CN116970860A - High-quality A286 high-temperature alloy and novel heat treatment method for improving hardness of A286 high-temperature alloy - Google Patents
High-quality A286 high-temperature alloy and novel heat treatment method for improving hardness of A286 high-temperature alloy Download PDFInfo
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- CN116970860A CN116970860A CN202310527035.XA CN202310527035A CN116970860A CN 116970860 A CN116970860 A CN 116970860A CN 202310527035 A CN202310527035 A CN 202310527035A CN 116970860 A CN116970860 A CN 116970860A
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- 238000010438 heat treatment Methods 0.000 title claims abstract description 45
- 239000000956 alloy Substances 0.000 title claims abstract description 34
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 33
- 238000000034 method Methods 0.000 title claims abstract description 29
- 230000032683 aging Effects 0.000 claims abstract description 46
- 229910000601 superalloy Inorganic materials 0.000 claims abstract description 33
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 17
- 239000006104 solid solution Substances 0.000 claims abstract description 9
- 229910052742 iron Inorganic materials 0.000 claims abstract description 8
- 239000002994 raw material Substances 0.000 claims abstract description 8
- 239000000243 solution Substances 0.000 claims description 28
- 238000001816 cooling Methods 0.000 claims description 21
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 8
- 239000011449 brick Substances 0.000 claims description 3
- 229910052698 phosphorus Inorganic materials 0.000 claims description 3
- 238000004519 manufacturing process Methods 0.000 abstract description 6
- 101000912561 Bos taurus Fibrinogen gamma-B chain Proteins 0.000 description 7
- 238000004321 preservation Methods 0.000 description 4
- 239000011159 matrix material Substances 0.000 description 3
- 238000011056 performance test Methods 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 230000035945 sensitivity Effects 0.000 description 3
- 238000009864 tensile test Methods 0.000 description 3
- 238000005520 cutting process Methods 0.000 description 2
- 230000002349 favourable effect Effects 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- RZJQYRCNDBMIAG-UHFFFAOYSA-N [Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Zn].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn] Chemical class [Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Zn].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn] RZJQYRCNDBMIAG-UHFFFAOYSA-N 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000007599 discharging Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 230000002431 foraging effect Effects 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 238000000926 separation method Methods 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
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Abstract
A high-quality A286 superalloy and a novel heat treatment method for improving the hardness of the A286 superalloy belong to the field of superalloy production. The element proportion of the high-quality A286 alloy is provided, and the alloy comprises the following raw materials in percentage by mass: 24.0% -27.0%, C:0.08% and following, si:1.0% and following, mn:1.0% and following, cr:13.30% -16.6%, mo:2% and following, ti:1.75% -2.30%, al:0.4% and following, P:0.03% and following, S:0.02% and following, V:0.25% -0.33%, B:0.001% -0.01% and the balance of iron, the heat treatment method improves the performances of hardness, tensile strength, yield strength and the like of the alloy by means of solid solution and two-stage aging heat treatment, the tensile strength of the treated high-quality A286 high-temperature alloy is up to 1234.4MPa, the yield strength is up to 808.1MPa, and the Vickers hardness is up to 335, and the method can be widely applied in production practice.
Description
Technical Field
The invention relates to the field of high-temperature alloy production, in particular to a high-quality A286 high-temperature alloy and a novel heat treatment method for improving the hardness of the A286 high-temperature alloy.
Background
The super alloy A286 has good high temperature resistance and corrosion resistance, and has good yield strength and processing plasticity at the temperature of less than 650 ℃, so that the super alloy A286 is particularly suitable for manufacturing bearing components of aeronautics and astronautics, fastener products such as screw core rod, bolts, nuts and the like, can also be used for producing products in various shapes such as disc, forge pieces, plates, bars and the like, and meets most of use requirements.
As a high-temperature alloy material commonly used in aviation and production and manufacture, a heat treatment system has close relation to the evolution of the structure and the performance of the A286 high-temperature alloy, and the high-temperature alloy is based on gamma austenite and has a face-centered cubic structure from room temperature to high temperature. The heat treatment system adopted is 950 ℃ for two hours of solid solution and 760 ℃ for 16 hours of aging, but when the heat treatment method is used in the conventional formula of the A286 alloy, the plasticity, strength and hardness of the alloy after heat treatment are often insufficient, and the main reason is that the favorable phase can be fully precipitated by high-temperature aging on one hand and the harmful phase can be precipitated and grown on the other hand.
Disclosure of Invention
One of the purposes of the invention is to provide a high-quality A286 superalloy, which has excellent tensile strength, yield strength and hardness after corresponding heat treatment; the invention improves the performance of high-quality A286 high-temperature alloy by a certain heat treatment method, and overcomes the defect of overlarge A286 notch sensitivity by a two-stage aging mode.
The first aim of the invention is to provide a high-quality A286 superalloy, which comprises the following raw materials in percentage by mass: 24.0% -27.0%, C:0.08% and following, si:1.0% and following, mn:1.0% and following, cr:13.30% -16.6%, mo:2% and following, ti:1.75% -2.30%, al:0.4% and following, P:0.03% and following, S:0.02% and following, V:0.25% -0.33%, B:0.001% -0.01% and the balance of iron, wherein the high-quality A286 superalloy has tensile strength up to 1234.4MPa, yield strength up to 808.1MPa and Vickers hardness up to 335.
In some embodiments, the material comprises Ni:24.17%, C:0.04%, si:0.21%, mn:0.25%, cr:13.70%, mo:1.21%, ti:2.13%, al:0.16%, P:0.016%, S:0.005%, V:0.29%, B:0.006% and the balance of iron.
The second object of the present invention is to provide a heat treatment method for high-quality a286 superalloy, comprising the steps of:
solid solution treatment, namely filling the formed A286 high-temperature alloy blank into a solid solution treatment furnace, heating to the solid solution temperature of 980 ℃, preserving heat for 2 hours, then performing rapid water cooling operation, and cooling to below 30 ℃; the A286 superalloy blank comprises the following raw materials in percentage by mass: 24.0% -27.0%, C:0.08% and following, si:1.0% and following, mn:1.0% and following, cr:13.30% -16.6%, mo:2% and following, ti:1.75% -2.30%, al:0.4% and following, P:0.03% and following, S:0.02% and following, V:0.25% -0.33%, B:0.001% -0.01%, and the balance being iron;
and (3) aging treatment, namely loading the A286 high-temperature alloy blank subjected to rapid water cooling operation into an aging treatment furnace, heating to 760 ℃, preserving heat for 8 hours, cooling to 650 ℃, preserving heat for 8 hours, and air cooling to obtain the high-quality A286 high-temperature alloy, wherein the tensile strength of the high-quality A286 high-temperature alloy is up to 1234.4MPa, the yield strength is up to 808.1MPa, and the Vickers hardness is up to 335.
The microstructure phase of the formed A286 superalloy blank is gamma+gamma ' +Ti (C, N) +M3B2, the precipitation temperature of gamma ' phase is 650 ℃, the gamma ' phase is dissolved at 830 ℃, the eta phase is dissolved at 720 ℃ and the eta phase is dissolved at 940 ℃. In the heating process of the solution treatment step, when the temperature rises to 830 ℃, the gamma ' phase starts to dissolve, the gamma ' phase is dissolved completely and homogenized in the heat preservation process, and the main purpose of rapid water cooling after the solution treatment is to enable the gamma ' phase alloy element dissolved in the matrix in the solution heating stage to be dissolved in the gamma matrix, and the ideal state is complete solution, no other phase is precipitated, and the condition is prepared for aging in the later stage. In order to ensure that the gamma' -phase of the favorable phase is fully precipitated and grown, and avoid excessive precipitation of eta phase, the alloy is subjected to heat treatment in a two-stage aging mode, the high-temperature aging of the first stage can fully precipitate the phase, and the low-temperature aging of the second stage can fully grow the phase.
In some embodiments, the rate of temperature increase is from 5 ℃/min to 8 ℃/min in both the solution treatment step and the aging treatment step.
In some embodiments, the spacing distance between each two a286 superalloy blanks during the solution treatment step is 20mm-30mm. Because the metal elements of the A286 high-temperature alloy are more in types and relatively poor in heat conductivity, the structure transformation is slow, in the heating process, the bar stock at the center part of the material tray is incompletely transformed, and a considerable amount of gamma 'phase is possibly undissolved in a matrix, so that the precipitation amount and the distribution state of the gamma' phase in aging cannot meet the requirements, and the effect of improving solid solution can be better achieved by controlling the interval distance between every two A286 high-temperature alloy blanks;
in some embodiments, each two a286 superalloy blanks are separated by refractory bricks during the solution treatment step.
In some specific embodiments, in the aging treatment step, the A286 high-temperature alloy blank subjected to water cooling and cooling treatment is put into an aging treatment furnace, the temperature in the aging treatment furnace is increased to 760 ℃ at the speed of 5 ℃/min-8 ℃/min, the temperature is kept for 8 hours, the temperature in the aging treatment furnace is cooled to 650 ℃, the temperature is kept for 8 hours, and the air cooling is performed.
In some embodiments, in the aging step, a continuous cooling operation is performed from 760 ℃ to 650 ℃, and the second-stage aging is directly started after cooling.
In some embodiments, the vacuum level of the furnace tubes of the solution treatment furnace and the aging treatment furnace is maintained at 1×10 in the solution treatment step and the aging treatment step -2 -1×10 -1 。
In some embodiments, the heat-preserving preheating is performed on the furnace tube of the solution treatment furnace and the furnace tube of the aging treatment furnace before the solution treatment step and the aging treatment step, respectively, wherein the heat-preserving temperature is 120 ℃ and the heat-preserving time is 2 hours.
Compared with the prior art, the invention has the following advantages:
(1) The invention relates to a high-quality A286 superalloy, which has tensile strength up to 1234.4MPa, yield strength up to 808.1MPa and Vickers hardness of 335 compared with the existing A286 superalloy.
(2) The heat treatment method is adopted to treat the A286 high-temperature alloy, and adopts a process of combining solution treatment and aging treatment, so that the A286 high-temperature alloy has good heat stability, good plasticity, tensile strength, yield strength, hardness and cutting processability after the heat treatment process is adopted, and the overall performance of the A286 high-temperature alloy is improved. The aging treatment step of the heat treatment method comprises two aging steps, wherein the aging of the A286 superalloy at the higher temperature of 760 ℃ can fully separate out and grow up gamma' -phase, the aging time is 8h, the separation of harmful phase eta-phase can be avoided, the hardness of the alloy can be greatly increased by the two aging steps at 650 ℃, the plasticity and toughness are improved, and the sensitivity of a notch is reduced.
Drawings
FIG. 1 is a graph showing the temperature profile of the solution treatment stage in example 1 of the present invention;
FIG. 2 is a graph of temperature profile during the aging treatment phase in example 1 of the present invention;
fig. 3 is a temperature profile of the solution treatment stage and the time-efficient treatment stage in example 2 of the present invention.
Detailed Description
The invention is further described below in connection with specific embodiments. The following examples are only for more clearly illustrating the technical aspects of the present invention, and are not intended to limit the scope of the present invention. The present patent application is not described in detail and is to be understood as being common general knowledge in the art.
A286 high-quality high-temperature alloy comprises the following raw materials in percentage by mass: 24.0% -27.0%, C:0.08% and following, si:1.0% and following, mn:1.0% and following, cr:13.30% -16.6%, mo:2% and following, ti:1.75% -2.30%, al:0.4% and following, P:0.03% and following, S:0.02% and following, V:0.25% -0.33%, B:0.001% -0.01%, and the balance of iron. In some embodiments, the Cr content may be 13.30%, 13.90%, 14.20%, 15.2%, 16.6%, or other values within a range; the Mo content may be 0.2%, 0.7%, 1.2%, 1.7%, 2% or other values within the range; the Ti content may be 1.75%, 1.80%, 2.05%, 2.10%, 2.30% or other values within the range.
Example 1
The embodiment provides an A286 superalloy round bar blank with the size of 8X 100mm, which is prepared from the following raw materials in percentage by mass: ni:24.17%, C:0.04%, cr:13.70%, mo:1.21%, ti:2.13%, al:0.16%, mn:0.25%, si:0.21%, P:0.016%, S:0.0005%, B:0.006%, V:0.29%, the balance being Fe.
As shown in fig. 1 and 2, the heat treatment method for improving the hardness thereof includes the steps of:
s1, heat preservation and preheating: starting a solution treatment furnace, heating up at a heating rate of 50 ℃/h, heating up the solution treatment furnace to 120 ℃ and preserving heat for 2h, and discharging air and steam in a furnace tube;
s2, solution treatment: as shown in figure 1, the formed A286 superalloy round bar blanks are put into a solution treatment furnace, when the furnace is filled, the round bar blanks are spaced by 30mm, the round bar blanks are separated by refractory bricks, the furnace filling amount before the solution treatment cannot be excessively large and is concentrated in the center of the furnace tube as much as possible, and the uniform heating is ensured; heating the round bar blank to 980 ℃ under the condition of controlling the heating rate to about 300 ℃/h, preserving heat for 2h, and then performing rapid water cooling operation;
s3, aging treatment
S31, a first-stage aging treatment: as shown in fig. 2, the round bar blank is heated to 760 ℃ and kept for 8 hours under the condition that the heating rate is controlled to be about 300 ℃/h, and then the furnace is cooled;
s32, two-stage aging treatment: as shown in FIG. 2, when the temperature was lowered to 650 ℃, the heat was preserved for 8 hours and then air-cooled.
Example 2
The present embodiment provides an a286 superalloy, the size and mass fraction of which are the same as those of embodiment 1, and the difference from embodiment 1 is that, as shown in fig. 3, the temperature of the solution treatment in this embodiment is 950 ℃, and the heat preservation time is 2h; the aging treatment temperature is 760 ℃ and the heat preservation time is 16h.
Test example 1
The round bar blanks obtained in example 1 and example 2 were subjected to tensile test performance tests, respectively, the performance test method was operated according to GB/T228.1-2010 Metal Material tensile test method, and the test results are shown in Table 1, sigma b For tensile strength, sigma 0.2 HV is Vickers hardness, which is the yield strength.
TABLE 1 tensile test Performance test results
| σ b (MPa) | σ 0.2 (MPa) | HV | |
| Example 1 | 1234.4 | 808.1 | 335 |
| Example 2 | 1168.5 | 755.3 | 256 |
As can be seen from Table 1, the tensile strength, yield strength and hardness of the A286 superalloy prepared by the heat treatment method provided by the invention are higher than those of the A286 superalloy prepared by the traditional heat treatment method, so that the A286 superalloy has good heat stability, heat resistance, plasticity and cutting processability after the A286 superalloy is subjected to the heat treatment process; meanwhile, by adopting the solution treatment and two-stage aging heat treatment processes, the A286 superalloy blank after heat treatment has excellent tensile strength, yield strength and hardness, thereby overcoming the notch sensitivity of the A286 superalloy.
The above-described preferred embodiments according to the present invention are intended to suggest that, from the above description, various changes and modifications can be made by the person skilled in the art without departing from the scope of the technical idea of the present invention. The technical scope of the present invention is not limited to the description, but must be determined according to the scope of claims.
Claims (10)
1. A high-quality A286 superalloy is characterized by comprising the following raw materials in percentage by mass: 24.0% -27.0%, C:0.08% and following, si:1.0% and following, mn:1.0% and following, cr:13.30% -16.6%, mo:2% and following, ti:1.75% -2.30%, al:0.4% and following, P:0.03% and following, S:0.02% and following, V:0.25% -0.33%, B:0.001% -0.01% and the balance of iron, wherein the high-quality A286 superalloy has tensile strength up to 1234.4MPa, yield strength up to 808.1MPa and Vickers hardness up to 335.
2. The high-quality a286 superalloy according to claim 1, comprising the raw materials Ni in mass fraction: 24.17%, C:0.04%, si:0.21%, mn:0.25%, cr:13.70%, mo:1.21%, ti:2.13%, al:0.16%, P:0.016%, S:0.005%, V:0.29%, B:0.006% and the balance of iron.
3. A method for heat treatment of a high quality a286 superalloy, comprising:
solid solution treatment, namely placing the A286 high-temperature alloy blank into a solid solution treatment furnace, heating to the solid solution temperature of 980 ℃, preserving heat for 2 hours, then performing rapid water cooling operation, and cooling to below 30 ℃; the A286 superalloy blank comprises the following raw materials in percentage by mass: 24.0% -27.0%, C:0.08% and following, si:1.0% and following, mn:1.0% and following, cr:13.30% -16.6%, mo:2% and following, ti:1.75% -2.30%, al:0.4% and following, P:0.03% and following, S:0.02% and following, V:0.25% -0.33%, B:0.001% -0.01%, and the balance being iron;
and (3) aging treatment, namely loading the A286 high-temperature alloy blank subjected to rapid water cooling operation into an aging treatment furnace, heating to 760 ℃, preserving heat for 8 hours, cooling to 650 ℃, preserving heat for 8-10 hours, and air cooling to obtain the high-quality A286 high-temperature alloy according to claim 1, wherein the high-quality A286 high-temperature alloy has tensile strength up to 1234.4MPa, yield strength up to 808.1MPa and Vickers hardness up to 335.
4. A heat treatment method according to claim 3, wherein in both the solution treatment step and the aging treatment step, the temperature rise rate is 5 ℃/min to 8 ℃/min.
5. A heat treatment method according to claim 3, wherein in the solution treatment step, the distance between every two a286 superalloy billets is 20mm-30mm.
6. A heat treatment method according to claim 3, wherein in the solution treatment step, every two a286 superalloy blanks are separated by refractory bricks.
7. A heat treatment method according to claim 3, wherein in the aging treatment step, a286 superalloy blank subjected to rapid water cooling operation is charged into the aging treatment furnace, the temperature in the aging treatment furnace is raised to 760 ℃ at a rate of 5 ℃/min-8 ℃/min, the temperature is kept for 8 hours, the temperature in the aging treatment furnace is lowered to 650 ℃, the temperature is kept for 8-10 hours, and air cooling is performed.
8. A heat treatment method according to claim 3, characterized in that in the aging treatment step, a continuous cooling operation is performed from 760 ℃ to 650 ℃, and the second aging is started directly after the cooling.
9. The heat treatment method according to claim 3, wherein in the solution treatment step and the aging treatment step, a degree of vacuum of a furnace tube of the solution treatment furnace and the aging treatment furnace is maintained at 1X 10 -2 -1×10 -1 。
10. The heat treatment method according to claim 3, wherein the heat-preserving preheating is performed on the furnace tube of the solution treatment furnace and the furnace tube of the aging treatment furnace, respectively, before the solution treatment step and the aging treatment step, at a temperature of 120 ℃ for a heat-preserving time of 2 hours.
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