A third generation nickel-based single crystal superalloy and a composition design method and a preparation method thereof

Abstract

The application provides a third-generation nickel-based single crystal superalloy and a composition design method and a preparation method thereof. V The application comprises the following steps: determining the element type of the nickel-based single crystal superalloy to be designed, screening the composition from different element compositions of the alloy to meet N The application can obtain the nickel-based single crystal superalloy with excellent high-temperature creep performance through the design method, and the creep life of the nickel-based single crystal superalloy can reach 388h under the condition of 1100 DEG C and 137MPa.

Description

Technical Field

[0001] This invention relates to the field of high-temperature alloy technology, and in particular to a third-generation nickel-based single-crystal high-temperature alloy and its composition design and preparation method. Background Technology

[0002] High thrust-to-weight ratio aero-engines are crucial national assets for promoting economic development and enhancing national core competitiveness. Nickel-based single-crystal superalloys are irreplaceable key materials for manufacturing aero-engine turbine blades, and their microstructure stability under service conditions determines the engine's operational safety. Under service conditions, nickel-based single-crystal superalloys are mainly subjected to the combined effects of high temperature and centrifugal force, and creep damage is the main failure mechanism of the alloy. Creep performance has become an important performance indicator for evaluating engine reliability.

[0003] To improve the creep performance of nickel-based single-crystal superalloys, a large number of refractory elements are added to the alloy to enhance microstructural stability by reducing the diffusion rate. The addition of Re increases the creep life at 1100℃ / 137MPa (the most common creep condition) from 30h to 300h. The concentrations of 0wt.%, 3wt.%, and 6wt.% Re are also key factors in differentiating the first three generations of alloys. However, the large addition of refractory elements makes it easy for topologically dense (TCP) phases to precipitate in the alloy. Since cracks easily form near the TCP phase, this leads to a sharp decrease in the alloy's creep performance. Therefore, balancing low diffusion rates with suppression of TCP phase precipitation to improve the microstructural stability of the alloy is crucial for enhancing the creep performance of third-generation nickel-based single-crystal superalloys.

[0004] Compositional design is the primary approach to achieving the aforementioned objectives. However, besides Re, nickel-based single-crystal superalloys also incorporate more than ten other alloying elements, including Co, Cr, Mo, W, Al, Ti, and Ta. This necessitates exploring hundreds of millions of compositional combinations through trial and error alone, significantly increasing the research cycle and cost. Researchers typically use diffusion coefficients and electron-hole ratios to represent the structural stability of the alloy. The diffusion coefficient is the weighted interdiffusion coefficient of different alloying elements within the Ni matrix. Characterization shows that alloys with smaller interdiffusion coefficients have higher creep lifetimes. The electron vacancy method calculates the average electron vacancy density (Nv) in the alloy; when Nv > 2.49, TCP phase will precipitate in the alloy, while Nv < 2.49, no TCP phase will precipitate. Therefore, considering all factors... By combining the Nv value with calculations and microstructure characteristics, it is expected to provide new ideas for the composition design of high creep performance, thereby obtaining a third-generation nickel-based single-crystal superalloy with high creep performance and improving its application value. Summary of the Invention

[0005] The purpose of this invention is to provide a third-generation nickel-based single-crystal superalloy with high creep performance, as well as its composition design and preparation method. Through the optimized design of the alloy composition, a nickel-based single-crystal superalloy with excellent creep performance can be obtained, reaching the leading level of creep performance of the first three generations of alloys in the world.

[0006] To achieve the above objectives, in a first aspect, the present invention provides a method for designing the composition of a nickel-based single-crystal superalloy with high creep performance, comprising the following steps:

[0007] S1. First, determine the element types and composition ranges of the existing third-generation nickel-based single-crystal superalloys. Calculate the different elemental compositions and select alloys that meet the requirements from these compositions. N V ≤1.59% of the component;

[0008] S2. From the components in step S1, select components whose sum of Cr, Re, W and Mo content m satisfies 13.4% ≤ m ≤ 14.5%, Co content n satisfies 3.0% ≤ n ≤ 3.3%, Re content v satisfies 5.0% ≤ v ≤ 6.0%, and Ta / Al is 1.3 to 1.5.

[0009] S3. Obtain an alloy that meets the composition described in step S2 through button ingots. Based on the average size of the dendrite trunk and the γ′ phase between the dendrites, select the nickel-based single crystal high-temperature alloy composition with the smallest average size of the γ′ phase, which is the high creep performance nickel-based single crystal high-temperature alloy.

[0010] Furthermore, the nickel-based single-crystal superalloy to be designed is a third-generation nickel-based single-crystal superalloy, and the element types are selected from Cr, Co, Al, Mo, W, Ta, Re, Hf, and Ni.

[0011] The initial content of each element is based on the composition range of existing third-generation nickel-based single-crystal superalloys, satisfying the following: Cr: 2.0–5.0%, Co: 3.0–12.5%, Al: 5.5–6.5%, Mo: 0–3.0%, W: 5.5–6.0%, Ta: 6.0–8.0%, Re: 4.5–6.5%, Hf: 0–0.2%, Ni: 50.0–80.0%.

[0012] Furthermore, in steps S1 and S3, the preferred method for screening the component range includes: designing the elemental composition ratio using 0.5% as the elemental content variable, wherein the Hf content is designed using 0.1% as the variable. Designing the composition within this range reduces workload and is reasonable, with each element fluctuating within a range of ±0.5, preferably ±0.3.

[0013] This invention provides a nickel-based single-crystal superalloy, the alloy composition by mass percentage comprising: Cr: 2.0–3.0%, Co: 3.0–3.3%, Al: 5.5%, Mo: 0.5–1.5%, W: 5.5–6.0%, Ta: 7.5–8.0%, Re: 5.0–6.0%, Hf: 0.1%, with the remainder being Ni and unavoidable impurities; the diffusion coefficient of the alloy composition is... And the electron vacancy Nv simultaneously satisfy N V ≤1.59. And the sum of the contents of Cr, Re, W and Mo, m, satisfies 13.4%≤m≤14.5%, the Co content, n, satisfies 3.0%≤n≤3.3%, the Re content, v, satisfies 5.0%≤v≤6.0%, and the Ta / Al (mass ratio) is 1.3~1.5.

[0014] In some preferred embodiments, the alloy composition by mass percentage includes: Cr: 2.0±0.3%, Co: 3.0±0.3%, Al: 5.5±0.3%, Mo: 0.5±0.3%, W: 5.5±0.3%, Ta: 7.5±0.3%, Re: 5.5±0.3%, Hf: 0.1±0.02%, with the remainder being Ni and unavoidable impurities, and the Ta / Al ratio being 1.3 to 1.5.

[0015] In a second aspect, the present invention provides a method for preparing the nickel-based single-crystal high-temperature alloy according to any one of the above claims, comprising: weighing alloy raw materials according to the mass percentage of alloy composition, and melting to obtain a master alloy; remelting and casting the master alloy and then directionally drawing to obtain a single crystal rod; and then heat-treating the single crystal rod to obtain the nickel-based single-crystal high-temperature alloy.

[0016] Furthermore, the average size of the dendrite trunk γ′ of the button ingot alloy obtained by melting in a vacuum arc melting furnace is less than 120 nm, preferably between 44 and 109 nm, and the size of the interdendritic γ′ is less than 200 nm, preferably between 70 and 192 nm. Alloy compositions with smaller γ′ phase sizes inside the button ingot alloy are selected as nickel-based single-crystal high-temperature alloy compositions.

[0017] Furthermore, the heat treatment includes solution treatment and aging treatment; the solution treatment includes: first, heating from room temperature to 1280℃ to 1300℃ at a rate of 5 to 10℃ / min and holding at that temperature for 2 to 6 hours; then heating to 1310℃ to 1320℃ at a rate of 2 to 5℃ / min and holding at that temperature for 1 to 5 hours; finally heating to 1320℃ to 1330℃ at a rate of 2 to 5℃ / min and holding at that temperature for 5 to 10 hours, followed by air cooling to room temperature.

[0018] Furthermore, the aging process includes: first heating to 1120℃~1180℃, holding at that temperature for 2~8 hours, and then air cooling to room temperature; then heating to 840℃~880℃, holding at that temperature for 20~30 hours, and then air cooling to room temperature.

[0019] The heat treatment was performed under an argon atmosphere.

[0020] Furthermore, the melting temperature is 1580℃~1700℃, and the vacuum degree should be maintained at 0.1MPa.

[0021] Furthermore, the remelting temperature is 1500–1560°C, and the time is 2–6 minutes;

[0022] And / or, the temperature gradient of the directional pulling is 30–80 K / cm, and the pulling rate of the single crystal is in the range of 50–160 μm / s.

[0023] Furthermore, after heat treatment, the average size of the γ′ phase in the nickel-based single-crystal superalloy is ≤300nm; the creep life of the nickel-based single-crystal superalloy under the condition of 1100℃ / 137MPa can reach 388h, which is a leading level among the first three generations of nickel-based single-crystal superalloys at home and abroad. Therefore, it can be used for aero-engine turbine blades that are subjected to high stress under high temperature conditions.

[0024] The beneficial effects of this invention are as follows:

[0025] 1. The composition design method for third-generation nickel-based single-crystal superalloys provided by this invention performs preliminary composition screening by synergistic limitation of diffusion coefficient and electron vacancy, then optimizes and limits the content and ratio of specific elements, and finally further screens the composition of nickel-based single-crystal superalloys with high creep performance by means of the average size of γ′ phase. This method is of great guiding significance for the composition design of third-generation nickel-based single-crystal superalloys and provides a new idea and approach for the design and preparation of nickel-based single-crystal superalloys with high creep performance.

[0026] 2. The third-generation nickel-based single-crystal high-temperature alloy provided by this invention, through the optimization of alloy composition, can obtain a nickel-based single-crystal high-temperature alloy with excellent creep performance. The creep life can reach 388h in a creep environment of 1100℃ / 137MPa, which is at a leading level among the first three generations of nickel-based single-crystal high-temperature alloys at home and abroad.

[0027] 3. The third-generation nickel-based single-crystal high-temperature alloy proposed in this invention has a low diffusion coefficient and a small average size of γ′ phase, as well as excellent microstructure stability. It does not precipitate topologically dense harmful phases (TCP) over a longer service life. Attached Figure Description

[0028] To more clearly illustrate the technical solutions in this invention or the prior art, the drawings used in the description of the embodiments or the prior art will be briefly introduced below. Obviously, the drawings described below are some embodiments of this invention. For those skilled in the art, other drawings can be obtained from these drawings without creative effort.

[0029] Figure 1 For the existing third-generation nickel-based single-crystal superalloys and N V value;

[0030] Figure 2 The diagram shows the dimensions of the dendrite trunks and interdendritic γ′ of the button ingot alloy in the as-cast state, as shown in Examples 1-26.

[0031] Figure 3 The image shows the microstructure of the alloy prepared in Example 1 after heat treatment (γ / γ′).

[0032] Figure 4 This is a comparison of the γ′ size of Example 1 with other existing third-generation alloys;

[0033] Figure 5 The TCP phase distribution after creep fracture in Example 1 is shown.

[0034] Figure 6 The creep curve of the alloy prepared in Example 1 under the condition of 1100℃ / 137MPa;

[0035] Figure 7 The creep properties of the alloy prepared in Example 1 are compared with those of three generations of nickel-based single-crystal high-temperature alloys from home and abroad. Detailed Implementation

[0036] To make the objectives, technical solutions, and advantages of this invention clearer, the technical solutions of this invention are described clearly and completely below. Obviously, the described embodiments are only some, not all, of the embodiments of this invention. All other embodiments obtained by those skilled in the art based on the embodiments of this invention without creative effort are within the scope of protection of this invention.

[0037] This invention provides a third-generation nickel-based single-crystal superalloy with high creep performance, achieving a reasonable diffusion coefficient through compositional design. and electron vacancy number (N) V The value is adjusted to balance low diffusion rate and suppression of TCP phase precipitation, thereby improving the creep performance of the alloy. Firstly, as... Figure 1 The image shows a third-generation nickel-based single-crystal superalloy. and N VValues. Among them, the CMSX-10 and CMSX-10K alloys both exhibit creep rupture life exceeding 300 hours under high temperature and low stress, placing them at an internationally advanced level. Therefore, based on their... and N V The upper limit of the value defines the range of values ​​as follows: N V ≤1.59.

[0038] Subsequently, based on the existing composition range of third-generation alloys, with 0.5% as a variable (Hf as a variable of 0.1%), the composition of the combined alloy was... and N V The value is calculated.

[0039] in accordance with and N V The range of values ​​was selected to determine the composition interval, which includes the following elemental components by mass percentage: Cr: 2.0–5.0%, Co: 3.0–12.5%, Al: 5.5–6.0%, Mo: 0–3.0%, W: 5.5–6.0%, Ta: 6.0–8.0%, Re: 4.5–6.0%, Hf: 0–0.2%, with the remainder being Ni and unavoidable impurities.

[0040] Furthermore, to balance low diffusion rate and suppression of TCP phase precipitation, the contents of refractory elements Cr, Re, W, and Mo must be limited to: 13.4% ≤ Cr + Re + W + Mo ≤ 14.5%, and the content of Co, the TCP phase suppressing element, must be 3.0% ≤ n ≤ 3.3%. The selection of these two types of boundary values ​​is also based on the range of corresponding parameters in the CMSX-10 and CMSX-10K alloys. Simultaneously, the Re content v is limited to 5.0% ≤ v ≤ 6.0%. In addition, to improve the strength of the γ′ phase and enhance the creep resistance of the alloy, the Ta / Al ratio is limited to 1.3–1.5.

[0041] Furthermore, based on mass percentage, the nickel-based single-crystal superalloy composition provided by the present invention preferably includes: Cr: 2.0-3.0%, Co: 3.0-3.3%, Al: 5.5%, Mo: 0.5-1.5%, W: 5.5-6.0%, Ta: 7.5-8.0%, Re: 5.0-6.0%, Hf: 0.1%, with the remainder being Ni and unavoidable impurities.

[0042] This invention selects 26 alloys from alloy compositions, the compositions of which are shown in Table 1, and prepares them into button ingot alloys using a vacuum arc melting furnace. Figure 2 This image shows the dimensions of the as-cast dendrite trunks and interdendritic γ′ phases in the button ingot alloys of Examples 1-26. Figure 2It can be seen that the average size of the dendritic trunk γ′ phase is 44–109 nm, and the interdendritic size is 70–192 nm, of which Example 1 ( Figure 2 The central pentagram indicates that the dendrite trunk and interdendritic space of the alloy in Example 1) are the smallest, indicating that the alloy composition has a low diffusion rate.

[0043] Table 1. Nominal composition (wt.%) of Examples 1-26

[0044] alloy Cr Co W Mo Al Re Ta Hf Example 1 2.0 3.0 5.5 0.5 5.5 5.5 7.5 0.1 Example 2 2.0 3.0 5.5 0.5 5.5 5.5 8.0 0.1 Example 3 2.0 3.0 5.5 0.5 5.5 6.0 7.5 0.1 Example 4 2.0 3.0 5.5 0.5 5.5 6.0 8.0 0.1 Example 5 2.0 3.0 5.5 1.0 5.5 5.0 7.5 0.1 Example 6 2.0 3.0 5.5 1.0 5.5 5.0 8.0 0.1 Example 7 2.0 3.0 5.5 1.0 5.5 5.5 7.5 0.1 Example 8 2.0 3.0 5.5 1.0 5.5 5.5 8.0 0.1 Example 9 2.0 3.0 5.5 1.5 5.5 5.0 7.5 0.1 Example 10 2.0 3.0 5.5 1.5 5.5 5.0 8.0 0.1 Example 11 2.0 3.0 6.0 0.5 5.5 5.0 7.5 0.1 Example 12 2.0 3.0 6.0 0.5 5.5 5.0 8.0 0.1 Example 13 2.0 3.0 6.0 0.5 5.5 5.5 7.5 0.1 Example 14 2.0 3.0 6.0 0.5 5.5 5.5 8.0 0.1 Example 15 2.0 3.0 6.0 1.0 5.5 5.0 7.5 0.1 Example 16 2.0 3.0 6.0 1.0 5.5 5.0 8.0 0.1 Example 17 2.5 3.0 5.5 0.5 5.5 5.0 7.5 0.1 Example 18 2.5 3.0 5.5 0.5 5.5 5.0 8.0 0.1 Example 19 2.5 3.0 5.5 0.5 5.5 5.5 7.5 0.1 Example 20 2.5 3.0 5.5 0.5 5.5 5.5 8.0 0.1 Example 21 2.5 3.0 5.5 1.0 5.5 5.0 7.5 0.1 Example 22 2.5 3.0 5.5 1.0 5.5 5.0 8.0 0.1 Example 23 2.5 3.0 6.0 0.5 5.5 5.0 7.5 0.1 Example 24 2.5 3.0 6.0 0.5 5.5 5.0 8.0 0.1 Example 25 3.0 3.0 5.5 0.5 5.5 5.0 7.5 0.1 Example 26 3.0 3.0 5.5 0.5 5.5 5.0 8.0 0.1

[0045] Furthermore, the alloy composition of Example 1 was used to prepare a nickel-based single-crystal high-temperature alloy test bar, including the following steps:

[0046] Elements Ni, Cr, Co, W, Mo, Ta, Re, Al, and Hf, which meet the composition range of Example 1, are sequentially placed into a vacuum induction melting furnace for melting at a temperature of 1580℃ to 1700℃. During the melting process, the vacuum level should be consistently maintained at 0.1 MPa. After obtaining the molten metal, it is cast to form a nickel-based single-crystal superalloy master alloy.

[0047] The nickel-based single-crystal superalloy master alloy obtained by vacuum melting is placed in a crucible of a vacuum induction directional solidification furnace for remelting. During this process, the refining temperature of the nickel-based single-crystal superalloy master alloy is 1500–1560℃, and the refining time is 2–6 min.

[0048] The crystal selection process adopts the spiral crystal selection method. A spiral crystal selector is set at the contact position between the bottom of the single crystal test rod shell and the water cooling plate to select the crystal, that is, to select the appropriate orientation seed crystal in the

[001] direction.

[0049] Molten metal is poured into a single-crystal test rod shell, and then pulled downwards to prepare a nickel-based single-crystal superalloy rod. During the pouring process, the pouring temperature is 1500–1545℃, and the pulling rate is selected as 3–5 mm / min for directional pulling. The single-crystal test rod shell is then pulled out of the heater, and cooled at the bottom using a water-cooling pan. This yields a cast nickel-based single-crystal superalloy rod.

[0050] Furthermore, the alloy test bar from Example 1 was subjected to heat treatment: at room temperature, it was heated to 1280℃~1300℃ at a rate of 5~10℃ / min and held for 2~6 hours; then the temperature was increased to 1310℃~1320℃ at a rate of 2~5℃ / min and held for 1~5 hours; then the temperature was increased to 1320℃~1330℃ at a rate of 2~5℃ / min and held for 5~10 hours. After removal, it was air-cooled to room temperature. A solution-treated nickel-based single-crystal superalloy test bar was obtained.

[0051] In this invention, the cooling rate after solution treatment is preferably 200–300 °C / min. This invention does not have special requirements for the cooling method, as long as the cooling rate can be achieved. In an embodiment of this invention, the cooling method is air cooling.

[0052] In this invention, to prevent oxidation of the alloy at high temperatures, a tube furnace is used for vacuum heat treatment of the test bars. Specifically, the tube furnace is evacuated at room temperature using a molecular pump, then the pump is turned off, and argon gas is introduced into the tube. This process needs to be repeated 3-5 times to ensure the tube is filled with argon. Throughout the process, gas is introduced at one end of the tube while venting is performed at the other end to maintain the required gas pressure and ensure that no gas other than argon is present inside the tube at high temperatures. This state should be maintained for an extended period until the heat treatment is complete.

[0053] Subsequently, an aging treatment was performed, starting from an initial temperature of 20℃ (room temperature), the furnace chamber was heated to 1120℃~1180℃ at a heating rate of 10℃ / min and held for 2~8 hours, then removed and air-cooled to room temperature. At this point, a nickel-based single crystal superalloy test bar after one aging was obtained.

[0054] Finally, a second aging treatment is performed. The nickel-based single-crystal superalloy test bar that has undergone the first aging treatment is placed in a tube furnace, and then heated to 840℃~880℃ at a heating rate of 5℃ / min and held for 20~30h. After that, the test bar is removed and air-cooled to room temperature. At this point, the nickel-based single-crystal superalloy test bar after the second aging treatment is obtained.

[0055] Within the elemental composition range defined by this invention, process parameters such as smelting, casting, and heat treatment have little impact on performance. That is, when the composition is fixed, nickel-based single-crystal high-temperature alloys with similar performance can be obtained within the defined parameter range, and the intermediate values ​​of each parameter range can be preferred.

[0056] Figure 3 The image shows the microstructure of the alloy prepared in Example 1 after heat treatment, specifically the γ / γ′ phase, with an average γ′ phase size of 297 nm. The smaller the γ′ phase size, the greater the resistance to dislocation movement during creep, and the better the creep performance. Figure 4 The figure shows a comparison of the γ′ phase size of the alloy of Example 1 with other third-generation alloys. It can be seen from the figure that the alloy of the present invention has a smaller γ′ phase size among the third-generation alloys.

[0057] Creep tests were conducted on the heat-treated alloy specimens from Example 1 at 1100℃ / 137MPa. Figure 5 and 6 The figures show the microstructure of the alloy in Example 1 after creep fracture and its creep curve at 1100℃ / 137MPa. No TCP phase precipitated in the alloy of Example 1 after creep fracture, and its creep life reached 388h.

[0058] Figure 7 This figure compares the creep performance of the alloy in Example 1 with that of three generations of nickel-based single-crystal superalloys from both domestic and international sources. As can be seen from the figure, the creep life of the alloy in Example 1 is among the best in the previous three generations of nickel-based single-crystal superalloys. The composition design method proposed above in this invention is expected to provide new ideas and criteria for the design of new alloys.

[0059] Finally, it should be noted that the above embodiments are only used to illustrate the technical solutions of the present invention, and not to limit them; although the present invention has been described in detail with reference to the foregoing embodiments, those skilled in the art should understand that modifications can still be made to the technical solutions described in the foregoing embodiments, or equivalent substitutions can be made to some of the technical features; and these modifications or substitutions do not cause the essence of the corresponding technical solutions to deviate from the spirit and scope of the technical solutions of the embodiments of the present invention.

Claims

1. A composition design method for a high-creep-property nickel-based single crystal superalloy, characterized by, The method comprises the following steps: S1, first determine the element types and composition intervals of the currently existing third generation nickel-based single crystal superalloys, obtain different element composition ratios by calculation, and screen out components that meet ≤5.87x10 -15 , N V ≤1.59 from the alloys with different element composition ratios; the designed nickel-based single crystal superalloy is a third generation nickel-based single crystal superalloy with element types selected from Cr, Co, Al, Mo, W, Ta, Re, Hf and Ni; the initial content of each element is based on the composition interval of the currently existing third generation nickel-based single crystal superalloys, and meets: Cr: 2.0-5.0%, Co: 3.0-12.5%, Al: 5.5-6.5%, Mo: 0-3.0%, W: 5.5-6.0%, Ta: 6.0-8.0%, Re: 4.5-6.5%, Hf: 0-0.2%, Ni: 50.0-80.0%; S2, from the components in step S1, the sum m of the contents of Cr, Re, W and Mo satisfies 13.4%≤m≤14.5%, the content n of Co satisfies 3.0%≤n≤3.3%, the content v of Re satisfies 5.0%≤v≤6.0%, and Ta / Al is 1.3-1.5; S3, obtaining the nickel-based single crystal high-temperature alloy components satisfying the components in step S2, and according to the average size of the dendrite stem and the interdendritic γ' phase, the nickel-based single crystal high-temperature alloy component with the smallest average size of the γ' phase is selected from the components, which is the nickel-based single crystal high-temperature alloy with high creep performance.

2. The composition design method of a high-creep-property nickel-based single crystal superalloy according to claim 1, characterized by, In steps S1 and S3, the design method of the components comprises: taking 0.5% as the variable of the content of each element, and designing the composition of each element, wherein the content of Hf is designed by taking 0.1% as the variable.

3. A nickel-based single crystal superalloy characterized by, The alloy composition is designed by the component design method of claim 1 or 2, and the alloy component is as follows in percentage by mass: Cr: 2.0-5.0%, Co: 3.0-12.5%, Al: 5.5-6.5%, Mo: 0-3.0%, W: 5.5-6.0%, Ta: 6.0-8.0%, Re: 4.5-6.5%, Hf: 0-0.1%, and the rest is Ni and inevitable impurities; the diffusion coefficient of the alloy component and the number of electron vacancies Nv simultaneously satisfy ≤5.87×10 -15 , N V ≤1.

59.

4. The nickel-base, single-crystal superalloy of claim 3, wherein, The sum m of the contents of Cr, Re, W and Mo satisfies 13.4%≤m≤14.5%, the content n of Co satisfies 3.0%≤n≤3.3%, the content v of Re satisfies 5.0%≤v≤6.0%, and Ta / Al is 1.3-1.

5.

5. The nickel-based single crystal superalloy of claim 3 or 4, wherein, The alloy component is as follows in terms of mass percentage: Cr: 2.0-3.0%, Co: 3.0-3.3%, Al: 5.5%, Mo: 0.5-1.5%, W: 5.5-6.0%, Ta: 7.5-8.0%, Re: 5.0-6.0%, Hf: 0.1%, and the rest is Ni and inevitable impurities.

6. A method of producing the nickel-based single crystal superalloy of any one of claims 3-5, characterized in that, The method comprises the following steps: The alloy raw materials are weighed according to the alloy component mass percentage, and a master alloy is obtained by melting; the master alloy is remelted and poured to obtain a single crystal rod by directional drawing; then the single crystal rod is heat treated to obtain the nickel-based single crystal high-temperature alloy.

7. The method of producing a nickel-based single crystal superalloy according to claim 6, characterized in that The heat treatment comprises solution treatment and aging treatment; the solution treatment comprises: first, heating from room temperature to 1280-1300℃ at a rate of 5-10℃ / min, and keeping the temperature for 2-6h; then, heating to 1310-1320℃ at a rate of 2-5℃ / min, and keeping the temperature for 1-5h; finally, heating to 1320-1330℃ at a rate of 2-5℃ / min, and keeping the temperature for 5-10h, and then air cooling to room temperature; And / or, the aging treatment comprises: first, heating to 1120-1180℃, keeping the temperature for 2-8h, and air cooling to room temperature; then, heating to 840-880℃, keeping the temperature for 20-30h, and air cooling to room temperature; The heat treatment is carried out in an argon atmosphere.

8. The method of producing a nickel-based single crystal superalloy according to claim 6, wherein The melting temperature is 1580-1700℃, and the vacuum degree should be kept at 0.1MPa; the remelting temperature is 1500-1560℃, and the time is 2-6min; And / or, the temperature gradient of the directional drawing is 30-80K / cm, and the drawing rate of the single crystal is 50-160μm / s.

9. The method of producing a nickel-based single crystal superalloy according to any one of claims 6 to 8, characterized in that After the heat treatment, the average size of the γ' phase in the nickel-based single crystal high-temperature alloy is ≤300nm; the creep life of the nickel-based single crystal high-temperature alloy under the condition of 1100℃ / 137MPa reaches 388h.

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