WO2021174726A1 - Nickel-based deformed high-temperature alloy having high aluminum content and preparation method therefor - Google Patents

Abstract

Provided is a nickel-based deformed high-temperature alloy having a high aluminum content and a preparation method therefor. Conventional Ni-Co-Cr components as matrix elements, the contents of alloy elements, especially the Al content of a solid solution strengthening phase γ' phase forming element, are increased, and the content of a strengthening phase γ' phase is increased to 55%-65%, so as to effectively improve the temperature bearing capability of the alloy. The appropriate addition of element Nb to the alloy can improve the stability of the γ' phase, thereby improving the performance of a casting-forging process, the reduction of the addition of element Cr can improve the long-term structural stability of the alloy at 850°C, and a high content of element Al can make up for the loss of surface stability caused by the decrease of element Cr. In addition, a dual process or triple process is used for the preparation and processing of an alloy raw material. The obtained nickel-based deformed high-temperature alloy solves the problem that there is no high-performance wheel forging material that can be used for a long time at 850℃, especially has excellent 850℃ tensile strength, yield strength and endurance life.

Description

Nickel-based deformed high-temperature alloy with high aluminum content and preparation method thereof Technical field

The invention belongs to the field of alloy preparation, and specifically relates to a nickel-based deformed high-temperature alloy with high aluminum content and a preparation method.

Background technique

The service temperature of advanced gas turbine engines, such as high-pressure compressor discs such as aero engines and gas turbines, and hot-end rotating roulette-type forgings such as turbine discs, has gradually increased, with a long-term service temperature of up to 850°C. The alloy materials required for roulette forgings are required to have excellent strength and plasticity at room temperature to 850°C, high temperature permanent creep properties, and long-term structural stability, as well as good casting and forging process properties.

At present, the largest amount of nickel-based deformed superalloy roulette materials used in domestic aero-engines is GH4169 alloy used below 650℃, and the highest use temperature is GH4720Li, GH4065A, GH4738 and other nickel-based deformed high-temperature alloy roulette materials used below 750℃. There are nickel-based deformed superalloy roulette materials such as GH4141 and GH4586 that can be used for a short time below 850℃, but they cannot meet the long-term use requirements above 850℃.

As we all know, the most effective way to increase the operating temperature of nickel-based superalloys is to increase the degree of alloying and increase the content of the strengthening phase γ'phase. However, excessive alloying will cause the alloy’s metallurgical segregation tendency and thermal plasticity to deteriorate, so a new type of alloy has been developed. Nickel-based deformed superalloy roulette materials are quite difficult. In terms of composition design, it is necessary not only to improve the overall performance of alloying to meet the requirements, but also to combine the existing technical conditions to make it have a certain process performance to ensure manufacturability. Traditional nickel-based superalloys with a γ'phase content of 55-65% can only be produced by powder metallurgy or casting (including equiaxed casting, directional solidification and single crystal solidification) processes. These alloys are produced by casting-forging processes. Because of the high tendency of element segregation, the easy formation of metallurgical defects, and poor hot working (forging) plasticity, this type of alloy composition is not suitable for the preparation of nickel-based deformed superalloy roulette materials. In addition, although some nickel-based superalloys prepared by powder metallurgy or casting processes can be used at temperatures up to 850°C, their uniformity and compactness are not as good as forgings produced by casting-forging processes. Especially for the high-temperature hot-end rotating parts of the roulette type, the casting-forging process is adopted to ensure the quality and reliability of the roulette forgings to the greatest extent, and at the same time, it can be industrialized with high efficiency and low cost. The direct use of powder metallurgy or casting alloy components for casting-forging process production will face incompatibility problems, such as the control of the content of easily segregated elements Ti and Mo, the control of the content of easily oxidized elements Hf, and the high-cost addition of Ta. , And the addition of B, Zr, Ce and other beneficial trace elements at the grain boundary, etc., the element ratio must be optimized and adjusted according to the characteristics of the casting-forging process.

Therefore, it is necessary to provide improved technical solutions to overcome the technical problems existing in the prior art.

Summary of the invention

In order to solve the problems existing in the prior art, the present invention provides a nickel-based deformed high-temperature alloy with high aluminum content and a preparation method thereof, which solves the problem that there is currently no high-performance wheel forging material that can be used for a long time at 850°C, especially with Excellent tensile strength, yield strength and longevity at 850°C.

The first aspect of the present invention provides a nickel-based deformed high-temperature alloy with high aluminum content. The composition ratio is calculated by mass percentage. The nickel-based deformed high-temperature alloy includes: C: 0.004 to 0.1%, W: 6.0 to 9.0%, Cr: 7.0～12.0%, Mo: 1.0～4.0%, Co: 14.0～17.5%, Ti: 0.8～2.5%, Al: 3.5～6.0%, Nb: 0.8～2.5%, Zr: 0.005～0.1%, Mg : 0.005～0.1%; Ce: 0.001～0.1%, B: 0.005～0.1%, Fe: 0.005～2.0%, the balance is Ni. The inventor has confirmed through research that the alloy prepared by this technical solution can be used to prepare wheel forgings for long-term use at 850°C. The diameter of the wheel disk forgings ranges from 200mm to 1200mm. The tensile strength at 850°C is greater than 800MPa, and the yield strength is greater than 650MPa. The endurance life of ℃/350MPa is more than 30h.

Further, in the nickel-based deformed superalloy, the composition ratio is calculated by mass percentage, and the nickel-based deformed superalloy includes: C: 0.01-0.08%, W: 6.5-8.0%, Cr: 7.5- 11.0%, Mo: 1.5 to 3.5%, Co: 14.5 to 17.5%, Ti: 1.0 to 2.0%, Al: 4.0 to 5.5%, Nb: 1.0 to 2.0%, Zr: 0.005 to 0.05%, Mg: 0.005 to 0.05 %; Ce: 0.001 to 0.05%, B: 0.005 to 0.05%, Fe: 0.01 to 1.5%, the balance is Ni; the nickel-based deformed superalloy also includes impurity elements, among the impurity elements, P ≤0.015%, Mn≤0.5%, Si≤0.5%, S≤0.015%, O≤0.005%, N≤0.01%, Ag≤0.005%, Ca≤0.01%, Sn≤0.01%, Pb≤0.001%, Cu ≤0.5%, Ta≤0.5%, V≤0.5%. The inventors have confirmed through research that the alloy prepared by this technical solution can be used to prepare roulette forgings for long-term use at 850°C. The diameter of the roulette forgings ranges from 200mm to 1200mm. The tensile strength at 850°C is greater than 850MPa, and the yield strength is greater than 700MPa. ℃/350MPa endurance life is greater than 50h.

Further, in the nickel-based deformed high-temperature alloy, the composition ratio is calculated by mass percentage, and the nickel-based deformed high-temperature alloy includes: C: 0.01～0.06%, W: 6.5-75%, Cr: 8.0～ 10.0%, Mo: 2.0 to 3.2%, Co: 15.0 to 16.5%, Ti: 1.2 to 1.8%, Al: 4.5 to 5.2%, Nb: 1.2 to 1.8%, Zr: 0.005 to 0.03%, Mg: 0.005 to 0.03 %; Ce: 0.001 to 0.03%, B: 0.005 to 0.03%, Fe: 0.01 to 1.2%, and the balance is Ni; the nickel-based deformed superalloy also includes impurity elements. Among the impurity elements, P ≤0.010%, Mn≤0.15%, Si≤0.15%, S≤0.005%, O≤0.002%, N≤0.005%, Ag≤0.0005%, Ca≤0.005%, Sn≤0.005%, Pb≤0.0005%, Cu ≤0.1%, Ta≤0.1%, V≤0.1%. The inventor has confirmed through research that the alloy prepared by this technical solution can be used to prepare wheel forgings for long-term use at 850°C. The diameter of the wheel disk forgings ranges from 200mm to 1200mm. The tensile strength at 850°C is greater than 900MPa, and the yield strength is greater than 750MPa. ℃/350MPa endurance life is greater than 100h.

Further, in the nickel-based deformed superalloy, the nickel-based deformed superalloy uses γ austenite as a matrix, and the mass percentage of the strengthening phase γ′ phase reaches 55-65%, and the strengthening The chemical composition of the phase is (Ni, Co) ₃ (Al, Ti, Nb). The inventors have confirmed through research that the high content of the strengthening phase γ'phase of the alloy prepared by this technical solution enables the alloy to have good tensile strength and durability at 850°C. At the same time, the addition of Nb element improves the γ'phase. stability.

Further, in the nickel-based deformed superalloy, the nickel-based deformed superalloy further includes a second phase, and the second phase includes: MC type carbide, M6C type carbide, M23C6 type carbide , MB2 type boride, M3B2 type boride. The inventor has confirmed through research that the alloy prepared by this technical solution can improve the durability of the alloy at 850°C.

Further, in the nickel-based deformed superalloy, in the nickel-based deformed superalloy, the mass percentage of the γ'phase content is 55-65%, and the long-term aging is more than 5000h in the temperature range of 650-900℃ , And the content of precipitated harmful phase μ phase does not exceed 1%. The inventors have confirmed through research that the high content of γ'phase in the alloy prepared by this technical solution ensures that the alloy has good mechanical properties in the temperature range of room temperature to 850°C, and at the same time, the harmful phase μ phase is rarely precipitated during long-term aging. , To ensure that the alloy can be used for a long time at 850°C.

The second aspect of the present invention provides a method for preparing a nickel-based deformed high-temperature alloy with high aluminum content, which is characterized in that it comprises the following steps:

Step 1: Use vacuum induction melting to smelt the metal raw material components described in any one of claims 1 to 5 into primary alloy ingots, and then refine them into secondary alloy ingots by electroslag remelting, and then refine by vacuum consumable remelting Is a tertiary alloy ingot to obtain an alloy ingot;

Step 2: After the alloy ingot obtained in Step 1 is subjected to high-temperature diffusion homogenization annealing, it is heated and forged into a bar;

Step 3: The bar obtained in step 2 is formed by blanking and die forging to obtain alloy wheel forgings;

Step 4: After heat treatment of the alloy wheel forging obtained in Step 3, a nickel-based deformed high-temperature alloy wheel forging for long-term use at 850°C is obtained.

The inventor has confirmed through research that through this technical solution, the existing high-temperature alloy smelting and forging equipment can be used to prepare wheel forgings with a diameter of 200mm to 1200mm of the patented alloy, and industrial production can be realized.

Further, in the preparation method, the vacuum induction smelting in step 1 includes treatment processes: evacuation, smelting period, refining and tapping; in the evacuation treatment process, the vacuum degree is 10 ～100Pa; In the treatment process of the smelting period, the temperature is controlled to be 1300°C-1650°C; in the refining treatment process, the temperature is controlled to be 1400°C to 1600°C, and the vacuum degree is 1-20 Pa; In the steel tapping treatment process, the temperature is controlled to 1420°C-1590°C, and it needs to be filled with 10000～50,000Pa argon protection. After the casting is finished, it is cooled for 0.5h～3h and then demoulded and cooled to obtain a primary alloy ingot. The inventor has confirmed through research that through this technical solution, a vacuum induction ingot of an alloy can be prepared, the alloy elements can be accurately controlled, and the steel ingot will not be hot-cracked, and can be used to prepare electrodes for remelting and refining.

Further, in the preparation method, the step 1 further includes: preparing the primary alloy ingot into an I electroslag remelting electrode, and the filling ratio of the I electroslag remelting electrode to the mold is In the electroslag remelting process, the composition ratio of electroslag used is CaF2: CaO: MgO: Al2O3: TiO2 = 65 to 75%: 10 to 20%: 0.5 to 5%: 10-20%: 0.5-5%, the steady-state melting rate is 1.0-6.0 kg/min, the cooling time after the completion of the secondary alloy ingot smelting (ie electroslag remelting) is 0.5h-6h, and then the Mold cooling. The inventor has confirmed through research that this technical solution can effectively reduce the inclusion content and the harmful impurity element S content in the alloy ingot after electroslag remelting the primary alloy ingot prepared by vacuum induction melting, and at the same time prepare electroslag with qualified composition. The ingot is used to prepare the vacuum consumable remelting electrode, which can significantly improve the quality of the electrode, improve the process stability of the vacuum consumable remelting process, and can prepare the electrode of the vacuum consumable ingot with a diameter of 500 mm.

Further, in the preparation method, the step 1 further includes: preparing the secondary alloy ingot into an II electroslag remelting electrode, and the filling ratio of the II electroslag remelting electrode to the mold is 0.75～0.95, melting rate 1.0～5.0kg/min, cooling time after tertiary alloy ingot smelting (ie vacuum consumable remelting) is 0.5h～3h, and then demolding and cooling. The inventor has confirmed through research that through this technical solution, through the above-mentioned vacuum consumable remelting, the metallurgical quality of the steel ingot can be significantly improved, and the compactness and thermoplasticity of the steel ingot can be improved.

Further, in the preparation method, in step 1, if the primary alloy ingot is an alloy ingot with a diameter of less than 500 mm, the treatment process for the primary alloy ingot will be changed to: The alloy ingot is directly subjected to vacuum consumable remelting to obtain the alloy ingot. The inventors have confirmed through research that through this technical solution, consumable ingots smaller than 500mm require a small electrode diameter, and the use of vacuum induction ingots to prepare electrodes can obtain good metallurgical quality, which not only shortens the process flow, but also effectively reduces costs.

Further, in the preparation method, in step 2, the high-temperature diffusion homogenization annealing includes heating, heat preservation and cooling processes; the heating rate is controlled to be 15-60°C/h, and the heat preservation The temperature is 1150 to 1250°C, the heat preservation time is 24 to 72 hours, and the cooling rate is controlled to be 5 to 55°C/h. The inventor has confirmed through research that through this technical solution, homogenized diffusion annealing can eliminate solidification stress, avoid hot cracking of steel ingots, and also eliminate low melting point phases, effectively reduce the degree of elemental dendritic segregation, and improve the thermoplasticity of steel ingots.

Further, in the preparation method, the step 2 further includes: the alloy ingot obtained in the step 1 is homogenized and annealed, heated to the forging temperature and kept at the temperature, and then out of the furnace for forging, and the heating rate before forging is controlled as follows: 15～60℃/h, the holding temperature is 1050℃～1180℃, and the holding time is 2h～8h. The forging billeting process includes upsetting and drawing. The forging time of a single fire time exceeds 5～30min, and then it is returned to the furnace for 1～6h. Before each forging, the surface of the alloy ingot is covered with asbestos for heat preservation, and the total forging ratio is controlled to be 5-20 to obtain bars. The inventor has confirmed through research that through this technical solution, the steel ingot can be forged and billeted using a fast forging machine, the steel ingot does not crack, and the as-cast structure can be transformed into an equiaxed crystal structure.

Further, in the preparation method, the step 3 further includes: cutting the bar obtained in step 2 according to the weight of the roulette forging to obtain the cut bar; the weight of the cut bar is the roulette forging The weight of the cut bar is 110-150%, the height-to-diameter ratio of the cut bar is controlled between 1.5-3.0, and the cut bar is heated to upset the billet, and the heating rate before forging is controlled to 20-50 ℃/h, the holding temperature is 1000°C-1150°C, the holding time is 2-8h, the upsetting deformation is 30-70%, and the disc blank is obtained. The inventor has confirmed through research that through this technical solution, the bar upsetting process is stable, and there are no forging defects such as forging cracks, large and small heads, and wrinkles.

Further, in the preparation method, the disc blank is heated and then die forged, the heating rate before forging is controlled to be 20-50°C/h, the holding temperature is 950°C to 1150°C, and the holding time is 2-8h, the forging deformation is 30-70%, and the mold heating temperature is 300-1050°C. The inventor has confirmed through research that through this technical solution, the roulette forging can be formed by die forging without forging cracking, the filling effect is good, and the uniformity of the structure is good.

Further, in the preparation method, in the step 4, the wheel forging obtained in the step 3 is subjected to heat treatment by machining, and the heat treatment includes solution treatment, intermediate aging treatment and aging treatment, so The solution treatment method is 1150～1220℃ and the temperature is 2-10h, the intermediate aging treatment method is 1000～1150℃ and the temperature is 2～10h. The aging treatment method is 760℃～920℃ and the temperature is 8 ~32h. The inventors have confirmed through research that through this technical solution, after heat treatment of the wheel disc forgings, uniform microstructure and good mechanical properties can be obtained, and at the same time, the internal stress in the forgings can be effectively reduced.

The beneficial effects created by the present invention:

This patent provides a nickel-based deformed high-temperature alloy with high aluminum content and a preparation method. Using the alloy composition and preparation method provided in this patent, a casting-forging process can be used to prepare wheel forgings with a diameter of 100 to 1200 mm at room temperature of 850°C. It has good mechanical properties and satisfactory service stability in the temperature range, which can fill the gap of domestic 850℃ deformable disc materials.

Description of the drawings

In order to explain the technical solution of the present invention more clearly, the following will briefly introduce the drawings that need to be used in the embodiments. It should be understood that the following drawings only show certain embodiments of the present invention, and therefore should not be It is regarded as a limitation of the scope. For those of ordinary skill in the art, without creative work, other related drawings can be obtained from these drawings.

Figure 1 is the thermodynamic equilibrium phase diagram of the invention alloy;

Figure 2 is the isothermal transformation curve (TTT curve) of the μ phase of the inventive alloy;

Fig. 3 is a flow chart of the preparation process of the alloy wheel forging of the present invention.

Detailed ways

The experimental methods without specific conditions in the following examples are usually determined in accordance with national standards. If there is no corresponding national standard, it shall be carried out in accordance with general international standards, conventional conditions, or conditions recommended by the manufacturer.

The features mentioned in the present invention or the features mentioned in the embodiments can be combined. All the features disclosed in this specification can be used in combination with any composition form, and each feature disclosed in the specification can be replaced by any alternative feature that can provide the same, equal or similar purpose. Therefore, unless otherwise specified, the disclosed features are only general examples of equal or similar features.

In the present invention, if there is no special description, all the technical features and preferred features mentioned in this article can be combined with each other to form a new technical solution.

In the present invention, unless otherwise specified, the nickel-based deformed superalloy mentioned herein includes impurity elements, such as P, Mn, Si, S, O, N, Ag, Ca, Sn, Pb, Cu, Ta, V and so on.

In order to make the technical means, creative features, objectives and effects of the present invention easy to understand, the following describes the present invention in conjunction with specific implementations, but the present invention includes but is not limited to these embodiments.

In order to develop a nickel-based deformed superalloy roulette material that can be used for a long time at 850℃, and at the same time has a controllable cost, on the one hand, no or less precious metals such as Ta and Re or strategic reserve elements such as Co and rare earth should be added as much as possible. Use the conventional elements of traditional nickel-based deformed superalloy roulette materials; on the other hand, it not only ensures that the alloy has satisfactory performance at 850°C, but also considers the casting-forging process performance of the alloy, and can utilize existing smelting and forging equipment, The forgings of roulettes with a diameter of 100-1200mm are prepared to realize mass production and low-cost production.

The alloy composition design ideas of this patent are as follows. The traditional Ni-Co-Cr component is used as the base element. By increasing the content of alloy elements, especially the high solid solution strengthening phase γ′ phase forming element Al content, the strengthening phase γ′ phase content is increased To 55%-65%, to effectively improve the alloy's temperature-bearing capacity. The appropriate addition of Nb to the alloy can improve the stability of the γ'phase, thereby improving the performance of the casting-forging process, reducing the addition of Cr can improve the long-term structural stability of the alloy at 850℃, and the high content of Al can make up for the decrease of the Cr element. Loss of surface stability caused by.

Ni element is a matrix element, because Ni has a stable austenite matrix without allotropic transformation, austenite has higher high temperature strength, and has higher chemical stability, and has excellent resistance at high temperatures. Oxidation and corrosion resistance.

The addition of Co element to Ni can not only play a solid solution strengthening effect, but also increase the solid solubility of Ni matrix components, reduce the stacking fault energy of the alloy, and improve high temperature performance; adding Cr element to Ni-Co, Cr Not only can it play a solid solution strengthening effect, but Cr can form a dense and automatically repairable Cr ₂ O ₃ oxide film on the surface of the alloy, so that the alloy has excellent oxidation and corrosion resistance. However, excessive Cr content will cause Ni -The solid solubility of the Co-Cr matrix components is reduced, and harmful μ phases are easily precipitated, which is not conducive to long-term service stability.

W and Mo are the most effective solid solution strengthening elements in Ni-based alloys. A high content of Mo is not conducive to the hot corrosion resistance of the alloy and promotes the precipitation of μ phase. A high content of W will cause the density of the alloy to increase, but in order to increase at the same time For the alloy's temperature-bearing capacity and high-temperature long-term structural stability, this patent adopts the design of high W and low Mo.

Al is the most effective element in the formation of precipitation strengthening phase γ'phase in Ni-based alloys, and Al element can form Al ₂ O ₃ oxide film, which can also improve the oxidation resistance and corrosion resistance of the alloy, but high content of Al element is not conducive to The forging and casting properties of the alloy. The Al content in traditional nickel-based wrought superalloys generally does not exceed 4%. On the one hand, the atomic number of Al is small, so the atomic percentage is high. If the Al content is increased to more than 4%, a higher content of γ'phase will be precipitated. Conducive to the thermoplasticity of the steel ingot, it will cause the thermoplasticity of the steel ingot to be significantly reduced; on the other hand, the increase in Al content will increase the viscosity of the molten steel, expand the temperature range of the solid liquidus, and extend the solidification time of the molten steel. Formation of looseness, and more γ'phases will be precipitated to form greater structural stress, which will cause cracking of the steel ingot in severe cases, which is not conducive to casting performance. In order to improve the high-temperature mechanical properties and oxidation resistance of the alloy, this patent increases the Al element content and reduces the Cr element content, thereby improving the high-temperature long-term structural stability.

Ti is also an effective precipitation strengthening phase γ'phase forming element in Ni-based alloys, but Ti element has a greater tendency to solidify and segregate. High Ti alloys are prone to form Ti-rich channel segregation metallurgical defects. Ti is also a strong MC type carbide. Forming elements; in order to improve the stability and strengthening effect of the γ'phase, this patent adopts a high Al and low Ti design, and the Ti content is controlled by adjusting the Al/Ti ratio.

Nb is also an effective precipitation strengthening phase γ′ phase forming element in Ni-based alloys. Nb entering into the γ′ phase can stabilize the γ′ phase, which can effectively reduce the precipitation rate of the γ′ phase during the cooling process, but the Nb element The solidification segregation tends to be greater. This patented alloy adopts a high γ′ phase design. In order to improve the stability of the γ′ phase and enhance the forging process performance, an appropriate amount of Nb element is added and controlled according to the total amount of Al+Ti+Nb.

C is an important element in nickel-based deformed superalloys. C mainly forms carbides. According to the composition of alloy elements, it can form _{various types of carbides such as MC type, M 6} C type and M ₂₃ C ₆ type; the carbide is at 850 ℃ It can improve the durability of the alloy at a high temperature. For this reason, an appropriate amount of C element is added to the alloy of this patent.

Fe element is also a constituent element of γ austenite, but too much Fe element addition will promote the precipitation of σ phase, which is not conducive to the stability of high temperature and long-term structure. However, too low Fe element content is detrimental to industrialized metallurgical production. This is because the high-temperature alloy smelting furnace of the factory usually produces some Fe-containing alloys. If the Fe requirement is too low, it is necessary to take measures such as washing the furnace or new furnace lining, which will not only affect the production efficiency, but may also cause the Fe element to exceed the standard and cause qualified The rate is reduced. For this reason, this patent comprehensively considers the ratio of each element, and at the same time assesses the maximum upper limit control of Fe element, so as to ensure industrial production while maximizing the high-temperature long-term structural stability of the alloy.

In the alloy composition design, this patent appropriately increases the Co element content and reduces the Cr element content in order to improve the solid solubility and long-term stability of the matrix components. The salient feature of this patent is to significantly increase the amount of Al element added. On the one hand, increasing the precipitation of γ'phase improves the mechanical properties of the alloy, and on the other hand, it makes up for the degradation of oxidation and corrosion resistance after the content of Cr element is reduced. Add appropriate amount of Ti and Nb elements to form a more stable (Ni,Co) ₃ (Al,Ti,Nb) type γ′ phase. Compared with the pure high Al Ni3Al type γ′ phase, add an appropriate amount of Nb and The γ'phase after Ti is more stable, which can effectively solve the problem of structural stress caused by the precipitation of γ'phase in the solidification process of the steel ingot after increasing the Al content, and can improve the forging performance of the steel ingot. In order to increase the solid solution strengthening effect and improve the high temperature tensile properties at 850°C, W and Mo elements are added at the same time to increase the W/Mo ratio and reduce the thermal corrosion resistance degradation and μ phase precipitation tendency caused by excessive Mo element content. In order to improve the high-temperature durability of the alloy at 850℃, adding appropriate amount of C element to form MC type, M ₆ C type and M ₂₃ C ₆ type and other types of carbide strengthening, adding appropriate amount of B element to form MB ₂ , M ₃ B Type ₂ boride improves high-temperature thermal strength. In order to further improve the process performance of alloy casting-forging, adding appropriate amounts of Mg and Ce elements to improve the properties of grain boundaries can improve the thermoplasticity of alloy ingots and optimize the process performance of casting-forging. Other elements such as P, Mn, Si, S, O, N, Ag, Ca, Sn, Pb, Cu, Ta, V, etc. are impurity elements, which are not conducive to the mechanical properties and process properties of the alloy, and are the lowest according to the smelting capacity. Content control.

In order to improve the cleanliness, homogeneity and compactness of ingots, after vacuum induction melting and casting of qualified primary alloy ingots, electroslag remelting refining is used to remove inclusions and S elements and improve the metallurgical quality of alloy ingots. The vacuum consumable remelting refining is used to further improve the metallurgical quality and obtain an alloy ingot with a certain degree of thermoplasticity.

The following is the alloy composition table and technical effect comparison table in specific examples and comparative examples.

Table 1 Alloy composition of Examples and Comparative Examples (the values in the table are percentage values)

To	C	W	Cr	Mo	Co	Ti	Al	Nb	Zr	Mg	Ce	B	Fe	Ni
Example 1	0.09	8.2	9.6	2.7	17.4	2.08	3.33	1.67	0.055	0.049	0.058	0.007	1.8	Remain
Example 2	0.02	8.7	11.2	3.0	14.7	1.19	5.87	2.02	0.032	0.007	0.042	0.028	0.008	Remain
Example 3	0.045	6.8	10.5	2.6	16.2	1.55	4.52	1.46	0.017	0.011	0.005	0.013	1.2	Remain
Example 4	0.01	7.8	8.4	2.3	14.1	0.84	4.81	2.23	0.024	0.017	0.03	0.044	0.45	Remain
Example 5	0.004	6.0	7.0	1.0	14.0	0.8	3.5	0.8	0.005	0.005	0.001	0.005	0.005	Remain
Example 6	0.1	9.0	12.0	4.0	17.5	2.5	6.0	2.5	0.1	0.1	0.1	0.1	2.0	Remain
Example 7	0.08	6.5	7.5	1.5	14.5	1.0	4.0	1.0	0.006	0.006	0.006	0.006	0.01	Remain
Example 8	0.06	8.0	11.0	3.5	17.0	2.0	5.5	2.0	0.05	0.05	0.05	0.05	1.5	Remain
Example 9	0.03	7.5	8.0	2.0	15.0	1.2	4.5	1.2	0.03	0.03	0.03	0.03	0.02	Remain
Example 10	0.04	7.0	10.0	3.2	16.5	1.8	5.2	1.8	0.02	0.02	0.02	0.02	1.2	Remain
Comparative example 1	0.045	6.8	10.5	2.6	16.2	1.55	4.52	1.46	0.002	0.001	0.001	0.003	1.2	Remain

Comparative example 2

0.045

4.8

10.5

4.8

16.2

1.55

4.52

1.46

0.017

0.011

0.005

0.013

2.2

Remain

Table 2 Comparison of process and physical and chemical test results between the embodiment and the comparative example

Example 1. A method for preparing a nickel-based deformed superalloy wheel forging that can be used for a long time at 850°C

In this embodiment, a nickel-based deformed high-temperature alloy wheel forging (with a diameter of 200 mm) that can be used for a long time at 850° C. is prepared, and the alloy composition is shown in the part of embodiment 1 in Table 1.

The preparation process of alloy roulette forgings is as follows:

The smelting adopts a dual process (namely, vacuum induction melting and vacuum consumable remelting). The diameter of the primary alloy ingot obtained by vacuum induction melting is 250mm, and the diameter of the alloy ingot obtained by vacuum consumable remelting is 305mm. Vacuum induction smelting includes the following steps: weighing raw materials according to the element ratio of the alloy, and performing vacuum induction smelting. The vacuum induction melting process includes several steps such as evacuation, smelting, refining and tapping. The vacuum in the evacuation stage is 50Pa, the temperature in the smelting period is controlled to 1550°C, the temperature in the refining period is controlled to 1500°C, and the vacuum degree in the refining stage is 10Pa. The temperature is controlled at 1490°C, and 10000Pa argon gas is filled for protection during tapping. After the casting is completed, it is cooled for 1.5 hours and then demolded and cooled to obtain a primary alloy ingot. The primary alloy ingot is machined to prepare a consumable remelting electrode. The filling ratio of the consumable remelting electrode to the mold is 0.8, the melting rate is 1.5kg/min, and the cooling time after the tertiary alloy ingot smelting is 1.5h, Then, it is demolded and cooled to obtain an alloy ingot.

The alloy ingot needs to undergo high temperature diffusion homogenization annealing treatment, including the process of heating, holding and cooling. The heating rate is controlled to 55°C/h, the holding temperature is 1200°C, the holding time is 30h, and the cooling rate is controlled to 25°C/h. After homogenization annealing, after machining, the alloy ingot is heated to the forging temperature for holding and then out of the furnace for forging. The heating rate before forging is controlled to 55℃/h, the holding temperature is 1140℃, and the holding time is 3h. The forging billeting process includes For upsetting and drawing, the forging time of a single fire is controlled within 1min-20min. After 20min, the temperature is returned to the furnace for 1h. Before each forging, the surface of the alloy ingot is covered with asbestos for heat preservation, and the total forging ratio is controlled to 12 to obtain the bar.

Cut the bar according to 150% of the weight of the roulette forging. The height-to-diameter ratio of the bar is controlled to 2.0. After the bar is heated, the billet is upset. The heating rate before forging is controlled to 50℃/h, and the holding temperature is 1120℃. The time is 2h, the upsetting deformation is 35%, and the disc blank is obtained. After the disc blank is heated, it is forged to form. The heating rate before forging is controlled to 50℃/h, the holding temperature is 1100℃, the holding time is 2h, the forging deformation is 55%, and the mold heating temperature is 1050℃. The alloy roulette forging is obtained.

The roulette forgings are machined for heat treatment. The heat treatment includes solution treatment, intermediate aging treatment and aging treatment. The solution treatment system is 1150℃ for 2h, the intermediate aging treatment system is 1000℃ for 3h, and the aging treatment system is 800℃ for 12h. .

In some implementations of this embodiment, the raw material may be selected from metallic nickel, metallic chromium or nickel-chromium alloy, metallic titanium, metallic aluminum, metallic molybdenum, metallic boron iron, metallic cobalt, metallic tungsten, nickel-tungsten alloy, niobium One or more of nickel alloy, vanadium iron, carbon electrode, master alloy.

Example 2. A method for preparing a nickel-based deformed high-temperature alloy wheel forging with a diameter of 550mm that can be used at 850°C for a long time

In this embodiment, a nickel-based deformed high-temperature alloy wheel forging with a diameter of 550 mm that can be used at 850° C. for a long time is prepared. The alloy composition is shown in Example 2 of Table 1.

The preparation process of alloy roulette forgings is as follows:

The smelting adopts a double process, vacuum induction melting + vacuum consumable remelting, the diameter of the primary alloy ingot in vacuum induction melting is 370mm, and the diameter of vacuum consumable remelting is 460mm. Vacuum induction smelting includes the following steps: weighing raw materials according to the element ratio of the alloy, and performing vacuum induction smelting. The vacuum induction melting process includes several steps such as evacuation, smelting, refining and tapping. The vacuum in the evacuation stage is 70Pa, the temperature in the smelting stage is controlled at 1580°C, the temperature in the refining stage is controlled at 1550°C, the vacuum in the refining stage is 15Pa, and the tapping The temperature is controlled at 1500℃, and 15000Pa argon gas is filled for protection during tapping. After the casting is finished, it is cooled for 2 hours and then demolded and cooled to obtain a primary alloy ingot. The primary alloy ingot is machined and prepared into a consumable remelting electrode. The filling ratio of the consumable remelting electrode to the mold is 0.8, the melting rate is 2.5kg/min, and the cooling time after the tertiary alloy ingot smelting is 2h, and then After demolding and cooling, an alloy ingot is obtained.

The high-temperature diffusion homogenization annealing of alloy ingots includes heating, holding and cooling processes. The heating rate is controlled at 45°C/h, the holding temperature is 1210°C, the holding time is 40h, and the cooling rate is controlled at 25°C/h. After homogenization annealing, the alloy ingot is machined, heated to the forging temperature, and then out of the furnace for forging. The heating rate before forging is controlled to 45°C/h, the holding temperature is 1160°C, and the holding time is 4h. The forging billeting process includes Upsetting and drawing length, the single-fire forging time exceeds 15 minutes and then returning to the furnace for 2 hours. Before each forging, the surface of the alloy ingot is covered with asbestos for heat preservation, and the total forging ratio is controlled to 8 to obtain the bar.

The bar is cut according to 130% of the weight of the roulette forging. The height-to-diameter ratio of the bar is controlled to 2.5. After the bar is heated, the billet is upset. The heating rate before forging is controlled to 45°C/h, and the holding temperature is 1140°C. The time is 4h, and the upsetting deformation is 40%. After the disc blank is heated, it is die forged. Before forging, the heating rate is controlled to 45℃/h, the holding temperature is 1120℃, the holding time is 4h, the forging deformation is 50%, and the mold heating temperature is 950℃. The alloy roulette forging is obtained.

The roulette forgings are machined and subjected to heat treatment. The heat treatment includes solution treatment, intermediate aging treatment and aging treatment. The solution treatment system is 1160℃ for 4 hours, the intermediate aging treatment system is 1050℃ for 4 hours, and the aging treatment system is 850℃ for 24 hours. .

In some implementations of this embodiment, the raw material may be selected from metallic nickel, metallic chromium or nickel-chromium alloy, metallic titanium, metallic aluminum, metallic molybdenum, metallic boron iron, metallic cobalt, metallic tungsten, nickel-tungsten alloy, niobium One or more of nickel alloy, vanadium iron, carbon electrode, master alloy.

Example 3. A 900mm diameter nickel-based wrought superalloy wheel forging that can be used at 850°C for a long time

In this embodiment, a nickel-based deformed high-temperature alloy wheel forging with a diameter of 900 mm that can be used at 850° C. for a long time is prepared. The alloy composition is shown in Example 3 of Table 1.

The preparation process of alloy roulette forgings is as follows:

The smelting adopts a triple process, vacuum induction melting + electroslag remelting + vacuum consumable remelting. The diameter of the primary alloy ingot in vacuum induction melting is 355mm, the diameter of electroslag remelting alloy ingot is 423mm, and the diameter of vacuum consumable remelting alloy ingot is 508mm. . Vacuum induction smelting includes the following steps: weighing raw materials according to the element ratio of the alloy, and performing vacuum induction smelting. The vacuum induction melting process includes several steps such as evacuation, smelting, refining and tapping. The vacuum in the evacuation stage is 20Pa, the temperature in the smelting stage is controlled at 1550°C, the temperature in the refining stage is controlled at 1500°C, and the vacuum degree in the refining stage is 4Pa, and the tapping The temperature is controlled at 1480°C, and 20,000 Pa argon gas is filled for protection during tapping. After casting is completed, it is cooled for 3 hours and then demolded and cooled to obtain a primary alloy ingot. The primary alloy ingot is machined to prepare an electroslag remelting electrode. The filling ratio of the electroslag remelting electrode to the mold is 0.8, and the electroslag ratio is CaF2: CaO: MgO: Al2O3: TiO2 = 65%: 15% : 1%: 15%: 4%, the steady-state melting rate is 5.0kg/min, the cooling time after the secondary alloy ingot smelting is completed is 2h, and then demolding and cooling. The secondary alloy ingot is machined to prepare an electroslag remelting electrode. The filling ratio of the electroslag remelting electrode to the mold is 0.83, the melting rate is 2.8kg/min, and the cooling time after the tertiary alloy ingot smelting is 2h, Then, it is demolded and cooled to obtain an alloy ingot.

The high-temperature diffusion homogenization annealing of alloy ingots includes heating, holding and cooling processes. The heating rate is controlled to 35°C/h, the holding temperature is 1190°C, the holding time is 50h, and the cooling rate is controlled to 25°C/h. After homogenization annealing, the alloy ingot is machined, heated to the forging temperature, and then out of the furnace for forging. The heating rate before forging is controlled to 35°C/h, the holding temperature is 1170°C, and the holding time is 6h. The forging billeting process includes Upsetting and drawing length, single-fire forging time exceeds 15 minutes, and then returning to the furnace for 2 hours. Before each forging, the surface of the alloy ingot is covered with asbestos for heat preservation, and the total forging ratio is controlled to 15 to obtain the bar.

The bar is cut according to 120% of the weight of the roulette forging, and the height-to-diameter ratio of the bar is controlled to 2.5. After the bar is heated, the billet is upset. The heating rate before forging is controlled to 35°C/h, and the holding temperature is 1120°C. The time is 4h, and the upsetting deformation is 40%. After the disc blank is heated, it is forged and formed. The heating rate before forging is controlled to 35℃/h, the holding temperature is 1120℃, the holding time is 4h, the forging deformation is 40%, and the mold heating temperature is 650℃. The alloy roulette forging is obtained.

The roulette forgings are machined for heat treatment. The heat treatment includes solution treatment, intermediate aging treatment and aging treatment. The solution treatment system is 1180℃ for 5h, the intermediate aging treatment system is 1050℃ for 4h, and the aging treatment system is 910℃ for 12h. .

In some implementations of this embodiment, the raw material may be selected from metallic nickel, metallic chromium or nickel-chromium alloy, metallic titanium, metallic aluminum, metallic molybdenum, metallic boron iron, metallic cobalt, metallic tungsten, nickel-tungsten alloy, niobium One or more of nickel alloy, vanadium iron, carbon electrode, master alloy.

Example 4. A nickel-based deformed high-temperature alloy wheel forging with a diameter of 1200mm that can be used at 850°C for a long time

In this embodiment, a nickel-based deformed high-temperature alloy wheel forging with a diameter of 1200 mm that can be used at 850° C. for a long time is prepared. The alloy composition is shown in Example 4 of Table 1.

The preparation process of alloy roulette forgings is as follows:

The smelting adopts a triple process, vacuum induction melting + electroslag remelting + vacuum consumable remelting, the diameter of the primary alloy ingot in vacuum induction melting is 440mm, the diameter of electroslag remelting alloy ingot is 580mm, and the diameter of vacuum consumable remelting alloy ingot is 660mm . Vacuum induction smelting includes the following steps: weighing raw materials according to the element ratio of the alloy, and performing vacuum induction smelting. The vacuum induction melting process includes several steps such as evacuation, smelting, refining and tapping. The vacuum in the evacuation stage is 30Pa, the temperature in the smelting stage is controlled to 1580°C, the temperature in the refining stage is controlled to 1550°C, the vacuum degree in the refining stage is 5Pa, and the steel is tapped. The temperature is controlled at 1480℃, and the steel is filled with 25000Pa argon protection during tapping. After the casting is completed, it is cooled for 3 hours and then demolded and cooled to obtain a primary alloy ingot. The primary alloy ingot is machined to prepare an electroslag remelting electrode. The filling ratio of the electrode to the mold is 0.75, and the electroslag ratio is CaF2: CaO: MgO: Al2O3: TiO2 = 68%: 14%: 2%: 14 %: 2%, the steady-state melting rate is 6.0kg/min, the cooling time after the secondary alloy ingot smelting is completed is 6h, and then demolding and cooling. The secondary alloy ingot is machined to prepare an electroslag remelting electrode. The filling ratio of the electroslag remelting electrode to the mold is 0.87, the melting rate is 3.8kg/min, and the cooling time after the tertiary alloy ingot smelting is 3h, Then, it is demolded and cooled to obtain an alloy ingot.

The high-temperature diffusion homogenization annealing of alloy ingots includes heating, holding and cooling processes. The heating rate is controlled at 15°C/h, the holding temperature is 1180°C, the holding time is 70h, and the cooling rate is controlled at 5°C/h. After homogenization annealing, after machining, the alloy ingot is heated to the forging temperature and kept warm and then out of the furnace for forging. The heating rate before forging is controlled to 15℃/h, the holding temperature is 1180℃, and the holding time is 6h. The forging billeting process includes Upsetting and drawing length, the single-fire forging time exceeds 15 minutes, and then returning to the furnace for 6 hours of heat preservation. Before each forging, the surface of the alloy ingot is covered with asbestos for heat preservation, and the total forging ratio is controlled to 8 to obtain the bar.

The bar is cut according to 110% of the weight of the roulette forging. The height-to-diameter ratio of the bar is controlled to 2.5. After the bar is heated, the billet is upset. The heating rate before forging is controlled to 35°C/h, and the holding temperature is 1150°C. The time is 4h, and the upsetting deformation is 50%. After the disc blank is heated, it is die forged. Before forging, the heating rate is controlled to 35℃/h, the holding temperature is 1100℃, the holding time is 4h, the forging deformation is 35%, and the mold heating temperature is 350℃. The alloy roulette forging is obtained.

The roulette forgings are machined for heat treatment. The heat treatment includes solution treatment, intermediate aging treatment and aging treatment. The solution treatment system is 1160℃ for 8h, the intermediate aging treatment system is 1100℃ for 10h, and the aging treatment system is 850℃ for 32h. .

In some implementations of this embodiment, the raw material may be selected from metallic nickel, metallic chromium or nickel-chromium alloy, metallic titanium, metallic aluminum, metallic molybdenum, metallic boron iron, metallic cobalt, metallic tungsten, nickel-tungsten alloy, niobium One or more of nickel alloy, vanadium iron, carbon electrode, master alloy.

Embodiment 5. A method for preparing a nickel-based deformed superalloy wheel forging that can be used for a long time at 850°C

In this embodiment, a nickel-based deformed high-temperature alloy wheel forging (with a diameter of 200 mm) that can be used for a long time at 850° C. is prepared, and the alloy composition is shown in the part of embodiment 5 in Table 1.

The preparation process of alloy wheel forgings, as shown in Figure 3, includes the following steps:

Step 1. The smelting adopts a dual process (namely, vacuum induction melting and vacuum consumable remelting), the diameter of the primary alloy ingot obtained by vacuum induction melting is 250 mm, and the diameter of the alloy ingot obtained by vacuum consumable remelting is 305 mm. Vacuum induction smelting includes the following steps: weighing raw materials according to the element ratio of the alloy, and performing vacuum induction smelting. The vacuum induction melting process includes several steps such as evacuation, smelting period, refining and tapping. The vacuum in the evacuation stage is 10Pa, the temperature in the smelting period is controlled to 1300°C, the temperature in the refining period is controlled to 1400°C, and the vacuum degree in the refining stage is 1Pa. The temperature is controlled at 1420°C, and the steel is filled with 20000Pa argon protection during tapping. After the casting is completed, it is cooled for 0.5h and then demolded and cooled to obtain a primary alloy ingot. The primary alloy ingot is processed into a consumable remelting electrode after machining. The filling ratio of the consumable remelting electrode to the mold is 0.75, the melting rate is 1.0kg/min, and the cooling time after the tertiary alloy ingot smelting is 0.5h, Then, it is demolded and cooled to obtain an alloy ingot.

Step 2. The alloy ingot needs to undergo high temperature diffusion homogenization annealing treatment, including the process of heating, holding and cooling. The heating rate is controlled to 15°C/h, the holding temperature is 1150°C, the holding time is 24h, and the cooling rate is controlled to 5°C/ h. After homogenization annealing, after machining, the alloy ingot is heated to the forging temperature and kept warm and then out of the furnace for forging. The heating rate before forging is controlled to 15℃/h, the holding temperature is 1050℃, and the holding time is 2h. The forging billeting process includes For upsetting and drawing length, the single-fire forging time is controlled between 1min and 5min. After 5min, the temperature is returned to the furnace for 1h. Before each forging, the surface of the alloy ingot is covered with asbestos for heat preservation, and the total forging ratio is controlled to 5 to obtain the bar.

Step 3. Cut the appropriate length of the bar according to 140% of the weight of the roulette forging. The height-to-diameter ratio of the bar is controlled to 1.5. After the bar is heated, the billet is upset, and the heating rate before forging is controlled to 20℃/h. The temperature is 1000°C, the holding time is 2h, the upsetting deformation is 30%, and the disc blank is obtained. After the disc blank is heated, it is forged and formed. The heating rate before forging is controlled to 20℃/h, the holding temperature is 950℃, the holding time is 2h, the forging deformation is 30%, and the mold heating temperature is 300℃. The alloy roulette forging is obtained.

Step 4. The roulette forgings are machined for heat treatment. The heat treatment includes solution treatment, intermediate aging treatment and aging treatment. The solution treatment system is 1150℃ for 2 hours, the intermediate aging treatment system is 1000℃ for 2 hours, and the aging treatment system is 760. Incubate at ℃ for 8h.

In some implementations of this embodiment, the raw material may be selected from metallic nickel, metallic chromium or nickel-chromium alloy, metallic titanium, metallic aluminum, metallic molybdenum, metallic boron iron, metallic cobalt, metallic tungsten, nickel-tungsten alloy, niobium One or more of nickel alloy, vanadium iron, carbon electrode, master alloy.

Example 6. A method for preparing a nickel-based deformed high-temperature alloy wheel forging with a diameter of 550mm that can be used at 850°C for a long time

In this embodiment, a nickel-based deformed high-temperature alloy wheel forging with a diameter of 550 mm that can be used at 850° C. for a long time is prepared. The alloy composition is shown in Example 6 of Table 1.

The preparation process of alloy wheel forgings, as shown in Figure 3, includes the following steps:

Step 1. The smelting adopts a dual process, vacuum induction melting + vacuum consumable remelting, the diameter of the primary alloy ingot in vacuum induction melting is 370mm, and the diameter of the vacuum consumable remelting alloy ingot is 460mm. Vacuum induction smelting includes the following steps: weighing raw materials according to the element ratio of the alloy, and performing vacuum induction smelting. The vacuum induction melting process includes several steps such as evacuation, smelting, refining and tapping. The vacuum in the evacuation stage is 100Pa, the temperature in the smelting stage is controlled at 1650°C, the temperature in the refining stage is controlled at 1600°C, and the vacuum in the refining stage is 20Pa. The temperature is controlled at 1590°C, 50,000Pa is filled with argon protection when tapping, and after casting is finished, it is cooled for 3 hours and then demoulded and cooled to obtain a primary alloy ingot. The primary alloy ingot is machined to prepare a consumable remelting electrode. The filling ratio of the consumable remelting electrode to the mold is 0.95, the melting rate is 6.0kg/min, and the cooling time after the tertiary alloy ingot smelting is 3h, and then After demolding and cooling, an alloy ingot is obtained.

Step 2. High-temperature diffusion homogenization annealing of alloy ingots includes heating, holding and cooling processes. The heating rate is controlled to 60°C/h, the holding temperature is 1250°C, the holding time is 72h, and the cooling rate is controlled to 55°C/h. After homogenization annealing, after machining, the alloy ingots are heated to the forging temperature for holding and then out of the furnace for forging. The heating rate before forging is controlled to 60℃/h, the holding temperature is 1180℃, and the holding time is 8h. The forging billeting process includes For upsetting and drawing, the single-fire forging time is controlled within 1min-30min. After 30min, it is returned to the furnace for 6h. Before each forging, the surface of the alloy ingot is covered with asbestos for heat preservation, and the total forging ratio is controlled to 20 to obtain the bar.

Step 3. Cut the bar according to 130% of the weight of the roulette forging. The height-to-diameter ratio of the bar is controlled to 3.0. After the bar is heated, the billet is upset, and the heating rate before forging is controlled to 50℃/h, and the holding temperature is At 1140℃, the holding time is 8h, and the upsetting deformation is 70%. After the disc blank is heated, it is forged and formed. The heating rate before forging is controlled to 50℃/h, the holding temperature is 1120℃, the holding time is 8h, the forging deformation is 70%, and the mold heating temperature is 1050℃. The alloy roulette forging is obtained.

Step 4. The roulette forgings are machined for heat treatment. The heat treatment includes solution treatment, intermediate aging treatment and aging treatment. The solution treatment system is 1220℃ for 10 hours, the intermediate aging treatment system is 1150℃ for 10 hours, and the aging treatment system is 920. Incubate at ℃ for 32h.

In some implementations of this embodiment, the raw material may be selected from metallic nickel, metallic chromium or nickel-chromium alloy, metallic titanium, metallic aluminum, metallic molybdenum, metallic boron iron, metallic cobalt, metallic tungsten, nickel-tungsten alloy, niobium One or more of nickel alloy, vanadium iron, carbon electrode, master alloy.

Example 7. A nickel-based deformed superalloy wheel forging with a diameter of 900mm that can be used at 850°C for a long time

In this embodiment, a nickel-based deformed high-temperature alloy diameter wheel forging that can be used for a long time at 850° C. is prepared, and the alloy composition is shown in Example 7 of Table 1.

The preparation process of alloy wheel forgings, as shown in Figure 3, includes the following steps:

Step 1. The smelting adopts the triple process, vacuum induction melting + electroslag remelting + vacuum consumable remelting. The diameter of the primary alloy ingot in vacuum induction melting is 355mm, the diameter of electroslag remelting alloy ingot is 423mm, and the vacuum consumable remelting alloy ingot The diameter is 508mm. Vacuum induction smelting includes the following steps: weighing raw materials according to the element ratio of the alloy, and performing vacuum induction smelting. The vacuum induction melting process includes several steps such as evacuation, smelting, refining and tapping. The vacuum in the evacuation stage is 20Pa, the temperature in the smelting stage is controlled at 1550°C, the temperature in the refining stage is controlled at 1500°C, and the vacuum degree in the refining stage is 4Pa. The tapping temperature is controlled at 1480°C, and 20,000 Pa argon protection is filled during tapping. After casting is completed, it is cooled for 2.5 hours and then demolded and cooled to obtain a primary alloy ingot. The primary alloy ingot is machined to prepare an electroslag remelting electrode. The filling ratio of the electroslag remelting electrode to the mold is 0.9, and the electroslag ratio is CaF2: CaO: MgO: Al2O3: TiO2 = 65%: 10% : 0.5%: 10%: 0.5%, the steady state melting rate is 5.0kg/min, the cooling time after the secondary alloy ingot smelting is completed is 0.5h, and then demolding and cooling. The secondary alloy ingot is machined to prepare an electroslag remelting electrode. The filling ratio of the electrode to the mold is 0.75, and the melting rate is 1.0kg/min. The cooling time after the tertiary alloy ingot smelting is completed is 1h, and then demolding and cooling. Obtain an alloy ingot.

Step 2. High-temperature diffusion homogenization annealing of alloy ingots includes heating, heat preservation and cooling processes. The heating rate is controlled to 35°C/h, the holding temperature is 1190°C, the holding time is 50h, and the cooling rate is controlled to 25°C/h. After homogenization annealing, the alloy ingot is machined, heated to the forging temperature, and then out of the furnace for forging. The heating rate before forging is controlled to 35°C/h, the holding temperature is 1170°C, and the holding time is 6h. The forging billeting process includes For upsetting and drawing length, the single-fire forging time is controlled between 1min and 15min. After 15min, the temperature is returned to the furnace for 2h. Before each forging, the surface of the alloy ingot is covered with asbestos for heat preservation, and the total forging ratio is controlled to 15 to obtain the bar.

Step 3. Cut the bar according to 140% of the weight of the roulette forging. The height-to-diameter ratio of the bar is controlled to 2.5. After the bar is heated, the billet is upset and the heating rate before forging is controlled to 35℃/h, and the holding temperature is 1110 ℃, the holding time is 4h, the upsetting deformation is 40%, and the disc blank is obtained. After the disc blank is heated, it is forged and formed. The heating rate before forging is controlled to 35℃/h, the holding temperature is 1120℃, the holding time is 4h, the forging deformation is 40%, and the mold heating temperature is 650℃. The alloy roulette forging is obtained.

Step 4. The roulette forgings are processed by machining for heat treatment. The heat treatment includes solution treatment, intermediate aging treatment and aging treatment. The solution treatment system is 1180℃ for 5 hours, the intermediate aging treatment system is 1050℃ for 8 hours, and the aging treatment system is 910 Incubate at ℃ for 20h.

In some implementations of this embodiment, the raw material may be selected from metallic nickel, metallic chromium or nickel-chromium alloy, metallic titanium, metallic aluminum, metallic molybdenum, metallic boron iron, metallic cobalt, metallic tungsten, nickel-tungsten alloy, niobium One or more of nickel alloy, vanadium iron, carbon electrode, master alloy.

Example 8. A 900mm diameter nickel-based deformed superalloy wheel forging that can be used for a long time at 850°C

In this embodiment, a nickel-based deformed high-temperature alloy wheel forging with a diameter of 900 mm that can be used at 850° C. for a long time is prepared. The alloy composition is shown in Example 8 of Table 1.

The preparation process of alloy wheel forgings, as shown in Figure 3, includes the following steps:

Step 1. The smelting adopts the triple process, vacuum induction melting + electroslag remelting + vacuum consumable remelting. The diameter of the primary alloy ingot in vacuum induction melting is 355mm, the diameter of electroslag remelting alloy ingot is 423mm, and the vacuum consumable remelting alloy ingot The diameter is 508mm. Vacuum induction smelting includes the following steps: weighing raw materials according to the element ratio of the alloy, and performing vacuum induction smelting. The vacuum induction melting process includes several steps such as evacuation, smelting, refining and tapping. The vacuum in the evacuation stage is 30Pa, the temperature in the smelting stage is controlled to 1580°C, the temperature in the refining stage is controlled to 1550°C, the vacuum degree in the refining stage is 5Pa, and the steel is tapped. The temperature is controlled at 1480℃, and the steel is filled with 25000Pa argon protection during tapping. After the casting is completed, it is cooled for 3 hours and then demolded and cooled to obtain a primary alloy ingot. The primary alloy ingot is machined to prepare an electroslag remelting electrode. The filling ratio of the electroslag remelting electrode to the mold is 0.9, and the electroslag ratio is CaF2: CaO: MgO: Al2O3: TiO2 = 75%: 20% : 5%: 20%: 5%, the steady-state melting rate is 4.0kg/min, the cooling time after the secondary alloy ingot smelting is completed is 6h, and then demolding and cooling. The secondary alloy ingot is machined to prepare an electroslag remelting electrode. The filling ratio of the electroslag remelting electrode to the mold is 0.87, the melting rate is 3.8kg/min, and the cooling time after the tertiary alloy ingot smelting is 3h, Then, it is demolded and cooled to obtain an alloy ingot.

Step 2. High-temperature diffusion homogenization annealing of alloy ingots includes heating, heat preservation and cooling processes. The heating rate is controlled to 20°C/h, the holding temperature is 1180°C, the holding time is 70h, and the cooling rate is controlled to 5°C/h. After homogenization annealing, after machining, the alloy ingot is heated to the forging temperature and kept warm and then out of the furnace for forging. The heating rate before forging is controlled to 15℃/h, the holding temperature is 1180℃, and the holding time is 6h. The forging billeting process includes For upsetting and drawing, the single-fire forging time is controlled within 1min-10min. After 10min, it is returned to the furnace for 2h. Before each forging, the surface of the alloy ingot is covered with asbestos for heat preservation, and the total forging ratio is controlled to 10 to obtain the bar.

Step 3. Cut the bar according to 125% of the weight of the roulette forging. The height-to-diameter ratio of the bar is controlled to 2. After the bar is heated, the billet is upset. The heating rate before forging is controlled to 35℃/h, and the holding temperature is 1150 ℃, holding time is 6h, upsetting deformation is 50%. After the disc blank is heated, it is forged and formed. The heating rate before forging is controlled to 40℃/h, the holding temperature is 1100℃, the holding time is 6h, the forging deformation is 35%, and the mold heating temperature is 350℃. The alloy roulette forging is obtained.

Step 4. The roulette forgings are processed by machining for heat treatment. The heat treatment includes solution treatment, intermediate aging treatment and aging treatment. The solution treatment system is 1160℃ for 8 hours, the intermediate aging treatment system is 1100℃ for 7 hours, and the aging treatment system is 850. Incubate at ℃ for 32h.

In some implementations of this embodiment, the raw material may be selected from metallic nickel, metallic chromium or nickel-chromium alloy, metallic titanium, metallic aluminum, metallic molybdenum, metallic boron iron, metallic cobalt, metallic tungsten, nickel-tungsten alloy, niobium One or more of nickel alloy, vanadium iron, carbon electrode, master alloy.

Example 9. A 900mm diameter nickel-based deformed superalloy wheel forging that can be used for a long time at 850°C

In this embodiment, a nickel-based deformed high-temperature alloy wheel forging with a diameter of 900 mm that can be used at 850° C. for a long time is prepared. The alloy composition is shown in Example 9 of Table 1.

The preparation process of alloy wheel forgings, as shown in Figure 3, includes the following steps:

Step 1. The smelting adopts the triple process, vacuum induction melting + electroslag remelting + vacuum consumable remelting. The diameter of the primary alloy ingot in vacuum induction melting is 355mm, the diameter of electroslag remelting alloy ingot is 423mm, and the vacuum consumable remelting alloy ingot The diameter is 508mm. Vacuum induction smelting includes the following steps: weighing raw materials according to the element ratio of the alloy, and performing vacuum induction smelting. The vacuum induction melting process includes several steps such as evacuation, smelting, refining and tapping. The vacuum in the evacuation stage is 20Pa, the temperature in the smelting stage is controlled to 1600°C, the temperature in the refining stage is controlled to 1500°C, the vacuum degree in the refining stage is 4Pa, and the steel is tapped. The temperature is controlled at 1480°C, and 20,000 Pa argon gas is filled for protection during tapping. After casting is completed, it is cooled for 3 hours and then demolded and cooled to obtain a primary alloy ingot. The primary alloy ingot is machined to prepare an electroslag remelting electrode. The filling ratio of the electrode to the mold is 0.8, and the electroslag ratio is CaF2: CaO: MgO: Al2O3: TiO2 = 70%: 15%: 1%: 15 %: 4%, the steady-state melting rate is 6.0kg/min, the cooling time after the secondary alloy ingot smelting is completed is 2h, and then demolding and cooling. The secondary alloy ingot is machined to prepare an electroslag remelting electrode. The filling ratio of the electroslag remelting electrode to the mold is 0.95, the melting rate is 5kg/min, and the cooling time after the tertiary alloy ingot smelting is 3h, and then After demolding and cooling, an alloy ingot is obtained.

Step 2. High-temperature diffusion homogenization annealing of alloy ingots includes heating, heat preservation and cooling processes. The heating rate is controlled to 35°C/h, the holding temperature is 1190°C, the holding time is 50h, and the cooling rate is controlled to 25°C/h. After homogenization annealing, after machining, the alloy ingot is heated to the forging temperature and kept warm and then out of the furnace for forging. The heating rate before forging is controlled to 35°C/h, the holding temperature is 1170°C, and the holding time is 7h. The forging billeting process includes For upsetting and drawing length, the forging time of a single fire is controlled within 1min~12min. After 12min, the temperature is returned to the furnace for 3h. Before each forging, the surface of the alloy ingot is covered with asbestos for heat preservation, and the total forging ratio is controlled to 17 to obtain the bar.

Step 3. Cut the bar according to 115% of the weight of the roulette forging. The height-to-diameter ratio of the bar is controlled to 2. After the bar is heated, the billet is upset, the heating rate before forging is controlled to 40℃/h, and the holding temperature is 1120 ℃, holding time is 7h, upsetting deformation is 60%. After the disc blank is heated, it is forged to form. The heating rate before forging is controlled to 45℃/h, the holding temperature is 1130℃, the holding time is 3h, the forging deformation is 60%, and the mold heating temperature is 650℃. The alloy roulette forging is obtained.

Step 4. The roulette forgings are machined for heat treatment. The heat treatment includes solution treatment, intermediate aging treatment and aging treatment. The solution treatment system is 1200°C for 3 hours, the intermediate aging treatment system is 1050°C for 4 hours, and the aging treatment system is 900 Incubate at ℃ for 25h.

In some implementations of this embodiment, this embodiment prepares a nickel-based deformed high-temperature alloy wheel forging with a diameter of 900 mm that can be used at 850°C for a long time and also includes impurity elements. Among the impurity elements, P = 0.015% , Mn = 0.5%, Si = 0.5%, S = 0.015%, O = 0.005%, N = 0.01%, Ag = 0.005%, Ca = 0.01%, Sn = 0.01%, Pb = 0.001%, Cu = 0.5% , Ta = 0.5%, V = 0.5%.

In some implementations of this embodiment, this embodiment prepares a nickel-based deformed high-temperature alloy wheel forging with a diameter of 900mm that can be used at 850°C for a long time and also includes impurity elements. Among the impurity elements, P=0.001% , Mn = 0.1%, Si = 0.2%, S = 0.003%, O = 0.001%, N = 0.0021%, Ag = 0.003%, Ca = 0.0011%, Sn = 0.001%, Pb = 0, Cu = 0, Ta =0, V=0.

In some implementations of this embodiment, the raw material may be selected from metallic nickel, metallic chromium or nickel-chromium alloy, metallic titanium, metallic aluminum, metallic molybdenum, metallic boron iron, metallic cobalt, metallic tungsten, nickel-tungsten alloy, niobium One or more of nickel alloy, vanadium iron, carbon electrode, master alloy.

Example 10, a nickel-based deformed superalloy wheel forging with a diameter of 600mm that can be used at 850°C for a long time

In this embodiment, a nickel-based deformed high-temperature alloy wheel forging with a diameter of 600 mm that can be used at 850° C. for a long time is prepared, and the alloy composition is shown in Example 10 in Table 1.

The preparation process of alloy wheel forgings, as shown in Figure 3, includes the following steps:

Step 1. The smelting adopts the triple process, vacuum induction melting + electroslag remelting + vacuum consumable remelting. The diameter of the primary alloy ingot in vacuum induction melting is 355mm, the diameter of electroslag remelting alloy ingot is 423mm, and the vacuum consumable remelting alloy ingot The diameter is 508mm. Vacuum induction smelting includes the following steps: weighing raw materials according to the element ratio of the alloy, and performing vacuum induction smelting. The vacuum induction melting process includes several steps such as evacuation, smelting, refining and tapping. The vacuum in the evacuation stage is 30Pa, the temperature in the smelting stage is controlled to 1580°C, the temperature in the refining stage is controlled to 1550°C, the vacuum degree in the refining stage is 5Pa, and the steel is tapped. The temperature is controlled at 1400°C, and 30,000 Pa is filled with argon protection during tapping. After casting is completed, it is cooled for 3 hours and then demolded and cooled to obtain a primary alloy ingot. The primary alloy ingot is machined to prepare an electroslag remelting electrode. The filling ratio of the electrode to the mold is 0.75, and the electroslag ratio is CaF2: CaO: MgO: Al2O3: TiO2 = 68%: 14%: 2%: 14 %: 2%, the steady-state melting rate is 5.0kg/min, the cooling time after the completion of the secondary alloy ingot smelting is 6h, and then demolding and cooling. The secondary alloy ingot is machined to prepare an electroslag remelting electrode. The filling ratio of the electroslag remelting electrode to the mold is 0.87, the melting rate is 3.8kg/min, and the cooling time after the tertiary alloy ingot smelting is 2h, Then, it is demolded and cooled to obtain an alloy ingot.

Step 2. High-temperature diffusion homogenization annealing of alloy ingots includes heating, holding and cooling processes. The heating rate is controlled to 15°C/h, the holding temperature is 1170°C, the holding time is 70h, and the cooling rate is controlled to 10°C/h. After homogenization annealing, after machining, the alloy ingot is heated to the forging temperature and kept warm and then out of the furnace for forging. The heating rate before forging is controlled to 30°C/h, the holding temperature is 1090°C, and the holding time is 5h. The forging billeting process includes For upsetting and drawing length, the forging time of a single fire is controlled within 1min-12min. After 12min, it is returned to the furnace for 3h. Before each forging, the surface of the alloy ingot is covered with asbestos for heat preservation, and the total forging ratio is controlled to 8 to obtain the bar.

Step 3. Cut the bar according to 145% of the weight of the roulette forging. The height-to-diameter ratio of the bar is controlled to 2.5. After the bar is heated, the billet is upset. The heating rate before forging is controlled to 35℃/h, and the holding temperature is 1150. ℃, holding time is 4h, upsetting deformation is 50%. After the disc blank is heated, it is die forged. Before forging, the heating rate is controlled to 35℃/h, the holding temperature is 1100℃, the holding time is 4h, the forging deformation is 35%, and the mold heating temperature is 350℃. The alloy roulette forging is obtained.

Step 4. The roulette forgings are machined for heat treatment. The heat treatment includes solution treatment, intermediate aging treatment and aging treatment. The solution treatment system is 1160℃ for 8 hours, the intermediate aging treatment system is 1100℃ for 10 hours, and the aging treatment system is 850. Incubate at ℃ for 30h.

In this embodiment, a nickel-based deformed superalloy wheel forging with a diameter of 600mm that can be used at 850°C for a long time in this embodiment also includes impurity elements. Among the impurity elements, P=0.010%, Mn= 0.15%, Si = 0.15%, S = 0.005%, O = 0.002%, N = 0.005%, Ag = 0.0005%, Ca = 0.005%, Sn = 0.005%, Pb = 0.0005%, Cu = 0.1%, Ta = 0.1%, V=0.1%.

In this embodiment, a nickel-based deformed superalloy wheel forging with a diameter of 600mm that can be used at 850°C for a long time in this embodiment also includes impurity elements. Among the impurity elements, P=0.010%, Mn= 0.102%, Si = 0.10%, S = 0.001%, O = 0.001%, N = 0.00015%, Ag = 0.0001%, Ca = 0.0015%, Sn = 0, Pb = 0.0, Cu = 0.01%, Ta = 0.01% , V=0.02%.

In some implementations of this embodiment, the raw material may be selected from metallic nickel, metallic chromium or nickel-chromium alloy, metallic titanium, metallic aluminum, metallic molybdenum, metallic boron iron, metallic cobalt, metallic tungsten, nickel-tungsten alloy, niobium One or more of nickel alloy, vanadium iron, carbon electrode, master alloy.

Example 11. A 600mm diameter nickel-based wrought superalloy wheel forging that can be used at 850°C for a long time

In this embodiment, a nickel-based deformed high-temperature alloy wheel forging with a diameter of 600 mm that can be used at 850° C. for a long time is prepared, and the alloy composition is shown in Example 10 in Table 1.

The difference from Example 10 is that: in step 1 of the preparation process of alloy wheel forgings, if the primary alloy ingot is an alloy ingot with a diameter of less than 500mm, the processing process for the primary alloy ingot will be changed The steps are: directly subjecting the primary alloy ingot to vacuum consumable remelting to obtain an alloy ingot.

The preparation process of alloy roulette forgings is as follows:

The smelting adopts a double process, vacuum induction melting + vacuum consumable remelting, the diameter of the primary alloy ingot in vacuum induction melting is 355mm, and the diameter of vacuum consumable remelting is 430mm. Vacuum induction smelting includes the following steps: Weigh the raw materials according to the element ratio of the alloy. The metal raw materials include: metallic nickel, metallic chromium or nickel-chromium alloy, metallic titanium, metallic aluminum, metallic molybdenum, boron iron, metallic cobalt, metallic tungsten, and nickel Tungsten alloys, niobium-nickel alloys, ferrovanadium, carbon electrodes, master alloys, etc. The vacuum induction smelting process includes several steps such as evacuation, smelting and smelting period, refining and tapping. The vacuum degree of the evacuation stage is 70Pa, the temperature in the melting period is controlled to 1580°C, the temperature in the refining period is controlled to 1550°C, and the refining stage The vacuum degree is 5Pa, the tapping temperature is controlled to 1500℃, and the tapping is filled with 15000Pa argon protection. After the casting is completed, it is cooled for 2h and then demolded and cooled to obtain a primary alloy ingot. The primary alloy ingot is machined and prepared into a consumable remelting electrode. The filling ratio of the consumable remelting electrode to the mold is 0.8, the melting rate is 2.5kg/min, and the cooling time after the tertiary alloy ingot smelting is 2h, and then After demolding and cooling, an alloy ingot is obtained.

The high-temperature diffusion homogenization annealing of alloy ingots includes heating, holding and cooling processes. The heating rate is controlled at 45°C/h, the holding temperature is 1210°C, the holding time is 40h, and the cooling rate is controlled at 25°C/h. After homogenization annealing, the alloy ingot is machined, heated to the forging temperature, and then out of the furnace for forging. The heating rate before forging is controlled to 45°C/h, the holding temperature is 1160°C, and the holding time is 4h. The forging billeting process includes For upsetting and drawing, the single-fire forging time exceeds 15 minutes and then returning to the furnace for 2 hours. Before each forging, the surface of the alloy ingot is covered with asbestos for heat preservation, and the total forging ratio is controlled to 10 to obtain the bar.

Cut 120% by weight of the bar according to the weight of the roulette forging. The height-to-diameter ratio of the bar is controlled to 2.5. After the bar is heated, the billet is upset. The heating rate before forging is controlled to 35°C/h, and the holding temperature is 1120°C. The holding time is 4h, and the upsetting deformation is 40%. After the disc blank is heated, it is forged and formed. The heating rate before forging is controlled to 35℃/h, the holding temperature is 1120℃, the holding time is 4h, the forging deformation is 40%, and the mold heating temperature is 650℃ to obtain the wheel. Disc forgings.

The roulette forgings are machined for heat treatment. The heat treatment includes solution treatment, intermediate aging treatment and aging treatment. The solution treatment system is 1180℃ for 5h, the intermediate aging treatment system is 1050℃ for 4h, and the aging treatment system is 910℃ for 12h. .

In some implementations of this embodiment, this embodiment prepares a nickel-based deformed superalloy wheel forging with a diameter of 600mm that can be used at 850°C for a long time and also includes impurity elements. Among the impurity elements, P = 0.015% , Mn = 0.5%, Si = 0.5%, S = 0.015%, O = 0.005%, N = 0.01%, Ag = 0.005%, Ca = 0.01%, Sn = 0.01%, Pb = 0.001%, Cu = 0.5% , Ta = 0.5%, V = 0.5%.

In some implementations of this embodiment, this embodiment prepares a nickel-based deformed superalloy wheel forging with a diameter of 600mm, which can be used at 850°C for a long time, also includes impurity elements. Among the impurity elements, P=0.001% , Mn = 0.1%, Si = 0.2%, S = 0.003%, O = 0.001%, N = 0.0021%, Ag = 0.003%, Ca = 0.0011%, Sn = 0.001%, Pb = 0, Cu = 0, Ta =0, V=0.

Example 12. A 600mm diameter nickel-based deformed superalloy wheel forging that can be used at 850°C for a long time

In this embodiment, a nickel-based deformed high-temperature alloy wheel forging with a diameter of 600 mm that can be used at 850° C. for a long time is prepared. The alloy composition is shown in Example 5 of Table 1.

The difference from Example 5 is: in step 1 of the preparation process of the alloy wheel forgings, if the primary alloy ingot is an alloy ingot with a diameter of less than 500mm, the processing process for the primary alloy ingot will be changed The steps are: directly subjecting the primary alloy ingot to vacuum consumable remelting to obtain an alloy ingot.

The other implementation process is the same as in Example 5.

In some implementations of this embodiment, this embodiment prepares a nickel-based deformed superalloy wheel forging with a diameter of 600mm that can be used at 850°C for a long time and also includes impurity elements. Among the impurity elements, P = 0.015% , Mn = 0.5%, Si = 0.5%, S = 0.015%, O = 0.005%, N = 0.01%, Ag = 0.005%, Ca = 0.01%, Sn = 0.01%, Pb = 0.001%, Cu = 0.5% , Ta = 0.5%, V = 0.5%.

In some implementations of this embodiment, this embodiment prepares a nickel-based deformed superalloy wheel forging with a diameter of 600mm, which can be used at 850°C for a long time, also includes impurity elements. Among the impurity elements, P=0.001% , Mn = 0.1%, Si = 0.2%, S = 0.003%, O = 0.001%, N = 0.0021%, Ag = 0.003%, Ca = 0.0011%, Sn = 0.001%, Pb = 0, Cu = 0, Ta =0, V=0.

Example 13. A 600mm diameter nickel-based deformed superalloy wheel forging that can be used at 850°C for a long time

In this embodiment, a nickel-based deformed high-temperature alloy wheel forging with a diameter of 600 mm that can be used at 850° C. for a long time is prepared. The alloy composition is shown in Example 6 of Table 1.

The difference from Example 6 is that in step 1 of the preparation process of alloy wheel forgings, if the primary alloy ingot is an alloy ingot with a diameter of less than 500mm, the processing process for the primary alloy ingot will be changed The steps are: directly subjecting the primary alloy ingot to vacuum consumable remelting to obtain an alloy ingot.

The other implementation process is the same as in Example 6.

In some implementations of this embodiment, this embodiment prepares a nickel-based deformed superalloy wheel forging with a diameter of 600mm that can be used at 850°C for a long time and also includes impurity elements. Among the impurity elements, P = 0.015% , Mn = 0.5%, Si = 0.5%, S = 0.015%, O = 0.005%, N = 0.01%, Ag = 0.005%, Ca = 0.01%, Sn = 0.01%, Pb = 0.001%, Cu = 0.5% , Ta = 0.5%, V = 0.5%.

In some implementations of this embodiment, this embodiment prepares a nickel-based deformed superalloy wheel forging with a diameter of 600mm, which can be used at 850°C for a long time, also includes impurity elements. Among the impurity elements, P=0.001% , Mn = 0.1%, Si = 0.2%, S = 0.003%, O = 0.001%, N = 0.0021%, Ag = 0.003%, Ca = 0.0011%, Sn = 0.001%, Pb = 0, Cu = 0, Ta =0, V=0.

Example 14. A nickel-based deformed superalloy wheel forging with a diameter of 600mm that can be used at 850°C for a long time

In this embodiment, a nickel-based deformed high-temperature alloy wheel forging with a diameter of 600 mm that can be used at 850° C. for a long time is prepared. The alloy composition is shown in Example 7 of Table 1.

The difference from Example 7 is that: in step 1 of the preparation process of alloy wheel forgings, if the primary alloy ingot is an alloy ingot with a diameter of less than 500mm, the processing process for the primary alloy ingot will be changed The steps are: directly subjecting the primary alloy ingot to vacuum consumable remelting to obtain an alloy ingot.

The other implementation process is the same as in Example 7.

In some implementations of this embodiment, this embodiment prepares a nickel-based deformed superalloy wheel forging with a diameter of 600mm that can be used at 850°C for a long time and also includes impurity elements. Among the impurity elements, P = 0.015% , Mn = 0.5%, Si = 0.5%, S = 0.015%, O = 0.005%, N = 0.01%, Ag = 0.005%, Ca = 0.01%, Sn = 0.01%, Pb = 0.001%, Cu = 0.5% , Ta = 0.5%, V = 0.5%.

In some implementations of this embodiment, this embodiment prepares a nickel-based deformed superalloy wheel forging with a diameter of 600mm, which can be used at 850°C for a long time, also includes impurity elements. Among the impurity elements, P=0.001% , Mn = 0.1%, Si = 0.2%, S = 0.003%, O = 0.001%, N = 0.0021%, Ag = 0.003%, Ca = 0.0011%, Sn = 0.001%, Pb = 0, Cu = 0, Ta =0, V=0.

Example 15. A 600mm diameter nickel-based deformed superalloy wheel forging that can be used at 850°C for a long time

In this embodiment, a nickel-based deformed high-temperature alloy wheel forging with a diameter of 600 mm that can be used at 850° C. for a long time is prepared, and the alloy composition is shown in Example 8 of Table 1.

The difference from Example 8 is that: in step 1 of the preparation process of alloy wheel forgings, if the primary alloy ingot is an alloy ingot with a diameter of less than 500mm, the processing process for the primary alloy ingot will be changed The steps are: directly subjecting the primary alloy ingot to vacuum consumable remelting to obtain an alloy ingot.

The other implementation process is the same as in Example 8.

In some implementations of this embodiment, this embodiment prepares a nickel-based deformed superalloy wheel forging with a diameter of 600mm that can be used at 850°C for a long time and also includes impurity elements. Among the impurity elements, P = 0.015% , Mn = 0.5%, Si = 0.5%, S = 0.015%, O = 0.005%, N = 0.01%, Ag = 0.005%, Ca = 0.01%, Sn = 0.01%, Pb = 0.001%, Cu = 0.5% , Ta = 0.5%, V = 0.5%.

In some implementations of this embodiment, this embodiment prepares a nickel-based deformed superalloy wheel forging with a diameter of 600mm, which can be used at 850°C for a long time, also includes impurity elements. Among the impurity elements, P=0.001% , Mn = 0.1%, Si = 0.2%, S = 0.003%, O = 0.001%, N = 0.0021%, Ag = 0.003%, Ca = 0.0011%, Sn = 0.001%, Pb = 0, Cu = 0, Ta =0, V=0.

Example 16. A 600mm diameter nickel-based deformed superalloy wheel forging that can be used for a long time at 850°C

In this embodiment, a nickel-based deformed high-temperature alloy wheel forging with a diameter of 600 mm that can be used at 850° C. for a long time is prepared. The alloy composition is shown in Example 9 of Table 1.

The difference from Example 9 is that in step 1 of the preparation process of alloy wheel forgings, if the primary alloy ingot is an alloy ingot with a diameter of less than 500mm, the processing process for the primary alloy ingot will be changed The steps are: directly subjecting the primary alloy ingot to vacuum consumable remelting to obtain an alloy ingot.

The other implementation process is the same as in Example 9.

In some implementations of this embodiment, this embodiment prepares a nickel-based deformed superalloy wheel forging with a diameter of 600mm that can be used at 850°C for a long time and also includes impurity elements. Among the impurity elements, P = 0.015% , Mn = 0.5%, Si = 0.5%, S = 0.015%, O = 0.005%, N = 0.01%, Ag = 0.005%, Ca = 0.01%, Sn = 0.01%, Pb = 0.001%, Cu = 0.5% , Ta = 0.5%, V = 0.5%.

In some implementations of this embodiment, this embodiment prepares a nickel-based deformed superalloy wheel forging with a diameter of 600mm, which can be used at 850°C for a long time, also includes impurity elements. Among the impurity elements, P=0.001% , Mn = 0.1%, Si = 0.2%, S = 0.003%, O = 0.001%, N = 0.0021%, Ag = 0.003%, Ca = 0.0011%, Sn = 0.001%, Pb = 0, Cu = 0, Ta =0, V=0.

Embodiment 17, performance measurement experiment

A nickel-based deformed superalloy used above 850°C obtained from any one of Examples 1 to 16 has been tested and analyzed by the inventor and found that this type of nickel-based deformed superalloy is based on Ni-Co-Cr elements. Component, forming a stable γ-austenite matrix, with the coherent precipitated γ'phase as the main strengthening phase, adding high content of γ'phase to form elements Al, Ti, Nb, and the highest mass percentage of γ'phase Reaching 55-65%, adding high content of W and Mo elements for solid solution strengthening, while adding an appropriate amount of B, Zr, Ce, Mg for microalloying to improve grain boundary properties, MC type and M6C type are precipitated in the alloy With M23C6 type carbides, MB2, M3B2 type borides and other second phases for composite strengthening, this part of the technical effect of the nickel-based deformed superalloy obtained in Example 1 is shown in Figure 1. The nickel-based deformations obtained in other examples The technical effect of this part of the superalloy is the same.

Refer to GB/T228.2 Metallic Material Tensile Test Part 2 High Temperature Test Method to carry out the test. The results show that under the condition of 850°C, the tensile strength of the alloy obtained from any one of Examples 1 to 16 can reach more than 850 MPa, and the yield strength can reach more than 700 MPa. According to GB/T2039 metal tensile creep and endurance test method, the results show that the alloy obtained from any one of Examples 1 to 16 has an endurance life of more than 100h under 350MPa.

The nickel-based deformed high-temperature alloy obtained from any one of Examples 1 to 16, has been aged for more than 5000 hours in the temperature range of 650 to 900 ℃ at room temperature, and the content of the precipitated harmful phase μ phase does not exceed 1%. Example 1 This part of the technical effect of the obtained nickel-based wrought superalloy is as shown in Figure 2. The part of the technical effect of the nickel-based wrought superalloy obtained in other embodiments is the same. In summary, it can be seen that the alloy obtained by the present invention can be used as 850 ℃ Long-term use of roulette material.

The nickel-based deformed superalloy obtained from any one of Examples 1 to 16, the chemical composition of the main strengthening phase γ'phase is (Ni, Co) ₃ (Al, Ti, Nb), containing a certain amount of Nb The γ′ phase after the element is more stable during the hot working process. The precipitation speed of the γ′ phase during the forging and billeting process under the free forging condition is slow, which avoids the problem of the deterioration of the thermoplasticity of the steel ingot caused by the strain aging precipitation, so that the alloy has sufficient Thermoplastic, can realize free forging and billeting.

The nickel-based deformed high-temperature alloy obtained from any one of Examples 1 to 16, adopts the smelting, forging blanking, forging forming and heat treatment processes provided by the present invention to prepare wheel forgings with a diameter of 100 to 1200 mm. Industrial production can be realized with conventional equipment, and it has good casting-forging process performance.

In summary, the nickel-based deformed superalloy roulette material that can be used for a long time at a temperature of 850°C and above obtained in any one of the embodiments 1 to 16 of the present invention can be prepared through reasonable composition design and preparation methods. The 100-1200mm roulette forgings have excellent tensile and durability properties at 850°C, good long-term structural stability, and the ability to be industrialized and mass-produced.

Comparative example 1. A nickel-based deformed superalloy wheel forging with a diameter of 900mm that can be used for a long time at 850℃

This comparative example prepares a nickel-based deformed superalloy wheel forging with a diameter of 900mm that can be used at 850℃ for a long time. The alloy composition is shown in Table 1 and Comparative Example 1. Compared with Example 3, trace elements such as B, Zr, Ce, Mg, etc. The content is lower.

The preparation process of alloy roulette forgings is as follows:

The smelting adopts a dual process, vacuum induction melting + vacuum consumable remelting. The diameter of the primary alloy ingot in vacuum induction melting is 355mm, the diameter of electroslag remelting alloy ingot is 440mm, and the diameter of vacuum consumable remelting alloy ingot is 508mm. Vacuum induction smelting includes the following steps: Weigh the raw materials according to the element ratio of the alloy. The metal raw materials include: metallic nickel, metallic chromium or nickel-chromium alloy, metallic titanium, metallic aluminum, metallic molybdenum, boron iron, metallic cobalt, metallic tungsten, and nickel Tungsten alloys, niobium-nickel alloys, ferrovanadium, carbon electrodes, return materials, etc. The vacuum induction melting process includes several steps such as evacuation, smelting, refining and tapping. The vacuum in the evacuation stage is 20Pa, the temperature in the smelting stage is controlled at 1550°C, the temperature in the refining stage is controlled at 1500°C, the vacuum in the refining stage is 4Pa, and the tapping The temperature is controlled at 1480°C, and 20,000 Pa argon protection is filled during tapping. After casting, it is cooled for 3 hours and then demolded and cooled to obtain a primary alloy ingot. The primary alloy ingot is machined and prepared into a consumable remelting electrode. The filling ratio of the electrode to the mold is 0.85, the melting rate is 3.5kg/min, and the cooling time after the tertiary alloy ingot smelting is 2h, and then demolding and cooling to obtain Alloy ingot.

The high-temperature diffusion homogenization annealing of alloy ingots includes heating, holding and cooling processes. The heating rate is controlled to 35°C/h, the holding temperature is 1190°C, the holding time is 50h, and the cooling rate is controlled to 25°C/h. After homogenization annealing, the alloy ingot is machined, heated to the forging temperature, and then out of the furnace for forging. The heating rate before forging is controlled to 35°C/h, the holding temperature is 1170°C, and the holding time is 6h. The forging billeting process includes Upsetting and drawing length, single-fire forging time exceeds 15 minutes, and then returning to the furnace for 2 hours. Before each forging, the surface of the alloy ingot is covered with asbestos for heat preservation, and the total forging ratio is controlled to 15 to obtain the bar.

Cut bars of appropriate length according to the weight of the roulette forgings. The height-to-diameter ratio of the bars is controlled to 2.5. After the bars are heated, the billet is upset. The heating rate before forging is controlled to 35°C/h, and the holding temperature is 1120°C. The time is 4h, and the upsetting deformation is 40%. After the disc blank is heated, it is forged and formed. The heating rate before forging is controlled to 35℃/h, the holding temperature is 1120℃, the holding time is 4h, the forging deformation is 40%, and the mold heating temperature is 650℃ to obtain the wheel. Disc forgings.

The roulette forgings are machined for heat treatment. The heat treatment includes solution treatment, intermediate aging treatment and aging treatment. The solution treatment system is 1180℃ for 5h, the intermediate aging treatment system is 1050℃ for 4h, and the aging treatment system is 910℃ for 12h. .

For the alloy bar prepared in Comparative Example 1, black spot metallurgical defects were found in low-power inspection, and cracking was obvious during the forging and billeting process, and the cracking tendency was greater than that of Example 3.

Comparative Example 2 A nickel-based deformed superalloy wheel forging with a diameter of 900mm that can be used for a long time at 850°C

In this comparative example, a nickel-based deformed superalloy wheel forging with a diameter of 900mm, which can be used for a long time at 850℃, is prepared in this comparative example. The alloy composition is shown in Table 1 and Comparative Example 2. Compared with Example 3, the Mo content is increased and the adjustment is lower. The W content increases the Fe content.

The preparation process of alloy roulette forgings is as follows:

The smelting adopts a double process, vacuum induction melting + electroslag remelting + vacuum consumable remelting. The diameter of the primary alloy ingot of vacuum induction melting is 355mm, the diameter of electroslag remelting alloy ingot is 423mm, and the diameter of vacuum consumable remelting alloy ingot is 508mm. Vacuum induction smelting includes the following steps: Weigh the raw materials according to the element ratio of the alloy. The metal raw materials include: metallic nickel, metallic chromium or nickel-chromium alloy, metallic titanium, metallic aluminum, metallic molybdenum, boron iron, metallic cobalt, metallic tungsten, and nickel Tungsten alloys, niobium-nickel alloys, ferrovanadium, carbon electrodes, return materials, etc. The vacuum induction melting process includes several steps such as evacuation, smelting, refining and tapping. The vacuum in the evacuation stage is 20Pa, the temperature in the smelting stage is controlled at 1550°C, the temperature in the refining stage is controlled at 1500°C, and the vacuum degree in the refining stage is 4Pa, and the tapping The temperature is controlled at 1480°C, and 20,000 Pa argon gas is filled for protection during tapping. After casting is completed, it is cooled for 3 hours and then demolded and cooled to obtain a primary alloy ingot. The primary alloy ingot is machined to prepare an electroslag remelting electrode. The filling ratio of the electrode to the mold is 0.8, and the electroslag ratio is CaF2: CaO: MgO: Al2O3: TiO2 = 65%: 15%: 1%: 15 %: 4%, the steady-state melting rate is 5.0kg/min, the cooling time after the completion of the secondary alloy ingot smelting is 2h, and then demolding and cooling. The secondary alloy ingot is machined and prepared into an electroslag remelting electrode. The filling ratio of the electrode to the mold is 0.83, and the melting rate is 2.8kg/min. The cooling time after the tertiary alloy ingot smelting is 2h, and then demolding and cooling. Obtain an alloy ingot.

The high-temperature diffusion homogenization annealing of alloy ingots includes heating, holding and cooling processes. The heating rate is controlled to 35°C/h, the holding temperature is 1190°C, the holding time is 50h, and the cooling rate is controlled to 25°C/h. After homogenization annealing, the alloy ingot is machined, heated to the forging temperature, and then out of the furnace for forging. The heating rate before forging is controlled to 35°C/h, the holding temperature is 1170°C, and the holding time is 6h. The forging billeting process includes Upsetting and drawing length, single-fire forging time exceeds 15 minutes, and then returning to the furnace for 2 hours. Before each forging, the surface of the alloy ingot is covered with asbestos for heat preservation, and the total forging ratio is controlled to 15 to obtain the bar.

Cut bars of appropriate length according to the weight of the roulette forgings. The height-to-diameter ratio of the bars is controlled to 2.5. After the bars are heated, the billet is upset. The heating rate before forging is controlled to 35°C/h, and the holding temperature is 1120°C. The time is 4h, and the upsetting deformation is 40%. After the disc blank is heated, it is forged and formed. The heating rate before forging is controlled to 35℃/h, the holding temperature is 1120℃, the holding time is 4h, the forging deformation is 40%, and the mold heating temperature is 650℃ to obtain the wheel. Disc forgings.

The roulette forgings are machined for heat treatment. The heat treatment includes solution treatment, intermediate aging treatment and aging treatment. The solution treatment system is 1180℃ for 5h, the intermediate aging treatment system is 1050℃ for 4h, and the aging treatment system is 910℃ for 12h. .

The alloy wheel forgings prepared in this comparative example were tested for high temperature and long-term microstructure stability. After the samples were aged for 3000 hours at 850℃, it was found that more harmful σ and μ phases were precipitated. When the stability of the tissue is poor.

Comparative analysis of comparative example 3 and other existing technologies

In order to study whether the existing technology has a promoting effect on the technology of the present invention, the inventor conducted the experiment of the following patented technology:

The test results show that the comparative patent CN110241331A alloy is also a highly alloyed nickel-based superalloy, and its composition ratio is similar to the alloy of the present invention, and the patented alloy is manufactured by powder metallurgy. However, the inventor found through experiments and comparisons that compared with the alloy of the present invention, the content of Ti element is higher, the content of W element is lower, and alloy elements such as Hf and Ta are added. For deformed superalloys produced by the casting-forging process, Ti element is an element that is easy to segregate. A high content of Ti element will increase the probability of formation of point deviation defects during the vacuum consumable remelting process; Hf element is an element that is extremely easy to oxidize. During the casting process, it is easily oxidized into HfO2 particles, and mixing into the molten pool will adversely affect the purity of the steel ingot.

Similarly, the comparative test results show that the comparative patent CN110205523A is also a highly alloyed nickel-based superalloy, and its composition ratio is similar to the alloy of the present invention, and the patented alloy is manufactured by powder metallurgy. Compared with the alloy of the present invention, the content of W element is low and the content of Mo element is high. The high Mo content is not conducive to the thermal stability of the alloy at 850°C, and harmful μ phase is easy to precipitate; the alloy also contains Hf element, which is not suitable for casting -Forging process production.

Similarly, the comparative test results show that the comparative patent CN108441705A is also a highly alloyed nickel-based superalloy, and its composition ratio is similar to that of the alloy of the present invention, and the patented alloy is manufactured by a casting-forging process. Compared with the alloy of the present invention, the content of W element is low, the content of Cr element is high, the solid solution strengthening effect is poor, the structure stability is not ideal, and it cannot meet the use requirement of 850℃; -Forging process production will have a greater risk of oxide inclusions.

Similarly, the comparative test results show that the comparative patent CN108425037A is also a highly alloyed nickel-based superalloy, and its composition ratio is similar to that of the alloy of the present invention, and the patented alloy is manufactured by powder metallurgy. Compared with the alloy of the present invention, the content of Ti element is high. Ti element increases the risk of metallurgical defects, and adds expensive Ta element for strengthening. The goal of low-cost alloys.

Similarly, the comparative test results show that the comparative patent CN108315599A is also a highly alloyed nickel-based superalloy, and its composition ratio is similar to that of the alloy of the present invention, and the patented alloy is manufactured by a casting-forging process. Compared with the alloy of the present invention, the content of W element is low, and a large amount of Nb element and Fe element are added. Nb element is an element with a very strong tendency to segregate. It is easy to precipitate harmful sigma phase when used under low temperature, so it cannot meet the requirements for use under high temperature conditions of 850°C.

Similarly, the comparative test results show that the comparative patent CN107760926A is also a highly alloyed nickel-based superalloy, and its composition ratio is similar to that of the alloy of the present invention, and the patented alloy is manufactured by a casting process. Compared with the alloy of the present invention, the Co content is low, which is not conducive to the structural stability of the alloy and the forging process performance; in addition, no beneficial trace elements such as Mg, Zr, Ce, etc. are added to the grain boundary, which is not suitable for high temperature deformation with equiaxed grains. Improved alloy properties.

The above are only the preferred specific embodiments of the present invention, but the protection scope of the present invention is not limited thereto. Any person skilled in the art can easily think of changes or changes within the technical scope disclosed by the present invention. All replacements should be covered within the protection scope of the present invention.

Claims (10)

1. A nickel-based deformed high-temperature alloy with high aluminum content, characterized in that the composition ratio is calculated by mass percentage, and the nickel-based deformed high-temperature alloy includes: C: 0.004 to 0.1%, W: 6.0 to 9.0%, and Cr: 7.0 to 12.0%, Mo: 1.0 to 4.0%, Co: 14.0 to 17.5%, Ti: 0.8 to 2.5%, Al: 3.5 to 6.0%, Nb: 0.8 to 2.5%, Zr: 0.005 to 0.1%, Mg: 0.005 ~0.1%; Ce: 0.001~0.1%, B: 0.005~0.1%, Fe: 0.005~2.0%, and the balance is Ni.
2. The nickel-based deformed superalloy according to claim 1, wherein the composition ratio is calculated by mass percentage, and the nickel-based deformed superalloy includes: C: 0.01-0.08%, W: 6.5-8.0%, Cr ：7.5～11.0%, Mo: 1.5～3.5%, Co: 14.5～17.5%, Ti: 1.0～2.0%, Al: 4.0～5.5%, Nb: 1.0～2.0%, Zr: 0.005～0.05%, Mg: 0.005～0.05%; Ce: 0.001～0.05%, B: 0.005～0.05%, Fe: 0.01～1.5%, the balance is Ni; the nickel-based deformed superalloy also includes impurity elements. Among them, P≤0.015%, Mn≤0.5%, Si≤0.5%, S≤0.015%, O≤0.005%, N≤0.01%, Ag≤0.005%, Ca≤0.01%, Sn≤0.01%, Pb≤0.001 %, Cu≤0.5%, Ta≤0.5%, V≤0.5%.
3. The nickel-based deformed superalloy according to claim 1, wherein the composition ratio is calculated by mass percentage, and the nickel-based deformed superalloy includes: C: 0.01 to 0.06%, W: 6.5 to 7.5%, Cr ：8.0～10.0%, Mo: 2.0～3.2%, Co: 15.0～16.5%, Ti: 1.2～1.8%, Al: 4.5～5.2%, Nb: 1.2～1.8%, Zr: 0.005～0.03%, Mg: 0.005～0.03%; Ce: 0.001～0.03%, B: 0.005～0.03%, Fe: 0.01～1.2%, the balance is Ni; the nickel-based deformed superalloy also includes impurity elements, in the impurity elements Among them, P≤0.010%, Mn≤0.15%, Si≤0.15%, S≤0.005%, O≤0.002%, N≤0.005%, Ag≤0.0005%, Ca≤0.005%, Sn≤0.005%, Pb≤0.0005 %, Cu≤0.1%, Ta≤0.1%, V≤0.1%.
4. The nickel-based wrought superalloy according to claim 1, wherein the nickel-based wrought superalloy uses γ austenite as a matrix, and the mass percentage of the strengthening phase γ'phase reaches 55-65%, so The chemical composition of the strengthening phase is (Ni, Co) ₃ (Al, Ti, Nb).
5. The nickel-based deformed superalloy according to claim 1, wherein the nickel-based deformed superalloy further includes a second phase, and the second phase includes: MC type carbide, M6C type carbide, M23C6 Type carbide, MB2 type boride, M3B2 type boride.
6. The nickel-based wrought superalloy according to claim 1, characterized in that, in the nickel-based wrought superalloy, the mass percentage of the γ'phase content is 55-65%, and the temperature range is 650-900℃ for a long time. The aging is more than 5000h, and the content of the precipitated harmful phase μ phase does not exceed 1%.
7. A method for preparing a nickel-based deformed high-temperature alloy with high aluminum content, which is characterized in that it comprises the following steps:

   Step 1: Use vacuum induction melting to smelt the metal raw material components described in any one of claims 1 to 5 into primary alloy ingots, and then refine them into secondary alloy ingots by electroslag remelting, and then refine by vacuum consumable remelting Is a tertiary alloy ingot to obtain an alloy ingot;

   Step 2: After the alloy ingot obtained in Step 1 is subjected to high-temperature diffusion homogenization annealing, it is heated and forged into a bar;

   Step 3: The bar obtained in step 2 is formed by blanking and die forging to obtain alloy wheel forgings;

   Step 4: After heat treatment of the alloy wheel forging obtained in Step 3, a nickel-based deformed high-temperature alloy wheel forging for long-term use at 850°C is obtained.
8. The preparation method according to claim 7, wherein the vacuum induction smelting in step 1 includes treatment processes: evacuation, smelting period, refining and tapping;

   In the evacuated treatment process, the vacuum degree is 10-100 Pa;

   In the treatment process during the smelting period, the temperature is controlled at 1300°C-1650°C;

   In the refining process, the temperature is controlled to be 1400°C to 1600°C, and the vacuum degree is 1 to 20 Pa;

   In the steel tapping treatment process, the temperature is controlled to 1420°C-1590°C, and argon protection is required to be filled with 10,000 to 50,000 Pa. After the casting is completed, it is cooled for 0.5 to 3 hours and then demolded and cooled to obtain a primary alloy ingot.
9. The preparation method according to claim 7, wherein the step 1 further comprises: preparing the primary alloy ingot into an I electroslag remelting electrode, the I electroslag remelting electrode and the crystallizer The filling ratio of slag is 0.75～0.9; in the process of electroslag remelting, the composition ratio of electroslag used is CaF2: CaO: MgO: Al2O3: TiO2 = 65 to 75%: 10 to 20%: 0.5 to 5%: 10-20%: 0.5-5%, the steady-state melting rate is 1.0-6.0 kg/min, the cooling time after the completion of the secondary alloy ingot smelting is 0.5h-6h, and then demolding and cooling.
10. The preparation method according to claim 7, wherein the step 1 further comprises: preparing the secondary alloy ingot into an II electroslag remelting electrode, the II electroslag remelting electrode and crystallizing The filling ratio of the device is 0.75～0.95, the melting rate is 1.0～5.0kg/min, the cooling time after the tertiary alloy ingot smelting is completed is 0.5h～3h, and then demolding and cooling.

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