Nickel-based superalloy with good stability and oxidation resistance, its preparation method and application

Abstract

The present invention belongs to the technical field of superalloys, and particularly relates to a nickel-based superalloy with good stability and oxidation resistance, and a preparation method and application thereof. A nickel-based superalloy with good stability and oxidation resistance disclosed by the present invention includes: C: 0.08 to 0.22%; Cr: 8.5 to 10.5%; Co: 9.5 to 11.5%; W: 8.0 to 10.0%; Mo: 0.15 to 1.55%; Ta: 3.0 to 4.5%; Al: 4.0 to 5.5%; Ti: 0.3 to 2.0%; B: 0.015 to 0.025%; Hf: 0.5 to 1.5%; Zr: 0.002 to 0.007%; Sr: 0.05 to 0.1%; Ba: 0.01 to 0.05%; Mg: 0.001 to 0.004%; Si ≤ 0.15%; Mn ≤ 0.05%; the balance is Ni and inevitable impurities, by mass percentage.

Description

Technical Field

[0001] The present invention belongs to the technical field of superalloys, and particularly relates to a nickel-based superalloy with good stability and oxidation resistance, and a preparation method and application thereof. Background Art

[0002] Nickel-based superalloys are a type of superalloy with nickel as the matrix and other alloying elements added, having relatively high strength, good oxidation resistance and corrosion resistance. However, with the development of aeroengines and gas turbines, the problem of fatigue failure of turbine blades has become increasingly prominent, which poses higher requirements for the stability and oxidation resistance of nickel-based superalloys.

[0003] Currently, the hot-end components of advanced aeroengines and gas turbines have working conditions up to 1300°C at most, with complex stress actions and demanding requirements for alloy materials. Alloys that can meet the mechanical properties will have problems such as weak stability and poor oxidation resistance. There are almost no alloys among the existing superalloys at home and abroad that can fully meet the requirements of good mechanical properties, strong stability and good oxidation resistance.

[0004] Therefore, how to produce superalloys that meet the usage requirements of aeroengines and gas turbines has received more and more extensive attention. Summary of the Invention

[0005] The present invention is made based on the inventor's discovery and recognition of the following facts and problems:

[0006] The superalloys used in fields such as advanced aeroengines and gas turbines are expected to achieve the following performance indicators: at room temperature, the tensile properties are Rm≥1150MPa, Rp0.2≥900MPa, A≥7%; at high temperature tensile of 900°C, Rm≥850MPa, Rp0.2≥650MPa, A≥8%, and no TCP phase is generated after 3000h at 980°C, and at the same time, it has good oxidation resistance. However, the current superalloys cannot simultaneously have good mechanical properties, stability and oxidation resistance. Therefore, it is necessary to further research and improve nickel-based superalloys.

[0007] The embodiments of the present invention aim to solve at least one of the technical problems in the related technologies to some extent. For this reason, the embodiments of the present invention propose a nickel-based superalloy with good stability and oxidation resistance. This nickel-based superalloy with good stability and oxidation resistance not only has excellent mechanical properties, but also has long-term stability and oxidation resistance, fully meeting the requirements of the design and use of advanced aeroengines and gas turbines, and is applicable to components such as turbine blades in the hot-end parts of aeroengines and gas turbines that serve in the medium and long term.

[0008] The nickel-based superalloy with good stability and oxidation resistance according to the embodiments of the present invention comprises: C: 0.08-0.22%; Cr: 8.5-10.5%; Co: 9.5-11.5%; W: 8.0-10.0%; Mo: 0.15-1.55%; Ta: 3.0-4.5%; Al: 4.0-5.5%; Ti: 0.3-2.0%; B: 0.015-0.025%; Hf: 0.5-1.5%; Zr: 0.002-0.007%; Sr: 0.05-0.1%; Ba: 0.01-0.05%; Mg: 0.001-0.004%; Si≤0.15%; Mn≤0.05%; the balance being Ni and inevitable impurities, by mass percentage.

[0009] The advantages and technical effects brought by the nickel-based superalloy with good stability and oxidation resistance according to the embodiments of the present invention are as follows: 1. In the embodiments of the present invention, the Sr element added to the alloy can refine the grains and improve the oxidation resistance of the alloy; 2. In the embodiments of the present invention, the element Ba added to the alloy can refine the as-cast structure and grains of the alloy. Adding Ba to the Mg-containing nickel-based alloy can improve the room-temperature tensile strength and elongation of the alloy, achieving a good match between strength and toughness. In addition, the Ba element can promote further deoxidation and desulfurization of the alloy, making the alloy pure; 3. In the embodiments of the present invention, by controlling the amounts of various metal elements within a reasonable range, the alloy not only has excellent tensile properties and creep life, but also has excellent oxidation resistance and can be applied to advanced aeroengines and gas turbines.

[0010] In some embodiments, Sr and Ba satisfy the relationship 0.2 < Sr + 12.5Ba < 0.6, where Sr and Ba are the values obtained by removing the percentage sign from the mass percentages of elements Sr and Ba in the nickel-based superalloy.

[0011] In some embodiments, Sr and Ba satisfy the relationship 0.31 ≤ Sr + 12.5Ba ≤ 0.58.

[0012] In some embodiments, Cr, B, and Sr satisfy the relationship 5.5 < Cr - 8.5B / Sr < 8.5, where Cr, B, and Sr are the values obtained by removing the percentage sign from the mass percentages of elements Cr, B, and Sr in the nickel-based superalloy.

[0013] In some embodiments, Cr, B, and Sr satisfy the relationship 6.2 ≤ Cr - 8.5B / Sr ≤ 7.8.

[0014] In some embodiments, it includes: C: 0.09 to 0.21%; Cr: 8.6 to 10.3%; Co: 9.6 to 11.4%; W: 8.1 to 9.8%; Mo: 0.35 to 1.52%; Ta: 3.1 to 4.4%; Al: 4.2 to 5.4%; Ti: 0.4 to 1.8%; B: 0.018 to 0.024%; Hf: 0.7 to 1.4%; Zr: 0.003 to 0.006%; Sr: 0.05 to 0.09%; Ba: 0.01 to 0.04%; Mg: 0.002 to 0.004%; Si ≤ 0.02%; Mn ≤ 0.02%; the balance is Ni and unavoidable impurities, by mass percentage.

[0015] An embodiment of the present invention also provides an application of a nickel-based superalloy with good stability and oxidation resistance in the hot-end components of an aeroengine.

[0016] An embodiment of the present invention also provides an application of a nickel-based superalloy with good stability and oxidation resistance in the hot-end components of a gas turbine.

[0017] An embodiment of the present invention also provides a preparation method of a nickel-based superalloy with good stability and oxidation resistance, comprising the following steps:

[0018] (1) According to the alloy design ratio, add raw materials of Cr, Co, W, Mo, Ta, B, Hf, Zr, Mg, Si, Mn, Ba, Sr and part of C into the crucible, heat and melt under vacuum, and then carry out heat preservation treatment;

[0019] (2) After the heat preservation treatment in step (1) is completed, add Al, Ti and the remaining C raw materials into the crucible, introduce argon, heat and melt under vacuum, and cast to obtain a nickel-based superalloy.

[0020] The advantages and technical effects brought by the preparation method of the nickel-based superalloy with good stability and oxidation resistance in the embodiments of the present invention are as follows: 1. In the method of the embodiments of the present invention, adding C element step by step is beneficial to removing gases in the alloy and can also improve the mechanical properties of the alloy; 2. The alloy prepared by the method of the embodiments of the present invention not only has excellent tensile properties and creep life, but also has excellent oxidation resistance, and can meet the requirements of the design and use of advanced aeroengines and gas turbines.

[0021] In some embodiments, in step (1), the part of C raw materials is 10 to 20% of the designed dosage of C raw materials. Specific embodiments

[0022] The embodiments of the present invention are described in detail below. The embodiments are exemplary and are intended to explain the present invention and should not be construed as limiting the present invention.

[0023] The nickel-based superalloy with good stability and oxidation resistance according to the embodiments of the present invention comprises: C: 0.08-0.22%; Cr: 8.5-10.5%; Co: 9.5-11.5%; W: 8.0-10.0%; Mo: 0.15-1.55%; Ta: 3.0-4.5%; Al: 4.0-5.5%; Ti: 0.3-2.0%; B: 0.015-0.025%; Hf: 0.5-1.5%; Zr: 0.002-0.007%; Sr: 0.05-0.1%; Ba: 0.01-0.05%; Mg: 0.001-0.004%; Si≤0.15%; Mn≤0.05%; the balance is Ni and unavoidable impurities, calculated by mass percentage.

[0024] The nickel-based superalloy with good stability and oxidation resistance according to the embodiments of the present invention, the Sr element added to the alloy can refine the grains and improve the oxidation resistance of the alloy; the element Ba added to the alloy can refine the as-cast structure and grains of the alloy. Adding Ba to the Mg-containing nickel-based alloy can improve the room-temperature tensile strength and elongation of the alloy, achieving a good match between strength and toughness. In addition, the Ba element can promote further deoxidation and desulfurization of the alloy, making the alloy pure. By controlling the dosages of various metal elements within a reasonable range, the alloy not only has excellent tensile properties and creep life, but also has excellent oxidation resistance and can be applied to advanced aeroengines and gas turbines.

[0025] Among them, the functions of each element in the alloy according to the embodiments of the present invention are as follows:

[0026] C: C can form MC-type carbides in the nickel-based superalloy to inhibit the growth of austenite grains during heating and form M 23 C6 and other types of carbides along the grain boundaries, playing a role in strengthening the grain boundaries, which can delay the initiation, propagation and coalescence of microcracks, thereby improving the high-temperature creep life of the alloy. In the embodiments of the present invention, the content of element C in the alloy is controlled to be 0.08-0.22%.

[0027] Cr: Cr can improve the oxidation resistance of the alloy and has a solid-solution strengthening effect. After aging treatment, it can also combine with C to form granular M 23 C6 distributed along the grain boundaries, playing a role in strengthening the grain boundaries. In the embodiments of the present invention, the content of element Cr is controlled to be 8.5-10.5%.

[0028] Co: Co is an important solution strengthening element and precipitation strengthening element, providing good solution strengthening effect for the alloy. It can significantly reduce the stacking fault energy of the matrix, widen the width of the extended dislocation, making it difficult for dislocations to bunch up and undergo cross-slip, thereby improving the creep resistance and rupture life of the alloy. Co can also partially replace the elements in the precipitation strengthening phase of the Ni3Al type phase, improving the stability of the phase during long-term service. In the embodiments of the present invention, the content of Co is controlled to be 9.5 - 11.5%.

[0029] W and Mo: W and Mo are the main solution strengthening elements. They can be dissolved in both the alloy matrix and the γ' strengthening phase, and at the same time can increase the interatomic binding force, raise the diffusion activation energy and recrystallization temperature, thereby effectively improving the high-temperature strength. In the embodiments of the present invention, the content of element Mo is controlled to be 0.15 - 1.55%, and the content of element W is controlled to be 8.0 - 10.0%.

[0030] Al, Ti and Ta: They are the forming elements of the strengthening phase γ' in nickel-based alloys. With the increase of the content of the three, the number of γ' increases, and the high-temperature creep and rupture properties are improved; in addition, Ti and Ta will also combine with C to form MC-type carbides, which hinder the growth and sliding of grain boundaries at high temperatures, playing a role in improving the high-temperature mechanical properties of nickel-based alloys. In the embodiments of the present invention, Al is controlled to be 4.0 - 5.5%, Ti is 0.3 - 2.0%, and Ta is 3.0 - 4.5%.

[0031] B: B atoms are easily enriched at grain boundaries, preventing harmful low-melting-point elements from segregating at grain boundaries and improving the grain boundary binding force; borides on grain boundaries can prevent grain boundary slip, void initiation and propagation, which is beneficial to improving the creep resistance and rupture life of the alloy. In the embodiments of the present invention, the content of B is controlled to be 0.015 - 0.025%.

[0032] Zr: Zr helps to purify grain boundaries and enhance grain boundary binding force. The combined addition of Zr and B helps to maintain the high-temperature strength and rupture life of the alloy, but excessive Zr is likely to reduce the processing performance. In the embodiments of the present invention, the content of Zr is controlled to be 0.002 - 0.007%.

[0033] Mg: Mg segregates at grain boundaries to improve grain boundary binding force and increase grain boundary strength. Mg atoms not only segregate at grain boundaries, but also at carbide phase boundaries and γ' phase boundaries. Mg atoms also enter γ' and carbides, which is beneficial to improving the mechanical properties of the alloy. In the embodiments of the present invention, the content of Mg is controlled to be 0.01 - 0.004%.

[0034] Ba: Ba can significantly refine the as-cast structure of the alloy, partially break the network-like β phase, and distribute it in small pieces at the grain boundaries. Moreover, the alloy grain refinement effect is remarkable. After adding Ba to the Ni-based alloy containing Mg, the tensile strength and elongation rate of the alloy can be improved simultaneously, achieving an excellent strength-ductility match; Ba can promote further deoxidation and desulfurization of the alloy in the alloy, making the alloy pure. In the embodiments of the present invention, the Ba content is controlled to be 0.01-0.05%.

[0035] Sr: The Sr element can significantly refine the grains, and the alloy grain size decreases with the increase of the Sr content. Sr can improve the oxidation resistance of the alloy. However, with the addition of Sr, a compound phase distributed in a network along the grain boundaries appears in the alloy, increasing the brittleness of the as-cast alloy; with the increase of the Sr content, the strength and elongation rate of the as-cast alloy both decrease. Therefore, in the embodiments of the present invention, the Sr content is controlled to be 0.05-0.1%.

[0036] In some embodiments, preferably, the Sr and Ba satisfy the relationship 0.2 < Sr + 12.5Ba < 0.6, where Sr and Ba are the values after removing the percentage sign from the mass percentage contents of the elements Sr and Ba in the Ni-based superalloy. Further preferably, the Sr and Ba satisfy the relationship 0.31 ≤ Sr + 12.5Ba ≤ 0.58.

[0037] In the embodiments of the present invention, limiting the Sr and Ba to satisfy the relationship 0.2 < Sr + 12.5Ba < 0.6 can give full play to the synergistic effect of Sr and Ba, which is beneficial to improving the stability and oxidation resistance of the alloy.

[0038] In some embodiments, preferably, the Cr, B, and Sr satisfy the relationship 5.5 < Cr - 8.5B / Sr < 8.5, where Cr, B, and Sr are the values after removing the percentage sign from the mass percentage contents of the elements Cr, B, and Sr in the Ni-based superalloy. Further preferably, the Cr, B, and Sr satisfy the relationship 6.2 ≤ Cr - 8.5B / Sr ≤ 7.8.

[0039] In the embodiments of the present invention, limiting the Cr, B, and Sr to satisfy the relationship 5.5 < Cr - 8.5B / Sr < 8.5 can give full play to the synergistic effect of Cr, B, and Sr, which is beneficial to improving the tensile properties and oxidation resistance of the alloy.

[0040] In some embodiments, preferably, the nickel-based superalloy with good stability and oxidation resistance includes: C: 0.09 - 0.21%; Cr: 8.6 - 10.3%; Co: 9.6 - 11.4%; W: 8.1 - 9.8%; Mo: 0.35 - 1.52%; Ta: 3.1 - 4.4%; Al: 4.2 - 5.4%; Ti: 0.4 - 1.8%; B: 0.018 - 0.024%; Hf: 0.7 - 1.4%; Zr: 0.003 - 0.006%; Sr: 0.05 - 0.09%; Ba: 0.01 - 0.04%; Mg: 0.002 - 0.004%; Si ≤ 0.02%; Mn ≤ 0.02%; the balance is Ni and unavoidable impurities, by mass percentage.

[0041] The embodiments of the present invention also provide an application of the nickel-based superalloy with good stability and oxidation resistance in the hot-end components of an aeroengine. The nickel-based superalloy with good stability and oxidation resistance in the embodiments of the present invention has excellent stability, tensile properties and oxidation resistance, and can be applied to the hot-end components of an aeroengine.

[0042] The embodiments of the present invention also provide an application of the nickel-based superalloy with good stability and oxidation resistance in the hot-end components of a gas turbine. The nickel-based superalloy with good stability and oxidation resistance in the embodiments of the present invention has excellent stability, tensile properties and oxidation resistance, and can be applied to the hot-end components of a gas turbine.

[0043] The embodiments of the present invention also provide a preparation method of the nickel-based superalloy with good stability and oxidation resistance, including the following steps:

[0044] (1) According to the alloy design ratio, add Cr, Co, W, Mo, Ta, B, Hf, Zr, Mg, Si, Mn, Ba, Sr and part of the C raw materials into the crucible, heat and melt them under vacuum, and then carry out heat preservation treatment;

[0045] (2) After the heat preservation treatment in step (1) is completed, add Al, Ti and the remaining C raw materials into the crucible, introduce argon, heat and melt them under vacuum, and cast to obtain the nickel-based superalloy.

[0046] The preparation method of the nickel-based superalloy with good stability and oxidation resistance in the embodiments of the present invention adds the C element step by step, which is beneficial to removing the gas in the alloy and can also improve the mechanical properties of the alloy; the obtained alloy not only has excellent tensile properties and creep life, but also has excellent oxidation resistance, and can meet the requirements of the design and use of advanced aeroengines and gas turbines.

[0047] In some embodiments, preferably, in step (1), the partial C raw material is 10-20% of the designed dosage of the C raw material. Further preferably, in step (1), the temperature for heat preservation is 1600°C to 1650°C, and the time for heat preservation is 10-30 min. In step (2), the amount of argon introduced is such that the pressure in the crucible is -0.02 to -0.1 MPa; the vacuum degree of the vacuum condition is <0.1 Pa, and the casting temperature is ≥1560°C.

[0048] The technical solution of the present invention will be described in detail below in conjunction with specific embodiments.

[0049] Example 1

[0050] (1) Add Cr, Co, W, Mo, Ta, B, Hf, Zr, Mg, Si, Mn, Ba, Sr and 15% of the C raw material into the crucible, heat it under vacuum until it melts completely, then control the temperature at 1610°C, control the vacuum degree to be less than 0.1 Pa, keep it warm for 10 min and then stop heating, and hold for 5 min;

[0051] (2) Add Al, Ti and the remaining C raw material into the crucible; at the same time, fill the furnace with argon until the pressure is -0.02 MPa, heat and melt it under the condition that the vacuum degree is less than 0.1 Pa, tap the steel at 1560°C for casting, cool it to room temperature, demold it, and perform surface sandblasting and grinding to remove the oxide scale to obtain a nickel-based superalloy.

[0052] The preparation methods of Examples 2-8 are the same as those of Example 1, except that the alloy compositions are different. The alloy compositions prepared in Examples 1-8 are shown in Table 1, and the performances are shown in Table 2.

[0053] Comparative Example 1

[0054] The preparation method of Comparative Example 1 is the same as that of Example 1, the difference is that the alloy composition is different, the alloy does not contain the Ba element, and the performance data of the alloy prepared in Comparative Example 1 are shown in Table 2.

[0055] Comparative Example 2

[0056] The preparation method of Comparative Example 2 is the same as that of Example 1, the difference is that the alloy composition is different, the Ba content in the alloy is 0.10%, and the performance data of the alloy prepared in Comparative Example 2 are shown in Table 2.

[0057] Comparative Example 3

[0058] The preparation method of Comparative Example 3 is the same as that of Example 1, the difference is that the alloy composition is different, the Cr content in the alloy is 8.0%, and the performance data of the alloy prepared in Comparative Example 3 are shown in Table 2.

[0059] Comparative Example 4

[0060] The preparation method of Comparative Example 4 was the same as that of Example 1, except that the alloy composition was different. The alloy did not contain Sr element. The performance data of the alloy obtained in Comparative Example 4 are shown in Table 2.

[0061] Comparative Example 5

[0062] The preparation method of Comparative Example 5 was the same as that of Example 1, except that the alloy composition was different. The content of element Sr in the alloy was 0.2%. The performance data of the alloy obtained in Comparative Example 5 are shown in Table 2.

[0063] Table 1

[0064] Example 1 Example 2 Example 3 Example 4 Example 5 Example 6 Example 7 Example 8 C(％) 0.09 0.1 0.15 0.19 0.09 0.14 0.16 0.21 Cr(％) 8.6 8.7 10.3 9.7 8.9 9.3 9.4 9.7 Co(%) 10.5 9.6 10.3 9.8 10.7 11.4 11.2 10.9 W(％) 8.5 9.5 8.6 8.1 9.4 9.8 9.1 8.9 Mo(%) 0.4 0.35 0.18 0.89 0.69 0.97 1.25 1.52 Ta(%) 3.5 3.2 4.2 4.1 4.4 3.9 3.1 3.7 Al(％) 4.5 4.2 5.2 4.8 5.4 4.7 4.3 4.9 Ti(%) 0.9 0.5 1.2 0.7 1.6 1.8 0.6 0.4 B(％) 0.021 0.024 0.018 0.022 0.019 0.024 0.023 0.021 Hf(%) 1.0 0.7 0.9 0.8 1.2 1.4 1.1 1.3 Zr(％) 0.005 0.003 0.006 0.004 0.006 0.005 0.004 0.005 Mg(%) 0.003 0.002 0.002 0.003 0.004 0.003 0.002 0.004 Si(%) 0.01 0.02 0.01 0.01 0.01 0.02 0.01 0.01 Mn(%) 0.01 0.01 0.01 0.01 0.01 0.02 0.01 0.01 Sr(％) 0.05 0.06 0.06 0.09 0.06 0.08 0.07 0.08 Ba(%) 0.01 0.02 0.01 0.03 0.04 0.04 0.03 0.04 Sr + 12.5Ba 0.175 0.310 0.185 0.465 0.560 0.580 0.445 0.580 Cr - 8.5B / Sr 5.030 5.300 7.750 7.622 6.208 6.750 6.607 7.469

[0065] Table 2

[0066]

[0067]

[0068] Note: 1. TCP phase test: The microstructure of the specimen after being treated at 980 °C for 3000 h was observed by scanning electron microscope;

[0069] 2. Rm is the tensile strength, Rp0.2 is the tensile yield strength, and A is the elongation;

[0070] 3. The average oxidation rate is the oxidation rate per unit area of the alloy at 900 °C / 100 h. The smaller this value is, the better the oxidation resistance.

[0071] It can be seen from the data in the above table that the nickel-based superalloys obtained in Examples 1 to 8 have very good tensile properties at room temperature and 900 °C. At room temperature, the tensile properties are Rm ≥ 1150 MPa, Rp0.2 ≥ 900 MPa, and A ≥ 7.5%; at 900 °C high-temperature tensile, Rm ≥ 890 MPa, Rp0.2 ≥ 680 MPa, and A ≥ 8.5%. And they have very good stability and oxidation resistance, and can meet the use requirements of superalloys in fields such as aeroengines and gas turbines. In particular, when the relational expressions 0.2 < Sr + 12.5Ba < 0.6 and 5.5 < Cr - 8.5B / Sr < 8.5 are satisfied, such as in Examples 4 to 8, the obtained nickel-based superalloys have more excellent properties.

[0072] In Comparative Example 1, element Ba was not contained. Although the tensile strength of the obtained nickel-based superalloy could be maintained at a relatively high level at room temperature and 900 °C, the elongation rates at room temperature and 900 °C were reduced to 7.0% and 6.0% respectively; in Comparative Example 2, the content of element Ba was too high, resulting in a significant decrease in the tensile strength and elongation rate of the alloy at room temperature and 900 °C, and the average oxidation rate increased to 0.25 g / m2 ·h, unable to meet the usage requirements.

[0073] In Comparative Example 3, the content of element Cr is too low. The prepared nickel-based superalloy still has a relatively high tensile strength at room temperature, but the elongation rate at room temperature is reduced to 5.5%, and both the tensile strength and elongation rate at 900 °C are significantly reduced, and the oxidation resistance is also reduced, unable to meet the usage requirements.

[0074] In Comparative Example 4, the Sr element is not added. Although the tensile strength and elongation rate of the prepared nickel-based superalloy can be maintained at a relatively high level at room temperature and 900 °C, the average oxidation rate increases to 0.17 g / m 2 ·h, and the oxidation resistance is relatively low. In Comparative Example 5, the content of the Sr element is too high, resulting in a significant reduction in the tensile strength and elongation rate of the prepared nickel-based superalloy at room temperature and 900 °C, unable to meet the usage requirements.

[0075] In the present invention, the terms "one embodiment", "some embodiments", "example", "specific example", or "some examples", etc. mean that the specific features, structures, materials, or characteristics described in connection with the embodiment or example are included in at least one embodiment or example of the present invention. In this specification, the schematic representations of the above terms do not necessarily refer to the same embodiment or example. Moreover, the specific features, structures, materials, or characteristics described can be combined in a suitable manner in any one or more embodiments or examples. In addition, without contradiction, those skilled in the art can combine and combine the different embodiments or examples described in this specification and the features of different embodiments or examples.

[0076] Although the above embodiments have been shown and described, it can be understood that the above embodiments are exemplary and should not be construed as limiting the present invention. Any changes, modifications, substitutions, and variations made by those of ordinary skill in the art to the above embodiments are within the protection scope of the present invention.

Claims

1. A nickel-based superalloy with good stability and antioxidant properties, characterized in that, Comprising: C: 0.08 - 0.22%; Cr: 8.5 - 10.5%; Co: 9.5 - 11.5%; W: 8.0 - 10.0%; Mo: 0.15 - 1.55%; Ta: 3.0 - 4.5%; Al: 4.0 - 5.5%; Ti: 0.3 - 2.0%; B: 0.015 - 0.025%; Hf: 0.5 - 1.5%; Zr: 0.002 - 0.007%; Sr: 0.05 - 0.1%; Ba: 0.01 - 0.05%; Mg: 0.001 - 0.004%; Si ≤ 0.15%; Mn ≤ 0.05%; the balance being Ni and unavoidable impurities, by mass percentage; The Sr and Ba satisfy the relationship 0.2 < Sr + 12.5Ba < 0.6, where Sr and Ba are the values after removing the percentage sign of the mass percentages of elements Sr and Ba in the nickel-based superalloy.

2. The nickel-based superalloy with good stability and oxidation resistance according to claim 1, characterized in that, The Sr and Ba satisfy the relationship 0.31 ≤ Sr + 12.5Ba ≤ 0.

58.

3. The nickel-based superalloy with good stability and antioxidant property according to claim 1, characterized in that, The Cr, B, and Sr satisfy the relationship 5.5 < Cr - 8.5B / Sr < 8.5, where Cr, B, and Sr are the values after removing the percentage sign of the mass percentages of elements Cr, B, and Sr in the nickel-based superalloy.

4. The nickel-based superalloy with good stability and oxidation resistance according to claim 3, characterized in that, The Cr, B, and Sr satisfy the relationship 6.2 ≤ Cr - 8.5B / Sr ≤ 7.

8.

5. The nickel-based superalloy with good stability and antioxidant property according to claim 1, wherein, Comprising: C: 0.09 - 0.21%; Cr: 8.6 - 10.3%; Co: 9.6 - 11.4%; W: 8.1 - 9.8%; Mo: 0.35 - 1.52%; Ta: 3.1 - 4.4%; Al: 4.2 - 5.4%; Ti: 0.4 - 1.8%; B: 0.018 - 0.024%; Hf: 0.7 - 1.4%; Zr: 0.003 - 0.006%; Sr: 0.05 - 0.09%; Ba: 0.01 - 0.04%; Mg: 0.002 - 0.004%; Si ≤ 0.02%; Mn ≤ 0.02%; the balance being Ni and unavoidable impurities, by mass percentage.

6. Application of the nickel-based superalloy with good stability and oxidation resistance according to any one of claims 1 - 5 in the hot-end components of an aeroengine.

7. Application of the nickel-based superalloy with good stability and oxidation resistance according to any one of claims 1 - 5 in the hot-end components of a gas turbine.

8. A method for preparing a nickel-based superalloy with good stability and antioxidant property according to any one of claims 1 to 5, characterized in that, Comprising the following steps: (1) According to the alloy design ratio, add Cr, Co, W, Mo, Ta, B, Hf, Zr, Mg, Si, Mn, Ba, Sr, and part of the C raw materials into the crucible, heat and melt under vacuum, and then carry out heat preservation treatment; (2) After the heat preservation treatment in step (1) is completed, add Al, Ti, and the remaining C raw materials into the crucible, introduce argon, heat and melt under vacuum, and cast to obtain the nickel-based superalloy.

9. The preparation method of the nickel-based superalloy with good stability and antioxidant property as described in claim 8, characterized in that, In step (1), the part of the C raw materials is 10 - 20% of the designed dosage of the C raw materials.

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