CN115011768A - Toughening heat treatment process capable of eliminating medium-temperature brittleness of high-temperature alloy - Google Patents
Toughening heat treatment process capable of eliminating medium-temperature brittleness of high-temperature alloy Download PDFInfo
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Abstract
The invention discloses a strengthening and toughening heat treatment process capable of eliminating medium-temperature brittleness of high-temperature alloy, which comprises the following steps of: keeping the temperature of 0-350 ℃ above the complete dissolution temperature of the high-temperature alloy precipitated phase gamma' in the crystal for 0.5-10 h, and then cooling to room temperature through a high-temperature cooling stage and a low-temperature cooling stage; and (3) high-temperature cooling stage: cooling from the gamma' precipitation starting temperature to a temperature 1-200 ℃ below the precipitation starting temperature of an intra-crystal precipitated phase, wherein the average cooling rate is 0.1-20 ℃/min; a low-temperature cooling stage: the average cooling rate is not lower than 2 ℃/min before cooling to the gamma' precipitation termination temperature from the end of the high-temperature cooling stage. After the strengthening and toughening treatment, the alloy strength and the alloy strength in a peak aging state reach the same level, and no obvious plasticity reduction phenomenon exists in a warm brittle zone, and compared with the traditional heat treatment process, the elongation of the alloy in the warm brittle zone is improved by more than 50%.
Description
Technical Field
The invention belongs to the technical field of metal heat treatment, and particularly relates to a strengthening and toughening heat treatment process capable of eliminating medium-temperature brittleness of high-temperature alloy.
Background
The high-temperature alloy is widely applied to a plurality of fields such as energy, chemical engineering, aerospace and the like due to excellent high-temperature strength performance, but the phenomenon that the plasticity of the high-temperature alloy is obviously reduced in a middle-temperature area becomes an important factor restricting the engineering popularization of the high-temperature alloy. A large number of researches show that the brittleness of the high-temperature alloy is increased sharply within the range of 500-900 ℃, and when the high-temperature alloy is used as a high-temperature pressure-bearing component, the early failure of the component can be caused, so that great potential safety hazard is formed on the service of equipment.
Previous studies have demonstrated that medium temperature brittleness of superalloys generally results from the initial stages of service. The mechanism of formation of medium temperature brittleness is still controversial at present, but is generally considered to be related to the microstructure of grain or phase boundaries. Reasonably regulating and controlling the interface strength and inhibiting the crack initiation and propagation are one of the key research technical fields of the development and popularization of high-temperature alloys.
Disclosure of Invention
In order to overcome the problems in the prior art, the invention aims to provide a strengthening and toughening heat treatment process capable of eliminating medium-temperature brittleness of high-temperature alloy.
In order to achieve the above purpose, the invention adopts the technical scheme that:
a strengthening and toughening heat treatment process capable of eliminating medium-temperature brittleness of high-temperature alloy is characterized in that the temperature of a high-temperature alloy precipitated phase gamma' in crystal is kept for 0.5 to 10 hours at 0 to 350 ℃ above the complete dissolution temperature, and then the high-temperature alloy is cooled to room temperature through a high-temperature cooling stage and a low-temperature cooling stage; wherein, the first and the second end of the pipe are connected with each other,
and (3) high-temperature cooling stage: cooling from the precipitation starting temperature of the intragranular precipitated phase gamma 'to a temperature 1-200 ℃ below the precipitation starting temperature of the intragranular precipitated phase gamma', wherein the average cooling rate is 0.1-20 ℃/min;
a low-temperature cooling stage: the average cooling rate is not lower than 2 ℃/min before cooling to the gamma' precipitation termination temperature from the end of the high-temperature cooling stage.
Further, the intragranular precipitated phase gamma' in the superalloy has L1 2 The structure conforms to the A3B type atomic ratio, wherein, the A element is Ni, Fe, Co or Mn, and the B element is Al, Ti, Nb, Ta, W, Mo, Zr or Hf.
Furthermore, during heat preservation, if the temperature is lower than the nucleation temperature of the crystal boundary precipitation phase, the heat preservation time is not more than 5 h.
Further, when the cooling rate in the high-temperature cooling stage is not constant, the instantaneous cooling rate at any moment is not lower than 0.01 ℃/min.
Further, after the high-temperature cooling stage is finished, an intragranular precipitated phase gamma' exists in the alloy crystal grain, the average size of the intragranular precipitated phase is not less than 20nm, and the volume fraction is not less than 5%.
Further, when the cooling rate in the low-temperature cooling stage is not constant, the instantaneous cooling rate at any time is not lower than 0.1 ℃/min.
Further, after the high-temperature cooling stage is finished, the intragranular precipitated phase gamma ' in the alloy crystal is in bimodal distribution, wherein particles with the average diameter not less than 30nm are gamma ' particles with a larger size, particles with the average diameter not more than 20nm are gamma ' particles with a smaller size, and the average diameter ratio of the gamma ' particles with the larger size to the gamma ' particles with the smaller size is not less than 5 times.
Further, after the low-temperature cooling stage is finished, heat preservation is carried out for 0-150 h, and then cooling is carried out to the room temperature.
Further, after the low-temperature cooling stage is finished, cooling to room temperature by adopting a water cooling, air cooling, oil cooling or furnace cooling mode.
Compared with the prior art, the invention has the following beneficial effects:
the strengthening and toughening heat treatment process of the invention does not need to be carried out in a gamma 'phase (gamma' meets L1) 2 Structure, preferably Ni 3 Al、Ni 3 (Al, Ti) and the like are intragranular precipitated phases) is subjected to aging heat preservation, but a part of the gamma ' phase is rapidly nucleated and grown to an optimal size by controlling the cooling rate, and a large amount of the gamma ' phase with fine size is precipitated at the periphery of the gamma ' phase. After the heat treatment of the alloy is finished, the volume fraction of the gamma ' phase in the crystal is not less than 10 percent, and the gamma ' phase is in bimodal distribution, wherein the average diameter of gamma ' particles with larger size is not less than 30nm, the average diameter of gamma ' particles with smaller size is not more than 20nm, the average diameter ratio of gamma ' particles with larger size and smaller size is not less than 5 times, and the gamma ' particles with larger size occupy the whole gamma ' phase in the crystalThe integral percentage is not less than 30 percent. After the strengthening and toughening treatment, the alloy strength and the peak aging state alloy strength reach the same level, and no obvious plasticity reduction phenomenon exists in the warm brittle zone, and compared with the traditional heat treatment process (aging heat preservation is carried out in a gamma' phase precipitation temperature range after solution treatment), the tensile elongation of the alloy in the warm brittle zone is improved by more than 50%. The high-temperature alloy treated by the strengthening and toughening process of the invention does not generate medium-temperature brittleness after further aging treatment in a medium-temperature zone.
Drawings
FIG. 1 is a morphology of an intragranular precipitated phase in example 1.
FIG. 2 is a tensile fracture morphology at 700 ℃ for example 1.
FIG. 3 is a diagram showing the morphology of the intergranular precipitate phase in comparative example 1.
FIG. 4 is a tensile fracture morphology at 700 ℃ of comparative example 1.
Detailed Description
The invention is described in further detail below with reference to the accompanying drawings:
a strengthening and toughening heat treatment process capable of eliminating medium-temperature brittleness of high-temperature alloy comprises the following steps: keeping the temperature of 0-350 ℃ above the complete dissolution temperature of the precipitated phase gamma' of the alloy in the crystal for 0.5-10 h, and then cooling to room temperature through a high-temperature cooling stage and a low-temperature cooling stage; wherein the content of the first and second substances,
and (3) high-temperature cooling stage: before cooling from the gamma 'precipitation starting temperature to the temperature 1-200 ℃ below the gamma' precipitation starting temperature, the average cooling rate of the alloy meets 0.1-20 ℃/min;
a low-temperature cooling stage: and before cooling to the gamma' precipitation termination temperature from the end of the high-temperature cooling stage, the average cooling rate of the alloy is not lower than 2 ℃/min.
The intragranular precipitated phase gamma' in the high-temperature alloy has L1 2 The structure accords with A3B type atomic ratio, wherein, the A element is Ni, Fe, Co or Mn, the B element is Al, Ti, Nb, Ta, W, Mo, Zr or Hf;
and during heat preservation, if the temperature is lower than the nucleation temperature of the crystal boundary precipitation phase, the heat preservation time is not more than 5 h.
When the cooling rate in the high-temperature cooling stage is not constant, the instantaneous cooling rate at any moment is not lower than 0.01 ℃/min.
After the high-temperature cooling stage is finished, an intragranular precipitated phase gamma' exists in the alloy crystal grain, the average size of the intragranular precipitated phase is not less than 20nm, and the volume fraction is not less than 5%.
When the cooling rate in the low-temperature cooling stage is not constant, the instantaneous cooling rate at any one time is not lower than 0.1 ℃/min.
And after the high-temperature cooling stage is finished, the intragranular precipitated phase gamma ' of the alloy is in bimodal distribution, wherein the particles with the average diameter of not less than 30nm are gamma ' particles with larger size, the particles with the average diameter of not more than 20nm are gamma ' particles with smaller size, and the average diameter ratio of the gamma ' particles with larger size to the gamma ' particles with smaller size is not less than 5 times.
And after the low-temperature cooling stage is finished, carrying out heat preservation for 0-150 h, and then cooling to room temperature.
And after the low-temperature cooling stage is finished, cooling to room temperature by adopting a water cooling, air cooling, oil cooling or furnace cooling mode.
The following are specific examples.
Example 1
The alloy comprises the following components in parts by weight: ZL201911296733.3, name: the high strength and high toughness antioxidant Fe-Ni-base high temperature alloy is prepared through vacuum consumable smelting and forging. The alloy is a precipitation strengthening type deformation high-temperature alloy, and the actually measured components after the preparation are measured according to the mass percentage and comprise C: 0.05%, Cr: 16%, Mn: 0.1%, Si: 0.025%, W: 0.3%, Mo: 0.6%, Ti: 1.8%, Al: 1.6%, B: 0.002%, Co: 1.0%, Fe: 40 percent and the balance of Ni, the precipitation starting temperature and the precipitation ending temperature of gamma' in the alloy are 875 ℃ and 580 ℃ respectively, the precipitation temperature of a grain boundary precipitation phase is 1020 ℃, and the heat treatment process is as follows:
keeping the temperature of the alloy at 1080 ℃ for 60min after the temperature of the alloy is raised along with the furnace, continuously cooling the alloy to 1000 ℃ at the average cooling rate of 4 ℃/min, keeping the temperature for 60min, continuously cooling to 875 ℃ at the average cooling rate of 4 ℃/min, and continuously cooling to 800 ℃ at the average cooling rate of 0.6 ℃/min; then the alloy is continuously cooled to 550 ℃ at the average cooling rate of 2 ℃/min; and finally, cooling to room temperature along with the furnace.
Example 2
The alloy comprises the following components in parts by weight: ZL202010383732.9, name: the high-strength high-temperature alloy for thermal power generating unit and its production process are characterized by that its preparation process adopts vacuum self-consumption smelting and forging forming process. The alloy is a precipitation strengthening type deformation high-temperature alloy, and the actually measured components after the preparation are measured according to the mass percentage and comprise C: 0.06%, Cr: 16%, Mn: 0.2%, Si: 0.15%, W: 1.6%, Mo: 1.2%, Ti: 2.2%, Al: 1.4%, B: 0.002%, Zr: 0.02%, Fe: 37 percent and the balance of Ni, wherein the precipitation starting temperature and the precipitation ending temperature of gamma' in the alloy are 890 ℃ and 610 ℃ respectively, the precipitation temperature of a grain boundary precipitation phase is 1030 ℃, and the heat treatment process is adopted as follows:
after the temperature of the alloy is raised along with the furnace, the temperature is kept at 1080 ℃ for 90min, the alloy is continuously cooled to 890 ℃ at the average cooling rate of 30 ℃/min, and is continuously cooled to 800 ℃ at the average cooling rate of 5 ℃/min; and then continuously cooling the alloy to 610 ℃ at the average cooling rate of 6 ℃/min, cooling the alloy to 600 ℃ along with the furnace after the alloy is cooled, preserving the heat for 24 hours, and finally cooling the alloy to room temperature by water.
Example 3
The alloy comprises the following components in parts by weight: ZL201910515309.7, name: the components of the low-chromium corrosion-resistant high-strength polycrystalline high-temperature alloy and the preparation method thereof are patented, and the preparation process adopts a hot-pressing sintering process for molding. The alloy is a solid solution and precipitation composite strengthening type powder metallurgy high-temperature alloy, and the actually measured components after the preparation are measured according to the mass percentage and comprise Cr: 17%, Co: 20%, Ti: 1.5%, Al: 4.0%, W: 7.0%, Si: 0.5%, Mn: 0.5%, Nb: 1.0%, C: 0.04 percent and the balance of Ni, the precipitation starting temperature and the precipitation stopping temperature of gamma' in the alloy are 1050 ℃ and 680 ℃ respectively, and the heat treatment process is as follows:
after the temperature of the alloy is raised along with the furnace, the temperature is kept at 1180 ℃ for 120min, the temperature is continuously reduced to 1050 ℃ at the average cooling rate of 20 ℃/min, and the temperature is continuously reduced to 950 ℃ at the average cooling rate of 10 ℃/min; then, the temperature is continuously reduced to 680 ℃ at the average cooling rate of 30 ℃/min, and the furnace is cooled to the room temperature after the temperature is completely reduced.
Example 4
The alloy components adopt the following patent numbers: ZL201910515324.1, name: the precipitation strengthening nickel-base high-chromium high-temperature alloy and its preparation process include vacuum smelting and casting. The alloy is a precipitation strengthening type casting high-temperature alloy, and the actually measured components after the preparation are measured according to the mass percentage and comprise Cr: 28%, Co: 15%, Ti: 2.5%, Al: 1.5%, W: 1.5%, Si: 0.5%, Mn: 0.5%, Nb: 0.5%, C: 0.04%, Fe: 0.5 percent, the balance being Ni, the precipitation starting temperature and the precipitation stopping temperature of gamma' in the alloy are 950 ℃ and 650 ℃ respectively, and the heat treatment process is as follows:
1) keeping the temperature of the alloy at 1150 ℃ for 120min after the temperature of the alloy is raised along with the furnace, continuously cooling to 1020 ℃ at the average cooling rate of 20 ℃/min after the temperature is raised, keeping the temperature for 4h, continuously cooling to 950 ℃ at the average cooling rate of 10 ℃/min, and finally continuously cooling to 850 ℃ at the average cooling rate of 5 ℃/min; then the temperature is continuously reduced to 650 ℃ at the average cooling rate of 30 ℃/min, and finally the water is cooled to the room temperature.
Example 5
The high-temperature alloy comprises the following components in patent number: ZL201910515324.1, name: the components in the patent of a precipitation strengthening type nickel-based high-chromium high-temperature alloy and a preparation method thereof adopt a casting molding process after vacuum smelting. The alloy is a precipitation strengthening type casting high-temperature alloy, and the actually measured components after the preparation are measured according to the mass percentage and comprise Cr: 28%, Co: 15%, Ti: 2.5%, Al: 1.5%, W: 1.5%, Si: 0.5%, Mn: 0.5%, Nb: 0.5%, C: 0.04%, Fe: 0.5 percent, the balance being Ni, the precipitation starting temperature and the precipitation stopping temperature of gamma' in the alloy are 950 ℃ and 650 ℃ respectively, and the heat treatment process is as follows:
1) and (3) a heat preservation stage: keeping the temperature of the alloy at 950 ℃ for 5h after the temperature of the alloy is raised along with the furnace, and starting cooling after the temperature is raised;
2) and (3) high-temperature stage: continuously cooling the alloy to 949 ℃ at an average cooling rate of 0.1 ℃/min, then preserving heat for 4h, continuously cooling to 900 ℃ at an average cooling rate of 10 ℃/min, and finally continuously cooling to 850 ℃ at an average cooling rate of 5 ℃/min;
3) a medium temperature stage: the alloy is continuously cooled to 650 ℃ at the average cooling rate of 2 ℃/min;
4) and (3) low-temperature stage: then furnace cooling to room temperature.
Example 6
The high-temperature alloy comprises the following components in patent number: ZL201910515324.1, name: the precipitation strengthening nickel-base high-chromium high-temperature alloy and its preparation process include vacuum smelting and casting. The alloy is a precipitation strengthening type casting high-temperature alloy, and the actually measured components after the preparation are measured according to the mass percentage and comprise Cr: 28%, Co: 15%, Ti: 2.5%, Al: 1.5%, W: 1.5%, Si: 0.5%, Mn: 0.5%, Nb: 0.5%, C: 0.04%, Fe: 0.5 percent, the balance being Ni, the precipitation starting temperature and the precipitation stopping temperature of gamma' in the alloy are 950 ℃ and 650 ℃ respectively, and the heat treatment process is as follows:
1) and (3) a heat preservation stage: keeping the temperature of the alloy at 1300 ℃ for 10h after the temperature of the alloy is raised along with the furnace, and starting cooling after the temperature is raised;
2) and (3) high-temperature stage: the alloy is continuously cooled to 949 ℃ at the average cooling rate of 10 ℃/min;
3) a medium temperature stage: the alloy is continuously cooled to 500 ℃ at the average cooling rate of 10 ℃/min;
4) and (3) low-temperature stage: then air-cooled to room temperature.
Example 7
The high-temperature alloy comprises the following components in patent number: ZL201910515324.1, name: the precipitation strengthening nickel-base high-chromium high-temperature alloy and its preparation process include vacuum smelting and casting. The alloy is a precipitation strengthening type casting high-temperature alloy, and the actually measured components after the preparation are measured according to the mass percentage and comprise Cr: 28%, Co: 15%, Ti: 2.5%, Al: 1.5%, W: 1.5%, Si: 0.5%, Mn: 0.5%, Nb: 0.5%, C: 0.04%, Fe: 0.5 percent, the balance being Ni, the precipitation starting temperature and the precipitation stopping temperature of gamma' in the alloy are 950 ℃ and 650 ℃ respectively, and the heat treatment process is as follows:
1) and (3) a heat preservation stage: keeping the temperature of the alloy at 1250 ℃ for 30min after the temperature of the alloy is raised along with the furnace, and starting cooling after the temperature is raised;
2) and (3) high-temperature stage: continuously cooling the alloy to 1020 ℃ at an average cooling rate of 30 ℃/min, then preserving heat for 4h, continuously cooling to 950 ℃ at an average cooling rate of 20 ℃/min, and finally continuously cooling to 750 ℃ at an average cooling rate of 10 ℃/min;
3) a medium temperature stage: the alloy is continuously cooled to 700 ℃ at the average cooling rate of 20 ℃/min;
4) a low-temperature stage: the oil was then cooled to room temperature.
Comparative example 1
The alloy comprises the following components in parts by weight: ZL201911296733.3, name: the high strength and high toughness antioxidant Fe-Ni-base high temperature alloy is prepared through vacuum consumable smelting and forging. The alloy is a precipitation strengthening type deformation high-temperature alloy, and the actually measured components after the preparation are measured according to the mass percentage and comprise C: 0.05%, Cr: 16%, Mn: 0.1%, Si: 0.025%, W: 0.3%, Mo: 0.6%, Ti: 1.8%, Al: 1.6%, B: 0.002%, Co: 1.0%, Fe: 40 percent and the balance of Ni, the precipitation starting temperature and the precipitation stopping temperature of gamma' in the alloy are 875 ℃ and 580 ℃ respectively, and the heat treatment process is as follows:
1) first-step solution treatment: heating the alloy to 950 ℃ along with the furnace, preserving heat for 0.5h, heating to 1080 ℃ after the alloy is finished, preserving heat for 90min, and then cooling to room temperature by water;
2) the second step of solution treatment: heating the alloy to 900 ℃ along with the furnace, heating to 1000 ℃ at the speed of 5 ℃/min, preserving the heat for 30min, and then cooling to room temperature by water;
3) aging treatment: heating the alloy to 650 ℃, then preserving heat for 24 hours, and cooling the alloy to room temperature in air after the alloy is finished;
comparative example 2
The alloy comprises the following components in parts by weight: ZL202010383732.9, name: a high-strength high-temp alloy for thermal power generating unit is prepared from high-strength high-temp alloy through vacuum smelting and forging. The alloy is a precipitation strengthening type deformation high-temperature alloy, and the actually measured components after the preparation are measured according to the mass percentage and comprise C: 0.06%, Cr: 16%, Mn: 0.2%, Si: 0.15%, W: 1.6%, Mo: 1.2%, Ti: 2.2%, Al: 1.4%, B: 0.002%, Zr: 0.02%, Fe: 37 percent, the balance being Ni, the precipitation starting temperature and the precipitation stopping temperature of gamma' in the alloy are 890 ℃ and 610 ℃ respectively, and the heat treatment process is as follows:
1) first-step solution treatment: heating the alloy to 950 ℃ along with the furnace, preserving heat for 0.5h, heating to 1080 ℃ after the alloy is finished, preserving heat for 90min, and then cooling to room temperature by water;
2) the second step of solution treatment: heating the alloy to 900 ℃ along with the furnace, heating to 1000 ℃ at the speed of 5 ℃/min, preserving the heat for 30min, and then cooling to room temperature by water;
3) the first step of aging treatment: heating the alloy to 650 ℃, then preserving the heat for 8 hours, and cooling the alloy to room temperature in air after the alloy is finished;
4) the second step of aging treatment: heating the alloy to 750 ℃, preserving heat for 4 hours, and cooling the alloy to room temperature in air after the alloy is finished;
table 1 shows the room temperature and high temperature tensile properties of the alloy after the heat treatment of examples 1-2, and it can be seen that the alloy has good strength and plasticity at all temperatures, and no obvious medium temperature brittleness occurs. In addition, after aging the alloy in the medium-temperature brittleness region for 20h, the alloy also has no obvious brittleness reduction in the process of drawing at 650 ℃ and 700 ℃ (Table 2). By adopting the traditional heat treatment process, the brittleness of the alloy can be obviously reduced when the alloy is stretched at 700 ℃.
TABLE 1 tensile Properties at Room temperature and elevated temperature after completion of Heat treatment in examples 1-2
TABLE 2 brittleness of examples 1-2 and comparative examples 1-2
Fig. 1 shows the morphology of the alloy structure after strengthening and toughening, and it can be seen that gamma' phases with two sizes appear in the alloy, wherein the larger size is about 70nm, the smaller size is less than 10nm, and the alloy fracture appears along the crystal and through crystal mixed fracture at 700 ℃, as shown in fig. 2. However, after the traditional heat treatment process is adopted, only a single-size gamma' phase exists in the alloy, and the reference figure 3 shows that; the tensile fracture has typical intergranular fracture characteristics, see fig. 4.
Claims (9)
1. A strengthening and toughening heat treatment process capable of eliminating medium-temperature brittleness of high-temperature alloy is characterized in that the temperature is kept for 0.5 to 10 hours at a temperature which is 0 to 350 ℃ above the complete dissolving temperature of a phase gamma' precipitated in a crystal of the high-temperature alloy, and then the high-temperature alloy is cooled to room temperature through a high-temperature cooling stage and a low-temperature cooling stage; wherein the content of the first and second substances,
a high-temperature cooling stage: cooling from the precipitation starting temperature of the intragranular precipitated phase gamma 'to a temperature 1-200 ℃ below the precipitation starting temperature of the intragranular precipitated phase gamma', wherein the average cooling rate is 0.1-20 ℃/min;
a low-temperature cooling stage: the average cooling rate is not lower than 2 ℃/min before cooling to the gamma' precipitation termination temperature from the end of the high-temperature cooling stage.
2. The strengthening and toughening heat treatment process capable of eliminating the medium-temperature brittleness of the high-temperature alloy according to claim 1, wherein the intragranular precipitated phase gamma' in the high-temperature alloy is L1 2 The structure conforms to the A3B type atomic ratio, wherein, the A element is Ni, Fe, Co or Mn, and the B element is Al, Ti, Nb, Ta, W, Mo, Zr or Hf.
3. The strengthening and toughening heat treatment process capable of eliminating the medium-temperature brittleness of the high-temperature alloy according to claim 1, wherein the heat preservation time is not more than 5 hours if the temperature is lower than the nucleation temperature of the grain boundary precipitation phase during heat preservation.
4. A strengthening and toughening process for eliminating the warm brittleness of high-temp alloy according to claim 1 where the instantaneous cooling rate at any time is not lower than 0.01 deg.C/min when the cooling rate in high-temp cooling stage is not constant.
5. The strengthening and toughening heat treatment process capable of eliminating the medium-temperature brittleness of the high-temperature alloy according to claim 1, wherein an intragranular precipitated phase gamma' exists in alloy crystal grains after the high-temperature cooling stage is finished, the average size of the intragranular precipitated phase is not less than 20nm, and the volume fraction is not less than 5%.
6. A strengthening and toughening heat treatment process capable of eliminating medium-temperature brittleness of high-temperature alloy according to claim 1, wherein when the cooling rate in the low-temperature cooling stage is not constant, the instantaneous cooling rate at any moment is not lower than 0.1 ℃/min.
7. The strengthening and toughening heat treatment process capable of eliminating the medium-temperature brittleness of the high-temperature alloy according to claim 1, wherein the intragranular precipitated phase γ ' of the alloy after the high-temperature cooling stage is in a bimodal distribution, wherein the particles with the average diameter of not less than 30nm are larger-size γ ' particles, the particles with the average diameter of not more than 20nm are smaller-size γ ' particles, and the average diameter ratio of the larger-size γ ' particles to the smaller-size γ ' particles is not less than 5 times.
8. The strengthening and toughening heat treatment process capable of eliminating the medium-temperature brittleness of the high-temperature alloy according to claim 1, wherein the heat preservation treatment is carried out after the low-temperature cooling stage is finished, the heat preservation time is 0-150 h, and then the high-temperature alloy is cooled to the room temperature.
9. The strengthening and toughening heat treatment process capable of eliminating the medium-temperature brittleness of the high-temperature alloy according to claim 1, wherein after the low-temperature cooling stage is finished, the high-temperature alloy is cooled to room temperature by adopting a water cooling mode, an air cooling mode, an oil cooling mode or a furnace cooling mode.
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