CN115852281B - Heating process for GH4720Li alloy - Google Patents
Heating process for GH4720Li alloy Download PDFInfo
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- CN115852281B CN115852281B CN202211597771.4A CN202211597771A CN115852281B CN 115852281 B CN115852281 B CN 115852281B CN 202211597771 A CN202211597771 A CN 202211597771A CN 115852281 B CN115852281 B CN 115852281B
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- 238000010438 heat treatment Methods 0.000 title claims abstract description 124
- 239000000956 alloy Substances 0.000 title claims abstract description 123
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 123
- 238000005242 forging Methods 0.000 claims abstract description 78
- 238000003825 pressing Methods 0.000 claims abstract description 6
- 239000013078 crystal Substances 0.000 abstract description 14
- 238000013021 overheating Methods 0.000 abstract description 8
- 230000000630 rising effect Effects 0.000 abstract description 7
- 238000000034 method Methods 0.000 abstract description 6
- 238000004321 preservation Methods 0.000 description 19
- 238000005336 cracking Methods 0.000 description 11
- 238000001556 precipitation Methods 0.000 description 5
- 230000035882 stress Effects 0.000 description 5
- 238000010586 diagram Methods 0.000 description 4
- 238000010587 phase diagram Methods 0.000 description 4
- 101000912561 Bos taurus Fibrinogen gamma-B chain Proteins 0.000 description 3
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 3
- 239000010931 gold Substances 0.000 description 3
- 229910052737 gold Inorganic materials 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 230000008646 thermal stress Effects 0.000 description 3
- 238000009826 distribution Methods 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 230000001737 promoting effect Effects 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000001514 detection method Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 238000013508 migration Methods 0.000 description 1
- 230000005012 migration Effects 0.000 description 1
- 238000012544 monitoring process Methods 0.000 description 1
- 230000001360 synchronised effect Effects 0.000 description 1
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Abstract
The invention discloses a heating process for GH4720Li alloy, which comprises the following steps: raising the temperature of the resistance furnace to 780-820 ℃ with the temperature raising rate of 20-30 ℃/min; placing GH4720Li alloy blank into a resistance furnace, and preserving heat at 780-820 ℃ for 55-65 min; heating to 880-920 ℃, and preserving heat for 55-65 min at a heating rate of 3-4 ℃/min; heating to 980-1020 ℃, and heating up at a rate of 8-10 ℃/min; preserving heat for 15-25 min; continuously heating to 1140 ℃ with the heating rate of 12-15 ℃/min; preserving heat for 15-25 min; forging and pressing for the first time to obtain an intermediate forging; preserving the temperature of the middle forging at 1140 ℃ for 3-8 min; and performing the second forging. The invention has simple temperature rising process, and the whole crystal grains and gamma' phase of the forging are uniform and fine; compared with the prior art, the heating temperature is lower, and the phenomenon of overheating can not occur.
Description
Technical Field
The invention relates to the technical field of GH4720Li alloy heating. In particular to a heating process for GH4720Li alloy.
Background
The GH4720Li alloy is widely used in the field of aviation due to its high temperature strength and use temperature. In general, it is considered that the precipitation of two main fine crystal structures, i.e., primary γ 'phase and secondary γ' phase, has an important influence on the mechanical properties of GH4720Li alloy. Therefore, in the case of heat treatment of GH4720Li alloy, it is generally considered that the sample is not cracked during forging, while promoting precipitation of primary γ 'phase around grain boundary and secondary γ' phase in crystal and refining of crystal grains. For this reason, patent document CN109504927B provides a GH4720Li heating method that promotes precipitation of primary γ 'phase around grain boundaries and secondary γ' phase in the crystal and refines grains: a gradient heating process is adopted between 800 and 1180 ℃, wherein: the heating rate is less than or equal to 1.5 ℃/min when the temperature is less than 1070 ℃, and the heating rate is less than or equal to 0.5 ℃/min when the temperature is greater than or equal to 1070 ℃;
the specific process of patent document CN109504927B is as follows:
(1) Heating GH4720Li alloy to 850 ℃, heating up to 1.2 ℃/min, and then preserving heat for 40min;
(2) Continuously heating the GH4720Li alloy to 900 ℃, wherein the heating rate is 1.5 ℃/min, and then preserving heat for 20min;
(3) Continuously heating the GH4720Li alloy to 950 ℃, keeping the temperature rising rate at 1.5 ℃/min, and then keeping the temperature for 30min;
(4) Continuously heating the GH4720Li alloy to 1000 ℃, keeping the temperature at a heating rate of 1.2 ℃/min, and then keeping the temperature for 40min;
(5) Continuously heating the GH4720Li alloy to 1070 ℃, wherein the heating rate is less than or equal to 1.4 ℃/min, and then preserving heat for 50min;
(6) Continuously heating the GH4720Li alloy to 1080 ℃, keeping the temperature rise rate at 0.5 ℃/min, and then keeping the temperature for 10min;
(7) Continuously heating the GH4720Li alloy to 1090 ℃, keeping the temperature rising rate at 0.5 ℃/min, and then keeping the temperature for 10min;
(8) Continuously heating the GH4720Li alloy to 1100 ℃, wherein the heating rate is 0.5 ℃/min, and then preserving heat for 10min;
(9) Continuously heating GH4720Li alloy to 1110 ℃, wherein the heating rate is 0.5 ℃/min, and then preserving heat for 20min;
(10) Continuously heating the GH4720Li alloy to 1120 ℃, keeping the temperature at a heating rate of 0.5 ℃/min, and then keeping the temperature for 20min;
(11) Continuously heating the GH4720Li alloy to 1130 ℃, keeping the temperature at a heating rate of 0.5 ℃/min, and then preserving the heat for 20min;
(12) Continuously heating GH4720Li alloy to 1140 ℃, wherein the heating rate is 0.5 ℃/min, and then preserving heat for 20min;
(13) Continuously heating GH4720Li alloy to 1150 ℃, wherein the heating rate is 0.5 ℃/min, and then preserving heat for 20min;
(14) Continuously heating GH4720Li alloy to 1160 ℃, keeping the temperature at the heating rate of 0.5 ℃/min, and then preserving the heat for 20min;
(15) Continuously heating GH4720Li alloy to 1170 ℃, wherein the heating rate is 0.5 ℃/min, and then preserving heat for 20min;
(16) Continuously heating the GH4720Li alloy to 1180 ℃, wherein the heating rate is 0.5 ℃/min, and then preserving the heat for 30min.
Patent document CN109504927B adopts gradient heating, optimizes heating rate, heat preservation temperature, heat preservation step and heat preservation time, promotes precipitation of primary gamma 'phase around grain boundary and secondary gamma' phase in crystal and refines crystal grains, so that cracking does not occur in forging.
However, the technical solution of patent document CN109504927B has the following drawbacks: the heating temperature is higher, so that overheating and overburning are easy to occur, and the grains are excessively grown and large to influence the performance of the forging; the heating time is too long, the gradient heating operation is complicated, and the cost is high; only the forging part is organized, but the whole structure is not clear. Therefore, it is necessary to design a heating process for GH4720Li alloy, which can avoid the occurrence of the above defects while promoting the precipitation of primary gamma '-phase around grain boundary and secondary gamma' -phase in grain boundary and refining grains, and at the same time avoid the phenomenon that forgings are easily cracked during forging.
Disclosure of Invention
Therefore, the technical problem to be solved by the invention is to provide a heating process for GH4720Li alloy, so as to solve the problems of overheating and overburning phenomena caused by overhigh heating temperature, overlong heating time and the like in the existing heating process, easiness in cracking in the forging process of a forging piece and the like.
In order to solve the technical problems, the invention provides the following technical scheme:
a heating process for a GH4720Li alloy, comprising the steps of:
step (1), heating the resistance furnace to 780-820 ℃ from room temperature, wherein the heating rate is 20-30 ℃/min;
step (2), placing GH4720Li alloy blank into a resistance furnace, and preserving heat for 55-65 min at 780-820 ℃;
continuously heating the GH4720Li alloy blank to 880-920 ℃ at a heating rate of 3-4 ℃/min; then preserving heat for 55-65 min;
continuously heating the GH4720Li alloy blank to 980-1020 ℃ at a heating rate of 8-10 ℃/min; then preserving heat for 15-25 min;
transferring the GH4720Li alloy blank into a gas furnace, and continuously heating the GH4720Li alloy blank to 1140 ℃ at a heating rate of 12-15 ℃/min; then preserving heat for 15-25 min;
step (6), forging the GH4720Li alloy blank for the first time, wherein the deformation is 45-55%, and obtaining a GH4720Li alloy intermediate forging;
step (7), placing the GH4720Li alloy intermediate forging back into a gas furnace, and continuously preserving heat for 3-8 min at 1140 ℃;
and (8) forging the GH4720Li alloy intermediate forging for the second time until the deformation reaches 70-80%, and heating the GH4720Li alloy to obtain the GH4720Li alloy forging.
The heating process for GH4720Li alloy comprises the steps of (1) heating a resistance furnace from room temperature to 800 ℃ for 30min.
The heating process for the GH4720Li alloy comprises the steps of (2) placing a GH4720Li alloy blank into a resistance furnace, and preserving heat at 800 ℃ for 60min.
The heating process for the GH4720Li alloy comprises the following steps of (3) continuously heating a GH4720Li alloy blank to 900 ℃ with the temperature rising rate of 3.5 ℃/min; then the temperature is kept for 60min.
The heating process for the GH4720Li alloy comprises the following steps of (4) continuously heating a GH4720Li alloy blank to 1000 ℃ with the heating rate of 10 ℃/min; then the temperature is kept for 20min.
Transferring the GH4720Li alloy blank into a gas furnace, and continuously heating the GH4720Li alloy blank to 1140 ℃ at a heating rate of 14 ℃/min; then the temperature is kept for 20min.
The heating process for GH4720Li alloy comprises the following steps of (6) forging and pressing a GH4720Li alloy blank for the first time, wherein the deformation is 50%; obtaining the GH4720Li alloy intermediate forging.
And (3) the heating process for the GH4720Li alloy, namely, in the step (7), placing the GH4720Li alloy intermediate forging back into a gas furnace, and keeping the temperature at 1140 ℃ for 5min.
And (3) performing second forging and pressing on the GH4720Li alloy intermediate forging until the deformation of the GH4720Li alloy intermediate forging is 80%, thereby obtaining the GH4720Li alloy forging.
The heating process for GH4720Li alloy comprises the following steps of (1) heating a resistance furnace from room temperature to 800 ℃ at a heating rate of 30 ℃/min; the slower heating rate can cause the excessively long consumption time of the production process, and the excessively fast heating rate can cause the fact that the actual temperature in the hearth is not synchronous with the heating rate, so that the uniformity of the temperature in the resistance furnace is poor;
step (2), placing GH4720Li alloy blank into a resistance furnace, and preserving heat at 800 ℃ for 60min; because the GH4720Li alloy billet has low-temperature cold brittleness in an environment with relatively low temperature, the GH4720Li alloy billet is prevented from being changed from a ductile state to a brittle state; however, if the GH4720Li alloy blank is put in when the temperature of the hearth is too high, the core and the surface of the GH4720Li alloy blank have large temperature difference to generate large thermal stress so as to generate deformation or cracking; according to the invention, the GH4720Li alloy blank is placed in the hearth at 800 ℃, so that the phenomena of low-temperature cold embrittlement and deformation cracking can be effectively avoided; the GH4720Li alloy blank can be fully heated after heat preservation for 60min, if the heat preservation time is too long, overheating or overburning is easy to cause, crystal grains grow up, and the performance is reduced; however, if the heat preservation time is too short, a blank which is not transparent to heat can appear, so that the GH4720Li alloy blank is too large in stress and difficult to deform;
continuously heating the GH4720Li alloy blank to 900 ℃ at a heating rate of 3.5 ℃/min; then preserving the temperature for 60min; during the heating up period of 800-900 ℃, if the heating up rate is lower than 3.5 ℃/min, the average grain size can grow up, and the heating up is too slow, so that the time cost is too high; if the temperature rising rate is higher than 3.5 ℃/min, the temperature difference between the surface and the core of the GH4720Li alloy blank is possibly overlarge, and the temperature on the dial does not accord with the actual temperature in the hearth; the main purpose of heat preservation at 900 ℃ is to ensure that the temperature of the surface and the core part of the GH4720Li alloy blank is consistent with that of a dial plate, and prevent the core part from deforming and cracking due to the fact that the core part does not reach the target temperature; if the temperature keeping time is too short at 900 ℃, the temperature of the GH4720Li alloy blank surface and the temperature of the core part are different and are inconsistent with the temperature of the dial; the long heat preservation time causes grain growth and overheat phenomenon, and the performance of GH4720Li alloy blank is reduced;
continuously heating the GH4720Li alloy blank to 1000 ℃ at a heating rate of 10 ℃/min; then preserving heat for 20min; a heating rate of less than 10 ℃/min may lead to an average grain size growth, and too slow a heating results in excessive time costs; the temperature rising rate higher than 10 ℃/min may cause inconsistent surface and core temperature, the precipitated phase cannot be fully dissolved in solid, and the temperature on the dial does not accord with the actual temperature in the hearth; 1. the heat preservation at 1000 ℃ mainly ensures that the temperature of the surface of the workpiece and the temperature of the core part are consistent with the dial plate, and prevents the core part from deforming and cracking caused by the fact that the core part does not reach the target temperature; the thermal conductivity of the GH4720Li alloy blank at 1000 ℃ is close to three times of the thermal conductivity of the initial heating temperature, so that the required heat preservation time is shorter than that before 1000 ℃, if the heat preservation time is too short at 1000 ℃, the temperature of the surface of the GH4720Li alloy blank and the temperature of the core part are different, the temperature of the GH4720Li alloy blank is inconsistent with the temperature of a dial, a precipitated phase cannot be fully dissolved in a solid, thermal stress is generated, and the final forging is cracked; the long heat preservation time causes grain growth and overheat phenomenon, and the performance of GH4720Li alloy blank is reduced;
transferring the GH4720Li alloy blank into a gas furnace, and continuously heating the GH4720Li alloy blank to 1140 ℃ at a heating rate of 14 ℃/min; then preserving heat for 20min; the heating rate of less than 14 ℃/min may lead to the growth of average grain size, and too slow heating causes excessive time cost; the temperature rising rate higher than 14 ℃/min can cause inconsistent surface and core temperature of GH4720Li alloy billets, and the temperature on the dial does not accord with the actual temperature in the hearth; the temperature is kept for 20min at 1140 ℃ to ensure that the temperature of the surface and the core of the GH4720Li alloy blank is consistent with that of a dial plate, and deformation and cracking caused by the core not reaching the target temperature are prevented; if the initial forging temperature is lower than 1140 ℃, the precipitated phase cannot be fully dissolved; the initial forging temperature is higher than 1140 ℃ and the phenomena of overheating and overburning occur. If the heat preservation time is too short at 1140 ℃, the temperature of the surface and the core part of the GH4720Li alloy blank is inconsistent with the temperature of the dial, the precipitated phase cannot be fully dissolved, thermal stress is generated, and the final forging is cracked; the long heat preservation time causes grain growth and overheat phenomenon, and the performance of GH4720Li alloy blank is reduced;
step (6), forging and pressing the GH4720Li alloy blank for the first time, wherein the deformation is 50%; obtaining GH4720Li alloy intermediate forging; if the deformation of the first forging is less than 50%, the crystal grains cannot be fully broken, and if the deformation is more than 50%, the stress is overlarge, and the phenomenon of workpiece cracking can occur;
step (7), placing the GH4720Li alloy intermediate forging back into a gas furnace, and continuously preserving heat for 5min at 1140 ℃; the purpose of heat preservation for 5min by a furnace return is that the deformation temperature interval of the material is narrower, the temperature of a workpiece is reduced below the deformation temperature interval in a free forging environment, the stress is overlarge, if the furnace return is not used for heat preservation, cracking is easy to occur, if the heat preservation time is less than 5min, the workpiece cannot be fully heated, and if the heat preservation time is more than 5min, the grain is easy to grow; the initial forging temperature is lower than 1140 ℃, and the precipitated phase cannot be fully dissolved; the initial forging temperature is higher than 1140 ℃ and the phenomena of overheating and overburning occur; the heat preservation at 1140 ℃ for 5min can avoid the problems;
and (8) forging the GH4720Li alloy intermediate forging for the second time until the deformation is 80%, and obtaining the GH4720Li alloy forging. If the deformation after the second forging is less than 80%, the grains cannot be fully refined, the performance cannot meet the use requirement, and if the deformation is more than 80%, the stress is overlarge, and the edge of the workpiece is possibly cracked; if the temperature is kept without returning to the furnace, the deformation is directly forged and pressed once to 80%, the surface temperature of the workpiece in the free forging environment can be reduced too fast, the difference between the core part and the surface temperature of the workpiece is large, and the stress is too large, so that the cracking phenomenon is caused.
The technical scheme of the invention has the following beneficial technical effects:
the GH4720Li alloy forging obtained by the heating process has uniform and fine overall crystal grains and gamma' -phase, and does not crack in the forging process. The gradient heating process in the heating process is simple, the heating temperature is lower than that in the prior art, the phenomena of overheating and overheating are avoided, and the structure uniformity and the performance are good; the heating process has short heating time and greatly reduces the cost; the operation is simple, and the feasibility is strong.
Drawings
FIG. 1 is a schematic diagram of a gradient heating process for GH4720Li alloy in an embodiment of the invention;
FIG. 2 is a physical diagram of a GH4720Li alloy forging prepared in an embodiment of the invention;
FIG. 3 is a graph of cross-section detection and plot of GH4720Li alloy forgings prepared in an embodiment of the invention;
FIG. 4 is a golden phase diagram of the edge of a GH4720Li alloy forging prepared in an embodiment of the invention;
FIG. 5 is a core gold phase diagram of a GH4720Li alloy forging prepared in an embodiment of the invention;
FIG. 6 is a gold phase diagram of a GH4720Li alloy forging diameter quarter made in an embodiment of the invention;
FIG. 7 is a scanning image of a gamma prime phase electron microscope of the edge of a GH4720Li alloy forging prepared in an embodiment of the invention;
FIG. 8 is a scanning image of a gamma prime phase electron microscope of a core of a GH4720Li alloy forging prepared in an embodiment of the invention;
FIG. 9 is a gamma prime electron microscope scan of a GH4720Li alloy forging prepared in the example of the invention at one quarter of the diameter.
Detailed Description
As shown in fig. 1, the heating process for the GH4720Li alloy of the present embodiment includes the steps of:
step (1), heating the resistance furnace from room temperature to 800 ℃ for 30min;
step (2), placing GH4720Li alloy blank into a resistance furnace, and preserving heat at 800 ℃ for 60min;
continuously heating the GH4720Li alloy blank to 900 ℃ at a heating rate of 3.5 ℃/min; then preserving the temperature for 60min;
continuously heating the GH4720Li alloy blank to 1000 ℃ at a heating rate of 10 ℃/min; then preserving heat for 20min;
transferring the GH4720Li alloy blank into a gas furnace, and continuously heating the GH4720Li alloy blank to 1140 ℃ at a heating rate of 14 ℃/min; then preserving heat for 20min;
step (6), forging and pressing the GH4720Li alloy blank for the first time, wherein the deformation is 50%; obtaining GH4720Li alloy intermediate forging;
step (7), placing the GH4720Li alloy intermediate forging back into a gas furnace, and continuously preserving heat for 5min at 1140 ℃;
and (8) forging the GH4720Li alloy intermediate forging for the second time until the deformation is 80%, and obtaining the GH4720Li alloy forging.
The GH4720Li alloy forging prepared by the embodiment is shown in a physical diagram in fig. 2, and monitoring points are taken according to the diagram in fig. 3 to detect the GH4720Li alloy forging. FIGS. 4 to 6 are gold phase diagrams of the GH4720Li alloy forging edge, core, and diameter quarter, respectively, prepared in this example; as can be seen from fig. 2, the surface of the forging prepared by the embodiment is uniform and smooth, and the phenomenon that the forging cracks due to uneven internal and external temperature distribution is effectively avoided. Under the secondary free forging hammer, the forging can bear 80% of large deformation without cracking. Under the condition of ensuring that the material is not damaged, the heating process can lead the deformation of the forging to reach 80 percent. From the alloy forging edge, core and diameter quarter of fig. 4-6, it can be seen that the grains at each part of the forging are fine and uniform, the average grain size is below 10 μm and the twinning phenomenon occurs. The heating process ensures that the internal and external temperature distribution of the forging is more uniform, can effectively avoid the phenomenon of grain growth caused by overhigh external temperature, and greatly improves the yield of the material.
FIGS. 7 to 9 are respectively scanning images of the GH4720Li alloy forging edge, core and diameter quarter of gamma prime phase electron microscope; as can be seen from fig. 7 to 9, the primary gamma 'phase and the secondary gamma' phase of the forging at each location are uniformly distributed, the primary gamma 'phase is mainly distributed on the grain boundary, and the secondary gamma' phase is mainly distributed in the grain. The large amount of primary gamma' phases can effectively inhibit the bow of the original crystal boundary and the crystal boundary migration process of recrystallized crystal grains, so that the crystal grain size of each part of the forging sample is fine and the structure is stable under the heating process.
It is apparent that the above examples are given by way of illustration only and are not limiting of the embodiments. Other variations or modifications of the above teachings will be apparent to those of ordinary skill in the art. It is not necessary here nor is it exhaustive of all embodiments. While the obvious variations or modifications which are extended therefrom remain within the scope of the claims of this patent application.
Claims (1)
1. A heating process for a GH4720Li alloy, comprising the steps of:
step (1), heating the resistance furnace from room temperature to 800 ℃ for 30min;
step (2), placing GH4720Li alloy blank into a resistance furnace, and preserving heat at 800 ℃ for 60min;
continuously heating the GH4720Li alloy blank to 900 ℃ at a heating rate of 3.5 ℃/min; then preserving the temperature for 60min;
continuously heating the GH4720Li alloy blank to 1000 ℃ at a heating rate of 10 ℃/min; then preserving heat for 20min;
transferring the GH4720Li alloy blank into a gas furnace, and continuously heating the GH4720Li alloy blank to 1140 ℃ at a heating rate of 14 ℃/min; then preserving heat for 20min;
step (6), forging and pressing the GH4720Li alloy blank for the first time, wherein the deformation is 50%; obtaining GH4720Li alloy intermediate forging;
step (7), placing the GH4720Li alloy intermediate forging back into a gas furnace, and continuously preserving heat for 5min at 1140 ℃;
and (8) forging the GH4720Li alloy intermediate forging for the second time until the deformation is 80%, and obtaining the GH4720Li alloy forging.
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| CN109504927A (en) * | 2018-12-17 | 2019-03-22 | 内蒙古工业大学 | A γ ' phase is precipitated and refines the GH4720Li heating means of crystal grain with transgranular secondary γ ' phase around promotion crystal boundary |
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| CN113235030A (en) * | 2021-05-20 | 2021-08-10 | 西安聚能高温合金材料科技有限公司 | Preparation method of large-size GH4169 high-temperature alloy bar |
| CN113564504A (en) * | 2021-07-14 | 2021-10-29 | 北京科技大学 | Heat treatment process for carrying out rapid aging on large-size GH4738 alloy forging |
| CN113560481A (en) * | 2021-07-30 | 2021-10-29 | 内蒙古工业大学 | Hot working process of GH4738 nickel-based high-temperature alloy |
| CN113604760A (en) * | 2021-07-14 | 2021-11-05 | 北京科技大学 | Method for improving strength stability of GH4738 alloy forging subjected to sub-solid solution treatment |
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2022
- 2022-12-12 CN CN202211597771.4A patent/CN115852281B/en active Active
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109504927A (en) * | 2018-12-17 | 2019-03-22 | 内蒙古工业大学 | A γ ' phase is precipitated and refines the GH4720Li heating means of crystal grain with transgranular secondary γ ' phase around promotion crystal boundary |
| CN112746231A (en) * | 2020-12-29 | 2021-05-04 | 北京钢研高纳科技股份有限公司 | Production process for gamma' phase pre-conditioning plasticization of high-performance high-temperature alloy |
| CN112893722A (en) * | 2021-01-15 | 2021-06-04 | 中国第二重型机械集团德阳万航模锻有限责任公司 | Rapid forming method for GH4720Li high-temperature alloy forging |
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| CN113564504A (en) * | 2021-07-14 | 2021-10-29 | 北京科技大学 | Heat treatment process for carrying out rapid aging on large-size GH4738 alloy forging |
| CN113604760A (en) * | 2021-07-14 | 2021-11-05 | 北京科技大学 | Method for improving strength stability of GH4738 alloy forging subjected to sub-solid solution treatment |
| CN113560481A (en) * | 2021-07-30 | 2021-10-29 | 内蒙古工业大学 | Hot working process of GH4738 nickel-based high-temperature alloy |
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| CN115852281A (en) | 2023-03-28 |
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