CN110666175B - Hot isostatic pressing forming method of nickel-based high-temperature alloy powder - Google Patents
Hot isostatic pressing forming method of nickel-based high-temperature alloy powder Download PDFInfo
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- 239000000843 powder Substances 0.000 title claims abstract description 80
- 238000001513 hot isostatic pressing Methods 0.000 title claims abstract description 75
- 238000000034 method Methods 0.000 title claims abstract description 54
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 title claims abstract description 46
- 239000000956 alloy Substances 0.000 title claims abstract description 46
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 45
- 229910052759 nickel Inorganic materials 0.000 title claims abstract description 23
- 229910000601 superalloy Inorganic materials 0.000 claims abstract description 24
- 238000002844 melting Methods 0.000 claims abstract description 22
- 230000008018 melting Effects 0.000 claims abstract description 22
- 238000010438 heat treatment Methods 0.000 claims abstract description 17
- 238000007789 sealing Methods 0.000 claims abstract description 9
- 238000003466 welding Methods 0.000 claims abstract description 9
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 16
- 238000004321 preservation Methods 0.000 claims description 13
- 238000001816 cooling Methods 0.000 claims description 11
- 229910052786 argon Inorganic materials 0.000 claims description 8
- 239000012535 impurity Substances 0.000 claims description 8
- 238000004806 packaging method and process Methods 0.000 claims description 8
- 238000000926 separation method Methods 0.000 claims description 8
- 239000002245 particle Substances 0.000 claims description 4
- 230000005496 eutectics Effects 0.000 claims description 3
- 238000012216 screening Methods 0.000 claims description 3
- 230000007547 defect Effects 0.000 abstract description 11
- 239000002994 raw material Substances 0.000 abstract 1
- 239000012071 phase Substances 0.000 description 16
- 101000912561 Bos taurus Fibrinogen gamma-B chain Proteins 0.000 description 5
- 239000013078 crystal Substances 0.000 description 5
- 239000000463 material Substances 0.000 description 5
- 238000007873 sieving Methods 0.000 description 5
- 238000005728 strengthening Methods 0.000 description 5
- 238000011161 development Methods 0.000 description 3
- 230000018109 developmental process Effects 0.000 description 3
- 238000001125 extrusion Methods 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 3
- 230000002159 abnormal effect Effects 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 230000002401 inhibitory effect Effects 0.000 description 2
- 239000007791 liquid phase Substances 0.000 description 2
- 238000004663 powder metallurgy Methods 0.000 description 2
- 238000005245 sintering Methods 0.000 description 2
- 239000000243 solution Substances 0.000 description 2
- CURLTUGMZLYLDI-UHFFFAOYSA-N Carbon dioxide Chemical compound O=C=O CURLTUGMZLYLDI-UHFFFAOYSA-N 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 229910002090 carbon oxide Inorganic materials 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 238000001192 hot extrusion Methods 0.000 description 1
- 238000010275 isothermal forging Methods 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 239000011164 primary particle Substances 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 238000012827 research and development Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000009827 uniform distribution Methods 0.000 description 1
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Classifications
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/12—Both compacting and sintering
- B22F3/14—Both compacting and sintering simultaneously
- B22F3/15—Hot isostatic pressing
-
- 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
- B22F5/00—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product
-
- 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
- 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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/0433—Nickel- or cobalt-based alloys
-
- 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
Abstract
The invention discloses a hot isostatic pressing forming method of a nickel-based superalloy powder disc, in particular to a hot isostatic pressing forming method of nickel-based superalloy powder, which is suitable for preparing a powder superalloy disc piece subjected to direct hot isostatic pressing forming, wherein the hot isostatic pressing forming method is implemented by taking superalloy powder prepared by a plasma rotating electrode method as a raw material, putting the powder into a sheath under a vacuum condition, sealing and welding the powder, and then carrying out hot isostatic pressing, wherein the temperature of the first hot isostatic pressing is 10-30 ℃ higher than the gamma' melting temperature, the pressure is not less than 100MPa, and the time is not more than 1 h; after the first step is finished, heating to 50-100 ℃ below the liquidus temperature, wherein the pressure is more than or equal to 100MPa, and the time is less than or equal to 30 min; after the second step, the temperature is reduced to 10-20 ℃ below the melting temperature of the low-melting-point phase, the pressure is not less than 100MPa, the temperature is kept for 30min, and the furnace is cooled. The invention can effectively inhibit the generation of PPB defects in the hot isostatic pressing process and improve the density of the alloy, thereby preparing the high-temperature alloy powder disc with uniform and compact tissues.
Description
Technical Field
The invention belongs to the technical field of high-temperature alloy powder metallurgy, and relates to a hot isostatic pressing forming method of nickel-based high-temperature alloy powder.
Background
The development level of the aircraft engine industry is the centralized embodiment of national industrial foundation, scientific and technological level and comprehensive national force and is also the important strategic guarantee of national safety and the status of the greater country. The technical progress of the aero-engine is closely related to the development of high-temperature alloy, and the high-temperature alloy is the most key structural material for promoting the development of the aero-engine. Military aircraft engines can generally be rated synthetically by their thrust-to-weight ratios. The most direct and effective technical measure to increase the thrust-to-weight ratio is to increase the gas temperature ahead of the turbine, so the properties and selection of superalloy materials are key factors in determining the performance of an aircraft engine. With the continuous upgrading of aviation equipment, the requirement on the thrust-weight ratio of an aero-engine is continuously improved, and the engine has greater and greater dependence on high-performance high-temperature alloy materials.
The traditional nickel-based high-temperature alloy turbine disk material has the defects of serious segregation, uneven structure and deteriorated thermal technological performance in the alloy due to the continuous increase of strengthening elements, and the requirements of a novel engine on a disk piece cannot be met by the conventional casting and deformation process. Since the last 70 s, the united states and russia began to produce nickel-base superalloys by powder metallurgy. The powder high-temperature alloy has the outstanding advantages of uniform structure and fine crystal grains, and the mechanical property and the thermal process property of the alloy are obviously improved. The powder high-temperature alloy is gradually developed into a preferred material for key hot-end components such as a turbine disc of a modern high-performance aircraft engine.
The main forming process of the powder superalloy is hot isostatic pressing, but due to the particularity of the process, after the powder superalloy is subjected to hot isostatic pressing, the structure mainly has defects such as Primary Particle Boundaries (PPB), Thermally Induced Porosity (TIP), inclusions and the like. The main components of PPB are carbon oxide and a thick gamma ' phase, the gamma ' phase is a main strengthening phase of the high-temperature alloy, aging precipitation of fine gamma ' with similar size and uniform distribution is carried out after solid solution strengthening is carried out at the temperature higher than the gamma ' phase, the fine gamma ' phase is a main strengthening mode of the high-temperature alloy, metallurgical bonding among powder particles can be weakened by the production of the PPB, the PPB becomes a weak link of the material, cracks are easy to initiate, crack expansion is accelerated, and the endurance strength and the fatigue life of the alloy are obviously reduced.
In order to improve the defects of PPB after hot isostatic pressing forming and improve the density and reliability of the alloy, research and development personnel at home and abroad make a series of attempts, in patent CN201310035088.6, the density of a finished piece is improved through two-step hot isostatic pressing, a disc blank with the density of 90% is obtained after the first hot isostatic pressing, a sheath is removed after the disc blank is cooled, and the second hot isostatic pressing is carried out by using a conventional hot isostatic pressing process. In patent CN107841697A, hot isostatic pressing is carried out at a temperature higher than the complete dissolution temperature of a gamma' phase by 50 ℃, and then large plastic deformation hot extrusion with an extrusion ratio of 4: 1-15: 1 is carried out at 1000-1140 ℃ to remove the original grain boundary and obtain a fine grain structure, so that the process is complex, and the operation difficulty of the extrusion process is high, and the cost is high. Russia uses the hot isostatic pressing after liquid phase sintering or the hot isostatic pressing after liquid phase sintering process to prepare the powder disc without original grain boundaries, the density of the prepared disc is lower, the density is improved by extrusion and isothermal forging, or the density of the alloy is improved by adopting a complex hot isostatic pressing temperature rise and heat preservation process. Other methods such as increasing the solution temperature and prolonging the solution time during heat treatment, and adding Hf and other elements to improve the grain boundary strengthening formed by PPB all increase the manufacturing cost of the powder superalloy.
Disclosure of Invention
The invention aims to provide a hot isostatic pressing forming method of nickel-based superalloy powder, which solves the problem of original grain boundary defects in the manufacturing process of a nickel-based superalloy disk piece in the prior art.
The technical scheme adopted by the invention is that the hot isostatic pressing forming method of the nickel-based superalloy powder disc specifically comprises the following steps:
step 1: preparing high-temperature alloy powder by using a plasma rotating electrode method, screening under the protection of argon, removing non-metallic impurities by electrostatic separation, packaging the powder in a sheath under a vacuum condition, and sealing and welding;
step 2: placing the sealed and welded sheath into hot isostatic pressing equipment, and performing hot isostatic pressing in a way of simultaneously raising temperature and pressure;
step 3, after the step 1 is finished, heating the powder to a temperature higher than the liquidus temperature, wherein the pressure is more than or equal to 100MPa, and the heat preservation time is 20-30 min;
and 4, after the step 2 is finished, cooling the powder to be below the melting temperature of the low-melting-point phase, keeping the temperature for 30-40 min under the pressure of more than or equal to 100MPa, and then stopping heating and cooling to room temperature to obtain the nickel-based high-temperature alloy powder disc.
In the step 1, the high-temperature alloy powder is sieved until the granularity is 50-150 mu m.
In step 2, the hot isostatic pressing temperature should be higher than the γ' melting temperature.
In the step 2, the hot isostatic pressing temperature is 10-30 ℃ higher than the gamma' melting temperature.
In the step 2, the hot isostatic pressure is more than or equal to 100MPa, and the heat preservation time is less than or equal to 1 h.
In step 3, the temperature of the powder is raised to 50-100 ℃ higher than the liquidus temperature.
In step 4, the powder is cooled to a temperature 10-20 ℃ lower than the melting temperature of the low-melting-point phase.
In the step 4, the melting temperature of the low-melting-point phase of the nickel-based alloy is (gamma + gamma') eutectic melting temperature.
The invention has the beneficial effects that:
1) according to the invention, hot isostatic pressing is carried out at 10-30 ℃ above the gamma' melting temperature by adjusting hot isostatic pressing process parameters, the heat preservation time is less than or equal to 1h, and the pressure is more than or equal to 100 MPa. Or obtaining the disc blank with the density of more than or equal to 95 percent. The hot isostatic pressing time in the process is less than or equal to 1h to avoid abnormal growth of crystal grains.
2) In the invention, the hot isostatic pressing is carried out at 50-100 ℃ below the liquidus temperature in the second step, the pressure is more than or equal to 100Pa, the heat preservation time is less than or equal to 30min, and the heat preservation is carried out at 50-100 ℃ below the liquidus temperature for 30min under high pressure, so that the coarse gamma' at the crystal boundary can be fully melted, thereby effectively inhibiting the formation of the original particle boundary, but the density of the disc part is reduced in the process, and the density of the disc part after the second step is about 90-95%.
3) In the third step, the temperature is kept for 30min at the temperature of 10-20 ℃ below the melting temperature of the low-melting-point phase and under the pressure of more than or equal to 100MPa, so that the low-melting-point phase is fully solidified, and the density of the alloy is remarkably improved to more than 99.9%.
Drawings
FIG. 1 is a view of a control group of FGH4097 powder disks produced using a conventional hot isostatic pressing process in an embodiment of a method of hot isostatic pressing of nickel-base superalloy powder disks of the present invention;
FIG. 2 is a view of a FGH4097 powder disk produced using a hot isostatic pressing method of a nickel-base superalloy powder disk of the present invention.
Detailed Description
The present invention will be described in detail below with reference to the accompanying drawings and specific embodiments.
The invention relates to a hot isostatic pressing forming method of a nickel-based superalloy powder disc, which comprises the following steps:
step 1: preparing high-temperature alloy powder by using a plasma rotating electrode method, screening under the protection of argon, removing non-metallic impurities by electrostatic separation, packaging the powder in a sheath under a vacuum condition, and sealing and welding;
step 2: placing the sealed and welded sheath into hot isostatic pressing equipment, and performing hot isostatic pressing in a way of simultaneously raising temperature and pressure;
step 3, after the step 1 is finished, heating the powder to a temperature higher than the liquidus temperature, wherein the pressure is more than or equal to 100MPa, and the heat preservation time is 20-30 min;
and 4, after the step 2 is finished, cooling the powder to be below the melting temperature of the low-melting-point phase, keeping the temperature for 30-40 min under the pressure of more than or equal to 100MPa, and then stopping heating and cooling to room temperature to obtain the nickel-based high-temperature alloy powder disc.
In the step 1, the high-temperature alloy powder is sieved until the granularity is 50-150 mu m.
In step 2, the hot isostatic pressing temperature should be higher than the γ' melting temperature.
In the step 2, the hot isostatic pressing temperature is 10-30 ℃ higher than the gamma' melting temperature.
In the step 2, the hot isostatic pressure is more than or equal to 100MPa, and the heat preservation time is less than or equal to 1 h.
In step 3, the temperature of the powder is raised to 50-100 ℃ higher than the liquidus temperature.
In step 4, the powder is cooled to a temperature 10-20 ℃ lower than the melting temperature of the low-melting-point phase.
In the step 4, the melting temperature of the low-melting-point phase of the nickel-based alloy is (gamma + gamma') eutectic melting temperature.
Example 1
A hot isostatic pressing method for FGH4097 alloy powder comprises the following steps:
(1) preparing high-temperature alloy powder by using a plasma rotating electrode method, sieving to 50-150 mu m under the protection of argon, removing non-metallic impurities by electrostatic separation, packaging the powder in a sheath under a vacuum condition, and sealing and welding. The attached drawing in the abstract shows the morphology of high-temperature alloy powder prepared by the plasma rotating electrode.
(2) Placing the sealed and welded sheath into hot isostatic pressing equipment, and performing hot isostatic pressing in a way of simultaneously raising temperature and pressure, wherein the hot isostatic pressing temperature in the first step is 1200 ℃, the pressure is 100MPa, and the temperature is kept for 1 h;
(3) after the first step is finished, heating to 1300 ℃, and keeping the temperature for 30min under the pressure of 100 MPa;
(4) and after the second step is finished, reducing the temperature to 1000 ℃, keeping the temperature for 30min under the pressure of 100MPa, and then stopping heating and cooling to room temperature to obtain the nickel-based superalloy powder disc.
FIG. 1 shows that the FGH4097 powder disk produced by the conventional hot isostatic pressing process has a distinct PPB defect in the texture of the disk, and FIG. 2 shows that the FGH4097 powder disk produced by the present invention has a dense texture after hot isostatic pressing and no distinct PPB defect is found.
TABLE 1 comparison of the Properties of powder disks produced by the conventional Process and the Process of the invention
Example 2
A hot isostatic pressing method for FGH4097 alloy powder comprises the following steps:
(1) preparing high-temperature alloy powder by using a plasma rotating electrode method, sieving to 50-150 mu m under the protection of argon, removing non-metallic impurities by electrostatic separation, packaging the powder in a sheath under a vacuum condition, and sealing and welding. The attached drawing in the abstract shows the morphology of high-temperature alloy powder prepared by the plasma rotating electrode.
(2) Placing the sealed and welded sheath into hot isostatic pressing equipment, and performing hot isostatic pressing in a way of simultaneously raising temperature and pressure, wherein the hot isostatic pressing temperature in the first step is 1210 ℃, the pressure is 100MPa, and the temperature is kept for 1 h;
(3) after the first step is finished, heating to 1270 ℃, and keeping the temperature for 30min under the pressure of 100 MPa;
(4) and after the second step is finished, reducing the temperature to 970 ℃, keeping the temperature for 30min under the pressure of 100MPa, and then stopping heating and cooling to room temperature to obtain the nickel-based superalloy powder disc.
Example 2 FGH4097 powder disks produced using the process of the present invention were texture dense after hot isostatic pressing and no significant PPB defects were found.
Example 3
A hot isostatic pressing method for FGH4097 alloy powder comprises the following steps:
(1) preparing high-temperature alloy powder by using a plasma rotating electrode method, sieving to 50-150 mu m under the protection of argon, removing non-metallic impurities by electrostatic separation, packaging the powder in a sheath under a vacuum condition, and sealing and welding. The attached drawing in the abstract shows the morphology of high-temperature alloy powder prepared by the plasma rotating electrode.
(2) Placing the sealed and welded sheath into hot isostatic pressing equipment, and performing hot isostatic pressing in a way of simultaneously raising temperature and pressure, wherein the hot isostatic pressing temperature in the first step is 1220 ℃, the pressure is 100MPa, and the heat is preserved for 1 h;
(3) after the first step is finished, raising the temperature to 1250 ℃, and preserving the heat for 30min under the pressure of 100 MPa;
(5) and after the second step is finished, reducing the temperature to 950 ℃, keeping the temperature for 30min under the pressure of 100MPa, and then stopping heating and cooling to room temperature to obtain the nickel-based superalloy powder disc.
Example 3 FGH4097 powder disks produced using the process of the present invention were texture dense after hot isostatic pressing and no significant PPB defects were found.
Example 4
A hot isostatic pressing method for FGH4097 alloy powder comprises the following steps:
(4) preparing high-temperature alloy powder by using a plasma rotating electrode method, sieving to 50-150 mu m under the protection of argon, removing non-metallic impurities by electrostatic separation, packaging the powder in a sheath under a vacuum condition, and sealing and welding. The attached drawing in the abstract shows the morphology of high-temperature alloy powder prepared by the plasma rotating electrode.
(5) Placing the sealed and welded sheath into hot isostatic pressing equipment, and performing hot isostatic pressing in a way of simultaneously raising temperature and pressure, wherein the hot isostatic pressing temperature in the first step is 1215 ℃, the pressure is 100MPa, and the heat is preserved for 1 h;
(6) after the first step is finished, heating to 1290 ℃, and keeping the temperature for 30min under the pressure of 100 MPa;
(6) and after the second step is finished, reducing the temperature to 980 ℃, preserving the heat for 30min under the pressure of 100MPa, and then stopping heating and cooling to room temperature to obtain the nickel-based superalloy powder disc.
Example 3 FGH4097 powder disks produced using the process of the present invention were texture dense after hot isostatic pressing and no significant PPB defects were found.
Example 5
A hot isostatic pressing method for FGH4097 alloy powder comprises the following steps:
(7) preparing high-temperature alloy powder by using a plasma rotating electrode method, sieving to 50-150 mu m under the protection of argon, removing non-metallic impurities by electrostatic separation, packaging the powder in a sheath under a vacuum condition, and sealing and welding. The attached drawing in the abstract shows the morphology of high-temperature alloy powder prepared by the plasma rotating electrode.
(8) Placing the sealed and welded sheath into hot isostatic pressing equipment, and performing hot isostatic pressing in a way of simultaneously raising temperature and pressure, wherein the hot isostatic pressing temperature in the first step is 1205 ℃, the pressure is 100MPa, and the temperature is kept for 1 h;
(9) after the first step is finished, heating to 1260 ℃, and preserving the heat for 30min under the pressure of 100 MPa;
(7) and after the second step is finished, reducing the temperature to 960 ℃, keeping the temperature for 30min under the pressure of 100MPa, and then stopping heating and cooling to room temperature to obtain the nickel-based superalloy powder disc.
Example 3 FGH4097 powder disks produced using the process of the present invention were texture dense after hot isostatic pressing and no significant PPB defects were found.
According to the method, the hot isostatic pressing is carried out at 10-30 ℃ above the gamma' melting temperature by adjusting the parameters of the hot isostatic pressing process, the heat preservation time is less than or equal to 1h, and the pressure is more than or equal to 100 MPa. Or obtaining the disc blank with the density of more than or equal to 95 percent. The hot isostatic pressing time in the process is less than or equal to 1h to avoid abnormal growth of crystal grains. In the invention, the hot isostatic pressing is carried out at 50-100 ℃ below the liquidus temperature in the second step, the pressure is more than or equal to 100Pa, the heat preservation time is less than or equal to 30min, and the heat preservation is carried out at 50-100 ℃ below the liquidus temperature for 30min under high pressure, so that the coarse gamma' at the crystal boundary can be fully melted, thereby effectively inhibiting the formation of the original particle boundary, but the density of the disc part is reduced in the process, and the density of the disc part after the second step is about 90-95%. In the third step, the temperature is kept for 30min at the temperature of 10-20 ℃ below the melting temperature of the low-melting-point phase and under the pressure of more than or equal to 100MPa, so that the low-melting-point phase is fully solidified, and the density of the alloy is remarkably improved to more than 99.9%.
Claims (3)
1. A hot isostatic pressing forming method of a nickel-based superalloy powder disc is characterized by comprising the following steps:
step 1: preparing high-temperature alloy powder by using a plasma rotating electrode method, screening under the protection of argon, removing non-metallic impurities by electrostatic separation, packaging the powder in a sheath under a vacuum condition, and sealing and welding;
step 2: placing the sealed and welded sheath into hot isostatic pressing equipment, and performing hot isostatic pressing in a way of simultaneously raising temperature and pressure; the hot isostatic pressing temperature is 10-30 ℃ higher than the gamma' melting temperature, the hot isostatic pressing pressure is more than or equal to 100MPa, and the heat preservation time is less than or equal to 1 h;
step 3, after the step 1 is finished, heating the powder to 50-100 ℃ below the liquidus temperature, wherein the pressure is more than or equal to 100MPa, and the heat preservation time is 20-30 min;
and 4, after the step 2 is finished, cooling the powder to a temperature 10-20 ℃ lower than the melting temperature of the low-melting-point phase, keeping the temperature for 30-40 min under the pressure of more than or equal to 100MPa, and then stopping heating and cooling to room temperature to obtain the nickel-based superalloy powder disc.
2. The method for hot isostatic pressing of nickel-based superalloy powder disks according to claim 1, wherein in step 1, the superalloy powder is sieved to a particle size of 50-150 μm.
3. The method of claim 1, wherein in step 4, the melting temperature of the low-melting-point phase of the nickel-based alloy is (γ + γ') eutectic melting temperature.
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| CN111579323B (en) * | 2020-05-09 | 2022-11-01 | 中国航发北京航空材料研究院 | High-throughput preparation and test method of powder superalloy inclusion sample |
| CN113388726B (en) * | 2021-06-04 | 2022-07-12 | 中国航发北京航空材料研究院 | Automatic control device and method for solid solution-quenching heat treatment of powder high-temperature alloy disc |
| CN114210977B (en) * | 2022-02-23 | 2022-05-17 | 西安欧中材料科技有限公司 | Device and method for preparing fine-particle-size powder high-temperature alloy hot isostatic pressing part |
| CN114672680B (en) * | 2022-03-07 | 2023-04-07 | 中南大学 | Step-by-step hot isostatic pressing method for additive manufacturing of nickel-based high-temperature alloy |
| CN115846689B (en) * | 2022-11-15 | 2023-08-18 | 哈尔滨工业大学（威海） | Solution treatment method for melting GH3230 alloy by laser powder bed and GH3230 alloy |
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| 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 |
| CN105004587A (en) * | 2015-07-09 | 2015-10-28 | 中国航空工业集团公司北京航空材料研究院 | Preparation and test method of nickel-based high temperature alloy powder rapid melting and solidifying sample |
| 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 |
| CN109706346A (en) * | 2018-12-28 | 2019-05-03 | 西安欧中材料科技有限公司 | A kind of nickel base superalloy and the article formed by alloy |
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