Heat treatment method and device for nickel-based alloy for 700 DEG C advanced ultra-supercritical unit

Abstract

The invention discloses a heat treatment method and device for a nickel-based alloy for a 700 DEG C advanced ultra-supercritical unit, and aims at an aging strengthening type nickel-based high-temperature alloy, only a solid solution heat treatment step before operation is reserved, and an aging heat treatment step in standard heat treatment is cancelled. The alloy is subjected to aging strengthening in the service process close to the aging temperature (650-850 DEG C) (not less than 1000 hours), the solid solution heat treatment temperature is controlled to be 1050-1150 DEG C, heat preservation is conducted for 1-3 hours, and water cooling or air cooling is adopted as the cooling mode. Impurities on the surface of the alloy are cleaned before solid solution heat treatment, parameters such as temperature, stress and strain are monitored in real time during operation of a unit to optimize the aging process, the process is simplified, the cost is reduced, and the production efficiency is improved while the lasting creep property of the alloy is guaranteed. And the field availability of the large alloy pipe fitting in preparation and installation of equipment such as a 700 DEG C advanced ultra-supercritical thermal power generation superheater and a reheater is improved.

Description

Technical Field

[0001] This invention belongs to the field of metal heat treatment, specifically relating to a heat treatment method and apparatus for nickel-based alloys used in advanced ultra-supercritical units at 700℃, applicable to the preparation and installation of superheater and reheater tubes for advanced ultra-supercritical thermal power generation at 650~750℃. Background Technology

[0002] Against the backdrop of global warming and increasingly severe environmental problems, the research and development and construction of advanced ultra-supercritical thermal power units with a capacity of one megawatt is one of the most important possible measures to optimize my country's energy structure, achieve emission reduction targets, and ensure national energy and economic security. This involves increasing steam temperature and pressure, and reducing energy consumption and heat efficiency. Advanced ultra-supercritical coal-fired power generation technology at 700℃ can significantly improve the power generation efficiency of units and substantially reduce emissions of pollutants and greenhouse gases such as CO2, making it a research hotspot in many countries worldwide.

[0003] Materials used in advanced ultra-supercritical power generation technology at 700℃ need to possess excellent comprehensive performance in terms of high-temperature strength, corrosion resistance, weldability, processing and manufacturing characteristics, repairability, and cost. For alloy pipe fittings used in superheaters and reheaters, which are the components in the highest temperature section of the boiler, high creep rupture strength is required; therefore, nickel-based high-temperature alloys are typically used.

[0004] In the material selection plans of several countries and organizations for advanced ultra-supercritical units at 700℃, imported nickel-based alloys such as Inconel 740 / Inconel 740H and Haynes 282 are important candidate materials for high-temperature heating surfaces. In addition, alloys such as GH984G, HT700, GH750 and C-HRA-1, which are independently developed in my country, have also become candidate materials for components of advanced ultra-supercritical units at 700℃.

[0005] Taking Inconel 740H alloy as an example, it is a precipitation-strengthened nickel-based superalloy developed by Special Metals in the United States for the Thermie AD700 project, a 700℃ advanced ultra-supercritical coal-fired power generation technology project in Europe. It is based on Ni-25Cr-20Co-0.5Mo and uses Ni3(Al,Ti,Nb) type γ′ phase as the main strengthening phase. The official standard heat treatment regime is a two-step heat treatment method: 1150℃ / 30min / WQ+800℃ / 16hr / AC. The first step, solution heat treatment, involves holding at 1150℃ for 30 minutes followed by water cooling. This process allows the coarse γ' strengthening phase particles and carbides to redissolve, precipitating a large number of fine γ′ phases. Simultaneously, carbides are distributed in granular or needle-like forms at grain boundaries and within grains. At this stage, due to the limited amount of carbides, the pinning effect is not significant, resulting in low creep strength. Therefore, a second step, intermediate heat treatment or aging heat treatment, involving holding at 800℃ for 16 hours followed by air cooling, is required to fully precipitate the strengthening phases in the alloy, thereby ensuring that the alloy possesses sufficiently high creep strength.

[0006] The other alloys mentioned above, similar to Inconel 740H, are precipitation-strengthened nickel-based superalloys with the γ′ phase as the main strengthening phase, and their standard heat treatment all include two steps: 1) The standard heat treatment regime for Haynes 282 is as follows: solution heat treatment at 1121-1149℃ for 30 min-2 h, followed by rapid cooling; the aging heat treatment consists of two steps: holding at 1010℃ for 2 h, followed by air cooling; holding at 788℃ for 8 h, followed by air cooling. 2) The standard heat treatment regime for HT700 is as follows: solution heat treatment at 1200-1260℃ for 25-45 minutes, followed by water cooling; and medium-temperature short-term aging heat treatment at 750℃~800℃, followed by holding for 30-60 minutes. 3) The standard heat treatment regime for GH984G is as follows: solution heat treatment at 1100±10℃ for 1 hour, followed by water quenching or air cooling; medium-temperature short-term aging heat treatment at 750±10℃, holding for 8 hours, followed by air cooling.

[0007] Typically, to ensure the machinability of materials, manufacturers supply them in a solution-treated state, and equipment manufacturers perform further welding and deformation before aging heat treatment. However, due to the size of the components, boiler parts usually require large heat treatment equipment to complete the aging heat treatment, which is quite difficult and consumes a lot of energy. Summary of the Invention

[0008] The purpose of this invention is to provide a heat treatment method and apparatus for nickel-based alloys used in advanced ultra-supercritical power units at 700℃, primarily targeting straight tube sections of alloy pipes subjected to relatively uniform stress during service. After welding and deformation, the solution-treated alloy does not require aging heat treatment, making it particularly suitable for the fabrication and installation of boiler tubes such as superheaters and reheaters in 700℃ advanced ultra-supercritical thermal power plants. This reduces costs, improves the on-site availability of large alloy pipe fittings, and ensures that the creep resistance of the nickel-based alloy used in 700℃ advanced ultra-supercritical power units remains unaffected.

[0009] To achieve the above objectives, the present invention adopts the following technical solution: A heat treatment method for nickel-based alloys used in advanced ultra-supercritical units at 700℃ includes: The first step is to complete the solution heat treatment before operation; The second step is to gradually complete the age hardening of the nickel-based alloy during service, wherein the nickel-based alloy is an age-hardening nickel-based high-temperature alloy.

[0010] A further improvement of the present invention is that the solution heat treatment temperature is 1050℃-1150℃, and after the furnace is heated to 300℃, the heating rate is controlled at 1-5℃ / min, the holding time is 1-3 hours, and the cooling method is water cooling or air cooling.

[0011] A further improvement of the present invention is that the nickel-based alloy is subjected to a temperature range of 750℃-850℃ during service and an operating time of not less than 1000 hours to complete the aging strengthening.

[0012] A further improvement of the present invention is that the nickel-based alloys include Inconel 740H, Haynes 282 and GH984G, and the aging treatment temperature and service temperature of these alloys are close to 800°C.

[0013] A further improvement of the present invention is that, before solution heat treatment, the surface of the nickel-based alloy is cleaned to remove oil and oxide scale impurities.

[0014] A further improvement of the present invention is that the surface cleaning is performed by sandblasting or chemical cleaning.

[0015] A further improvement of the present invention is that, during the operation of the 700℃ advanced ultra-supercritical unit, the temperature, stress and strain parameters of the nickel-based alloy are monitored in real time, and the parameter change trend is analyzed by using a data fitting algorithm to optimize the aging strengthening process of the alloy.

[0016] A heat treatment apparatus for nickel-based alloys used in advanced ultra-supercritical units at 700℃, comprising: Solution heat treatment unit, used to complete solution heat treatment before operation; An age-hardening unit is used to gradually complete the age-hardening of a nickel-based alloy during service, wherein the nickel-based alloy is an age-hardening nickel-based high-temperature alloy.

[0017] A further improvement of the present invention is that the solution heat treatment temperature is 1050℃-1150℃, and after the furnace is heated to 300℃, the heating rate is controlled at 1-5℃ / min, the holding time is 1-3 hours, and the cooling method is water cooling or air cooling.

[0018] A further improvement of the present invention is that, during the operation of the 700℃ advanced ultra-supercritical unit, the temperature, stress and strain parameters of the nickel-based alloy are monitored in real time, and the parameter change trend is analyzed by using a data fitting algorithm to optimize the aging strengthening process of the alloy.

[0019] Compared with the prior art, the present invention has at least the following beneficial technical effects: This invention provides a heat treatment method and apparatus for nickel-based alloys used in advanced ultra-supercritical units at 700℃. The nickel-based alloy is an age-hardening nickel-based high-temperature alloy. Its standard heat treatment includes two steps: solution treatment and aging. The solution heat treatment step is completed only before operation, eliminating the aging heat treatment step in the standard heat treatment. The aging process of the alloy is completed during its service life at a temperature close to the aging temperature. The technical parameters controlled in the process are: eliminating the aging heat treatment in the standard heat treatment system, so that the aging process and the service process of the alloy are carried out simultaneously, and the age hardening of the alloy is gradually completed during service.

[0020] Furthermore, the solution heat treatment temperature is 1050℃-1150℃, the holding time is 1-3 hours, and the cooling method is water cooling or air cooling. These solution heat treatment parameters can fully dissolve the coarse γ' strengthening phase particles and carbides in the alloy, laying a good foundation for subsequent age hardening.

[0021] The nickel-based alloy is operated at a temperature range of 750℃-850℃ for at least 1000 hours to complete age hardening. Under these temperature and time conditions, the alloy can effectively complete the age hardening process during service and obtain good performance.

[0022] The nickel-based alloys include, but are not limited to, Inconel 740H, Haynes 282, and GH984G, and the aging treatment temperature and service temperature of these alloys are close to 800°C, making them suitable for the heat treatment method of this invention.

[0023] Before solution heat treatment, the surface of the nickel-based alloy is cleaned to remove impurities such as oil and oxide scale. Surface cleaning can be performed by sandblasting or chemical cleaning. This cleaning ensures the effectiveness of the solution heat treatment and allows the alloy to achieve better properties.

[0024] During operation of the 700℃ advanced ultra-supercritical unit, parameters such as temperature, stress, and strain of the nickel-based alloy are monitored in real time. Data fitting algorithms are used to analyze parameter variation trends and optimize the alloy's aging strengthening process. This monitoring and optimization method allows for better control of the alloy's aging strengthening process based on actual operating conditions, ensuring optimal alloy performance.

[0025] In summary, the present invention provides a heat treatment method and apparatus for nickel-based alloys used in advanced ultra-supercritical units at 700℃. When the service temperature of these alloy components is between 750℃ and 850℃, it is close to the aging temperature of the alloy, and the aging strengthening process can be gradually completed during service. This method simplifies the heat treatment process, reduces the number of aging heat treatment steps, and lowers the dependence on large-scale heat treatment equipment, thereby reducing boiler manufacturing costs, while ensuring that the alloy's creep resistance does not decrease. Simultaneously, it eliminates the need for on-site aging treatment, significantly improving the alloy's usability in the field. Attached Figure Description

[0026] To more clearly illustrate the specific embodiments of the present invention or the technical solutions in the prior art, the drawings used in the description of the specific embodiments or the prior art will be briefly introduced below. Obviously, the drawings described below are some embodiments of the present invention. For those skilled in the art, other drawings can be obtained from these drawings without creative effort.

[0027] Figure 1 This is a simplified heat treatment process flow diagram of the present invention; Figure 2 This is a flowchart of the two-step heat treatment process for the comparative example of the present invention; Figure 3 These are metallographic photographs taken after creep has been completed according to an embodiment of the present invention. Figure 4 These are metallographic photographs of the comparative creep model of this invention after completion; Figure 5 This is a SEM image of an embodiment of the present invention after creep has been completed; Figure 6 This is a SEM image of the comparative creep model of the present invention after completion; Figure 7 This is a comparison of the XRD patterns of the embodiments and comparative examples after creep was completed. Figure 8 These are metallographic photographs taken after creep has been completed according to an embodiment of the present invention. Figure 9 These are metallographic photographs of the comparative creep model of this invention after completion; Figure 10 These are metallographic photographs taken after creep has been completed according to an embodiment of the present invention. Figure 11These are metallographic photographs of the comparative creep model of this invention after completion; Figure 12 This is a structural block diagram of the device of the present invention. Detailed Implementation

[0028] In the following description, only certain exemplary embodiments are briefly described. As those skilled in the art will recognize, the described embodiments can be modified in various ways without departing from the spirit or scope of the invention. Therefore, the drawings and description are considered to be exemplary in nature and not restrictive.

[0029] In the description of this invention, it should be understood that, when used in this specification and the appended claims, the terms "comprising" and "including" indicate the presence of the described features, integrals, steps, operations, elements and / or components, but do not exclude the presence or addition of one or more other features, integrals, steps, operations, elements, components and / or collections thereof.

[0030] It should also be understood that the terminology used in this specification is for the purpose of describing particular embodiments only and is not intended to limit the invention. As used in this specification and the appended claims, the singular forms “a,” “an,” and “the” are intended to include the plural forms unless the context clearly indicates otherwise.

[0031] It should also be further understood that the term "and / or" as used in this specification and the appended claims refers to any combination of one or more of the associated listed items and all possible combinations, and includes such combinations.

[0032] The accompanying drawings illustrate various structural schematic diagrams according to embodiments disclosed in this invention. These drawings are not to scale, and some details have been enlarged for clarity, and some details may have been omitted. The shapes of the various regions and layers shown in the drawings, as well as their relative sizes and positional relationships, are merely exemplary and may deviate from reality due to manufacturing tolerances or technical limitations. Furthermore, those skilled in the art can design regions / layers with different shapes, sizes, and relative positions as needed.

[0033] The embodiments of the present invention will now be described in detail with reference to the accompanying drawings.

[0034] Example 1 This invention provides a heat treatment method for nickel-based alloys used in advanced ultra-supercritical units at 700℃, comprising: The first step is to complete the solution heat treatment before operation; The second step is to gradually complete the age hardening of the nickel-based alloy during service, wherein the nickel-based alloy is an age-hardening nickel-based high-temperature alloy.

[0035] In this embodiment, the solution heat treatment temperature is 1050℃-1150℃. After the furnace is heated to 300℃, the heating rate is controlled at 1-5℃ / min, the holding time is 1-3 hours, and the cooling method is water cooling or air cooling.

[0036] In this embodiment, the nickel-based alloy operates at a temperature range of 750°C to 850°C for at least 1000 hours to complete age hardening.

[0037] In this embodiment, the nickel-based alloys include Inconel 740H, Haynes 282, and GH984G, and the aging treatment temperature and service temperature of these alloys are close to 800°C.

[0038] In this embodiment, before solution heat treatment, the nickel-based alloy is surface cleaned to remove oil and oxide scale impurities.

[0039] In this embodiment, the surface cleaning is performed by sandblasting or chemical cleaning.

[0040] In this embodiment, when the 700℃ advanced ultra-supercritical unit is running, the temperature, stress, and strain parameters of the nickel-based alloy are monitored in real time, and the parameter change trend is analyzed by using a data fitting algorithm to optimize the aging strengthening process of the alloy.

[0041] Example 2 The specific material used in this invention is Inconel 740H, and its measured composition is shown in Table 1.

[0042] Table 1. Mass fraction (wt%) of chemical composition of Inconel 740H in this invention.

[0043] The one-step heat treatment process used in this embodiment of the invention is as follows: Inconel 740H alloy is heated to 1150℃ for austenitization, held at that temperature for 60 minutes, and then water-cooled to room temperature, thus eliminating the need for the aging heat treatment process of holding at 800℃ for 16 hours and then air-cooling to room temperature. The process is as follows: Figure 1 As shown.

[0044] The two-step heat treatment process used in the comparative example of this invention is as follows: Inconel 740H alloy is heated to 1150℃ for austenitization, held at that temperature for 60 minutes, and then water-cooled to room temperature; the alloy is then held at 800℃ for 16 hours and air-cooled to room temperature. The comparative example uses the standard heat treatment regime provided by the alloy manufacturer. The process is as follows: Figure 2 As shown.

[0045] The two alloys after the above heat treatment were subjected to high-temperature creep tests under the same temperature and stress conditions until fracture, and their creep performance data were obtained. The specific experimental parameters and fracture time are shown in Table 2.

[0046] Table 2 Creep fracture time of Inconel 740H in the examples and comparative examples.

[0047] As can be seen from Table 2, the creep properties of the samples after the simplified heat treatment of the present invention not only did not decrease compared with those after standard heat treatment, but actually increased slightly, exhibiting superior creep fracture properties. Figure 3 These are metallographic photographs taken after creep has been completed according to an embodiment of the present invention. Figure 4 These are metallographic photographs of the comparative creep model of this invention after completion; Figure 5 This is a SEM image of an embodiment of the present invention after creep has been completed; Figure 6 These are SEM images of the comparative creep model of this invention after completion. From... Figure 3-6 It can be seen that although the grain size of the alloy varies slightly due to the different sampling locations in the thick-walled pipe, there is no significant difference in the grain boundary precipitates after the creep experiment between the two groups of samples; both exhibit a continuous granular distribution of M... 23 C6 type carbides contain a large number of twins within the crystal. Figure 7 These are XRD patterns comparing the embodiments and comparative examples of the present invention after creep completion. Figure 7 It can be seen that the phase composition of the two alloy samples after the creep test is consistent, both being a homogeneous austenitic phase, with no large amount of harmful phases generated.

[0048] Example 3 The specific material used in this invention is 617B, and its measured composition is shown in Table 3.

[0049] Table 3. Chemical composition mass fraction (wt%) of 617B in this invention

[0050] The one-step heat treatment process used in this embodiment of the invention is as follows: the 617B alloy is heated to 1050℃ for austenitization, held for 3 hours, and then water-cooled to room temperature, thus eliminating the aging heat treatment process of holding at 800℃ for 16 hours and air-cooling to room temperature.

[0051] The two-step heat treatment process used in the comparative example of this invention is as follows: the 617B alloy is heated to 1050℃ for austenitization, held at that temperature for 3 hours, and then water-cooled to room temperature; the alloy is then held at 800℃ for 16 hours and air-cooled to room temperature. The comparative example is a standard heat treatment process provided by the alloy manufacturer.

[0052] The two alloys after the above heat treatment were subjected to high-temperature creep tests under the same temperature and stress conditions until fracture, and their creep performance data were obtained. The specific experimental parameters and fracture time are shown in Table 4.

[0053] Table 4. Creep fracture time of 617B in the Examples and Comparative Examples

[0054] As can be seen from Table 4, the creep properties of the samples after the simplified heat treatment of the present invention not only did not decrease compared with those after standard heat treatment, but actually increased slightly, exhibiting superior creep fracture properties. Figure 8 These are metallographic photographs taken after creep has been completed according to an embodiment of the present invention. Figure 9 These are metallographic photographs of the comparative creep model of this invention after completion; Figure 5 These are SEM images taken after creep has been completed according to an embodiment of the present invention; from Figure 8-9 It can be seen that although the grain size of the alloy varies slightly due to the different sampling locations in the thick-walled pipe, there is no significant difference in the grain boundary precipitates after the creep experiment between the two groups of samples; both exhibit a continuous granular distribution of M... 23 C6 type carbides contain a large number of twins within the crystal.

[0055] Example 4 The specific material used in this invention is Haynes 282, and its measured composition is shown in Table 5.

[0056] Table 5. Mass fraction (wt%) of chemical composition of Haynes 282 in this invention

[0057] The one-step heat treatment process used in this embodiment of the invention is as follows: the Haynes 282 alloy is heated to 1100℃ for austenitization, held for 1 hour, and then water-cooled to room temperature, thus eliminating the aging heat treatment process of holding at 800℃ for 16 hours and air-cooling to room temperature.

[0058] The two-step heat treatment process used in the comparative example of this invention is as follows: the Haynes 282 alloy is heated to 1100℃ for austenitization, held at that temperature for 1 hour, and then water-cooled to room temperature; the alloy is then held at 800℃ for 16 hours and air-cooled to room temperature. The comparative example uses the standard heat treatment process provided by the alloy manufacturer.

[0059] The two alloys after the above heat treatment were subjected to high-temperature creep tests under the same temperature and stress conditions until fracture, and their creep performance data were obtained. The specific experimental parameters and fracture time are shown in Table 6.

[0060] Table 6 Creep fracture time of Haynes 282 in the examples and comparative examples

[0061] As can be seen from Table 6, the creep properties of the samples after the simplified heat treatment of the present invention not only did not decrease compared with those after standard heat treatment, but actually increased slightly, exhibiting superior creep fracture properties. Figure 10 These are metallographic photographs taken after creep has been completed according to an embodiment of the present invention. Figure 11 These are metallographic photographs of the comparative creep model of this invention after completion; Figure 5 These are SEM images taken after creep has been completed according to an embodiment of the present invention; from Figure 10-11 It can be seen that although the grain size of the alloy varies slightly due to the different sampling locations in the thick-walled pipe, there is no significant difference in the grain boundary precipitates after the creep experiment between the two groups of samples; both exhibit a continuous granular distribution of M... 23 C6 type carbides contain a large number of twins within the crystal.

[0062] Example 5 like Figure 12 As shown, the present invention provides a heat treatment device for nickel-based alloys used in advanced ultra-supercritical units at 700℃, comprising: Solution heat treatment unit, used to complete solution heat treatment before operation; An age-hardening unit is used to gradually complete the age-hardening of a nickel-based alloy during service, wherein the nickel-based alloy is an age-hardening nickel-based high-temperature alloy.

[0063] In this embodiment, the solution heat treatment temperature is 1050℃-1150℃. After the furnace is heated to 300℃, the heating rate is controlled at 1-5℃ / min, the holding time is 1-3 hours, and the cooling method is water cooling or air cooling.

[0064] In this embodiment, when the 700℃ advanced ultra-supercritical unit is running, the temperature, stress, and strain parameters of the nickel-based alloy are monitored in real time, and the parameter change trend is analyzed by using a data fitting algorithm to optimize the aging strengthening process of the alloy.

[0065] The foregoing has shown and described the basic principles, main features, and advantages of the present invention. It will be apparent to those skilled in the art that the invention is not limited to the details of the exemplary embodiments described above, and that the invention can be implemented in other specific forms without departing from its spirit or essential characteristics. Therefore, the embodiments should be considered illustrative and non-limiting in all respects, and the scope of the invention is defined by the appended claims rather than the foregoing description. Thus, all variations falling within the meaning and scope of equivalents of the claims are intended to be included within the scope of the invention. No reference numerals in the claims should be construed as limiting the scope of the claims.

[0066] Furthermore, it should be understood that although this specification describes embodiments, not every embodiment contains only one independent technical solution. This narrative style is merely for clarity. Those skilled in the art should consider the specification as a whole, and the technical solutions in each embodiment can be appropriately combined to form other embodiments that can be understood by those skilled in the art. The above content is only for illustrating the technical concept of the present invention and should not be construed as limiting the scope of protection of the present invention. Any modifications made based on the technical concept proposed in this invention shall fall within the scope of protection of the claims of this invention.

Claims

1. A heat treatment method of a nickel-based alloy for a 700°C advanced ultra-supercritical unit, characterized by, The application relates to a method for optimizing the aging strengthening process of nickel-based alloys in a 700 DEG C advanced ultra-supercritical unit. The first step is to complete the solid solution heat treatment before operation. The second step is to gradually complete the aging strengthening of the nickel-based alloy in service, wherein the nickel-based alloy is an aging strengthening type nickel-based high-temperature alloy.

2. The heat treatment method of the nickel-based alloy for the 700℃ advanced ultra-supercritical unit according to claim 1, characterized in that, The solid solution heat treatment temperature is 1050-1150 DEG C, the temperature is increased to 300 DEG C in the furnace, the temperature increasing speed is controlled to be 1-5 DEG C / min, the holding time is 1-3 hours, and the cooling mode is water cooling or air cooling.

3. The heat treatment method of the nickel-based alloy for the 700℃ advanced ultra-supercritical unit according to claim 1, characterized in that, The temperature range of the nickel-based alloy in the service process is 750-850 DEG C, and the operation time is not less than 1000 hours to complete the aging strengthening.

4. The heat treatment method of the nickel-based alloy for the 700℃ advanced ultra-supercritical unit according to claim 1, characterized in that, The nickel-based alloy includes Inconel 740H, Haynes 282 and GH984G, and the aging treatment temperature and the service temperature of the alloys are close to 800 DEG C.

5. The heat treatment method of the nickel-based alloy for the 700℃ advanced ultra-supercritical unit according to claim 1, characterized in that, Before the solid solution heat treatment, the nickel-based alloy is subjected to surface cleaning to remove oil stains and oxide scale impurities.

6. The heat treatment method of the nickel-based alloy for the 700℃ advanced ultra-supercritical unit according to claim 5, characterized in that, The surface cleaning adopts sand blasting treatment or chemical cleaning.

7. The heat treatment method of the nickel-based alloy for a 700℃ advanced ultra-supercritical unit according to claim 1, characterized in that, When the 700 DEG C advanced ultra-supercritical unit is operated, the temperature, stress and strain parameters of the nickel-based alloy are monitored in real time, the parameter change trend is analyzed by using a data fitting algorithm, and the aging strengthening process of the alloy is optimized.

8. A heat treatment device for a nickel-based alloy for a 700°C advanced ultra-supercritical unit, characterized by, The application also relates to a device for optimizing the aging strengthening process of nickel-based alloys in a 700 DEG C advanced ultra-supercritical unit. The device comprises a solid solution heat treatment unit for completing the solid solution heat treatment before operation. The device comprises an aging strengthening unit for gradually completing the aging strengthening of the nickel-based alloy in service, wherein the nickel-based alloy is an aging strengthening type nickel-based high-temperature alloy. 9.The heat treatment device for nickel-based alloy used in 700℃ advanced ultra-supercritical unit of claim 8, characterized in that, The solid solution heat treatment temperature is 1050-1150 DEG C, the temperature is increased to 300 DEG C in the furnace, the temperature increasing speed is controlled to be 1-5 DEG C / min, the holding time is 1-3 hours, and the cooling mode is water cooling or air cooling. 10.The heat treatment device for a nickel-based alloy used in a 700℃ advanced ultra-supercritical unit according to claim 8, characterized in that, When the 700 DEG C advanced ultra-supercritical unit is operated, the temperature, stress and strain parameters of the nickel-based alloy are monitored in real time, the parameter change trend is analyzed by using a data fitting algorithm, and the aging strengthening process of the alloy is optimized.

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