Ni-Fe-based high-temperature alloy material, preparation method thereof and application thereof in ammonia thermal reaction kettle

Abstract

The application belongs to the technical field of metallurgy, and proposes a Ni-Fe-based high-temperature alloy material, a preparation method thereof and application of the material in ammonia thermal reaction kettles. The Ni-Fe-based high-temperature alloy material comprises the following components in percentage by mass: Ni: 40-45%, Cr: 15-20%, Nb: 2.5-3.5%, Ta: 1.5-2.5%, Al: 0.4-0.6%, Ti: 0.85-1.25%, C: <0.06%, and the balance is Fe and other inevitable impurities. Compared with the prior art, the Ni-Fe-based high-temperature alloy material has high strength under high-temperature and high-pressure environments and excellent impact toughness at low temperatures, and can be particularly used in ammonia thermal method reaction kettle body materials.

Description

Technical Field

[0001] This invention relates to the field of metallurgical technology, and in particular to a Ni-Fe based high-temperature alloy material, its preparation method, and its application in an ammonia-thermal reactor. Background Technology

[0002] Gallium nitride (GaN), as a representative of third-generation wide-bandgap semiconductor materials, holds an irreplaceable core position in fields such as optoelectronics and high-frequency high-power microwave devices. The ammonothermal method is considered the most promising technology for achieving high-quality, large-size GaN single-crystal mass production. However, the ammonothermal method operates under extremely harsh conditions. The reactor typically needs to operate continuously for weeks or even months at high temperatures (550℃~650℃) and ultra-high pressures (100 MPa~300 MPa). This extreme physicochemical environment places extremely high demands on the reactor material.

[0003] When traditional alloys are held at 650℃ for extended periods, the metastable strengthening phases (such as the γ′′ phase) are highly susceptible to transformation into the harmful δ phase, or the precipitation of TCP phases (such as the σ phase or the Laves phase), leading to severe "hot brittleness" in the material. This results in the reactor lacking sufficient impact toughness (typically far below 50 J) during shutdown cooling, depressurization, or handling at liquid ammonia filling temperatures (such as -60℃), making it highly prone to catastrophic brittle fracture.

[0004] In the field of traditional commercially available wrought nickel-based superalloys (such as IN718, IN706, Rene41, and Waspaloy), especially for alloys used in the manufacture of critical rotating components such as turbine disks for aero-engines, the inherent contradiction and trade-off between high-temperature strength stability and low-temperature impact toughness has always been a core challenge in materials design and application. This contradiction stems from the conflicting requirements of both for microstructure, particularly grain boundary state and precipitated phase characteristics. Essentially, it is about finding a specific balance point between these contradictions. Existing technologies mainly adopt the following strategies, but all of them are accompanied by new problems, such as: the trade-off in composition design, strictly controlling the total amount of aluminum and titanium and the Al / Ti ratio to balance the strengthening of precipitated phases and the tendency for grain boundary brittleness. However, the upper limit of the total amount of strengthening elements is limited by the sharp decline in toughness and hot workability; fine control of heat treatment regime: compromise of aging regime, on the premise of ensuring the full precipitation of the main strengthening phase (such as γ″ phase in IN718, γ′ phase in Waspaloy), controlling the aging temperature and duration to avoid excessive growth of grain boundary carbides and precipitation of harmful phases, but it is often difficult to make the two aspects of performance reach their respective optimal values ​​at the same time.

[0005] Existing commercial wrought nickel-based superalloy technologies have the following drawbacks: The grain boundary carbide strengthening mechanism, which relies on high-temperature strength stability, is inherently conflicted with the grain boundary cleanliness and toughness required for low-temperature impact toughness. Traditional thermomechanical processing (TMP) and heat treatment can only adjust this contradiction to an acceptable "compromise" within a specific alloy composition framework, but cannot achieve a synergistic improvement. When service environments require components to maintain strength stability at higher temperatures while also withstanding greater impact loads at low temperatures (such as the more stringent requirements placed on turbine disks by next-generation high thrust-to-weight ratio engines), this compromise-based design faces the risk of failure.

[0006] CN104583432A provides a Ni-based alloy containing, by mass ratio, 30-40% Fe, 14-16% Cr, 1.2-1.7% Ti, 1.1-1.5% Al, 1.9-2.7% Nb, and 40 ppm-150 ppm P, with the remainder being Ni and unavoidable impurities. This Ni-based alloy relies on a relatively high content of Al (1.1-1.5%) and Ti (1.2-1.7%) to promote the formation of precipitation-strengthening phases. However, the high Al and Ti content tends to promote grain boundary embrittlement during long-term hot service. Furthermore, a technical means to address hydrogen embrittlement is the mandatory addition of 40 ppm-150 ppm of phosphorus (P) to "suppress excessive hydrogen accumulation at grain boundaries by increasing grain boundary uniformity." However, the segregation of P often adversely affects the low-temperature toughness of the material.

[0007] CN104884662A provides an Fe-Ni based alloy with excellent high-temperature properties and resistance to hydrogen embrittlement. The composition of the Fe-Ni based alloy, by mass%, is as follows: C: 0.005% to 0.10%, Si: 0.01% to 0.10%, P: less than 0.015%, S: less than 0.003%, Ni: 23.0% to 27.0%, Cr: 12.0% to 16.0%, Mo: less than 0.01%, Nb: less than 0.01%, W: 2.5% to 6.0%, Al: 1.5% to 2.5%, and Ti: 1.5% to 2.5%, with the balance being Fe and other unavoidable impurities. To avoid the precipitation of brittle phases under long-term aging, this Fe-Ni based alloy, which has excellent high-temperature properties and resistance to hydrogen embrittlement, adopts a scheme that limits Nb (below 0.01%) and instead relies on the addition of 2.5~6.0% W and a single γ' phase (requiring a volume ratio of more than 15%) to maintain strength.

[0008] Therefore, for the structural materials of ammonia thermoelectric reactors, there is an urgent need for a new alloy composition and corresponding preparation method. The goal is no longer to find the traditional "balance point", but to break the conflict of the above-mentioned microstructure requirements and develop a deformable nickel-based superalloy and its preparation method that can simultaneously achieve excellent high-temperature strength and low-temperature impact toughness. Summary of the Invention

[0009] The purpose of this invention is to provide a Ni-Fe-based high-temperature alloy material, its preparation method, and its application in an ammothermal reactor in order to solve the above-mentioned problems. The Ni-Fe-based high-temperature alloy material has high strength under high temperature (550~650℃) and high pressure (around 150MPa) conditions and excellent impact toughness at low temperature (around -60℃), and can be used as a material for the body of an ammothermal reactor.

[0010] The objective of this invention is achieved through the following technical solution: The first objective of this invention is to provide a Ni-Fe-based superalloy material, wherein the composition of the Ni-Fe-based superalloy material comprises, by mass percentage, the following: Ni: 40~45%, Cr: 15~20%, Nb: 2.5~3.5%, Ta: 1.5~2.5%, Al: 0.4~0.6%, Ti: 0.85~1.25%, C: <0.06%, balance being Fe and other unavoidable impurities.

[0011] Furthermore, the structure of the Ni-Fe based superalloy material is a γ′+γ′′ dual-phase reinforced structure.

[0012] Furthermore, in the Ni-Fe based superalloy material, by mass percentage, B: <0.006%, P: <0.02%.

[0013] Furthermore, in this invention, the Al+Ti element content is <6% and the Ti / Al ratio is >1.5.

[0014] Furthermore, the Ni-Fe-based superalloy material maintains a tensile yield strength of over 1 GP at room temperature and a tensile strength of over 980 MPa at a high temperature of 650℃. The room temperature elongation and high temperature elongation of the Ni-Fe-based superalloy material are both greater than 20%, and the impact energy can reach 60J or even 80J at a low temperature of -60℃.

[0015] Furthermore, the Ni-Fe based superalloy material has an alloy grain size of 4.0 to 5.0.

[0016] Furthermore, the Ni-Fe-based high-temperature alloy material is suitable for high-temperature, high-pressure, and low-temperature service environments, and is particularly suitable for use as a material for ammonothermal reactor bodies.

[0017] The second objective of this invention is to provide a method for preparing Ni-Fe-based high-temperature alloy materials. This method can be carried out by conventional smelting methods, or by plastic processing and machining of the Ni-Fe-based high-temperature alloy materials of this invention, such as rolling or forging, depending on the application requirements.

[0018] Furthermore, in order to obtain the Ni-Fe-based superalloy material, the Ni-Fe-based superalloy material is melted by vacuum suspension melting.

[0019] Furthermore, the preparation method includes the following steps: S1. The chemical composition ratio of the Ni-Fe based high-temperature alloy material is controlled within ±0.1% by the following method: Weigh the elemental metal raw materials, clean and dry them to obtain cleaned and dried elemental metal raw materials, wherein the elemental metal raw materials include Fe, Ni, Cr, Nb, Ta, Al, and Ti; S2. Place the cleaned and dried elemental metal raw material obtained in step S1 into a vacuum suspension melting furnace. After reaching a certain vacuum level, introduce protective gas and remelt for casting to obtain the initial ingot. S3. After homogenization heat treatment, the initial ingot obtained in step S2 is hot rolled to obtain a hot-rolled high-temperature alloy plate. S4. The hot-rolled high-temperature alloy sheet obtained in step S3 is subjected to heat treatment to further improve the mechanical properties of the alloy, thereby obtaining the Ni-Fe based high-temperature alloy material.

[0020] Further, in step S1, the cleaning and drying process includes the following steps: ultrasonically cleaning the elemental metal raw material to remove surface oil, oxides and other impurities, and then placing it in a vacuum drying oven (120℃×2h) for drying.

[0021] Furthermore, in step S2, the vacuum degree is 1×10⁻⁶. -3 Pa; Furthermore, in step S2, the protective gas is argon.

[0022] Furthermore, in step S2, the remelting is performed 5 times.

[0023] Further, in step S3, the homogenization heat treatment conditions include: a two-stage homogenization heat treatment, first heat treatment at 1155~1165℃ for 16~20h, and then heat treatment at 1175~1185℃ for 22~26h.

[0024] More preferably, in step S3, the homogenization heat treatment conditions include: a two-stage homogenization heat treatment of first heat treatment at 1160℃ for 18h and then heat treatment at 1180℃ for 24h, i.e., a two-stage homogenization heat treatment of 1160℃×18h+1180℃×24h.

[0025] Further, in step S3, the hot rolling conditions include: an initial rolling temperature of 1100~1200℃, a final rolling temperature of not less than 1000℃, and a total hot rolling deformation of 45~55%.

[0026] More preferably, in step S3, the hot rolling conditions include: an initial rolling temperature of 1150°C, a final rolling temperature of not less than 1000°C, and a total hot rolling deformation of 50%.

[0027] Further, in step S3, after hot rolling, the material is placed in air to cool to room temperature to obtain the hot-rolled high-temperature alloy sheet.

[0028] Further, in step S4, the conditions of the heat treatment regime include: heat treatment at 1040~1060℃ for 0.8~1.2h, cooling in air to room temperature, heat treatment at 710~730℃ for 7~9h, furnace cooling at a cooling rate of 50~60℃ / h to 610~630℃, heat treatment at 610~630℃ for 7~9h, and cooling in air to room temperature.

[0029] More preferably, in step S4, the conditions of the heat treatment regime include: heat treatment at 1050℃ for 1 hour, cooling to room temperature in air, heat treatment at 720℃±5℃ for 8 hours, furnace cooling to 620℃ at a cooling rate of 55℃ / h, heat treatment at 620℃ for 8 hours, cooling to room temperature in air, i.e., 1050℃×1h, air cooling + 720℃×8h, furnace cooling to 620℃×8h at a cooling rate of 55℃ / h, air cooling. Alternatively, 1050℃×1h, air cooling + 720℃±5℃×8h, furnace cooling to 620℃×8h at a rate of 55℃ / h, air cooling.

[0030] The third objective of this invention is to provide an application of Ni-Fe-based high-temperature alloy material in an ammonia thermal reactor, wherein the Ni-Fe-based high-temperature alloy material is used as the reactor body material of the ammonia thermal reactor.

[0031] The technical concept of this invention includes: A highly stable, corrosion-resistant matrix is ​​constructed by precisely controlling the mass percentages of Ni (40-50%) and Cr (15-20%), and the proportions of Nb (2.5-3.5%), Ta (1.5-2.5%), Al (0.4-0.6%), and Ti (0.85-1.25%) are strictly limited to form a precipitation dual-phase composite reinforcement structure (γ′+γ′′ dual-phase reinforcement structure). While ensuring the above high-performance alloying design, iron (Fe) is used as the balance to form a Ni-Fe composite austenitic matrix that combines high strength and toughness, corrosion resistance, and controllable cost.

[0032] The dual-phase composite reinforcement structure of γ′(Ni3Al) and γ′′(Ni3Nb) is the core microstructure characteristic that determines the mechanical properties of materials (especially high-temperature strength, creep resistance and fracture toughness).

[0033] The alloy composition of the Ni-Fe based superalloy material is as follows: Ni: 40~45%. Ni acts as a matrix element, stabilizing the austenite (γ) structure. In the high-temperature, high-pressure liquid ammonia environment of the ammonothermal process, high nickel content can greatly improve the alloy's resistance to stress corrosion cracking and nitriding. Content below 40% leads to a decrease in corrosion resistance and microstructural stability; above 50% significantly increases manufacturing costs. For Ni-Fe based alloys, the 40~50% range is sufficient to balance good high-temperature strength and economy.

[0034] Cr: 15~20%. Cr is mainly used to provide oxidation and corrosion resistance. Cr can form a dense oxide protective film on the alloy surface to resist the erosion of harsh environments. If it is less than 15%, the continuity and stability of the protective film are insufficient to cope with corrosion in the ammonothermal process; if it is more than 20%, it is easy to promote the precipitation of harmful topologically close-packed phases (TCP phases, such as σ phases) under long-term high-temperature service, resulting in severe embrittlement of the alloy.

[0035] Nb: 2.5%~3.5%. Nb is an important solid solution strengthening and precipitation strengthening element. It can form the γ′′ phase, which significantly improves the yield strength of the alloy. If the content is below 2.5%, the strengthening effect is not obvious and the alloy cannot withstand the high pressure of the reactor. If the content is above 3.5%, it is easy to cause the precipitation of brittle Laves phase or excessive harmful δ phase, which reduces the plasticity and processing performance of the alloy.

[0036] Ta (1.5-2.5%) works synergistically with Nb, dissolving in the matrix or participating in the formation of a reinforcing phase. Tantalum effectively improves the stability of the reinforcing phase at high temperatures, slows down its coarsening rate, and further improves corrosion resistance. Tantalum is an expensive heavy metal element. Below 1.5%, it cannot exert a significant high-temperature stabilizing effect; above 2.5%, it not only significantly increases costs but also increases alloy density and may induce phase transformation instability.

[0037] Al (0.4-0.6%) and Ti (0.85-1.25%) are the core elements for forming the γ′ (Ni3(Al,Ti)) precipitate strengthening phase. These fine, dispersed precipitates are the main source of high-temperature strength in Ni-Fe based alloys. The ratio of Al to Ti needs to be carefully controlled. Too low a content results in insufficient γ′ phase, leading to substandard high-temperature strength; too high a content (especially Ti) can easily promote the transformation of the γ′ phase into the harmful acicular η phase (Ni3Ti) at high temperatures, significantly reducing the alloy's impact toughness and creep rupture life.

[0038] C: <0.06%. As an additive element, C forms carbides that can inhibit grain coarsening in the alloy and precipitate at grain boundaries to anchor the grains, thereby improving high-temperature strength and creep rupture life. However, when the C content is too high, it will lead to the precipitation of a continuous carbide network at the grain boundaries, consuming the surrounding Cr element, resulting in chromium depletion at the grain boundaries, and reducing the alloy's plasticity, toughness, and resistance to intergranular corrosion. Therefore, the upper limit is set at 0.06%.

[0039] Fe: Balance. As an important component of the matrix, it forms a solid solution together with nickel. Adding an appropriate amount of iron can significantly reduce material costs while maintaining good hot working and mechanical properties.

[0040] Furthermore, with a boron content of <0.006%, trace amounts of boron can segregate at grain boundaries, purifying them and strengthening grain boundary bonding, significantly improving the alloy's high-temperature tensile plasticity and creep rupture life. However, boron readily forms low-melting-point borides at grain boundaries, leading to "hot brittleness" (hot working cracking) during hot working (such as forging). Therefore, the upper limit is set at 0.006%.

[0041] Furthermore, with P < 0.02%, phosphorus readily segregates at grain boundaries, weakening grain boundary bonding, causing intergranular embrittlement, and deteriorating the alloy's weldability. Therefore, the upper limit is set at 0.02%.

[0042] This invention is a composition design method that effectively coordinates the contradiction between high-temperature strength stability and low-temperature impact toughness. Existing technologies usually seek a compromise between precipitation strengthening and grain boundary embrittlement. However, this invention improves the thermodynamic stability of the strengthening phase at high temperatures and delays the precipitation of brittle phases during long-term service by introducing 1.5~2.5% Ta element and a specific ratio of Nb, Al, and Ti to work synergistically. At the same time, by strictly controlling trace impurity elements such as C (as well as B and P) at a specific low level, the grain boundary state is improved and the brittle fracture sensitivity of the material in low-temperature environments is reduced.

[0043] This invention can be stably implemented in industry. The alloy smelting and processing procedures (such as vacuum suspension smelting, hot rolling, and standard solution aging treatment) can all be completed using existing conventional metallurgical equipment. The process parameters are well-defined, and the invention exhibits good industrial repeatability. Furthermore, the alloy prepared by this invention meets the creep resistance and pressure requirements of gallium nitride ammonothermal reactors at 650°C, and its impact toughness of 60J at -60°C provides effective safety assurance for reactor shutdown, pressure relief, and low-temperature operation, demonstrating clear industrial application value.

[0044] In this invention, the main components are divided into the following roles: γ′′ phase: mainly formed by Nb, Ta can partially replace Nb to form Ni3(Nb,Ta).

[0045] The γ′ phase is mainly composed of Al and Ti, forming a Ni3(Al,Ti) face-centered cubic structure. Nb and Ta can also dissolve into γ′, enhancing its strength and stability. Therefore, Al and Ti themselves do not directly constitute γ′′, but they consume some Nb and Ta by forming γ′, thus affecting the actual amount of γ′′ precipitated.

[0046] The indirect influence mechanisms on the γ′′ phase include: Competing element allocation: As the Al and Ti contents increase, the volume fraction of the γ′ phase increases. The γ′ forming elements Al and Ti will "compete" for Ni in the matrix, while some Nb will be allocated into the γ′ phase (forming Nb-containing γ′, i.e., Ni3(Al,Ti,Nb)). This leads to a decrease in the amount of Nb available for forming a pure γ′′ phase, and a decrease in the volume fraction of γ′′.

[0047] Changes in the γ′ / γ′′ ratio: In standard Inconel 718 alloys, the strengthening phase is predominantly γ′′, with γ′ being secondary. The (Al+Ti) / Nb ratio is typically controlled within a certain range. If the total Al and Ti content is high, the γ′ ratio increases, and the γ′′ ratio decreases. The alloy strengthening mechanism shifts from γ′′ coherent distortion strengthening to γ′′ ordered strengthening becoming dominant, thus altering the strength characteristics.

[0048] Stability and over-aging: Increased Al and Ti will raise the dissolution temperature of γ′, but excessive Ti may promote the formation of η phase (Ni3Ti, hexagonal close-packed), further consuming Nb and Ti, severely weakening the strengthening effect of γ′′ and γ′, and deteriorating plasticity and toughness (as in the previous comparative example 12, when Ti was 1.5%, η phase appeared, and plasticity dropped sharply).

[0049] Compared with the prior art, the beneficial effects of the present invention are reflected in the following aspects: 1) This invention provides a Ni-Fe based superalloy material, its preparation method, and its application in an ammonia thermoelectric reactor. By controlling the content and ratio of solid solution strengthening elements Nb+Ta and precipitation strengthening elements Al / Ti, and combining a solid solution + aging dual-stage heat treatment system, the alloy forms a γ′+γ′′ dual-phase strengthening structure, and a deformable nickel-based superalloy suitable for the service conditions of ammonia thermoelectric reactor structural materials is successfully developed.

[0050] 2) This invention provides a Ni-Fe-based superalloy material, its preparation method, and its application in an ammothermal reactor. To maintain a tensile strength of over 980 MPa at 650°C, this invention designs the proportions of Nb, Ta, Al, and Ti. The addition of Al (0.4~0.6%) and Ti (0.85~1.25%) promotes the precipitation of fine, dispersed γ' phases, while Nb (2.5~3.5%) promotes the formation of high-strength γ'' phases. Furthermore, this invention specifically introduces 1.5~2.5% Ta (tantalum). Ta not only plays a role in solid solution strengthening but, more importantly, it can partially replace atoms in the precipitated phase, significantly reducing the coarsening rate of the strengthening phase during long-term holding at 650°C and effectively inhibiting the transformation of the metastable γ'' phase into the harmful needle-like δ phase. This dual-phase composite strengthening and highly stable phase transformation control mechanism allows the alloy to maintain excellent high-temperature pressure resistance even after long-term ammothermal crystal growth.

[0051] 3) This invention provides a Ni-Fe-based superalloy material, its preparation method, and its application in an ammothermal reactor. It is specifically designed to address the harsh conditions encountered during the ammothermal crystal growth process of gallium nitride (GaN), including high temperature, high pressure, and strong corrosion. The ammothermal GaN preparation process typically requires withstanding extremely high internal pressure at around 650°C. The Ni-Fe-based superalloy material provided by this invention maintains excellent high-temperature strength at this temperature. Applying this Ni-Fe-based superalloy material to ammothermal pressure vessels (reactor bodies) effectively overcomes the limitations of existing materials in terms of temperature and pressure resistance. The bottleneck is addressed to ensure that the reactor can operate safely and stably for a long time under process conditions with higher temperatures and greater pressures. When the ammothermal reactor is shut down and depressurized, disassembled and transported at the liquid ammonia filling temperature, the reactor material faces a great risk of brittle fracture. The alloy prepared by this invention has an impact toughness of up to 80J at -60℃. Even after long-term high-temperature hot service, the material can still maintain excellent resistance to cold brittleness, which fundamentally reduces the risk of cracking during cold handling and maintenance of the equipment, and greatly improves the safety and operational fault tolerance of the ultra-high pressure vessel throughout its entire life cycle.

[0052] 4) This invention provides a Ni-Fe based high-temperature alloy material, its preparation method, and its application in an ammothermal reactor. Unlike the traditional element ratio approach, this invention introduces a new alloying strategy to improve the comprehensive mechanical properties of the material in different temperature ranges while ensuring high-temperature strength. Different phase stabilization strategies are proposed (introducing Ta and optimizing Al / Ti). By introducing 1.5~2.5% Ta element, and adjusting the Al and Ti contents to 0.4~0.6% and 0.85~1.25% respectively. The addition of Ta effectively improves the thermodynamic stability of the strengthening phase at high temperatures and delays phase transformation coarsening during long aging. In addition, in view of the risk of cold embrittlement faced by the reactor when it is shut down and depressurized and rotated at the liquid ammonia filling temperature, the technical route of adding P element to resist hydrogen embrittlement was abandoned. Instead, P was strictly limited to <0.02%, while controlling trace elements such as C (as well as B and P), which effectively reduced the sensitivity of intergranular brittle fracture at low temperatures. This allows the alloy of the present invention to maintain an impact toughness of 80J at -60℃, thereby providing a higher safety redundancy over the entire temperature range covering high-temperature operation and low-temperature shutdown.

[0053] 5) This invention provides a Ni-Fe based high-temperature alloy material, its preparation method, and its application in an ammothermal reactor. It adopts an elemental strengthening system and an anti-corrosion matrix design, and uses a Nb-Ta synergistic dual-phase strengthening mechanism. While retaining 2.5~3.5% Nb to obtain excellent solid solution / precipitation strengthening of the γ'' phase, as long as an appropriate amount of Ta (1.5~2.5%) is introduced for synergistic effect, it can effectively suppress the transformation of metastable phases into harmful phases (such as Laves phase or δ phase). This breaks through the design limitation that Nb must be removed to prevent embrittlement and is a balanced dual-phase composite strengthening route. Attached Figure Description

[0054] Figure 1 The tensile stress-strain curve of the Ni-Fe based superalloy material in Example 1 is shown. Figure 2 The image shows the EBSD inverse pole figure (IPF) of the Ni-Fe based superalloy material in Example 1 after solution treatment and aging heat treatment.

[0055] Figure 3 This is a schematic diagram of the coincident lattice (CSL) grain boundaries of the Ni-Fe based superalloy material in Example 1 after solution treatment and aging heat treatment.

[0056] Figure 4 This is a statistical diagram of the grain size of the Ni-Fe based superalloy material in Example 1 after solution treatment and aging heat treatment.

[0057] Figure 5The image shows a selected electron diffraction (SAED) image along the

[001] zone axis of the Ni-Fe based superalloy material of Example 1 after solution treatment and aging heat treatment.

[0058] Figure 6 The images shown are high-resolution transmission electron microscopy (HR-TEM) and fast Fourier transform (FFT) images of the Ni-Fe based superalloy material of Example 1 after solution treatment and aging heat treatment along the

[001] zone axis.

[0059] Figure 7 The typical load-displacement curves of the Ni-Fe based superalloy material in Example 1 after solution treatment and aging heat treatment at -60℃ are shown in the low-temperature impact test. Detailed Implementation

[0060] The present invention will now be described in detail with reference to specific embodiments, but this is by no means a limitation thereof. Any preparation methods, materials, structures, or compositional ratios not explicitly described in this technical solution are considered common technical features disclosed in the prior art.

[0061] Unless otherwise specified, the reagents, methods, instruments, and equipment used in this invention are conventional in the art. Unless otherwise specified, the reagents and materials used in the following examples are all commercially available.

[0062] In the following examples or comparative examples, the Ni-Fe based superalloy materials or Ni-Fe based alloy materials, by mass percentage, B: <0.006%, P: <0.02%.

[0063] Example 1 This embodiment provides a Ni-Fe-based superalloy material. The actual chemical composition of the Ni-Fe-based superalloy material was tested by ICP-MS (inductively coupled plasma mass spectrometry) and a carbon-sulfur analyzer. The composition of the Ni-Fe-based superalloy material, by mass percentage, includes the following: Ni: 42.28%, Cr: 16.32%, Nb: 3.35%, Ta: 1.82%, Al: 0.61%, Ti: 1.96%, Fe: 33.42%; C: 0.028%. Balance: other unavoidable impurities.

[0064] This embodiment also provides a method for preparing the above-mentioned Ni-Fe-based high-temperature alloy material, the method comprising the following steps: S1. The chemical composition ratio of the Ni-Fe based high-temperature alloy material is controlled within ±0.1%. The elemental metal raw material is weighed, and then ultrasonically cleaned to remove surface oil, oxides and other impurities. After cleaning, it is placed in a vacuum drying oven for drying (120℃×2h) to obtain the cleaned and dried elemental metal raw material. The elemental metal raw material is Fe, Ni, Cr, Nb, Ta, Al and Ti, and C comes from a small amount of C impurities in the elemental metal raw material. S2. Place the cleaned and dried elemental metal raw material obtained in step S1 into a vacuum suspension melting furnace, and achieve a vacuum degree of 1×10⁻⁶. -3 After Pa, argon gas is introduced as a protective gas and the mixture is remelted 5 times before being cast to obtain an initial ingot of about 20 kg. S3. The initial ingot obtained in step S2 is subjected to homogenization heat treatment (two-stage homogenization heat treatment of 1160℃×18h+1180℃×24h) followed by hot rolling (initial rolling temperature is 1150℃, final rolling temperature is not lower than 1000℃ (after exiting the furnace at 1150℃, the ingot temperature drops due to heat dissipation in the air during the rolling process, so it is only necessary to limit the ingot temperature to not lower than 1000℃. If the ingot temperature is lower than 1000℃ during the rolling process, it needs to be re-melted), with a total hot rolling deformation of 50%), to obtain the hot-rolled high-temperature alloy plate; S4. The hot-rolled high-temperature alloy sheet obtained in step S3 is subjected to a heat treatment regime (heat treatment regime of 1050℃×1h, air cooling + 720℃×8h, furnace cooling to 620℃×8h at a cooling rate of 55℃ / h, air cooling) to further improve the mechanical properties of the alloy and obtain the Ni-Fe based high-temperature alloy material.

[0065] like Figure 1 As shown, the tensile stress-strain curve of the Ni-Fe based superalloy material in Example 1 is shown. According to the curve analysis, the room temperature tensile yield strength is 1155±16MPa, the tensile strength is 1302±14MPa, the elongation is 29.5±3%, and the 650℃ tensile yield strength is 851±3MPa, 986±9 MPa, and 22.2±1.1%.

[0066] like Figure 2 As shown, the IPF (Integrated Photoformation) images along the normal direction of the Ni-Fe based superalloy sample after solution treatment and aging heat treatment are displayed, confirming that it has a fully recrystallized microstructure. DRX (Dynamic Recrystallization) grains and obvious annealing twins promote multiple orientations, resulting in a relatively random texture. Figure 3As shown, numerous ∑3 annealed twin boundaries (blue lines) are observed in the grain boundary network, along with a small number of ∑9 (green lines) and ∑27 (yellow lines) secondary grain boundaries. The red lines representing LAGBs (orientation difference between 2° and 15°) are extremely rare, and almost no obvious subgrain boundary network is observed within the grains. This characteristic demonstrates that the deformation storage energy and high-density dislocations introduced by the preceding heat treatment process were fully released through recovery and recrystallization during the subsequent heat treatment, reducing the residual strain within the matrix to a low level. The black lines representing HAGBs (orientation difference > 15°) network constitute a fully recrystallized equiaxed crystal morphology. Figure 4 As shown in the grain size distribution diagram, the average grain diameter is approximately 88.75 μm, and the grain size of the Ni-Fe based superalloy material reaches the 3.0~5.0 level.

[0067] like Figure 5 , 6 The images shown are, respectively, the selected electron diffraction (SAED) image, the high-resolution transmission electron microscope (HR-TEM) image, and the fast Fourier transform (FFT) image along the

[001] zone axis of the Ni-Fe based superalloy material of Example 1 after solution treatment and aging heat treatment. Figure 5 , 6 The dual-phase composite reinforced structure of γ′(Ni3Al) and γ′′(Ni3Nb) was demonstrated.

[0068] like Figure 7 As shown, the typical load-displacement curves of the Ni-Fe based superalloy material in Example 1 after solution treatment and aging heat treatment at -60℃ are presented, illustrating the typical instrumented impact load-displacement curves of this alloy at -60℃. By numerically integrating the region below the load curve, the crack initiation energy (W) can be quantitatively obtained. i ), crack propagation energy (W) p The test results show that the peak load (F) of the sample at -60℃ is... max The peak displacement reached 28.63 kN, corresponding to a peak displacement (S). Fmax The thickness is 1.52 mm. The above data indicates that the alloy possesses excellent load-bearing capacity and the ability to coordinate plastic deformation before V-notch crack initiation at -60℃. The specific composition of the impact absorption energy was calculated based on numerical integration, with crack propagation energy reaching as high as 45 J. This high propagation energy consumption indicates that the material has a strong ability to resist crack instability and propagation during dynamic mechanical response, maintaining stable toughness characteristics.

[0069] Example 2 This embodiment provides a Ni-Fe-based superalloy material. Other conditions are basically the same as in Example 1, except that: In this embodiment, the actual chemical composition of the Ni-Fe-based superalloy material was tested using ICP-MS (Inductively Coupled Plasma Mass Spectrometry) and a carbon-sulfur analyzer. The composition of the Ni-Fe-based superalloy material, by mass percentage, includes the following: Ni: 42.13%, Cr: 16.19%, Nb: 2.98%, Ta: 1.95%, Al: 0.57%, Ti: 0.95%, Fe: 33.81%; C: 0.024%. Balance: other unavoidable impurities.

[0070] Comparative Example 1 This comparative example provides a Ni-Fe based alloy material, with other conditions basically the same as in Example 1, except that: In this comparative example, the actual chemical composition of the Ni-Fe based alloy material was tested using ICP-MS (Inductively Coupled Plasma Mass Spectrometry) and a carbon-sulfur analyzer. The composition of the Ni-Fe based high-temperature material, by mass percentage, includes the following: Ni: 43.29%, Cr: 18.15%, Ta: 2.12%, Al: 0.49%, Ti: 1.12%, Fe: 34.78%; C: 0.024%. Balance: other unavoidable impurities.

[0071] Comparative Example 2 This comparative example provides a Ni-Fe based alloy material, with other conditions basically the same as in Example 1, except that: In this comparative example, the actual chemical composition of the Ni-Fe based alloy material was tested using ICP-MS (Inductively Coupled Plasma Mass Spectrometry) and a carbon-sulfur analyzer. The composition of the Ni-Fe based high-temperature material, by mass percentage, includes the following: Ni: 42.89%, Cr: 19.02%, Nb: 3.36%, Al: 0.52%, Ti: 1.16%, Fe: 33.01%; C: 0.028%. Balance: other unavoidable impurities.

[0072] Comparative Example 3 This comparative example provides a Ni-Fe based alloy material, with other conditions basically the same as in Example 1, except that: In this comparative example, the actual chemical composition of the Ni-Fe based alloy material was tested using ICP-MS (Inductively Coupled Plasma Mass Spectrometry) and a carbon-sulfur analyzer. The composition of the Ni-Fe based high-temperature material, by mass percentage, includes the following: Ni: 42.96%, Cr: 17.36%, Nb: 3.19%, Ta: 2.05%, Ti: 0.99%, Fe: 33.42%, C: 0.019%. Balance: other unavoidable impurities.

[0073] Comparative Example 4 This comparative example provides a Ni-Fe based alloy material, with other conditions basically the same as in Example 1, except that: In this comparative example, the actual chemical composition of the Ni-Fe based alloy material was tested using ICP-MS (Inductively Coupled Plasma Mass Spectrometry) and a carbon-sulfur analyzer. The composition of the Ni-Fe based high-temperature material, by mass percentage, includes the following: Ni: 43.54%, Cr: 17.49%, Nb: 3.24%, Ta: 1.77%, Al: 0.48%, Fe: 33.45%; C: 0.025%. Balance: other unavoidable impurities.

[0074] Comparative Example 5 This comparative example provides a Ni-Fe based alloy material, with other conditions basically the same as in Example 1, except that: In this comparative example, the actual chemical composition of the Ni-Fe based alloy material was tested using ICP-MS (Inductively Coupled Plasma Mass Spectrometry) and a carbon-sulfur analyzer. The composition of the Ni-Fe based high-temperature material, by mass percentage, includes the following: Ni: 43.27%, Cr: 16.97%, Nb: 1.87%, Ta: 1.82%, Al: 0.55%, Ti: 1.24%, Fe: 34.24%; C: 0.027%. Balance: other unavoidable impurities.

[0075] Comparative Example 6 This comparative example provides a Ni-Fe based alloy material, with other conditions basically the same as in Example 1, except that: In this comparative example, the actual chemical composition of the Ni-Fe based alloy material was tested using ICP-MS (Inductively Coupled Plasma Mass Spectrometry) and a carbon-sulfur analyzer. The composition of the Ni-Fe based high-temperature material, by mass percentage, includes the following: Ni: 44.35%, Cr: 18.32%, Nb: 2.89%, Ta: 0.87%, Al: 0.44%, Ti: 1.18%, Fe: 31.91%; C: 0.029%. Balance: other unavoidable impurities.

[0076] Comparative Example 7 This comparative example provides a Ni-Fe based alloy material, with other conditions basically the same as in Example 1, except that: In this comparative example, the actual chemical composition of the Ni-Fe based alloy material was tested using ICP-MS (Inductively Coupled Plasma Mass Spectrometry) and a carbon-sulfur analyzer. The composition of the Ni-Fe based high-temperature material, by mass percentage, includes the following: Ni: 44.67%, Cr: 18.44%, Nb: 3.08%, Ta: 2.36%, Al: 0.18%, Ti: 0.96%, Fe: 30.26%; C: 0.028%. Balance: other unavoidable impurities.

[0077] Comparative Example 8 This comparative example provides a Ni-Fe based alloy material, with other conditions basically the same as in Example 1, except that: In this comparative example, the actual chemical composition of the Ni-Fe based alloy material was tested using ICP-MS (Inductively Coupled Plasma Mass Spectrometry) and a carbon-sulfur analyzer. The composition of the Ni-Fe based high-temperature material, by mass percentage, includes the following: Ni: 43.54%, Cr: 16.79%, Nb: 2.96%, Ta: 1.98%, Al: 0.42%, Ti: 0.41%, Fe: 33.85%; C: 0.031%. Balance: other unavoidable impurities.

[0078] Comparative Example 9 This comparative example provides a Ni-Fe based alloy material, with other conditions basically the same as in Example 1, except that: In this comparative example, the actual chemical composition of the Ni-Fe based alloy material was tested using ICP-MS (Inductively Coupled Plasma Mass Spectrometry) and a carbon-sulfur analyzer. The composition of the Ni-Fe based high-temperature material, by mass percentage, includes the following: Ni: 42.87%, Cr: 17.96%, Nb: 4.58%, Ta: 2.01%, Al: 0.58%, Ti: 1.09%, Fe: 30.86%; C: 0.034%. Balance: other unavoidable impurities.

[0079] Comparative Example 10 This comparative example provides a Ni-Fe based alloy material, with other conditions basically the same as in Example 1, except that: In this comparative example, the actual chemical composition of the Ni-Fe based alloy material was tested using ICP-MS (Inductively Coupled Plasma Mass Spectrometry) and a carbon-sulfur analyzer. The composition of the Ni-Fe based high-temperature material, by mass percentage, includes the following: Ni: 43.74%, Cr: 17.87%, Nb: 3.39%, Ta: 3.15%, Al: 0.53%, Ti: 1.22%, Fe: 30.06%; C: 0.029%. Balance: other unavoidable impurities.

[0080] Comparative Example 11 This comparative example provides a Ni-Fe based alloy material, with other conditions basically the same as in Example 1, except that: In this comparative example, the actual chemical composition of the Ni-Fe based alloy material was tested using ICP-MS (Inductively Coupled Plasma Mass Spectrometry) and a carbon-sulfur analyzer. The composition of the Ni-Fe based high-temperature material, by mass percentage, includes the following: Ni: 44.25%, Cr: 16.82%, Nb: 3.22%, Ta: 2.24%, Al: 0.95%, Ti: 1.07%, Fe: 31.41%; C: 0.028%. Balance: other unavoidable impurities.

[0081] Comparative Example 12 This comparative example provides a Ni-Fe based alloy material, with other conditions basically the same as in Example 1, except that: In this comparative example, the actual chemical composition of the Ni-Fe based alloy material was tested by ICP-MS (inductively coupled plasma mass spectrometry). The composition of the Ni-Fe based high-temperature material, by mass percentage, includes the following: Ni: 42.90%, Cr: 19.12%, Nb: 3.15%, Ta: 2.41%, Al: 0.44%, Ti: 1.98%, Fe: 29.97%; C: 0.023%. Balance: other unavoidable impurities.

[0082] Comparative Example 13 This comparative example provides a Ni-Fe based alloy material, with other conditions basically the same as in Example 1, except that: In this comparative example, the actual chemical composition of the Ni-Fe based alloy material was tested using ICP-MS (Inductively Coupled Plasma Mass Spectrometry) and a carbon-sulfur analyzer. The composition of the Ni-Fe based high-temperature material, by mass percentage, includes the following: Ni: 42.09%, Cr: 16.72%, Nb: 3.39%, Ta: 1.89%, Al: 1.72%, Ti: 4.47%, Fe: 29.69%; C: 0.022%. Balance: other unavoidable impurities.

[0083] Comparative Example 14 This comparative example provides a Ni-Fe based alloy material, with other conditions basically the same as in Example 1, except that: In this comparative example, the actual chemical composition of the Ni-Fe based alloy material was tested using ICP-MS (Inductively Coupled Plasma Mass Spectrometry) and a carbon-sulfur analyzer. The composition of the Ni-Fe based high-temperature material, by mass percentage, includes the following: Ni: 44.19%, Cr: 18.10%, Nb: 3.27%, Ta: 1.86%, Al: 1.31%, Ti: 1.24%, Fe: 30.01%; C: 0.017%. Balance: other unavoidable impurities.

[0084] For the Ni-Fe based superalloy materials of Examples 1 and 1-14 above, or the Ni-Fe based alloy materials of the comparative examples, corresponding mechanical property test specimens were prepared by conventional machining methods. The mechanical property tests included room temperature tensile tests, 650°C tensile tests, and -60°C low-temperature impact tests. At least three parallel samples were taken for the tensile and impact tests to ensure the repeatability of the test results. The room temperature and high temperature (650°C) tensile properties and -60°C low-temperature impact properties of the Ni-Fe based superalloy materials were tested in accordance with GB / T 228.1-2021 Metallic materials - Tensile testing - Part 1: Room temperature test method, GB / T 228.2-2015 Metallic materials - Tensile testing - Part 2: High temperature test method, and GB / T 229-2020 Metallic materials - Charpy pendulum impact test method.

[0085] The room temperature and high temperature (650℃) tensile properties of the Ni-Fe based superalloy material are shown in Table 1.

[0086] The -60℃ low-temperature impact properties of the Ni-Fe based superalloy material are shown in Table 2.

[0087] Table 1 Tensile properties of Ni-Fe based superalloy materials. Table 2 Low-temperature impact properties of Ni-Fe based superalloy materials. Based on the above embodiments and comparative examples: The alloy composition range for this example is: Al 0.4~0.6%, Ti 0.85~1.25%, Nb 2.5~3.5%. This system achieves composite strengthening with γ′′ as the main component and γ′ as a secondary component by balancing the ratio of Al+Ti to Nb: the moderate Al and Ti contents ensure sufficient volume fraction of γ′ to assist in strengthening, while avoiding excessive Nb deposition, thus guaranteeing a large amount of γ′′ precipitation.

[0088] Nb and Ta are the main forming elements of the γ′′-Ni3(Nb,Ta) phase. Comparative Example 1 contains no Nb, so the γ′′ phase cannot form, resulting in a significant decrease in yield strength at room temperature and 650°C. Although the impact energy shows a slight increase, the strength is rendered unusable. Comparative Example 2 contains only Nb and no Ta; while the γ′′ phase can form, it is unstable, and the room / high-temperature strength is lower than in the previous example. The combined effect of adding either Nb or Ta individually is far less than that of adding them together, confirming that the coexistence of Nb and Ta can form a more stable γ′′ phase, producing a synergistic strengthening effect greater than the sum of its parts (1+1>2).

[0089] Complete removal of Al in Comparative Example 3 and complete removal of Ti in Comparative Example 4 both resulted in a significant reduction in the content of the γ′-Ni3(Al,Ti) phase, leading to the loss of auxiliary strengthening in the alloy. The room temperature / high temperature yield strength of Comparative Examples 3 and 4 decreased significantly. Without the γ′ phase, Nb was entirely used to form γ″, but due to the insufficient total amount of strengthening phase and the loss of the unique contribution of γ′ to high-temperature strength, both room temperature and high-temperature strength decreased significantly. Simultaneously, plasticity increased significantly, further confirming the crucial role of the γ′ phase in improving strength and hardness.

[0090] When the Nb or Ta content is below the lower limit (Comparative Example 5, Comparative Example 6), the volume fraction of the γ′′ phase is insufficient, the strength decreases slightly, and the impact energy increases slightly.

[0091] When Al or Ti is below the lower limit (Comparative Examples 7 and 8), γ′ decreases, and Nb is mainly used for γ′′, but the strength decreases due to insufficient total amount of overall strengthening phase.

[0092] When the Nb or Ta content is higher than the upper limit (Comparative Example 9, Comparative Example 10), the excess Nb and Ta promote the precipitation of a large amount of δ-Ni3Nb and Laves brittle phase at the grain boundaries. Although the strength decreases slightly, the plasticity and impact toughness decrease significantly, indicating severe embrittlement, which cannot meet the requirements of engineering applications.

[0093] When Al or Ti exceeds the upper limit (Comparative Examples 11 and 12), γ′ is excessive and may produce the η phase, γ′′ decreases and the tissue becomes brittle, and the impact energy drops sharply.

[0094] The γ′′ phase is not directly related to the Al and T contents, but rather through an indirect negative correlation established by the competition of the γ′ / γ′′ phase for Nb. Properly controlling the (Al+Ti) / Nb ratio and their respective contents is key to obtaining the ideal γ′′+γ′ strengthening ratio.

[0095] When the total Al+Ti content reaches 6.0% (Comparative Example 13), the volume fraction of the γ′ phase (Ni3(Al,Ti)) in the alloy increases sharply, far exceeding the γ′′ phase to become the dominant strengthening phase. At the same time, the excess Ti promotes the formation of a large amount of brittle η-Ni3Ti phase.

[0096] The performance of Ti / Al≤1.5 (Comparative Example 14) deteriorates, and the strengthening effectiveness of the γ′ phase decreases: Ti is the main strengthening element in the γ′ phase. The decrease in Ti / Al ratio reduces the antiphase domain boundary energy of the γ′ phase, weakens the strengthening contribution, and reduces the yield strength at room temperature and 650℃.

[0097] The example simultaneously satisfies Al+Ti < 6% and Ti / Al > 1.5, achieving: The γ′′ phase (Ni3Nb,Ta) is dispersed in large quantities, providing the main strengthening effect; The γ′ phase provides appropriate auxiliary enhancement without competing for too much Nb. Grain boundary trace η phase binding improves long service life; The microstructure within the hot working window is a single-phase γ (or contains a small amount of grain boundary carbides), exhibiting good forging plasticity.

[0098] The failure of any one of these conditions leads to a drastic change in properties: excessive Al+Ti content results in embrittlement and difficulty in deformation; excessive Ti / Al content results in insufficient strength. Therefore, Al+Ti < 6% and Ti / Al > 1.5 are the essential criteria for the alloy of this invention to achieve high strength, high toughness, good hot workability, and high-temperature creep resistance.

[0099] The above description of the embodiments is provided to enable those skilled in the art to understand and use the invention. It will be apparent to those skilled in the art that various modifications can be made to these embodiments, and the general principles described herein can be applied to other embodiments without inventive effort. Therefore, the present invention is not limited to the above embodiments, and any improvements and modifications made by those skilled in the art based on the disclosure of the present invention without departing from the scope of the invention should be within the protection scope of the present invention.

Claims

1. A Ni-Fe based superalloy material, characterized in that, The composition of the Ni-Fe-based superalloy material, by mass percentage, includes the following: Ni: 40~45%, Cr: 15~20%, Nb: 2.5~3.5%, Ta: 1.5~2.5%, Al: 0.4~0.6%, Ti: 0.85~1.25%, C: <0.06%, balance being Fe and unavoidable impurities; The structure of the Ni-Fe based superalloy material is a γ′+γ′′ dual-phase reinforced structure; In the Ni-Fe based superalloy material, by mass percentage, B: <0.006%, P: <0.02%; The preparation method of the Ni-Fe based superalloy material includes the following steps: S1. According to the composition of the Ni-Fe based high-temperature alloy material, the elemental metal raw materials are weighed, cleaned and dried to obtain cleaned and dried elemental metal raw materials, wherein the elemental metal raw materials include Fe, Ni, Cr, Nb, Ta, Al and Ti. S2. Place the cleaned and dried elemental metal raw material obtained in step S1 into a vacuum suspension melting furnace. After reaching a certain vacuum level, introduce protective gas and remelt for casting to obtain the initial ingot. S3. After homogenization heat treatment, the initial ingot obtained in step S2 is hot rolled to obtain a hot-rolled high-temperature alloy plate. S4. The hot-rolled high-temperature alloy sheet obtained in step S3 is subjected to heat treatment according to the heat treatment regime to obtain the Ni-Fe based high-temperature alloy material.

2. The Ni-Fe based superalloy material according to claim 1, characterized in that, The Ni-Fe based superalloy material maintains a tensile strength of over 980 MPa at a high temperature of 650°C.

3. A method for preparing a Ni-Fe-based superalloy material as described in any one of claims 1-2, characterized in that, The preparation method includes the following steps: S1. According to the composition of the Ni-Fe based high-temperature alloy material, the elemental metal raw materials are weighed, cleaned and dried to obtain cleaned and dried elemental metal raw materials, wherein the elemental metal raw materials include Fe, Ni, Cr, Nb, Ta, Al and Ti. S2. Place the cleaned and dried elemental metal raw material obtained in step S1 into a vacuum suspension melting furnace. After reaching a certain vacuum level, introduce protective gas and remelt for casting to obtain the initial ingot. S3. After homogenization heat treatment, the initial ingot obtained in step S2 is hot rolled to obtain a hot-rolled high-temperature alloy plate. S4. The hot-rolled high-temperature alloy sheet obtained in step S3 is subjected to heat treatment according to the heat treatment regime to obtain the Ni-Fe based high-temperature alloy material.

4. The method for preparing Ni-Fe-based superalloy material according to claim 3, characterized in that, In step S1, the cleaning and drying process includes the following steps: ultrasonically cleaning the elemental metal raw material, and then placing it in a vacuum drying oven for drying.

5. The method for preparing Ni-Fe-based high-temperature alloy material according to claim 3, characterized in that, In step S2, the vacuum degree is 1×10⁻⁶. -3 Pa; In step S2, the protective gas is argon. In step S2, the remelting is performed 4 to 6 times.

6. The method for preparing Ni-Fe-based superalloy material according to claim 3, characterized in that, In step S3, the homogenization heat treatment conditions include: a two-stage homogenization heat treatment, first heat treatment at 1155~1165℃ for 16~20h, and then heat treatment at 1175~1185℃ for 22~26h. In step S3, the hot rolling conditions include: an initial rolling temperature of 1100~1200℃, a final rolling temperature of not less than 1000℃, and a total hot rolling deformation of 45~55%; In step S3, after hot rolling, the material is placed in air to cool to room temperature to obtain the hot-rolled high-temperature alloy sheet.

7. The method for preparing Ni-Fe-based high-temperature alloy material according to claim 3, characterized in that, In step S4, the conditions of the heat treatment regime include: heat treatment at 1040~1060℃ for 0.8~1.2h, cooling to room temperature in air, heat treatment at 710~730℃ for 7~9h, furnace cooling to 610~630℃ at a cooling rate of 50~60℃ / h, heat treatment at 610~630℃ for 7~9h, and cooling to room temperature in air.

8. The method for preparing Ni-Fe-based high-temperature alloy material according to claim 7, characterized in that, The Ni-Fe based superalloy material has an alloy grain size of 4.0 to 5.

0.

9. The application of a Ni-Fe based superalloy material as described in any one of claims 1-2 in an ammothermal reactor, characterized in that, The Ni-Fe-based high-temperature alloy material is used as the vessel body material of the ammonothermal reactor.

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