A nickel-based powder superalloy and a method of making the same

Abstract

The application discloses a kind of nickel-based powder superalloy and preparation method thereof, belong to superalloy technical field, to solve the existing nickel-based powder superalloy is used at 750 ℃ Low creep resistance problem.Nickel-based powder superalloy The mass fraction of each element includes: C 0.06%~0.07%, Co 17.0%~19.0%, Cr 9.0%~11.0%, Mo 2.3%~2.7%, W 3.4%~4.8%, Ta2.9%~4.5%, Al 3.0%~3.4%, Ti 2.8%~3.2%, Nb 1.2%~1.8%, Hf 0.2%~0.4%, Zr 0.04%~0.06%, B 0.03%~0.05%, Mg 0.002%~0.010%, and the balance of Ni.The nickel-based powder superalloy of the application has high creep resistance above 750 ℃.

Description

TECHNICAL FIELD

[0001] The present application belongs to the technical field of high-temperature alloy, and particularly relates to a nickel-based powder high-temperature alloy and a preparation method thereof. BACKGROUND

[0002] Turbine disk is one of the most important hot end components in an engine, and the turbine disk alloy is required to have high tensile strength and excellent high-temperature creep resistance during service, and the turbine disk alloy is required to have a small tendency of TCP phase precipitation during long-term service, so that the alloy has good high-temperature microstructure stability to ensure that the mechanical property attenuation of the alloy is reduced to the minimum.

[0003] The existing nickel-based powder high-temperature alloy for turbine disk, such as FGH4098 alloy, has a maximum use temperature limited to 750 DEG C, and importantly, the anti-creep performance is insufficient during long-term use at 750 DEG C, which cannot meet the requirement of the creep performance at high temperature of 750 DEG C. SUMMARY

[0004] In view of the above analysis, the present application aims to provide a nickel-based powder high-temperature alloy and a preparation method thereof, which are used to solve the following technical problem: the existing nickel-based powder high-temperature alloy has low anti-creep performance at 750 DEG C.

[0005] The purpose of the present application is mainly achieved by the following technical scheme:

[0006] On one hand, the present application provides a nickel-based powder high-temperature alloy, and the mass fraction of each element of the nickel-based powder high-temperature alloy comprises: C 0.06% to 0.07%, Co 17.0% to 19.0%, Cr 9.0% to 11.0%, Mo 2.3% to 2.7%, W 3.4% to 4.8%, Ta 2.9% to 4.5%, Al 3.0% to 3.4%, Ti 2.8% to 3.2%, Nb 1.2% to 1.8%, Hf 0.2% to 0.4%, Zr 0.04% to 0.06%, B 0.03% to 0.05%, Mg 0.002% to 0.010%, and the balance of Ni.

[0007] Further, the mass fraction ratio of (C+Ti) / (Ti+Nb+Ta+Hf) is 0.25 to 0.65.

[0008] Further, the total mass fraction of Co, Cr, Mo and W is 33.0% to 36.0%.

[0009] Further, the total mass fraction of W and Ta is 7.0% to 8.0%.

[0010] Further, the mass fraction ratio of Ta to W (Ta / W) is 0.6 to 1.3.

[0011] Further, the total mass fraction of Al, Ti, Nb, Ta and Hf is 10.0% to 13.0%.

[0012] Further, the total mass fraction of Al and Ti is 6.0% to 6.4%.

[0013] Further, the microstructure of the nickel-based powder superalloy comprises a γ matrix phase and precipitated phases, the microstructure is uniform, and the precipitated phases are dispersedly distributed; the precipitated phases mainly comprise γ' phases, MC type carbides and M3B2 type borides; the composition of the γ' phases is (Ni, Co)3(Al, Ti, Ta, Nb, W, Hf) type, the composition of the MC type carbides is (Ti, Ta, Nb, Hf)C type; the element Ta is mainly distributed in the γ' phases; and the element Mg enters the γ matrix phase and is segregated on the grain boundaries.

[0014] The application further provides a preparation method of the nickel-based powder superalloy.

[0015] Step 1, the alloy is prepared by adopting a vacuum induction melting process according to the mass fraction, and an alloy bar is obtained;

[0016] Step 2, the alloy bar is powdered by adopting a plasma rotating electrode method, is sieved and is electrostatically treated, and 50 μm to 150 μm alloy powder is obtained;

[0017] Step 3, under vacuum conditions, the alloy powder is loaded into a low-carbon steel jacket, is degassed and is sealed and welded, and then is subjected to hot isostatic pressing forming, and an ingot blank is obtained;

[0018] Step 4, the ingot blank is subjected to heat treatment, the heat treatment comprises solid solution treatment and aging treatment, and a nickel-based powder superalloy with high creep resistance is obtained.

[0019] Further, in Step 4, the solid solution treatment process parameters are 1190 ℃ to 1210 ℃ / 2 h to 6 h / air cooling, and the aging treatment process parameters are 790 ℃ to 820 ℃ / 4 h to 16 h / air cooling.

[0020] Compared with the prior art, the application can at least realize one of the following beneficial effects:

[0021] a) The application is strengthened by adding solid solution strengthening elements (Co, Cr, Mo, W), adding γ' phase forming elements (Al, Ti, Nb, Ta, Hf) and grain boundary strengthening elements (B, Zr, Mg); by adding high (W+Ta) content and appropriate amount of element Mg, and cooperating with coarse grains, the excellent high-temperature creep resistance of the alloy is realized, so that the composition range with good comprehensive mechanical properties is obtained.

[0022] b) In the nickel-based powder superalloy provided by the application, element Mg is segregated on the grain boundary of the gamma matrix phase, which plays a role in strengthening the grain boundary, thereby improving the creep resistance and the stress-rupture strength; Mg and element S form high-melting-point MgS, which plays a role in purifying the grain boundary and reducing the harmful effect of S; by controlling the content ratio of (C+Ti) / (Ti+Nb+Ta+Hf) to be less than 0.65, MC-type carbides are eliminated from precipitating on the boundary of the original powder particles, i.e., the original powder particle boundary structure (PPBS) is eliminated, so as to avoid the mechanical property degradation caused by the original powder particle boundary structure; by coordinately controlling the contents of elements Co, Cr, Mo, W and Ta, the TCP phase precipitation tendency is reduced, the high-temperature microstructure stability of the alloy is improved, and the alloy has a higher maximum working temperature.

[0023] c) The microstructure of the nickel-based powder superalloy in the application includes a gamma matrix phase and precipitates, the microstructure is uniform, and the precipitates are dispersedly distributed; the precipitates mainly include a gamma prime phase, MC-type carbides and M3B2-type borides; the gamma prime phase is of the type (Ni, Co)3(Al, Ti, Ta, Nb, W, Hf), the MC-type carbides are of the type (Ti, Ta, Nb, Hf)C; element Ta is mainly distributed in the gamma prime phase; and element Mg is segregated on the grain boundary of the gamma matrix phase.

[0024] d) The nickel-based powder superalloy provided by the application has excellent comprehensive performance, and has high creep resistance at 750 DEG C or above, so that the maximum working temperature of the high-temperature alloy in the application can be 750 DEG C or above, and the maximum working temperature can be higher.

[0025] e) In the preparation method in the application, the nickel-based powder superalloy with high creep resistance can be obtained by air cooling in the solid solution treatment and aging treatment steps, the process is simple, and compared with the commonly used salt cooling or oil cooling, the cooling method is economical, environmentally friendly and widely applicable.

[0026] Other features and advantages of the application will be set forth in the following description of the application, and in part will become apparent to those skilled in the art from the description, or can be learned by practice of the application. The objects and other advantages of the application can be realized and attained by the methods written in the specification. BRIEF DESCRIPTION OF DRAWINGS

[0027] The accompanying drawings are included to provide a further understanding of the application and are incorporated in and constitute a part of this specification, illustrate embodiments of the application and together with the description serve to explain the principles of the application.

[0028] Figure 1 The gamma prime phase morphology characterization results of the heat-treated state of the GNPM11 nickel-based powder superalloy in the embodiments of the application.

[0029] Figure 2 The LM parameter P and stress σ relationship characterization results of the nickel-based powder superalloy in the embodiments of the application. DETAILED DESCRIPTION

[0030] The preferred embodiments of the present application are described in detail below, which are only used to illustrate the principles of the present application, and are not used to limit the scope of the present application.

[0031] The present application provides a nickel-based powder superalloy, the mass fraction of each element of the nickel-based powder superalloy comprising: C 0.06%~0.07%, Co 17.0%~19.0%, Cr 9.0%~11.0%, Mo 2.3%~2.7%, W 3.4%~4.8%, Ta 2.9%~4.5%, Al 3.0%~3.4%, Ti 2.8%~3.2%, Nb 1.2%~1.8%, Hf 0.2%~0.4%, Zr 0.04%~0.06%, B 0.03%~0.05%, Mg 0.002%~0.010%, and the balance of Ni.

[0032] Specifically, the mass fraction ratio of (C+Ti) / (Ti+Nb+Ta+Hf) is 0.30~0.42, the total mass fraction of Co, Cr, Mo and W is 33.0%~36.0%, the total mass fraction of W and Ta is 7.0%~8.0%, the mass fraction ratio of Ta / W is 0.6~1.3, the total mass fraction of Al, Ti, Nb, Ta and Hf is 10.0%~13.0%, and the total mass fraction of Al and Ti is 6.0%~6.4%.

[0033] Specifically, the microstructure of the nickel-based powder superalloy of the present application comprises a γ matrix phase and a precipitate phase, the microstructure is uniform, and the precipitate phase is dispersedly distributed; the precipitate phase mainly comprises a γ' phase, an MC type carbide and an M3B2 type boride; the composition of the γ' phase is (Ni, Co)3(Al, Ti, Ta, Nb, W, Hf) type, and the composition of the MC type carbide is (Ti, Ta, Nb, Hf)C type; the element Ta is mainly distributed in the γ' phase; and the element Mg enters the γ matrix phase and is segregated on the grain boundary.

[0034] Specifically, the content of the above-mentioned γ' phase is 53%~55% (mass fraction).

[0035] Specifically, 62%~70% of Ta enters the γ' phase.

[0036] Specifically, the complete dissolution temperature of the above-mentioned γ' phase is 1160°C~1190°C.

[0037] Specifically, considering that the effect of coarse grains on improving creep resistance cannot be ignored, the grain size of the above-mentioned high-creep-resistance nickel-based powder superalloy is 5.0~5.5 grade.

[0038] The elements in the application are explained in detail below, and the content refers to the mass fraction of each element.

[0039] The application is strengthened by adding solid solution strengthening elements (Co, Cr, Mo, W), adding γ' phase forming elements (Al, Ti, Nb, Ta, Hf) and grain boundary strengthening elements (B, Zr, Mg); by adding high (W+Ta) content and appropriate amount of element Mg, and cooperating with coarse grains, the excellent high temperature creep resistance of the alloy is realized, so that the composition range with good comprehensive mechanical properties is obtained.

[0040] In the nickel-based powder high-temperature alloy of the application, element Mg is segregated on the grain boundary of the γ matrix phase, which plays a role in strengthening the grain boundary, thereby improving the creep resistance and endurance strength; Mg and element S form high melting point MgS, which plays a role in purifying the grain boundary and reducing the harmful effect of S; appropriate amount of Mg can effectively disperse and refine the grain boundary coarse carbide, too low content of Mg has no obvious effect, and too high content of Mg causes the grain boundary carbide to gather, which is easy to form cracks during the creep process, and has an adverse effect. Therefore, in the application, Mg is controlled at 0.002% to 0.010%.

[0041] Secondly, in the application, by controlling the (C+Ti) / (Ti+Nb+Ta+Hf) content ratio to be less than 0.65, MC type carbide is eliminated from the powder original particle boundary, that is, the powder original particle boundary structure (PPBS) is eliminated, so as to avoid the mechanical property degradation caused thereby; therefore, in the application, the (C+Ti) / (Ti+Nb+Ta+Hf) mass fraction ratio is controlled to be 0.30 to 0.42.

[0042] By coordinating the content of elements such as Co, Cr, Mo, W and Ta, the application reduces the TCP phase precipitation tendency, improves the high temperature structure stability of the alloy, and makes the alloy have a higher maximum working temperature. Therefore, in the application, the total mass fraction of Co, Cr, Mo and W is controlled to be 33.0% to 36.0%.

[0043] Due to the crystal structure, atomic size, self-diffusion coefficient and other factors of elements W and Ta, W and Ta can enter the gamma matrix and the gamma' phase, Ta mostly enters the gamma' phase, thus strengthening the gamma matrix and the gamma' phase, and the effect of Ta on strengthening the gamma' phase is more significant; W and Ta help to improve the high-temperature creep resistance of the alloy, and the effect of Ta on improving the high-temperature creep resistance is more obvious; Ta makes element W have a back-distribution effect, that is, with the increase of the amount of Ta, the increase of W entering the gamma matrix phase; the higher the total amount of W and Ta, the better the high-temperature creep resistance and the better the durability; only when the total mass fraction of W and Ta is 7.0% or more, excellent 750℃ creep resistance and durability can be obtained. Therefore, in the present application, the total mass fraction of W and Ta is controlled to be 7.0-8.0%, and the mass fraction ratio of Ta to W is controlled to be 0.6-1.3.

[0044] In order to further improve the creep resistance of the nickel-based powder high-temperature alloy, the mass fraction of each element in the nickel-based powder high-temperature alloy of the present application can include: C 0.062%-0.066%, Co 17.8%-18.4%, Cr 9.6%-10.4%, Mo 2.3%-2.5%, W 3.4%-4.6%, Ta 2.9%-4.1%, Al 3.1%-3.4%, Ti 2.9%-3.1%, Nb 1.3%-1.6%, Hf 0.22%-0.38%, Zr 0.045%-0.055%, B 0.035%-0.05%, Mg 0.002%-0.007%, and the balance of Ni.

[0045] Preferably, the mass fraction ratio of (C+Ti) / (Ti+Nb+Ta+Hf) is controlled to be 0.32-0.40.

[0046] Preferably, the total mass fraction of Co, Cr, Mo and W is controlled to be 33.0%-35.5%.

[0047] Preferably, the total mass fraction of W and Ta is controlled to be 7.3%-8.0%.

[0048] Preferably, the mass fraction ratio of Ta to W is controlled to be 0.65-1.15.

[0049] Preferably, the total mass fraction of Al, Ti, Nb, Ta and Hf is controlled to be 10.5%-12.5%.

[0050] Preferably, the total mass fraction of Al and Ti is controlled to be 6.10%-6.35%.

[0051] The present application also provides a preparation method of the nickel-based powder high-temperature alloy, comprising the following steps:

[0052] Step 1, the alloy is prepared by vacuum induction melting process according to mass fraction ratio, and the alloy bar is obtained;

[0053] Step 2, the alloy bar is powdered by plasma rotating electrode method, screened, and electrostatically treated to obtain 50-150 micron alloy powder;

[0054] Step 3, under vacuum condition, the alloy powder is loaded into a low-carbon steel jacket, degassed and sealed, and then hot isostatic pressing is performed to obtain an ingot blank;

[0055] Step 4, the ingot blank is heat treated, the heat treatment includes solution treatment and aging treatment, and a nickel-based powder high-temperature alloy is obtained.

[0056] Specifically, in the above step 2, the micron-sized alloy powder with uniform alloy composition is obtained by cooling in argon + helium mixed gas during the powdering process at a very fast cooling rate.

[0057] Specifically, in the above step 3, the process parameters of hot isostatic pressing are as follows: temperature 1190-1210℃, pressure 120-140MPa, and holding time 3-6h.

[0058] Specifically, in the above step 4, the solution treatment process parameters are 1190-1210℃ / 2-6h / air cooling, and the aging treatment process parameters are 790-820℃ / 4-16h / air cooling.

[0059] In the preparation method of the present application, the micron-sized alloy powder of the high-temperature alloy is cooled at a high cooling rate to form, so that the alloy composition is uniform.

[0060] The high-creep-resistant nickel-based powder high-temperature alloy of the present application has uniform microstructure, dispersed distribution of precipitated phase, eliminates macrosegregation, can further improve the alloying degree, and makes the alloy have good high-temperature tensile strength, yield strength and high-temperature creep resistance.

[0061] Specifically, the mechanical properties of the above nickel-based powder high-temperature alloy are as follows:

[0062] Mechanical properties at 750℃: tensile strength reaches 1200MPa or more (e.g. 1213-1235MPa), yield strength 1015MPa or more (e.g. 1018-1050MPa), elongation after fracture 10% or more (e.g. 10%-11%), and reduction of area 10% or more (e.g. 10%-11%).

[0063] 750℃ creep resistance: under the test condition of 750℃ / 650MPa, plastic strain is 0.21% or less (e.g. 0.17%-0.21%), the endurance life is 470h or more (e.g. 476-566h), and the minimum creep rate is 1.1x10-8 s -1 For example, 7.7 x 10 -9 ~ 1.1 x 10 -8 s -1 The 750℃ / 100h stress-rupture strength is greater than 760MPa.

[0064] In the preparation method of the present application, the high-creep-resistance nickel-based powder superalloy can be obtained by air cooling in the solution treatment and aging treatment steps, and the process is simple, economical, environmentally friendly and widely applicable compared with the commonly used salt cooling or oil cooling.

[0065] The highest working temperature of the high-creep-resistance nickel-based powder superalloy of the present application can reach 750℃ or above, and the 750℃ / 100h stress-rupture strength is greater than 760MPa, which can meet the stringent requirements of the engine on the material performance at high temperature and can be used as a high-temperature material in a temperature scene of 750℃ or above.

[0066] The advantages of the composition and process parameter precise control of the nickel-based powder superalloy of the present application will be demonstrated below with specific examples and comparative examples.

[0067] Examples

[0068] The present example provides a nickel-based powder superalloy. The composition and process conditions of the nickel-based powder superalloy of the present example are shown in Table 1. Among them, GNPM11-GNPM13 are examples of the present application. # and 2 # are samples with relatively poor effects in the research process of the inventors, and FGH4098 is a commonly used nickel-based powder superalloy at present, which is a comparative example of the present application.

[0069] The preparation method of the above nickel-based powder superalloy is as follows:

[0070] (1) The raw materials are prepared according to the chemical composition and mass fraction of the superalloy, and the 25kg vacuum induction melting process is used to prepare the alloy rod;

[0071] (2) The alloy rod is used to prepare a high-temperature alloy powder by a plasma rotating electrode method, and the alloy powder is sieved and electrostatically treated to obtain an alloy powder with a particle size of 50-150μm;

[0072] (3) The alloy powder is loaded into a low-carbon steel jacket under vacuum conditions, degassed and sealed;

[0073] (4) The sealed jacket is subjected to hot isostatic pressing to obtain an ingot;

[0074] (5) heat treating the formed ingot to obtain the powder superalloy part; the heat treatment comprises solid solution treatment and aging treatment.

[0075] Table 1 composition and preparation process parameters of nickel-based powder superalloy samples

[0076]

[0077]

[0078] The microstructure of the above alloy after heat treatment and long-term aging is observed by a metallographic microscope, and the GNPM11-GNPM13, 1 # and 2 # Microstructure of the nickel-based powder superalloy.

[0079] Taking the GNPM11 nickel-based powder superalloy as an example, the γ' phase form of the heat treated state is shown in Figure 1 .

[0080] The microstructure of the nickel-based powder superalloy provided by the application mainly comprises a matrix γ phase, a γ' phase, MC type carbide and M3B2 type boride, the composition of the γ' phase is (Ni, Co)3(Al, Ti, Ta, Nb, W, Hf) type, the composition of the MC type carbide is (Ti, Ta, Nb, Hf)C type; the element Ta is mainly distributed in the γ' phase; and the element Mg enters the γ matrix phase and is segregated on the grain boundary.

[0081] The GNPM11-GNPM13, 1 # and 2 # The content of the γ' phase of the nickel-based powder superalloy is 53%-55% (mass fraction), the complete dissolution temperature of the γ' phase is 1170-1180℃, and the grain size is 5.0-5.5 levels. The coarse grains are beneficial to improve the creep resistance and the endurance life.

[0082] The microstructure observation shows that the nickel-based powder superalloy does not precipitate TCP phase after 750℃ / 3000h aging heat treatment, and it has excellent high-temperature microstructure stability at 750℃.

[0083] The GNPM11-GNPM13, 1 # and 2 # The 750℃ mechanical properties and 750℃ creep resistance of the nickel-based powder superalloy are listed in Table 2 and Table 3 respectively, and the relationship between the LM parameter P and the stress σ is shown in Figure 2 .

[0084] Table 2 750℃ mechanical properties of the nickel-based powder superalloy

[0085] Alloy No. [R m / MPa]]> [R p0.2 / MPa]]> A / ％ Z / ％ GNPM11 1224 1025 10.0 11.0 GNPM12 1232 1030 10.5 10.8 GNPM13 1213 1018 10.0 10.0 1 # ]] 1208 1016 11.2 11.6 2 # ]] 1209 1015 11.3 11.8 FGH4098 1220 1020 24.0 24.5

[0086] Table 3 Creep resistance of nickel-based powder superalloy at 750℃

[0087] Alloy No. Test Condition 50h Plastic Strain / % Minimum creep rate / s -1 ]] Endurance Life / h GNPM11 750°C / 650MPa 0.21 1.1 x 10 -8 ]]> 476 GNPM12 750°C / 650MPa 0.17 7.7 x 10 -9 ]]> 502 GNPM13 750°C / 650MPa 0.18 8.5 x 10 -9 ]]> 566 1 # ]] 750°C / 650MPa 0.43 1.8 x 10 -8 ]]> 375 2 # ]] 750°C / 650MPa 0.38 1.5 x 10 -8 ]]> 392 FGH4098 750°C / 650MPa 0.64 2.3 x 10 -8 ]]> 197

[0088] From the data in Table 3 and Figure 2 It can be seen that, compared with the existing FGH4098 alloy, the minimum creep rate of the alloy of the present application at 750℃ is greatly reduced, and the endurance life and endurance strength are also greatly improved. The endurance strength of the alloy of the present application at 750℃ / 100h is greater than 760MPa. It can be seen that the nickel-based powder superalloy provided by the present application has excellent high-temperature creep resistance at 750℃.

[0089] The above description is merely preferred specific embodiments of the present application, but the protection scope of the present application is not limited thereto, and any changes or substitutions easily thought of by those skilled in the art within the technical scope disclosed by the present application should be covered within the protection scope of the present application.

Claims

1. A nickel-based powder superalloy, characterized in that, The mass fractions of each element in the nickel-based powder superalloy include: C 0.06%~0.07%, Co 17.0%~19.0%, Cr 9.0%~11.0%, Mo 2.3%~2.7%, W 3.4%~4.8%, Ta 2.9%~4.5%, Al 3.0%~3.4%, Ti 2.8%~3.2%, Nb 1.2%~1.8%, Hf 0.2%~0.4%, Zr 0.04%~0.06%, B 0.03%~0.05%, Mg 0.002%~0.010%, and the balance Ni; The mass fraction ratio of (C+Ti) / (Ti+Nb+Ta+Hf) is 0.30~0.42; The total mass fraction of W and Ta is 7.0%~8.0%; The mass fraction ratio of Ta to W, Ta / W, is 0.6~1.3; The microstructure of the nickel-based powder superalloy comprises a γ matrix phase and precipitated phases, exhibiting a uniform structure with the precipitated phases being diffusely distributed. The precipitated phases mainly include the γ′ phase, MC-type carbides, and M3B2-type borides. The γ′ phase is of the (Ni,Co)3(Al,Ti,Ta,Nb,W,Hf) type, and the MC-type carbides are of the (Ti,Ta,Nb,Hf)C type. Element Ta is mainly distributed in the γ′ phase, while element Mg enters the γ matrix phase and agglomerates at the grain boundaries. The mass fraction of the γ′ phase is 53%~55%, with 62%~70% of Ta entering the γ′ phase, and the grain size of the nickel-based powder superalloy is grade 5.0~5.5; The creep resistance of the nickel-based powder superalloy at 750℃ is as follows: Test conditions 750℃ / 650MPa: Plastic strain below 0.21% after 50h, creep rupture life above 470h, minimum creep rate 1.1×10⁻⁶. -8 s -1 Below, the creep strength at 750℃ / 100h is greater than 760MPa.

2. The nickel-based powder superalloy according to claim 1, characterized in that, The mass fraction ratio of (C+Ti) / (Ti+Nb+Ta+Hf) is 0.32~0.

40.

3. The nickel-based powder superalloy according to claim 1, characterized in that, The total mass fraction of Co, Cr, Mo, and W is 33.0% to 36.0%.

4. The nickel-based powder superalloy according to claim 1, characterized in that, The total mass fraction of W and Ta is 7.3%~8.0%.

5. The nickel-based powder superalloy according to claim 1, characterized in that, The mass fraction ratio of Ta to W, Ta / W, is 0.65 to 1.

15.

6. The nickel-based powder superalloy according to claim 1, characterized in that, The total mass fraction of Al, Ti, Nb, Ta, and Hf is 10.0% to 13.0%.

7. The nickel-based powder superalloy according to claim 1, characterized in that, The total mass fraction of Al and Ti is 6.0% to 6.4%.

8. A method for preparing a nickel-based powder superalloy, characterized in that, The method for manufacturing the nickel-based powder superalloy according to any one of claims 1-7 comprises the following steps: Step 1: Prepare the alloy using vacuum induction melting process according to the mass fraction ratio, and obtain alloy bars; Step 2: The alloy rod is powdered, sieved, and electrostatically treated using the plasma rotating electrode method to obtain alloy powder with a thickness of 50μm~150μm. Step 3: Under vacuum conditions, the alloy powder is loaded into a low-carbon steel sleeve, degassed and sealed, and then hot isostatically pressed to obtain an ingot. Step 4: Heat treat the ingot, including solution treatment and aging treatment, to obtain a nickel-based powder superalloy with high creep resistance.

9. The preparation method according to claim 8, characterized in that, In step 4, the solution treatment process parameters are: 1190℃~1210℃ / 2h~6h / air cooling, and the aging treatment process parameters are: 790℃~820℃ / 4h~16h / air cooling.

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