of 4.91g/cm3Tap density of 5.18g/cm3The powder sphericity ratio was 0.99.
The GH99 powder comprises the following elements in percentage by mass: 17.0-21.2% of Cr, 5.0-8.0% of Co, 5.5-7.0% of W, 3.5-4.2% of Mo, 1.7-2.4% of Al, 1.0-1.5% of Ti, no more than 1.0% of Fe, no more than 0.055% of C, no more than 0.035% of Mn, less than 0.003% of Si, B, Ce, P and S, and the balance of Ni.
(2.1) drawing a three-dimensional solid model required by printing in Magic 14.0 software, slicing after setting printing parameters, and importing the three-dimensional solid model into printing equipment;
(2.2) selecting a stainless steel substrate, preheating to 180 ℃, and then carrying out entity printing in an argon environment;
and (2.3) after printing is finished, taking out the substrate after the substrate is cooled to room temperature, and separating the sample from the substrate by using wire cutting after the substrate is taken out.
Further, the LPBF process parameters in step S2.1) are: the laser power (310W), the laser scanning speed (975mm/s), the scanning interval (0.12mm) and the powder coating thickness are 0.04mm, and the rotation angle of two adjacent layers is 67 degrees by adopting a strips scanning strategy.
The heat treatment process in the step (3) is a combination of solid solution and aging heat treatment, and specifically comprises the following steps:
(3.1) solution Heat treatment: keeping the temperature at 1150 ℃ for 1.5h, air-cooling to room temperature, and then carrying out the step (3.2);
(3.2) aging heat treatment: keeping the temperature at 950 ℃ for 8h, and cooling to room temperature along with the furnace.
The mechanical properties of the formed sample (without heat treatment) are as follows: the tensile strength is 964MPa, the yield strength is 682MPa, and the elongation is 39%.
Mechanical properties of the heat-treated sample: the tensile strength is 1120MPa, the yield strength is 709MPa, and the elongation is 42%.
Example 3
A forming process for preparing GH99 through laser powder bed melting comprises the following specific steps:
(1) preparing GH99 nickel-based superalloy powder by SS-PREP, preheating the prepared powder in a drying oven at 110 ℃ for 6 hours, and cooling for later use.
(2) And (3) carrying out laser powder bed melting process forming on the powder obtained in the step (1), and preparing a high-density defect-free sample through process optimization.
(3) And (3) carrying out solid solution and aging heat treatment on the alloy (2), and obtaining the alloy with excellent mechanical properties after selecting an optimal heat treatment process.
In the step (1), the powder material is prepared into a rotary electrode, the rotating speed of the rotary electrode is 31000r/min, the current is 1230A, the feeding speed is 3mm/s, the argon atmosphere is adopted, and the cooling temperature is 25 ℃.
The particle size distribution of the powder meets the requirements that D10 is 16-25 mu m, D50 is 34-42 mu m, and D90 is 50-55 mu m; other test results satisfy the Hall flow rate of 13.0s/50g and the apparent density of 4.91g/cm3Tap density of 5.19g/cm3The powder sphericity ratio was 0.98.
The GH99 powder comprises the following elements in percentage by mass: 17.0-21.2% of Cr, 5.0-8.0% of Co, 5.5-7.0% of W, 3.5-4.2% of Mo, 1.7-2.4% of Al, 1.0-1.5% of Ti, no more than 1.0% of Fe, no more than 0.055% of C, no more than 0.035% of Mn, less than 0.003% of Si, B, Ce, P and S, and the balance of Ni.
The step (2) comprises the following steps:
(2.1) drawing a three-dimensional solid model required by printing in Magic 14.0 software, slicing after setting printing parameters, and importing the three-dimensional solid model into printing equipment;
(2.2) selecting a stainless steel substrate, preheating to 200 ℃, and then performing entity printing in an argon environment;
and (2.3) after the printing is finished, taking out the substrate after the substrate is cooled to room temperature, and separating the sample from the substrate by linear cutting after the substrate is taken out.
Further, the LPBF process parameters in step S2.1) are: the laser power (320W), the laser scanning speed (1000mm/s), the scanning interval (0.13mm) and the powder coating thickness are 0.04mm, and the rotation angle of two adjacent layers is 67 degrees by adopting a strips scanning strategy.
The heat treatment process in the step (3) is a combination of solid solution and aging heat treatment, and specifically comprises the following steps:
(3.1) solution Heat treatment: keeping the temperature at 1200 ℃ for 1h, air-cooling to room temperature, and then carrying out the step (3.2);
(3.2) aging heat treatment: keeping the temperature at 980 ℃ for 6h, and cooling to room temperature along with the furnace.
The mechanical properties of the formed sample (without heat treatment) are as follows: the tensile strength was 961MPa, the yield strength was 687MPa, and the elongation was 40%, as shown in FIG. 3.
Mechanical property of the heat-treated sample: the tensile strength was 1109MPa, the yield strength was 715MPa, and the elongation was 44%, as shown in FIG. 3.
The above embodiments are only a part of the embodiments of the present invention, and do not include all the embodiments. The present invention is not limited to the above embodiments, and can be modified appropriately without departing from the concept and the original spirit of the present invention, and the present invention does not affect the substantial contents of the present invention.
Claims (2)
1. A forming process for preparing GH99 nickel-based alloy by melting a laser powder bed is characterized by comprising the following steps of:
s1) preparing GH99 nickel-based high-temperature alloy powder by SS-PREP, preheating the prepared powder for 4-6 hours in a drying box at 80-120 ℃, and cooling for later use;
s2) carrying out laser powder bed melting process forming on the powder obtained in S1) to prepare a sample;
s3) carrying out solid solution and aging heat treatment on the sample obtained in S2) to obtain an alloy;
in the step S1), the powder material is prepared into a rotary electrode, the rotating speed is 20000-;
the particle size distribution of the powder meets the requirements that D10 is 16-25 mu m, D50 is 34-42 mu m, and D90 is 50-55 mu m;
step S2) includes the steps of:
s2.1) drawing a three-dimensional solid model required by printing in Magic 14.0 software, slicing after setting printing parameters, and importing the three-dimensional solid model into printing equipment; the set printing parameters are: the laser power is 280W-320W, the laser scanning speed is 900 mm/s-1010 mm/s, the scanning distance is 0.11 mm-0.14 mm, the powder layer thickness is 0.04mm, a strips scanning strategy is adopted, and the rotation angle of two adjacent layers is 67 degrees;
s2.2) selecting a stainless steel substrate, preheating to 180-200 ℃, and then carrying out entity printing in an argon environment;
s2.3) after printing is finished, taking out the substrate after the substrate is cooled to room temperature, and separating the sample from the substrate by linear cutting after the substrate is taken out;
the heat treatment process of the step S3) is a combination of solid solution and aging heat treatment, and specifically comprises the following steps:
s3.1) solution heat treatment: preserving heat for 1-2 h at 1100-1200 ℃, then cooling to room temperature by air, and then carrying out S.3.2);
s3.2) aging heat treatment: preserving heat for 5-10 h at 900-980 ℃, and cooling to room temperature along with the furnace.
2. The forming process for preparing GH99 Ni-based alloy through laser powder bed melting as claimed in claim 1, wherein the GH99 powder comprises the following elements by mass percent: 17.0-21.2% of Cr, 5.0-8.0% of Co, 5.5-7.0% of W, 3.5-4.2% of Mo, 1.7-2.4% of Al, 1.0-1.5% of Ti, no more than 1.0% of Fe, no more than 0.055% of C, no more than 0.035% of Mn, no more than 0.003% of Si, B, Ce, P and S and the balance of Ni.
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| CN117235463A (en) * | 2023-11-13 | 2023-12-15 | 北京科技大学 | Nondestructive testing method for alloy defect inner wall oxide film spatial distribution |
Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| 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 |
| CN107116219A (en) * | 2017-05-22 | 2017-09-01 | 西安欧中材料科技有限公司 | A kind of laser powdering increasing material manufacturing method of use SS PREP Ti6Al4V spherical powders |
| CN108247049A (en) * | 2017-12-21 | 2018-07-06 | 西安欧中材料科技有限公司 | A kind of selective laser increasing material manufacturing method using CoCrMo alloy powders |
| CN110918987A (en) * | 2019-10-30 | 2020-03-27 | 株洲航发动科南方燃气轮机有限公司 | Preparation method of 3D printing turbine blade and turbine guide blade |
| US20200131604A1 (en) * | 2018-10-25 | 2020-04-30 | Rolls-Royce Plc | Powder alloy composition, gas turbine engine component and method for manufacture of the same |
| CN112589115A (en) * | 2020-11-24 | 2021-04-02 | 北京星航机电装备有限公司 | Selective laser melting forming process for GH4099 nickel-based alloy component |
| CN113817935A (en) * | 2021-08-18 | 2021-12-21 | 盘星新型合金材料(常州)有限公司 | High-purity nickel-based high-temperature alloy and preparation method of spherical powder thereof |
-
2022
- 2022-03-02 CN CN202210202566.7A patent/CN114559054A/en active Pending
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| 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 |
| CN107116219A (en) * | 2017-05-22 | 2017-09-01 | 西安欧中材料科技有限公司 | A kind of laser powdering increasing material manufacturing method of use SS PREP Ti6Al4V spherical powders |
| CN108247049A (en) * | 2017-12-21 | 2018-07-06 | 西安欧中材料科技有限公司 | A kind of selective laser increasing material manufacturing method using CoCrMo alloy powders |
| US20200131604A1 (en) * | 2018-10-25 | 2020-04-30 | Rolls-Royce Plc | Powder alloy composition, gas turbine engine component and method for manufacture of the same |
| CN110918987A (en) * | 2019-10-30 | 2020-03-27 | 株洲航发动科南方燃气轮机有限公司 | Preparation method of 3D printing turbine blade and turbine guide blade |
| CN112589115A (en) * | 2020-11-24 | 2021-04-02 | 北京星航机电装备有限公司 | Selective laser melting forming process for GH4099 nickel-based alloy component |
| CN113817935A (en) * | 2021-08-18 | 2021-12-21 | 盘星新型合金材料(常州)有限公司 | High-purity nickel-based high-temperature alloy and preparation method of spherical powder thereof |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN117235463A (en) * | 2023-11-13 | 2023-12-15 | 北京科技大学 | Nondestructive testing method for alloy defect inner wall oxide film spatial distribution |
| CN117235463B (en) * | 2023-11-13 | 2024-01-30 | 北京科技大学 | Nondestructive testing method for alloy defect inner wall oxide film spatial distribution |
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