CN111187946A - Nickel-based wrought superalloy with high aluminum content and preparation method thereof - Google Patents

Abstract

The invention provides a nickel-based wrought superalloy with high aluminum content and a preparation method thereof, wherein a traditional Ni-Co-Cr component is used as a base element, and the temperature bearing capacity of the alloy is effectively improved by increasing the content of alloy elements, particularly increasing the content of element Al formed by a gamma 'phase of a solid solution strengthening phase and increasing the content of the gamma' phase of the strengthening phase to 55-65%. The addition of Nb element in proper amount in the alloy can improve the stability of gamma' phase, further improve the casting-forging process performance, reduce the addition of Cr element and improve the long-term structure stability of the alloy at 850 ℃, and the high content of Al element can make up the surface stability loss caused by the reduction of Cr element. Meanwhile, a duplex process or a triple process is adopted for preparing and processing alloy raw materials, and the obtained nickel-based wrought superalloy solves the problem that no high-performance wheel disc forging material which can be used at 850 ℃ is available at present, and particularly has excellent tensile strength and yield strength at 850 ℃ and long service life.

Description

Nickel-based wrought superalloy with high aluminum content and preparation method thereof

Technical Field

The invention belongs to the field of alloy preparation, and particularly relates to a nickel-based wrought superalloy with high aluminum content and a preparation method thereof.

Background

The service temperature of the hot-end rotating wheel disc type forge pieces such as a high-pressure compressor disc and a turbine disc of an advanced gas turbine engine, such as an aircraft engine and a gas turbine, is gradually increased, and the maximum long-term service temperature is 850 ℃. The alloy material required by the wheel disc forging is required to have excellent strength and plasticity, high-temperature lasting creep property and long-term structure property stability at room temperature to 850 ℃, and also has good casting and forging technological properties.

At present, the largest amount of the nickel-based wrought high-temperature alloy wheel disc materials for domestic aeroengines is GH4169 alloy used below 650 ℃, the highest use temperature is GH4720Li, GH4065A, GH4738 and other nickel-based wrought high-temperature alloy wheel disc materials used below 750 ℃, the nickel-based wrought high-temperature alloy wheel disc materials for short-term use below 850 ℃, such as GH4141, GH4586 and the like, but the long-term use requirement above 850 ℃ cannot be met.

As is known, the most effective way to improve the service temperature of the nickel-based superalloy is to improve the alloying degree and increase the content of a reinforcing phase gamma' phase, but too high alloying degree causes great metallurgical segregation tendency and poor thermoplasticity of the alloy, so that great difficulty exists in developing a novel nickel-based deformed superalloy wheel disc material, and not only is the comprehensive performance required by alloying improved in component design, but also certain technological properties are required to be ensured by combining with the prior art conditions so as to ensure manufacturability. The traditional nickel-based high-temperature alloy with the gamma' phase content of 55-65% can only be produced by adopting a powder metallurgy or casting (including equiaxial casting, directional solidification and single crystal solidification) process, and the alloy produced by adopting a casting-forging process faces the problems of large element segregation tendency, easy formation of metallurgical defects, poor hot working (forging) plasticity and the like, so that the alloy components are not suitable for preparing the nickel-based deformed high-temperature alloy wheel disc material. In addition, although some nickel-based superalloys produced by powder metallurgy or casting processes can be used at temperatures up to 850 ℃, they have less structural homogeneity and compactness than forgings produced by cast-forging processes. Particularly, the high-temperature hot end rotating part of the wheel disc is produced by adopting a casting-forging process, so that the quality reliability of the wheel disc forging can be ensured to the greatest extent, and the industrial production with high efficiency and low cost can be realized. The direct use of powder metallurgy or cast alloy components for the cast-forging process has the disadvantages of inadaptation, such as the control of the content of segregation-prone elements Ti and Mo, the control of the content of oxidation-prone elements Hf, the addition of high-cost Ta elements, the addition of beneficial trace elements such as B, Zr, Ce and other grain boundaries, and the like, and the optimization and adjustment of the element proportion must be performed according to the characteristics of the cast-forging process.

Therefore, there is a need to provide an improved technical solution to overcome the technical problems in the prior art.

Disclosure of Invention

In order to solve the problems in the prior art, the invention provides the nickel-based wrought superalloy with high aluminum content and the preparation method thereof, and solves the problem that no high-performance wheel disc forging material which can be used at 850 ℃ is available at present, and particularly the high-performance wheel disc forging material has excellent tensile strength and yield strength at 850 ℃ and long service life.

The invention provides a nickel-based wrought superalloy with high aluminum content, which comprises the following components in percentage by mass: c: 0.004-0.1%, W: 6.0-9.0%, 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%, and the balance of Ni. The inventor proves that the alloy prepared by the technical scheme can be used for preparing wheel disc forgings used at 850 ℃, the diameter range of the wheel disc forgings is 200-1200 mm, the tensile strength at 850 ℃ is more than 800MPa, the yield strength is more than 650MPa, and the lasting life at 850 ℃/350MPa is more than 30 h.

Further, in the nickel-based wrought superalloy, the composition ratio is, in mass percent, that: 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% of Ni; the nickel-based wrought superalloy also comprises impurity elements, wherein P is less than or equal to 0.015%, Mn is less than or equal to 0.5%, Si is less than or equal to 0.5%, S is less than or equal to 0.015%, O is less than or equal to 0.005%, N is less than or equal to 0.01%, Ag is less than or equal to 0.005%, Ca is less than or equal to 0.01%, Sn is less than or equal to 0.01%, Pb is less than or equal to 0.001%, Cu is less than or equal to 0.5%, Ta is less than or equal to 0.5%, and V is. The inventor proves that the alloy prepared by the technical scheme can be used for preparing wheel disc forgings used at 850 ℃, the diameter range of the wheel disc forgings is 200-1200 mm, the tensile strength at 850 ℃ is more than 850MPa, the yield strength is more than 700MPa, and the lasting life at 850 ℃/350MPa is more than 50 h.

Further, in the nickel-based wrought superalloy, the composition ratio is, in mass percent, that: c: 0.01-0.06%, W: 6.5-7.5%, 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% of Ni; the nickel-based wrought superalloy also comprises impurity elements, wherein P is less than or equal to 0.010%, Mn is less than or equal to 0.15%, Si is less than or equal to 0.15%, S is less than or equal to 0.005%, O is less than or equal to 0.002%, N is less than or equal to 0.005%, Ag is less than or equal to 0.0005%, Ca is less than or equal to 0.005%, Sn is less than or equal to 0.005%, Pb is less than or equal to 0.0005%, Cu is less than or equal to 0.1%, Ta is less than or equal to 0.1%, and V is. The inventor proves that the alloy prepared by the technical scheme can be used for preparing wheel disc forgings used at 850 ℃, the diameter range of the wheel disc forgings is 200-1200 mm, the tensile strength at 850 ℃ is more than 900MPa, the yield strength is more than 750MPa, and the lasting life at 850 ℃/350MPa is more than 100 h.

Further, in the nickel-based wrought superalloy, gamma austenite is used as a matrix, the mass percentage content of a reinforcing phase gamma' phase reaches 55-65%, and the chemical composition of the reinforcing phase is (Ni, Co)₃(Al, Ti, Nb). The inventor proves that the alloy prepared by the technical scheme has good tensile strength and durability at 850 ℃ due to the high-content strengthening phase gamma 'phase, and the stability is improved by adding the Nb element modified gamma' phase.

Further, in the nickel-base wrought superalloy, the nickel-base wrought superalloy further comprises a second phase, the second phase comprising: MC type carbide, M6C type carbide, M23C6 type carbide, MB2 type boride, and M3B2 type boride. The inventor proves that the alloy prepared by the technical scheme can improve the durability of the alloy at 850 ℃.

Furthermore, in the nickel-based wrought superalloy, the mass percentage of gamma' phase content in the nickel-based wrought superalloy is 55-65%, the nickel-based wrought superalloy is aged for more than 5000 hours at the temperature of 650-900 ℃ for a long time, and the content of precipitated harmful phase mu phase is not more than 1%. The inventor proves that the alloy prepared by the technical scheme has good mechanical property in the temperature range of room temperature to 850 ℃ due to the high content of the gamma' phase, and can be used for a long time at 850 ℃ due to less harmful phase mu phase precipitation in long-term aging.

The second aspect of the invention provides a preparation method of a nickel-based wrought superalloy with high aluminum content, which is characterized by comprising the following steps:

step 1: smelting the metal raw material components of any claim 1 to 5 into a primary alloy ingot by vacuum induction smelting, remelting and refining the primary alloy ingot by electroslag to obtain a secondary alloy ingot, and remelting and refining the secondary alloy ingot by vacuum consumable melting to obtain a third alloy ingot to obtain an alloy ingot;

step 2: after the alloy ingot obtained in the step 1 is subjected to high-temperature diffusion homogenization annealing, heating, forging and cogging to form a bar;

and step 3: performing blanking and die forging on the bar obtained in the step 2 to obtain an alloy wheel disc forging;

and 4, step 4: and (4) carrying out heat treatment on the alloy wheel disc forged piece obtained in the step (3) to obtain the nickel-based deformation high-temperature alloy wheel disc forged piece used at the long time of 850 ℃.

The inventor proves that through the technical scheme, the wheel disc forging with the alloy diameter of 200-1200 mm can be prepared by adopting the existing smelting and forging equipment for the high-temperature alloy, and the industrial production can be realized.

Further, in the preparation method, the vacuum induction melting in the step 1 comprises the following treatment processes: evacuating, smelting period, refining and tapping; in the vacuumizing treatment process, the vacuum degree is 10-100 Pa; in the treatment process in the smelting period, the temperature is controlled to be 1300-1650 ℃; in the refining treatment process, the temperature is controlled to be 1400-1600 ℃, and the vacuum degree is 1-20 Pa; in the tapping treatment process, the temperature is controlled to be 1420-1590 ℃, and 10000-50000 Pa argon gas is filled for protection, after casting, the cast ingot is cooled for 0.5-3 h, and then demoulding and cooling are carried out, so that a primary alloy ingot is obtained. The inventor proves that by the technical scheme, the vacuum induction ingot of the alloy can be prepared, the alloy elements can be accurately controlled, the steel ingot can not be subjected to heat cracking, and the vacuum induction ingot can be used for preparing remelting and refining electrodes.

Further, in the preparation method, the step 1 further comprises: preparing the primary alloy ingot into an I electroslag remelting electrode, wherein the filling ratio of the I electroslag remelting electrode to the crystallizer is 0.75-0.9; in the electroslag remelting process, the adopted electroslag has the component proportion of CaF 2: CaO: MgO: al2O 3: 65-75% of TiO 2: 10-20%: 0.5-5%: 10-20%: 0.5-5%, the steady-state melting speed is 1.0-6.0 kg/min, the cooling time after the secondary alloy ingot is melted (i.e. electroslag remelting) is 0.5-6 h, and then demoulding and cooling are carried out. The inventor proves that through the technical scheme, after the primary alloy ingot prepared by vacuum induction melting is subjected to electroslag remelting, the inclusion content and the content of harmful impurity elements S in the alloy ingot can be effectively reduced, and meanwhile, the electroslag ingot with qualified components is prepared and used for preparing a vacuum consumable remelting electrode, so that the quality of the electrode can be remarkably improved, the process stability in the vacuum consumable remelting process is improved, and the electrode of the vacuum consumable ingot with the diameter of 500mm can be prepared.

Further, in the preparation method, the step 1 further comprises: and preparing the secondary alloy ingot into an II electroslag remelting electrode, wherein the filling ratio of the II electroslag remelting electrode to the crystallizer is 0.75-0.95, the melting speed is 1.0-5.0 kg/min, the cooling time after the third alloy ingot smelting (namely vacuum consumable remelting) is finished is 0.5-3 h, and then demolding and cooling are carried out. The inventor proves that by means of the technical scheme, the metallurgical quality of the steel ingot can be remarkably improved through the vacuum consumable remelting, and the compactness and the thermoplasticity of the steel ingot are improved.

Further, in the preparation method, in step 1, if the primary alloy ingot is an alloy ingot with a diameter less than 500mm, the treatment process of the primary alloy ingot is changed to: and directly carrying out vacuum consumable remelting on the primary alloy ingot to obtain the alloy ingot. The inventor proves that through the technical scheme, the diameter of the electrode required by the consumable ingot smaller than 500mm is small, the vacuum induction ingot is adopted to prepare the electrode, good metallurgical quality can be obtained, the process flow can be shortened, and the cost can be effectively reduced.

Further, in the preparation method, in the step 2, the high-temperature diffusion homogenization annealing comprises the processes of temperature rise, heat preservation and cooling; the heating speed is controlled to be 15-60 ℃/h, the heat preservation temperature is 1150-1250 ℃, the heat preservation time is 24-72 h, and the cooling speed is controlled to be 5-55 ℃/h. The inventor proves that through the technical scheme, the solidification stress can be eliminated through the homogenization diffusion annealing, the hot cracking of the steel ingot is avoided, the low-melting-point phase can be eliminated, the segregation degree of the dendrite of the element is effectively reduced, and the thermoplasticity of the steel ingot is improved.

Further, in the preparation method, the step 2 further comprises: and (2) carrying out homogenizing annealing on the alloy ingot obtained in the step (1), heating to a forging temperature, preserving heat, discharging from a furnace, forging, wherein the heating temperature rise speed before forging is controlled to be 15-60 ℃/h, the heat preservation temperature is 1050-1180 ℃, the heat preservation time is 2-8 h, the forging and cogging process comprises upsetting and drawing out, the single-fire forging time exceeds 5-30 min, then returning to the furnace, preserving heat for 1-6 h, coating asbestos on the surface of the alloy ingot before forging every time, preserving heat, and controlling the total forging ratio to be 5-20 to obtain the bar. The inventor proves that through the technical scheme, the steel ingot can be forged and cogging by using a quick forging machine, the steel ingot does not crack, and the cast structure can be converted into an isometric crystal structure.

Further, in the preparation method, the step 3 further includes: cutting the bar obtained in the step 2 according to the weight of the wheel disc forging to obtain a cut bar; the weight of the cut bar is 110-150% of that of the wheel disc forging piece, the height-diameter ratio of the cut bar is controlled to be 1.5-3.0, the cut bar is subjected to upsetting to form a blank after being heated, the heating and temperature rising speed before forging is controlled to be 20-50 ℃/h, the heat preservation temperature is 1000-1150 ℃, the heat preservation time is 2-8 h, and the upsetting deformation is 30-70%, so that the disc blank is obtained. The inventor proves that through the technical scheme, the bar upsetting process is stable, and forging defects such as forging cracks, large heads, small heads, wrinkles and the like do not occur.

Further, in the preparation method, the disc blank is subjected to die forging forming after being heated, the heating speed before forging is controlled to be 20-50 ℃/h, the heat preservation temperature is 950-1150 ℃, the heat preservation time is 2-8 h, the die forging deformation is 30-70%, and the die heating temperature is 300-1050 ℃. The inventor proves that through the technical scheme, the die forging forming of the wheel disc forging piece can be realized, the forging cracking does not occur, the mold filling effect is good, and the tissue uniformity is good.

Further, in the preparation method, in the step 4, the wheel disc forging obtained in the step 3 is subjected to machining and heat treatment, wherein the heat treatment comprises solid solution treatment, intermediate aging treatment and aging treatment, the solid solution treatment method is heat preservation at 1150-1220 ℃ for 2-10 h, the intermediate aging treatment method is heat preservation at 1000-1150 ℃ for 2-10 h, and the aging treatment method is heat preservation at 760-920 ℃ for 8-32 h. The inventor proves that through the technical scheme, the wheel disc forging can obtain uniform microstructure and good mechanical property after being subjected to heat treatment, and the internal stress in the forging can be effectively reduced.

The beneficial effects created by the invention are as follows:

the patent provides a high-aluminum-content nickel-based deformation superalloy and a preparation method, and by adopting the alloy components and the preparation method provided by the patent, a wheel disc forging with the diameter of 100-1200 mm can be prepared by adopting a casting-forging process, the high-aluminum-content nickel-based deformation superalloy has good mechanical property and satisfactory service stability within the temperature range of 850 ℃ at room temperature, and can fill the blank of a domestic 850 ℃ deformation disc material.

Drawings

In order to more clearly illustrate the technical solution of the present invention, the drawings needed to be used in the embodiments will be briefly described below, it should be understood that the following drawings only illustrate some embodiments of the present invention and therefore should not be considered as limiting the scope, and for those skilled in the art, other related drawings can be obtained according to these drawings without inventive effort.

FIG. 1 is a thermodynamic equilibrium phase diagram of the inventive alloy;

FIG. 2 is a plot of the isothermal transformation of the μ phase (TTT curve) of the inventive alloy;

FIG. 3 is a flow chart of the alloy wheel disc forging manufacturing process of the invention.

Detailed Description

The experimental methods of the following examples, which are not specified under specific conditions, are generally determined according to national standards. If there is no corresponding national standard, it is carried out according to the usual international standards, to the conventional conditions or to the conditions recommended by the manufacturer.

The features mentioned with reference to the invention or the features mentioned with reference to the embodiments can be combined. All the features disclosed in this specification may be combined in any combination, and each feature disclosed in this specification may be replaced by alternative features serving the same, equivalent or similar purpose. Thus, unless expressly stated otherwise, the features disclosed are merely generic examples of equivalent or similar features.

In the present invention, all the technical features mentioned herein and preferred features may be combined with each other to form a new technical solution, if not specifically stated.

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

In order to make the technical means, the original characteristics, the achieved purposes and the effects of the invention easy to understand, the invention is further described with the specific embodiments, but the invention includes but is not limited to the embodiments.

In order to develop a nickel-based wrought superalloy wheel disc material which can be used at 850 ℃ for a long time and has controllable cost, on one hand, noble metals such as Ta and Re or strategic reserve elements such as Co and rare earth are not added or are added less, and the conventional elements of the traditional nickel-based wrought superalloy wheel disc material are used as much as possible; on the other hand, the alloy is ensured to have satisfactory performance at 850 ℃, meanwhile, the casting-forging process performance of the alloy is considered, the existing smelting and forging equipment can be utilized to prepare wheel disc forgings with the diameters of 100-1200 mm, and the mass and low-cost production is realized.

The alloy composition design idea is as follows, the traditional Ni-Co-Cr component is taken as a matrix element, and the temperature bearing capacity of the alloy is effectively improved by increasing the content of alloy elements, particularly the content of element Al formed by a high solid solution strengthening phase gamma 'phase and increasing the content of the strengthening phase gamma' phase to 55-65%. The addition of Nb element in proper amount in the alloy can improve the stability of gamma' phase, further improve the casting-forging process performance, reduce the addition of Cr element and improve the long-term structure stability of the alloy at 850 ℃, and the high content of Al element can make up the surface stability loss caused by the reduction of Cr element.

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

Co is added into Ni, which not only can play a role in solid solution strengthening, but also can improve the solid solubility of Ni matrix components, reduce the stacking fault energy of the alloy and improve the high-temperature performance; the Cr element is added into the Ni-Co, the Cr not only can play a role in solid solution strengthening, but also can form compact and automatically-repaired Cr on the surface of the alloy₂O₃The oxidation film ensures that the alloy has excellent oxidation resistance and corrosion resistance, but the solid solubility of the Ni-Co-Cr matrix component is reduced due to the excessively high Cr content, and harmful mu phase is easy to precipitate, which is not favorable for long-term service stability.

W and Mo are the most effective solid solution strengthening elements in the Ni-based alloy, the high content of Mo is not beneficial to the hot corrosion resistance of the alloy and promotes mu phase precipitation, the high content of W can cause the density of the alloy to be increased, but in order to simultaneously improve the temperature bearing capacity and the high-temperature long-term structure stability of the alloy, the design of high W and low Mo is adopted in the patent.

Al is the most effective element for forming the gamma' -phase of the precipitation strengthening phase in the Ni-based alloy, and Al element is capable of forming Al₂O₃The oxidation film can also improve the oxidation resistance and the corrosion resistance of the alloy, but the high content of Al element is not beneficial to the forging and casting performance of the alloy. The Al content in the traditional nickel-based wrought superalloy is generally not more than 4%, on one hand, the atomic number of Al is small, so that the atomic percentage is high, the Al content is increased to more than 4%, a higher-content gamma' phase is precipitated, the thermoplasticity of steel ingots is not facilitated, and the thermoplasticity of the steel ingots is obviously reduced; on the other hand, the increase of the Al content can increase the viscosity of the molten steel, enlarge the temperature range of a solid-liquid phase line, prolong the solidification time of the molten steel, easily form looseness in the casting and solidification process of steel ingots, and also separate out more gamma 'phases to form larger gamma' phasesThe structural stress can cause the steel ingot to crack when being serious, and is not favorable for the casting performance. In order to improve the high-temperature mechanical property and the oxidation resistance of the alloy, the Al element content is improved, the Cr element content is reduced, and the high-temperature long-term tissue stability is further improved.

Ti is also an effective forming element of a precipitation strengthening phase gamma' phase in the Ni-based alloy, but the solidification segregation tendency of Ti is large, a high Ti alloy is easy to form Ti-rich channel segregation type metallurgical defects, and Ti is also a strong forming element of MC type carbide; in order to improve the stability and the strengthening effect of a gamma' phase, the design of high Al and low Ti is adopted, and the content of Ti is controlled by adjusting the Al/Ti ratio.

Nb is also an effective element for forming a precipitation strengthening phase gamma 'phase in the Ni-based alloy, and Nb entering the gamma' phase can play a role in stabilizing the gamma 'phase and effectively reduce the precipitation speed of the gamma' phase in the cooling process, but the solidification segregation tendency of Nb element is large. The alloy adopts a high gamma 'phase design, and in order to improve the stability of the gamma' phase and improve the forging process performance, a proper amount of Nb element is added and is controlled according to the total amount of Al + Ti + Nb.

C is an important element in the nickel-based wrought superalloy, mainly forms carbide, and can form MC type and M type according to the composition of alloy elements₆C and M₂₃C₆Various types of carbides such as type; the carbide can improve the durability of the alloy at the high temperature of 850 ℃, and therefore, a proper amount of C element is added into the alloy.

Fe is a gamma austenite component element at the same time, but too much Fe promotes the precipitation of sigma phase, which is not favorable for the long-term structure stability at high temperature, while too low Fe content is unfavorable for the industrial metallurgical production. This is because some alloys containing Fe are usually produced in the high temperature alloy smelting furnace of the factory, and if the Fe requirement is too low, measures such as furnace washing or new furnace lining are required, which not only affects the production efficiency, but also may cause the Fe element to exceed the standard, resulting in the decrease of the qualification rate. Therefore, the proportion of each element is comprehensively considered, the maximum upper limit control of the Fe element is examined, the industrial production is guaranteed, and the high-temperature long-time structure stability of the alloy is improved to the maximum extent.

In the aspect of alloy component design, the content of Co element is properly improved and the content of Cr element is reduced in order to improve the solid solubility and long-term stability of the matrix components. The method is remarkably characterized in that the addition amount of Al element is remarkably increased, on one hand, the precipitation amount of gamma' phase is increased to improve the mechanical property of the alloy, and on the other hand, the attenuation of oxidation resistance and corrosion resistance after the content of Cr element is reduced is compensated. Adding appropriate amount of Ti and Nb elements to form more stable (Ni, Co)₃Compared with the pure high-Al Ni3Al type gamma ' phase, the (Al, Ti, Nb) type gamma ' phase is more stable after adding a proper amount of Nb and Ti, can effectively solve the problem of structural stress caused by the precipitation of the gamma ' phase in the process of solidifying the steel ingot after increasing the Al content, and can improve the forging performance of the steel ingot. In order to improve the solid solution strengthening effect and the high-temperature tensile property at 850 ℃, W and Mo elements are added simultaneously, the W/Mo ratio is increased, and the hot corrosion resistance attenuation and the mu phase precipitation tendency caused by excessively high Mo element content are reduced. In order to improve the high-temperature endurance property of the alloy at 850 ℃, a proper amount of C element is added to form MC type and M type₆C and M₂₃C₆Strengthening various types of carbide such as type, and adding a proper amount of B element to form MB₂、M₃B₂The type boride improves high-temperature heat resistance. In order to further improve the casting-forging process performance of the alloy, a proper amount of Mg and Ce elements are added to improve the grain boundary performance, improve the thermoplasticity of the alloy cast ingot and optimize the casting-forging process performance. Other elements such as P, Mn, Si, S, O, N, Ag, Ca, Sn, Pb, Cu, Ta, V and the like are impurity elements, are not beneficial to the mechanical property and the process property of the alloy and are controlled according to the minimum content of smelting capacity.

In order to improve the cleanliness, homogeneity and compactness of the cast ingot, after a primary alloy ingot with qualified components is smelted and cast in a vacuum induction mode, electroslag remelting refining is adopted to remove inclusions and S elements and improve the metallurgical quality of the alloy ingot, and then vacuum consumable remelting refining is adopted to further improve the metallurgical quality, so that the alloy ingot with certain thermoplasticity is obtained.

The following are tables comparing the alloy composition and the technical effects in the specific examples and comparative examples.

TABLE 1 alloy compositions of examples and comparative examples (values in the tables are percentage values)

TABLE 2 comparison of the Process and physicochemical test results for the examples and comparative examples

Embodiment 1, preparation method of nickel-based wrought superalloy wheel disc forging capable of being used at 850 DEG C

This example produced a nickel base wrought superalloy disk forging (200 mm diameter) that could be used at 850 c long with the alloy composition shown in table 1 for example 1.

The preparation process of the alloy wheel disc forging comprises the following steps:

the smelting adopts a duplex process (namely vacuum induction smelting and vacuum consumable remelting), the diameter of an alloy ingot obtained by vacuum induction smelting is 250mm, and the diameter of an alloy ingot obtained by vacuum consumable remelting is 305 mm. The vacuum induction melting comprises the following steps: weighing raw materials according to the element proportion of the alloy, and carrying out vacuum induction melting. The vacuum induction smelting process comprises the steps of evacuation, smelting period, refining, tapping and the like, wherein the vacuum degree in the evacuation period is 50Pa, the temperature in the smelting period is 1550 ℃, the temperature in the refining period is 1500 ℃, the vacuum degree in the refining period is 10Pa, the tapping temperature is 1490 ℃, 10000Pa argon is filled for protection during tapping, and after casting is completed, cooling is carried out for 1.5 hours, demoulding and cooling are carried out, so that a primary alloy ingot is obtained. And machining the primary alloy ingot to prepare a consumable remelting electrode, wherein the filling ratio of the consumable remelting electrode to the crystallizer is 0.8, the melting speed is 1.5kg/min, the cooling time after the three times of alloy ingot melting is 1.5h, and then demolding and cooling are carried out to obtain the alloy ingot.

The alloy ingot needs to be subjected to high-temperature diffusion homogenization annealing treatment, which comprises the processes of heating, heat preservation and cooling, wherein the heating speed is controlled to be 55 ℃/h, the heat preservation temperature is 1200 ℃, the heat preservation time is 30h, and the cooling speed is controlled to be 25 ℃/h. After carrying out homogenizing annealing on the alloy ingot, machining the alloy ingot, heating the alloy ingot to a forging temperature, keeping the temperature, then discharging the alloy ingot out of a furnace for forging, controlling the heating speed to be 55 ℃/h before forging, the heat preservation temperature to be 1140 ℃ and the heat preservation time to be 3h, wherein the forging and cogging process comprises upsetting and drawing, the single-fire forging time is controlled to be 1-20 min, the alloy ingot is returned to the furnace for heat preservation for 1h after more than 20min, the surface of the alloy ingot is coated with asbestos before each forging, the heat preservation is carried out, and the total forging ratio is controlled to be 12, so that the.

Cutting a bar according to 150% of the weight of the wheel disc forging, controlling the height-diameter ratio of the bar to be 2.0, heating the bar, upsetting the bar to form a blank, controlling the heating speed before forging to be 50 ℃/h, the heat preservation temperature to be 1120 ℃, the heat preservation time to be 2h, and the upsetting deformation to be 35%, thereby obtaining the disc blank. And heating the disc blank, and then performing die forging forming, wherein the heating speed before forging is controlled to be 50 ℃/h, the heat preservation temperature is 1100 ℃, the heat preservation time is 2h, the die forging deformation is 55%, and the die heating temperature is 1050 ℃, so that the alloy wheel disc forging can be obtained.

The wheel disc forging is subjected to heat treatment through machining, wherein the heat treatment comprises solution treatment, intermediate aging treatment and aging treatment, the solution treatment system is used for preserving heat for 2 hours at 1150 ℃, the intermediate aging treatment system is used for preserving heat for 3 hours at 1000 ℃, and the aging treatment system is used for preserving heat for 12 hours at 800 ℃.

In some embodiments of this embodiment, the raw material may be selected from one or more of metallic nickel, metallic chromium or nichrome, metallic titanium, metallic aluminum, metallic molybdenum, ferroboron, metallic cobalt, metallic tungsten, nickel-tungsten alloy, niobium-nickel alloy, ferrovanadium, carbon electrode, and intermediate alloy.

Embodiment 2, preparation method of nickel-based wrought superalloy wheel disc forging with diameter of 550mm and capable of being used at 850 DEG C

This example produced a 550mm diameter disk forging of nickel-base wrought superalloy that could be used at 850 c long with the alloy compositions shown in table 1, example 2.

The preparation process of the alloy wheel disc forging comprises the following steps:

the smelting adopts a duplex process, vacuum induction smelting and vacuum consumable remelting, the diameter of an alloy ingot subjected to vacuum induction smelting once is 370mm, and the diameter of an alloy ingot subjected to vacuum consumable remelting is 460 mm. The vacuum induction melting comprises the following steps: weighing raw materials according to the element proportion of the alloy, and carrying out vacuum induction melting. The vacuum induction melting process comprises the steps of evacuation, melting period, refining, tapping and the like, wherein the vacuum degree in the evacuation period is 70Pa, the temperature in the melting period is 1580 ℃, the temperature in the refining period is 1550 ℃, the vacuum degree in the refining period is 15Pa, the tapping temperature is 1500 ℃, argon gas with 15000Pa is filled for protection when tapping, and the alloy ingot is obtained after the casting is finished and the alloy ingot is cooled for 2 hours after demoulding and cooling. And machining the primary alloy ingot to prepare a consumable remelting electrode, wherein the filling ratio of the consumable remelting electrode to the crystallizer is 0.8, the melting speed is 2.5kg/min, the cooling time after the three times of alloy ingot melting is 2 hours, and then demolding and cooling to obtain the alloy ingot.

The high-temperature diffusion homogenization annealing of the alloy ingot comprises the processes of temperature rise, heat preservation and cooling, wherein the temperature rise speed is controlled to be 45 ℃/h, the heat preservation temperature is 1210 ℃, the heat preservation time is 40h, and the cooling speed is controlled to be 25 ℃/h. After carrying out homogenizing annealing on the alloy ingot, machining the alloy ingot, heating the alloy ingot to a forging temperature, keeping the temperature, then discharging the alloy ingot out of a furnace for forging, controlling the heating speed to be 45 ℃/h before forging, the heat preservation temperature to be 1160 ℃, the heat preservation time to be 4h, carrying out forging cogging process including upsetting and drawing out, returning the alloy ingot to the furnace for heat preservation for 2h after single-fire forging time exceeds 15min, coating asbestos on the surface of the alloy ingot before each forging for heat preservation, and controlling the total forging ratio to be 8 to obtain the bar.

Cutting a bar according to 130% of the weight of the wheel disc forging, controlling the height-diameter ratio of the bar to be 2.5, upsetting the bar after heating the bar to form a blank, controlling the heating speed before forging to be 45 ℃/h, the heat preservation temperature to be 1140 ℃, the heat preservation time to be 4h, and the upsetting deformation to be 40%. And heating the disc blank, and then performing die forging forming, wherein the heating temperature rise speed before forging is controlled to be 45 ℃/h, the heat preservation temperature is 1120 ℃, the heat preservation time is 4h, the die forging deformation is 50%, and the die heating temperature is 950 ℃, so that the alloy wheel disc forging can be obtained.

And (3) carrying out heat treatment on the wheel disc forging through machining, wherein the heat treatment comprises solution treatment, intermediate aging treatment and aging treatment, the solution treatment system is heat preservation for 4h at 1160 ℃, the intermediate aging treatment system is heat preservation for 4h at 1050 ℃, and the aging treatment system is heat preservation for 24h at 850 ℃.

In some embodiments of this embodiment, the raw material may be selected from one or more of metallic nickel, metallic chromium or nichrome, metallic titanium, metallic aluminum, metallic molybdenum, ferroboron, metallic cobalt, metallic tungsten, nickel-tungsten alloy, niobium-nickel alloy, ferrovanadium, carbon electrode, and intermediate alloy.

Example 3 Nickel base wrought superalloy wheel disc forging with 900mm diameter capable of being used at 850 DEG C

A900 mm diameter disk forging of nickel-based wrought superalloy capable of being used at 850 ℃ length was prepared in this example, and the alloy compositions are shown in Table 1, example 3.

The preparation process of the alloy wheel disc forging comprises the following steps:

the smelting adopts a triple process, namely vacuum induction smelting, electroslag remelting and vacuum consumable remelting, wherein the diameter of an alloy ingot subjected to vacuum induction smelting is 355mm, the diameter of an electroslag remelting alloy ingot is 423mm, and the diameter of a vacuum consumable remelting alloy ingot is 508 mm. The vacuum induction melting comprises the following steps: weighing raw materials according to the element proportion of the alloy, and carrying out vacuum induction melting. The vacuum induction smelting process comprises the steps of evacuation, smelting period, refining, tapping and the like, wherein the vacuum degree in the evacuation period is 20Pa, the temperature in the smelting period is 1550 ℃, the temperature in the refining period is 1500 ℃, the vacuum degree in the refining period is 4Pa, the tapping temperature is 1480 ℃, 20000Pa argon is filled for protection during tapping, and after casting is completed, the ingot is cooled for 3 hours, demoulded and cooled to obtain a primary alloy ingot. Machining the primary alloy ingot to prepare an electroslag remelting electrode, wherein the filling ratio of the electroslag remelting electrode to a crystallizer is 0.8, and the electroslag ratio is CaF 2: CaO: MgO: al2O 3: TiO2 ═ 65%: 15%: 1%: 15%: 4 percent, the steady-state melting speed is 5.0kg/min, the cooling time after the secondary alloy ingot is melted is 2 hours, and then the ingot is demoulded and cooled. And machining the secondary alloy ingot to prepare an electroslag remelting electrode, wherein the filling ratio of the electroslag remelting electrode to a crystallizer is 0.83, the melting speed is 2.8kg/min, the cooling time after the third alloy ingot is melted is 2 hours, and then demolding and cooling are carried out to obtain the alloy ingot.

The high-temperature diffusion homogenization annealing of the alloy ingot comprises the processes of heating, heat preservation and cooling, wherein the heating speed is controlled to be 35 ℃/h, the heat preservation temperature is 1190 ℃, the heat preservation time is 50h, and the cooling speed is controlled to be 25 ℃/h. After carrying out homogenizing annealing on the alloy ingot, machining the alloy ingot, heating the alloy ingot to a forging temperature, keeping the temperature, then discharging the alloy ingot out of a furnace for forging, controlling the heating speed to be 35 ℃/h before forging, the heat preservation temperature to be 1170 ℃, the heat preservation time to be 6h, carrying out forging cogging process including upsetting and drawing out, returning the alloy ingot to the furnace for heat preservation for 2h after single-fire forging time exceeds 15min, coating asbestos on the surface of the alloy ingot before forging each time for heat preservation, and controlling the total forging ratio to be 15 to obtain the bar.

Cutting a bar according to 120% of the weight of the wheel disc forging, controlling the height-diameter ratio of the bar to be 2.5, upsetting the bar after heating the bar to form a blank, controlling the heating speed before forging to be 35 ℃/h, the heat preservation temperature to be 1120 ℃, the heat preservation time to be 4h, and the upsetting deformation to be 40%. And heating the disc blank, and then performing die forging forming, wherein the heating temperature rise speed before forging is controlled to be 35 ℃/h, the heat preservation temperature is 1120 ℃, the heat preservation time is 4h, the die forging deformation is 40%, and the die heating temperature is 650 ℃, so that the alloy wheel disc forging can be obtained.

The wheel disc forging is subjected to heat treatment through machining, wherein the heat treatment comprises solid solution treatment, intermediate aging treatment and aging treatment, the solid solution treatment system is 1180 ℃ and is kept warm for 5 hours, the intermediate aging treatment system is 1050 ℃ and is kept warm for 4 hours, and the aging treatment system is 910 ℃ and is kept warm for 12 hours.

In some embodiments of this embodiment, the raw material may be selected from one or more of metallic nickel, metallic chromium or nichrome, metallic titanium, metallic aluminum, metallic molybdenum, ferroboron, metallic cobalt, metallic tungsten, nickel-tungsten alloy, niobium-nickel alloy, ferrovanadium, carbon electrode, and intermediate alloy.

Example 4 Nickel base wrought superalloy wheel disc forging with 1200mm diameter capable of being used at 850 DEG C

This example produced a 1200mm diameter disc forging of nickel-base wrought superalloy that could be used at 850 c long with the alloy composition shown in table 1, example 4.

The preparation process of the alloy wheel disc forging comprises the following steps:

the smelting adopts a triple process, namely vacuum induction smelting, electroslag remelting and vacuum consumable remelting, wherein the diameter of an alloy ingot subjected to vacuum induction smelting once is 440mm, the diameter of the electroslag remelting alloy ingot is 580mm, and the diameter of the vacuum consumable remelting alloy ingot is 660 mm. The vacuum induction melting comprises the following steps: weighing raw materials according to the element proportion of the alloy, and carrying out vacuum induction melting. The vacuum induction melting process comprises the steps of evacuation, melting period, refining, tapping and the like, wherein the vacuum degree in the evacuation period is 30Pa, the temperature in the melting period is controlled to be 1580 ℃, the temperature in the refining period is controlled to be 1550 ℃, the vacuum degree in the refining period is 5Pa, the tapping temperature is controlled to be 1480 ℃, 25000Pa argon is filled for protection during tapping, and after casting is completed, the alloy ingot is cooled for 3 hours, demoulded and cooled to obtain a primary alloy ingot. Machining the primary alloy ingot to prepare an electroslag remelting electrode, wherein the filling ratio of the electrode to a crystallizer is 0.75, and the electroslag ratio is CaF 2: CaO: MgO: al2O 3: TiO 2-68%: 14%: 2%: 14%: 2 percent, the steady-state melting speed is 6.0kg/min, the cooling time after the secondary alloy ingot is melted is 6 hours, and then the ingot is demoulded and cooled. And machining the secondary alloy ingot to prepare an electroslag remelting electrode, wherein the filling ratio of the electroslag remelting electrode to a crystallizer is 0.87, the melting speed is 3.8kg/min, the cooling time after the third alloy ingot is melted is 3 hours, and then demolding and cooling are carried out to obtain the alloy ingot.

The high-temperature diffusion homogenization annealing of the alloy ingot comprises the processes of heating, heat preservation and cooling, wherein the heating speed is controlled to be 15 ℃/h, the heat preservation temperature is 1180 ℃, the heat preservation time is 70h, and the cooling speed is controlled to be 5 ℃/h. After carrying out homogenizing annealing on the alloy ingot, machining the alloy ingot, heating the alloy ingot to a forging temperature, keeping the temperature, then discharging the alloy ingot out of a furnace for forging, controlling the heating speed before forging to be 15 ℃/h, the heat preservation temperature to be 1180 ℃, keeping the heat preservation time to be 6h, carrying out forging cogging process including upsetting and drawing out, returning the alloy ingot to the furnace for keeping the heat for 6h after single-fire forging time exceeds 15min, covering asbestos on the surface of the alloy ingot before each forging, keeping the heat, and controlling the total forging ratio to be 8 to obtain the bar.

Cutting a bar according to 110% of the weight of the wheel disc forging, controlling the height-diameter ratio of the bar to be 2.5, upsetting the bar after heating the bar to form a blank, controlling the heating speed before forging to be 35 ℃/h, the heat preservation temperature to be 1150 ℃, the heat preservation time to be 4h, and the upsetting deformation to be 50%. And heating the disc blank, and then performing die forging forming, wherein the heating temperature rise speed before forging is controlled to be 35 ℃/h, the heat preservation temperature is 1100 ℃, the heat preservation time is 4h, the die forging deformation is 35%, and the die heating temperature is 350 ℃, so that the alloy wheel disc forging can be obtained.

And (3) carrying out heat treatment on the wheel disc forging through machining, wherein the heat treatment comprises solution treatment, intermediate aging treatment and aging treatment, the solution treatment system is heat preservation for 8 hours at 1160 ℃, the intermediate aging treatment system is heat preservation for 10 hours at 1100 ℃, and the aging treatment system is heat preservation for 32 hours at 850 ℃.

In some embodiments of this embodiment, the raw material may be selected from one or more of metallic nickel, metallic chromium or nichrome, metallic titanium, metallic aluminum, metallic molybdenum, ferroboron, metallic cobalt, metallic tungsten, nickel-tungsten alloy, niobium-nickel alloy, ferrovanadium, carbon electrode, and intermediate alloy.

Embodiment 5, preparation method of nickel-based wrought superalloy wheel disc forging capable of being used at 850 DEG C

This example produced a nickel base wrought superalloy disk forging (200 mm diameter) that could be used at 850 c long with the alloy composition shown in table 1, example 5.

The preparation process of the alloy wheel disc forging piece is shown in FIG. 3 and comprises the following steps:

step 1, adopting a duplex process (namely vacuum induction melting and vacuum consumable remelting) for smelting, wherein the diameter of an alloy ingot obtained by vacuum induction melting is 250mm, and the diameter of an alloy ingot obtained by vacuum consumable remelting is 305 mm. The vacuum induction melting comprises the following steps: weighing raw materials according to the element proportion of the alloy, and carrying out vacuum induction melting. The vacuum induction smelting process comprises the steps of evacuation, smelting period, refining, tapping and the like, wherein the vacuum degree in the evacuation period is 10Pa, the temperature in the smelting period is controlled to be 1300 ℃, the temperature in the refining period is controlled to be 1400 ℃, the vacuum degree in the refining period is 1Pa, the tapping temperature is controlled to be 1420 ℃, 20000Pa argon is filled for protection during tapping, and after casting is completed, the ingot is cooled for 0.5h, demoulding and cooling are carried out, so that a primary alloy ingot is obtained. And machining the primary alloy ingot to prepare a consumable remelting electrode, wherein the filling ratio of the consumable remelting electrode to the crystallizer is 0.75, the melting speed is 1.0kg/min, the cooling time after the three times of alloy ingot melting is 0.5h, and then demolding and cooling are carried out to obtain the alloy ingot.

And 2, carrying out high-temperature diffusion homogenization annealing treatment on the alloy ingot, wherein the annealing treatment comprises the processes of heating, heat preservation and cooling, the heating speed is controlled to be 15 ℃/h, the heat preservation temperature is 1150 ℃, the heat preservation time is 24h, and the cooling speed is controlled to be 5 ℃/h. After carrying out homogenizing annealing on the alloy ingot, machining the alloy ingot, heating the alloy ingot to a forging temperature, keeping the temperature, then discharging the alloy ingot out of a furnace for forging, controlling the heating speed to be 15 ℃/h before forging, the heat preservation temperature to be 1050 ℃, the heat preservation time to be 2h, carrying out forging cogging process including upsetting and drawing out, controlling the single-fire forging time to be 1-5 min, returning the alloy ingot to the furnace for heat preservation for 1h after more than 5min, coating asbestos on the surface of the alloy ingot before each forging, keeping the temperature, and controlling the total forging ratio to be 5 to obtain the bar.

And 3, cutting a bar with a proper length according to 140% of the weight of the wheel disc forging, controlling the height-diameter ratio of the bar to be 1.5, upsetting the bar after heating the bar to form a blank, controlling the heating speed to be 20 ℃/h before forging, keeping the temperature to be 1000 ℃, keeping the temperature for 2h, and keeping the upsetting deformation to be 30%, thereby obtaining the disc blank. And heating the disc blank, and then performing die forging forming, wherein the heating temperature rise speed before forging is controlled to be 20 ℃/h, the heat preservation temperature is 950 ℃, the heat preservation time is 2h, the die forging deformation is 30%, and the die heating temperature is 300 ℃, so that the alloy wheel disc forging can be obtained.

And 4, carrying out heat treatment on the wheel disc forging through machining, wherein the heat treatment comprises solid solution treatment, intermediate aging treatment and aging treatment, the solid solution treatment system is heat preservation for 2 hours at 1150 ℃, the intermediate aging treatment system is heat preservation for 2 hours at 1000 ℃, and the aging treatment system is heat preservation for 8 hours at 760 ℃.

In some embodiments of this embodiment, the raw material may be selected from one or more of metallic nickel, metallic chromium or nichrome, metallic titanium, metallic aluminum, metallic molybdenum, ferroboron, metallic cobalt, metallic tungsten, nickel-tungsten alloy, niobium-nickel alloy, ferrovanadium, carbon electrode, and intermediate alloy.

Embodiment 6, preparation method of nickel-based wrought superalloy wheel disc forging with diameter of 550mm capable of being used at 850 DEG C

This example produced a 550mm diameter disk forging of nickel-base wrought superalloy that could be used at 850 c long with the alloy compositions shown in table 1, example 6.

The preparation process of the alloy wheel disc forging piece is shown in FIG. 3 and comprises the following steps:

step 1, smelting adopts a duplex process, and comprises vacuum induction smelting and vacuum consumable remelting, wherein the diameter of an alloy ingot subjected to vacuum induction smelting once is 370mm, and the diameter of an alloy ingot subjected to vacuum consumable remelting is 460 mm. The vacuum induction melting comprises the following steps: weighing raw materials according to the element proportion of the alloy, and carrying out vacuum induction melting. The vacuum induction melting process comprises the steps of evacuation, melting period, refining, tapping and the like, wherein the vacuum degree in the evacuation period is 100Pa, the temperature in the melting period is 1650 ℃, the temperature in the refining period is 1600 ℃, the vacuum degree in the refining period is 20Pa, the tapping temperature is 1590 ℃, argon gas with 50000Pa is filled for protection when tapping, and after casting, the alloy ingot is cooled for 3 hours, demoulded and cooled to obtain a primary alloy ingot. And machining the primary alloy ingot to prepare a consumable remelting electrode, wherein the filling ratio of the consumable remelting electrode to the crystallizer is 0.95, the melting speed is 6.0kg/min, the cooling time after the three times of alloy ingot melting is 3 hours, and then demolding and cooling to obtain the alloy ingot.

And 2, carrying out high-temperature diffusion homogenization annealing on the alloy ingot, wherein the annealing comprises the processes of heating, heat preservation and cooling, the heating speed is controlled to be 60 ℃/h, the heat preservation temperature is 1250 ℃, the heat preservation time is 72h, and the cooling speed is controlled to be 55 ℃/h. After carrying out homogenizing annealing on the alloy ingot, machining the alloy ingot, heating the alloy ingot to a forging temperature, keeping the temperature, then discharging the alloy ingot out of a furnace for forging, controlling the heating speed to be 60 ℃/h before forging, the heat preservation temperature to be 1180 ℃, the heat preservation time to be 8h, carrying out forging cogging process including upsetting and drawing out, controlling the single-fire forging time to be 1-30 min, returning the alloy ingot to the furnace for heat preservation for 6h after exceeding 30min, covering asbestos on the surface of the alloy ingot before each forging, keeping the heat preservation, and controlling the total forging ratio to be 20 to obtain the bar.

And 3, cutting a bar according to 130% of the weight of the wheel disc forging, controlling the height-diameter ratio of the bar to be 3.0, heating the bar, upsetting the bar to form a blank, controlling the heating rate to be 50 ℃/h before forging, keeping the temperature to be 1140 ℃, keeping the temperature for 8h, and keeping the upsetting deformation to be 70%. And heating the disc blank, and then performing die forging forming, wherein the heating temperature rise speed before forging is controlled to be 50 ℃/h, the heat preservation temperature is 1120 ℃, the heat preservation time is 8h, the die forging deformation is 70%, and the die heating temperature is 1050 ℃, so that the alloy wheel disc forging can be obtained.

And 4, carrying out heat treatment on the wheel disc forging through machining, wherein the heat treatment comprises solution treatment, intermediate aging treatment and aging treatment, the solution treatment system is used for keeping the temperature at 1220 ℃ for 10 hours, the intermediate aging treatment system is used for keeping the temperature at 1150 ℃ for 10 hours, and the aging treatment system is used for keeping the temperature at 920 ℃ for 32 hours.

In some embodiments of this embodiment, the raw material may be selected from one or more of metallic nickel, metallic chromium or nichrome, metallic titanium, metallic aluminum, metallic molybdenum, ferroboron, metallic cobalt, metallic tungsten, nickel-tungsten alloy, niobium-nickel alloy, ferrovanadium, carbon electrode, and intermediate alloy.

Example 7 Nickel base wrought superalloy wheel disc forging with 900mm diameter capable of being used at 850 DEG C

This example produced a nickel base wrought superalloy diameter disk forging that could be used at 850 c long with the alloy compositions shown in table 1, example 7.

The preparation process of the alloy wheel disc forging piece is shown in FIG. 3 and comprises the following steps:

step 1, smelting adopts a triple process, namely vacuum induction smelting, electroslag remelting and vacuum consumable remelting, wherein the diameter of an alloy ingot subjected to vacuum induction smelting is 355mm, the diameter of the electroslag remelting alloy ingot is 423mm, and the diameter of the vacuum consumable remelting alloy ingot is 508 mm. The vacuum induction melting comprises the following steps: weighing raw materials according to the element proportion of the alloy, and carrying out vacuum induction melting. The vacuum induction smelting process comprises the steps of evacuation, smelting period, refining, tapping and the like, wherein the vacuum degree in the evacuation period is 20Pa, the temperature in the smelting period is controlled to be 1550 ℃, the temperature in the refining period is controlled to be 1500 ℃, the vacuum degree in the refining period is 4Pa, the tapping temperature is controlled to be 1480 ℃, 20000Pa argon is filled for protection during tapping, and the alloy ingot is demoulded and cooled after being cooled for 2.5 hours after casting is completed to obtain a primary alloy ingot. Machining the primary alloy ingot to prepare an electroslag remelting electrode, wherein the filling ratio of the electroslag remelting electrode to a crystallizer is 0.9, and the electroslag ratio is CaF 2: CaO: MgO: al2O 3: TiO2 ═ 65%: 10%: 0.5%: 10%: 0.5 percent, the steady state melting speed is 5.0kg/min, the cooling time after the secondary alloy ingot is melted is 0.5h, and then demoulding and cooling are carried out. And machining the secondary alloy ingot to prepare an electroslag remelting electrode, wherein the filling ratio of the electrode to a crystallizer is 0.75, the melting speed is 1.0kg/min, the cooling time after the third alloy ingot is melted is 1h, and then demolding and cooling are carried out to obtain the alloy ingot.

And 2, carrying out high-temperature diffusion homogenization annealing on the alloy ingot, wherein the annealing comprises the processes of heating, heat preservation and cooling, the heating speed is controlled to be 35 ℃/h, the heat preservation temperature is 1190 ℃, the heat preservation time is 50h, and the cooling speed is controlled to be 25 ℃/h. After carrying out homogenizing annealing on the alloy ingot, machining the alloy ingot, heating the alloy ingot to a forging temperature, keeping the temperature, then discharging the alloy ingot out of a furnace for forging, controlling the heating speed to be 35 ℃/h before forging, the heat preservation temperature to be 1170 ℃, the heat preservation time to be 6h, carrying out forging cogging process including upsetting and drawing out, controlling the single-fire forging time to be 1-15 min, returning the alloy ingot to the furnace for heat preservation for 2h after exceeding 15min, coating asbestos on the surface of the alloy ingot before each forging, keeping the temperature, and controlling the total forging ratio to be 15 to obtain the bar.

And 3, cutting a bar according to 140% of the weight of the wheel disc forging, controlling the height-diameter ratio of the bar to be 2.5, upsetting the bar after heating the bar to form a blank, controlling the heating speed to be 35 ℃/h before forging, controlling the heat preservation temperature to be 1110 ℃, controlling the heat preservation time to be 4h, and controlling the upsetting deformation to be 40% to obtain the disc blank. And heating the disc blank, and then performing die forging forming, wherein the heating temperature rise speed before forging is controlled to be 35 ℃/h, the heat preservation temperature is 1120 ℃, the heat preservation time is 4h, the die forging deformation is 40%, and the die heating temperature is 650 ℃, so that the alloy wheel disc forging can be obtained.

And 4, carrying out heat treatment on the wheel disc forging through machining, wherein the heat treatment comprises solid solution treatment, intermediate aging treatment and aging treatment, the solid solution treatment system is 1180 ℃ and is kept warm for 5 hours, the intermediate aging treatment system is 1050 ℃ and is kept warm for 8 hours, and the aging treatment system is 910 ℃ and is kept warm for 20 hours.

In some embodiments of this embodiment, the raw material may be selected from one or more of metallic nickel, metallic chromium or nichrome, metallic titanium, metallic aluminum, metallic molybdenum, ferroboron, metallic cobalt, metallic tungsten, nickel-tungsten alloy, niobium-nickel alloy, ferrovanadium, carbon electrode, and intermediate alloy.

Example 8 Nickel base wrought superalloy wheel disc forging with 900mm diameter capable of being used at 850 DEG C

A900 mm diameter disk forging of nickel-based wrought superalloy capable of being used at 850 ℃ length was prepared in this example, and the alloy composition is shown in Table 1, example 8.

The preparation process of the alloy wheel disc forging piece is shown in FIG. 3 and comprises the following steps:

step 1, smelting adopts a triple process, namely vacuum induction smelting, electroslag remelting and vacuum consumable remelting, wherein the diameter of an alloy ingot subjected to vacuum induction smelting is 355mm, the diameter of the electroslag remelting alloy ingot is 423mm, and the diameter of the vacuum consumable remelting alloy ingot is 508 mm. The vacuum induction melting comprises the following steps: weighing raw materials according to the element proportion of the alloy, and carrying out vacuum induction melting. The vacuum induction melting process comprises the steps of evacuation, melting period, refining, tapping and the like, wherein the vacuum degree in the evacuation period is 30Pa, the temperature in the melting period is controlled to be 1580 ℃, the temperature in the refining period is controlled to be 1550 ℃, the vacuum degree in the refining period is 5Pa, the tapping temperature is controlled to be 1480 ℃, 25000Pa argon is filled for protection during tapping, and after casting is completed, the alloy ingot is cooled for 3 hours, demoulded and cooled to obtain a primary alloy ingot. Machining the primary alloy ingot to prepare an electroslag remelting electrode, wherein the filling ratio of the electroslag remelting electrode to a crystallizer is 0.9, and the electroslag ratio is CaF 2: CaO: MgO: al2O 3: 75% of TiO 2: 20%: 5%: 20%: 5 percent, the steady state melting speed is 4.0kg/min, the cooling time after the secondary alloy ingot is melted is 6 hours, and then demoulding and cooling are carried out. And machining the secondary alloy ingot to prepare an electroslag remelting electrode, wherein the filling ratio of the electroslag remelting electrode to a crystallizer is 0.87, the melting speed is 3.8kg/min, the cooling time after the third alloy ingot is melted is 3 hours, and then demolding and cooling are carried out to obtain the alloy ingot.

And 2, carrying out high-temperature diffusion homogenization annealing on the alloy ingot, wherein the high-temperature diffusion homogenization annealing comprises the processes of heating, heat preservation and cooling, the heating speed is controlled to be 20 ℃/h, the heat preservation temperature is 1180 ℃, the heat preservation time is 70h, and the cooling speed is controlled to be 5 ℃/h. After carrying out homogenizing annealing on the alloy ingot, machining the alloy ingot, heating the alloy ingot to a forging temperature, keeping the temperature, then discharging the alloy ingot out of a furnace for forging, controlling the heating speed to be 15 ℃/h before forging, the heat preservation temperature to be 1180 ℃, the heat preservation time to be 6h, carrying out forging cogging process including upsetting and drawing out, controlling the single-fire forging time to be 1-10 min, returning the alloy ingot to the furnace for heat preservation for 2h after 10min, covering asbestos on the surface of the alloy ingot before forging each time for heat preservation, and controlling the total forging ratio to be 10 to obtain the bar.

And 3, cutting a bar according to 125% of the weight of the wheel disc forging, controlling the height-diameter ratio of the bar to be 2, upsetting the bar after heating the bar to form a blank, controlling the heating speed before forging to be 35 ℃/h, the heat preservation temperature to be 1150 ℃, the heat preservation time to be 6h, and upsetting deformation to be 50%. And heating the disc blank, and then performing die forging forming, wherein the heating temperature rise speed before forging is controlled to be 40 ℃/h, the heat preservation temperature is 1100 ℃, the heat preservation time is 6h, the die forging deformation is 35%, and the die heating temperature is 350 ℃, so that the alloy wheel disc forging can be obtained.

And 4, carrying out heat treatment on the wheel disc forging through machining, wherein the heat treatment comprises solution treatment, intermediate aging treatment and aging treatment, the solution treatment system is heat preservation for 8 hours at 1160 ℃, the intermediate aging treatment system is heat preservation for 7 hours at 1100 ℃, and the aging treatment system is heat preservation for 32 hours at 850 ℃.

In some embodiments of this embodiment, the raw material may be selected from one or more of metallic nickel, metallic chromium or nichrome, metallic titanium, metallic aluminum, metallic molybdenum, ferroboron, metallic cobalt, metallic tungsten, nickel-tungsten alloy, niobium-nickel alloy, ferrovanadium, carbon electrode, and intermediate alloy.

Example 9 Nickel base wrought superalloy wheel disc forging with 900mm diameter capable of being used at 850 DEG C

This example produced a 900mm diameter disk forging of nickel-base wrought superalloy that could be used at 850 c long with the alloy composition shown in table 1, example 9.

The preparation process of the alloy wheel disc forging piece is shown in FIG. 3 and comprises the following steps:

step 1, smelting adopts a triple process, namely vacuum induction smelting, electroslag remelting and vacuum consumable remelting, wherein the diameter of an alloy ingot subjected to vacuum induction smelting is 355mm, the diameter of the electroslag remelting alloy ingot is 423mm, and the diameter of the vacuum consumable remelting alloy ingot is 508 mm. The vacuum induction melting comprises the following steps: weighing raw materials according to the element proportion of the alloy, and carrying out vacuum induction melting. The vacuum induction melting process comprises the steps of evacuation, melting period, refining, tapping and the like, wherein the vacuum degree in the evacuation period is 20Pa, the temperature in the melting period is controlled to be 1600 ℃, the temperature in the refining period is controlled to be 1500 ℃, the vacuum degree in the refining period is 4Pa, the tapping temperature is controlled to be 1480 ℃, 20000Pa argon is filled for protection during tapping, and after casting is completed, cooling is carried out for 3 hours, demoulding and cooling are carried out, so that a primary alloy ingot is obtained. Machining the primary alloy ingot to prepare an electroslag remelting electrode, wherein the filling ratio of the electrode to a crystallizer is 0.8, and the electroslag ratio is CaF 2: CaO: MgO: al2O 3: 70% of TiO 2: 15%: 1%: 15%: 4 percent, the steady-state melting speed is 6.0kg/min, the cooling time after the secondary alloy ingot is melted is 2 hours, and then the ingot is demoulded and cooled. And machining the secondary alloy ingot to prepare an electroslag remelting electrode, wherein the filling ratio of the electroslag remelting electrode to a crystallizer is 0.95, the melting speed is 5kg/min, the cooling time after the third alloy ingot is melted is 3 hours, and then demolding and cooling are carried out to obtain the alloy ingot.

And 2, carrying out high-temperature diffusion homogenization annealing on the alloy ingot, wherein the annealing comprises the processes of heating, heat preservation and cooling, the heating speed is controlled to be 35 ℃/h, the heat preservation temperature is 1190 ℃, the heat preservation time is 50h, and the cooling speed is controlled to be 25 ℃/h. After carrying out homogenizing annealing on the alloy ingot, machining the alloy ingot, heating the alloy ingot to a forging temperature, keeping the temperature, then discharging the alloy ingot out of a furnace for forging, controlling the heating speed to be 35 ℃/h before forging, the heat preservation temperature to be 1170 ℃, the heat preservation time to be 7h, carrying out forging cogging process including upsetting and drawing out, controlling the single-fire forging time to be 1-12 min, returning the furnace for heat preservation for 3h after exceeding 12min, coating asbestos on the surface of the alloy ingot before each forging, keeping the heat preservation, and controlling the total forging ratio to be 17 to obtain the bar.

And 3, cutting a bar according to 115% of the weight of the wheel disc forging, controlling the height-diameter ratio of the bar to be 2, heating the bar, upsetting and making a blank, controlling the heating speed before forging to be 40 ℃/h, the heat preservation temperature to be 1120 ℃, the heat preservation time to be 7h, and the upsetting deformation to be 60%. And heating the disc blank, and then performing die forging forming, wherein the heating temperature rise speed before forging is controlled to be 45 ℃/h, the heat preservation temperature is 1130 ℃, the heat preservation time is 3h, the die forging deformation is 60%, and the die heating temperature is 650 ℃, so that the alloy wheel disc forging can be obtained.

And 4, carrying out heat treatment on the wheel disc forging through machining, wherein the heat treatment comprises solution treatment, intermediate aging treatment and aging treatment, the solution treatment system is used for keeping the temperature of 1200 ℃ for 3h, the intermediate aging treatment system is used for keeping the temperature of 1050 ℃ for 4h, and the aging treatment system is used for keeping the temperature of 900 ℃ for 25 h.

In some embodiments of this example, a 900mm diameter nickel-base wrought superalloy disk forging that can be used at 850 ℃ is prepared that also includes impurity elements where P is 0.015%, Mn is 0.5%, Si is 0.5%, S is 0.015%, O is 0.005%, N is 0.01%, Ag is 0.005%, Ca is 0.01%, Sn is 0.01%, Pb is 0.001%, Cu is 0.5%, Ta is 0.5%, and V is 0.5%.

In some embodiments of this embodiment, a 900mm diameter ni-based wrought superalloy wheel forging that can be used at 850 ℃ is prepared that also includes impurity elements where P is 0.001%, Mn is 0.1%, Si is 0.2%, S is 0.003%, O is 0.001%, N is 0.0021%, Ag is 0.003%, Ca is 0.0011%, Sn is 0.001%, Pb is 0, Cu is 0, Ta is 0, and V is 0.

In some embodiments of this embodiment, the raw material may be selected from one or more of metallic nickel, metallic chromium or nichrome, metallic titanium, metallic aluminum, metallic molybdenum, ferroboron, metallic cobalt, metallic tungsten, nickel-tungsten alloy, niobium-nickel alloy, ferrovanadium, carbon electrode, and intermediate alloy.

Example 10 Nickel base wrought superalloy wheel disc forging with a diameter of 600mm that can be used at 850 deg.C

This example produced a 600mm diameter disc forging of nickel-base wrought superalloy that could be used at 850 c long with the alloy composition shown in table 1, example 10.

The preparation process of the alloy wheel disc forging piece is shown in FIG. 3 and comprises the following steps:

step 1, smelting adopts a triple process, namely vacuum induction smelting, electroslag remelting and vacuum consumable remelting, wherein the diameter of an alloy ingot subjected to vacuum induction smelting is 355mm, the diameter of the electroslag remelting alloy ingot is 423mm, and the diameter of the vacuum consumable remelting alloy ingot is 508 mm. The vacuum induction melting comprises the following steps: weighing raw materials according to the element proportion of the alloy, and carrying out vacuum induction melting. The vacuum induction melting process comprises the steps of evacuation, melting period, refining, tapping and the like, wherein the vacuum degree in the evacuation period is 30Pa, the temperature in the melting period is controlled to be 1580 ℃, the temperature in the refining period is controlled to be 1550 ℃, the vacuum degree in the refining period is 5Pa, the tapping temperature is controlled to be 1400 ℃, 30000Pa argon is filled for protection during tapping, and the alloy ingot is obtained after being cooled for 3 hours after casting. Machining the primary alloy ingot to prepare an electroslag remelting electrode, wherein the filling ratio of the electrode to a crystallizer is 0.75, and the electroslag ratio is CaF 2: CaO: MgO: al2O 3: TiO 2-68%: 14%: 2%: 14%: 2 percent, the steady-state melting speed is 5.0kg/min, the cooling time after the secondary alloy ingot is melted is 6 hours, and then demoulding and cooling are carried out. And machining the secondary alloy ingot to prepare an electroslag remelting electrode, wherein the filling ratio of the electroslag remelting electrode to a crystallizer is 0.87, the melting speed is 3.8kg/min, the cooling time after the third alloy ingot is melted is 2 hours, and then demolding and cooling are carried out to obtain the alloy ingot.

And 2, carrying out high-temperature diffusion homogenization annealing on the alloy ingot, wherein the heating process, the heat preservation process and the cooling process are included, the heating speed is controlled to be 15 ℃/h, the heat preservation temperature is 1170 ℃, the heat preservation time is 70h, and the cooling speed is controlled to be 10 ℃/h. After carrying out homogenizing annealing on the alloy ingot, machining the alloy ingot, heating the alloy ingot to a forging temperature, keeping the temperature, then discharging the alloy ingot out of a furnace for forging, controlling the heating speed before forging to be 30 ℃/h, the heat preservation temperature to be 1090 ℃ and the heat preservation time to be 5h, wherein the forging and cogging process comprises upsetting and drawing out, the single-fire forging time is controlled to be 1-12 min, the alloy ingot is returned to the furnace for heat preservation for 3h after the temperature exceeds 12min, the surface of the alloy ingot is coated with asbestos before each forging for heat preservation, and the total forging ratio is controlled to be 8, so that the bar is.

And 3, cutting a bar according to 145% of the weight of the wheel disc forging, controlling the height-diameter ratio of the bar to be 2.5, upsetting the bar after heating the bar to form a blank, controlling the heating speed to be 35 ℃/h before forging, controlling the heat preservation temperature to be 1150 ℃, controlling the heat preservation time to be 4h, and controlling the upsetting deformation to be 50%. And heating the disc blank, and then performing die forging forming, wherein the heating temperature rise speed before forging is controlled to be 35 ℃/h, the heat preservation temperature is 1100 ℃, the heat preservation time is 4h, the die forging deformation is 35%, and the die heating temperature is 350 ℃, so that the alloy wheel disc forging can be obtained.

And 4, carrying out heat treatment on the wheel disc forging through machining, wherein the heat treatment comprises solution treatment, intermediate aging treatment and aging treatment, the solution treatment system is heat preservation for 8 hours at 1160 ℃, the intermediate aging treatment system is heat preservation for 10 hours at 1100 ℃, and the aging treatment system is heat preservation for 30 hours at 850 ℃.

In this example, a 600mm diameter disc forging of a nickel-base wrought superalloy that can be used at 850 ℃ length was prepared that also included impurity elements, where P is 0.010%, Mn is 0.15%, Si is 0.15%, S is 0.005%, O is 0.002%, N is 0.005%, Ag is 0.0005%, Ca is 0.005%, Sn is 0.005%, Pb is 0.0005%, Cu is 0.1%, Ta is 0.1%, and V is 0.1%.

In this example, a 600mm diameter disc forging of a nickel-base wrought superalloy that can be used at 850 ℃ was prepared that also included impurity elements, where P is 0.010%, Mn is 0.102%, Si is 0.10%, S is 0.001%, O is 0.001%, N is 0.00015%, Ag is 0.0001%, Ca is 0.0015%, Sn is 0, Pb is 0.0, Cu is 0.01%, Ta is 0.01%, and V is 0.02%.

In some embodiments of this embodiment, the raw material may be selected from one or more of metallic nickel, metallic chromium or nichrome, metallic titanium, metallic aluminum, metallic molybdenum, ferroboron, metallic cobalt, metallic tungsten, nickel-tungsten alloy, niobium-nickel alloy, ferrovanadium, carbon electrode, and intermediate alloy.

Example 11 Nickel base wrought superalloy wheel disc forging with a diameter of 600mm that can be used at 850 deg.C

This example produced a 600mm diameter disc forging of nickel-base wrought superalloy that could be used at 850 c long with the alloy composition shown in table 1, example 10.

The difference from example 10 is that: in step 1 of the preparation process of the alloy wheel disc forging, if the primary alloy ingot is an alloy ingot with the diameter smaller than 500mm, the treatment process of the primary alloy ingot is changed into the following steps: and directly carrying out vacuum consumable remelting on the primary alloy ingot to obtain the alloy ingot.

The preparation process of the alloy wheel disc forging comprises the following steps:

the smelting adopts a duplex process, vacuum induction smelting and vacuum consumable remelting, the diameter of an alloy ingot subjected to vacuum induction smelting once is 355mm, and the diameter of an alloy ingot subjected to vacuum consumable remelting is 430 mm. The vacuum induction melting comprises the following steps: weighing raw materials according to the element proportion of the alloy, wherein the metal raw materials comprise: metallic nickel, metallic chromium or nichrome, metallic titanium, metallic aluminum, metallic molybdenum, ferroboron, metallic cobalt, metallic tungsten, nickel-tungsten alloy, niobium-nickel alloy, ferrovanadium, carbon electrode, intermediate alloy, and the like. The vacuum induction smelting process comprises the steps of evacuation, material melting and smelting period, refining, tapping and the like, wherein the vacuum degree in the evacuation period is 70Pa, the temperature in the melting period is controlled to be 1580 ℃, the temperature in the refining period is controlled to be 1550 ℃, the vacuum degree in the refining period is 5Pa, the tapping temperature is controlled to be 1500 ℃, argon gas with 15000Pa is filled for protection during tapping, and the alloy ingot is demoulded and cooled after being cooled for 2 hours after casting is completed to obtain a primary alloy ingot. And machining the primary alloy ingot to prepare a consumable remelting electrode, wherein the filling ratio of the consumable remelting electrode to the crystallizer is 0.8, the melting speed is 2.5kg/min, the cooling time after the three times of alloy ingot melting is 2 hours, and then demolding and cooling to obtain the alloy ingot.

The high-temperature diffusion homogenization annealing of the alloy ingot comprises the processes of temperature rise, heat preservation and cooling, wherein the temperature rise speed is controlled to be 45 ℃/h, the heat preservation temperature is 1210 ℃, the heat preservation time is 40h, and the cooling speed is controlled to be 25 ℃/h. After carrying out homogenizing annealing on the alloy ingot, machining the alloy ingot, heating the alloy ingot to a forging temperature, preserving heat, discharging the alloy ingot from a furnace, forging the alloy ingot, controlling the heating speed before forging to be 45 ℃/h, the heat preservation temperature to be 1160 ℃, the heat preservation time to be 4h, carrying out forging cogging process including upsetting and drawing out, returning the alloy ingot to the furnace after the single-fire forging time exceeds 15min, preserving heat for 2h, coating asbestos on the surface of the alloy ingot before forging each time, preserving heat, and controlling the total forging ratio to be 10 to obtain the bar.

Cutting a bar material with the weight of 120 percent according to the weight of the wheel disc forging piece, controlling the height-diameter ratio of the bar material to be 2.5, upsetting the heated bar material to form a blank, controlling the heating speed before forging to be 35 ℃/h, the heat preservation temperature to be 1120 ℃, the heat preservation time to be 4h, and the upsetting deformation to be 40 percent. And heating the disc blank, and then performing die forging forming, wherein the heating temperature rise speed before forging is controlled to be 35 ℃/h, the heat preservation temperature is 1120 ℃, the heat preservation time is 4h, the die forging deformation is 40%, and the die heating temperature is 650 ℃, so that the wheel disc forging is obtained.

The wheel disc forging is subjected to heat treatment through machining, wherein the heat treatment comprises solid solution treatment, intermediate aging treatment and aging treatment, the solid solution treatment system is 1180 ℃ and is kept warm for 5 hours, the intermediate aging treatment system is 1050 ℃ and is kept warm for 4 hours, and the aging treatment system is 910 ℃ and is kept warm for 12 hours.

In some embodiments of this embodiment, a 600mm diameter disc forging of a nickel-base wrought superalloy that can be used at 850 ℃ length is prepared that also includes impurity elements where P is 0.015%, Mn is 0.5%, Si is 0.5%, S is 0.015%, O is 0.005%, N is 0.01%, Ag is 0.005%, Ca is 0.01%, Sn is 0.01%, Pb is 0.001%, Cu is 0.5%, Ta is 0.5%, and V is 0.5%.

In some embodiments of this embodiment, a 600mm diameter ni-based wrought superalloy disk forging that can be used at 850 ℃ is prepared that also includes impurity elements where P is 0.001%, Mn is 0.1%, Si is 0.2%, S is 0.003%, O is 0.001%, N is 0.0021%, Ag is 0.003%, Ca is 0.0011%, Sn is 0.001%, Pb is 0, Cu is 0, Ta is 0, and V is 0.

Example 12 Nickel base wrought superalloy wheel disc forging with a diameter of 600mm that can be used at 850 deg.C

This example produced a 600mm diameter disc forging of nickel-base wrought superalloy that could be used at 850 c long with the alloy composition shown in table 1, example 5.

The difference from example 5 is that: in step 1 of the preparation process of the alloy wheel disc forging, if the primary alloy ingot is an alloy ingot with the diameter smaller than 500mm, the treatment process of the primary alloy ingot is changed into the following steps: and directly carrying out vacuum consumable remelting on the primary alloy ingot to obtain the alloy ingot.

The other processes were the same as in example 5.

In some embodiments of this embodiment, a 600mm diameter disc forging of a nickel-base wrought superalloy that can be used at 850 ℃ length is prepared that also includes impurity elements where P is 0.015%, Mn is 0.5%, Si is 0.5%, S is 0.015%, O is 0.005%, N is 0.01%, Ag is 0.005%, Ca is 0.01%, Sn is 0.01%, Pb is 0.001%, Cu is 0.5%, Ta is 0.5%, and V is 0.5%.

In some embodiments of this embodiment, a 600mm diameter ni-based wrought superalloy disk forging that can be used at 850 ℃ is prepared that also includes impurity elements where P is 0.001%, Mn is 0.1%, Si is 0.2%, S is 0.003%, O is 0.001%, N is 0.0021%, Ag is 0.003%, Ca is 0.0011%, Sn is 0.001%, Pb is 0, Cu is 0, Ta is 0, and V is 0.

Example 13 Nickel base wrought superalloy wheel disc forging with 600mm diameter usable at 850 deg.C

This example produced a 600mm diameter disc forging of nickel-base wrought superalloy that could be used at 850 c long with the alloy compositions shown in table 1, example 6.

The difference from example 6 is that: in step 1 of the preparation process of the alloy wheel disc forging, if the primary alloy ingot is an alloy ingot with the diameter smaller than 500mm, the treatment process of the primary alloy ingot is changed into the following steps: and directly carrying out vacuum consumable remelting on the primary alloy ingot to obtain the alloy ingot.

The other processes were the same as in example 6.

In some embodiments of this embodiment, a 600mm diameter disc forging of a nickel-base wrought superalloy that can be used at 850 ℃ length is prepared that also includes impurity elements where P is 0.015%, Mn is 0.5%, Si is 0.5%, S is 0.015%, O is 0.005%, N is 0.01%, Ag is 0.005%, Ca is 0.01%, Sn is 0.01%, Pb is 0.001%, Cu is 0.5%, Ta is 0.5%, and V is 0.5%.

In some embodiments of this embodiment, a 600mm diameter ni-based wrought superalloy disk forging that can be used at 850 ℃ is prepared that also includes impurity elements where P is 0.001%, Mn is 0.1%, Si is 0.2%, S is 0.003%, O is 0.001%, N is 0.0021%, Ag is 0.003%, Ca is 0.0011%, Sn is 0.001%, Pb is 0, Cu is 0, Ta is 0, and V is 0.

Example 14 Nickel base wrought superalloy wheel disc forging with 600mm diameter usable at 850 deg.C

This example produced a 600mm diameter disc forging of nickel-base wrought superalloy that could be used at 850 c long with the alloy compositions shown in table 1, example 7.

The difference from example 7 is that: in step 1 of the preparation process of the alloy wheel disc forging, if the primary alloy ingot is an alloy ingot with the diameter smaller than 500mm, the treatment process of the primary alloy ingot is changed into the following steps: and directly carrying out vacuum consumable remelting on the primary alloy ingot to obtain the alloy ingot.

The other processes were performed in the same manner as in example 7.

In some embodiments of this embodiment, a 600mm diameter disc forging of a nickel-base wrought superalloy that can be used at 850 ℃ length is prepared that also includes impurity elements where P is 0.015%, Mn is 0.5%, Si is 0.5%, S is 0.015%, O is 0.005%, N is 0.01%, Ag is 0.005%, Ca is 0.01%, Sn is 0.01%, Pb is 0.001%, Cu is 0.5%, Ta is 0.5%, and V is 0.5%.

In some embodiments of this embodiment, a 600mm diameter ni-based wrought superalloy disk forging that can be used at 850 ℃ is prepared that also includes impurity elements where P is 0.001%, Mn is 0.1%, Si is 0.2%, S is 0.003%, O is 0.001%, N is 0.0021%, Ag is 0.003%, Ca is 0.0011%, Sn is 0.001%, Pb is 0, Cu is 0, Ta is 0, and V is 0.

Example 15 Nickel base wrought superalloy wheel disc forging with 600mm diameter usable at 850 deg.C

This example produced a 600mm diameter disc forging of nickel-base wrought superalloy that could be used at 850 c long with the alloy composition shown in table 1, example 8.

The difference from example 8 is that: in step 1 of the preparation process of the alloy wheel disc forging, if the primary alloy ingot is an alloy ingot with the diameter smaller than 500mm, the treatment process of the primary alloy ingot is changed into the following steps: and directly carrying out vacuum consumable remelting on the primary alloy ingot to obtain the alloy ingot.

The other processes were the same as in example 8.

In some embodiments of this embodiment, a 600mm diameter disc forging of a nickel-base wrought superalloy that can be used at 850 ℃ length is prepared that also includes impurity elements where P is 0.015%, Mn is 0.5%, Si is 0.5%, S is 0.015%, O is 0.005%, N is 0.01%, Ag is 0.005%, Ca is 0.01%, Sn is 0.01%, Pb is 0.001%, Cu is 0.5%, Ta is 0.5%, and V is 0.5%.

In some embodiments of this embodiment, a 600mm diameter ni-based wrought superalloy disk forging that can be used at 850 ℃ is prepared that also includes impurity elements where P is 0.001%, Mn is 0.1%, Si is 0.2%, S is 0.003%, O is 0.001%, N is 0.0021%, Ag is 0.003%, Ca is 0.0011%, Sn is 0.001%, Pb is 0, Cu is 0, Ta is 0, and V is 0.

Example 16 Nickel base wrought superalloy wheel disc forging with a diameter of 600mm that can be used at 850 deg.C

This example produced a 600mm diameter disc forging of nickel-base wrought superalloy that could be used at 850 c long with the alloy composition shown in table 1, example 9.

The difference from example 9 is that: in step 1 of the preparation process of the alloy wheel disc forging, if the primary alloy ingot is an alloy ingot with the diameter smaller than 500mm, the treatment process of the primary alloy ingot is changed into the following steps: and directly carrying out vacuum consumable remelting on the primary alloy ingot to obtain the alloy ingot.

The other processes were the same as in example 9.

In some embodiments of this embodiment, a 600mm diameter disc forging of a nickel-base wrought superalloy that can be used at 850 ℃ length is prepared that also includes impurity elements where P is 0.015%, Mn is 0.5%, Si is 0.5%, S is 0.015%, O is 0.005%, N is 0.01%, Ag is 0.005%, Ca is 0.01%, Sn is 0.01%, Pb is 0.001%, Cu is 0.5%, Ta is 0.5%, and V is 0.5%.

In some embodiments of this embodiment, a 600mm diameter ni-based wrought superalloy disk forging that can be used at 850 ℃ is prepared that also includes impurity elements where P is 0.001%, Mn is 0.1%, Si is 0.2%, S is 0.003%, O is 0.001%, N is 0.0021%, Ag is 0.003%, Ca is 0.0011%, Sn is 0.001%, Pb is 0, Cu is 0, Ta is 0, and V is 0.

Example 17 Performance measurement experiment

The nickel-based wrought superalloy used at 850 ℃ or higher, obtained from any of examples 1-16, was found by the inventors, the nickel-based wrought superalloy takes Ni-Co-Cr elements as matrix components to form a stable gamma austenite matrix, taking a gamma ' phase precipitated in a coherent way as a main strengthening phase, adding high-content gamma ' phase to form elements Al, Ti and Nb, wherein the mass percentage of the gamma ' phase can reach 55-65%, adding high-content W, Mo element to carry out solid solution strengthening, meanwhile, proper amounts of B, Zr, Ce and Mg are added to carry out micro-alloying to improve the performance of grain boundaries, MC type, M6C type and M23C6 type carbides are precipitated in the alloy, second phases such as MB2 type and M3B2 type borides are compounded and strengthened, the technical effect of the part of the nickel-based wrought superalloy obtained in the embodiment 1 is as shown in figure 1, and the technical effect of the part of the nickel-based wrought superalloy obtained in other embodiments is similar.

Refer to GB/T228.2 metal material tensile test 2 part high temperature test method for carrying out the detection. The results show that the tensile strength and yield strength of the alloy obtained from any of examples 1 to 16 can reach 850MPa or more and 700MPa or more at 850 ℃. The test is carried out by referring to a GB/T2039 metal tensile creep and endurance test method, and the result shows that the endurance life of the alloy obtained from any one of the embodiments 1 to 16 under 350MPa is more than 100 h.

The nickel-based wrought superalloy obtained in any one of the embodiments 1 to 16 is aged for a long time for more than 5000 hours at room temperature within a temperature range of 650 to 900 ℃, the content of precipitated harmful phase mu phase is not more than 1%, the technical effect of the nickel-based wrought superalloy obtained in the embodiment 1 is shown in fig. 2, and the technical effect of the nickel-based wrought superalloy obtained in other embodiments is similar to that of the nickel-based wrought superalloy obtained in other embodiments, so that the nickel-based wrought superalloy obtained in the invention can be used as a wheel disc material used at 850 ℃.

The Ni-based wrought superalloy obtained in any of examples 1-16, having a chemical composition of (Ni, Co) as a primary strengthening phase γ' phase₃(Al, Ti and Nb), the gamma 'phase is more stable in the hot working process after containing a certain amount of Nb element, the precipitation speed of the gamma' phase is slow in the forging and cogging process under the free forging condition, the problem of steel ingot thermoplasticity degradation caused by strain aging precipitation is avoided, the alloy has enough thermoplasticity, and the free forging and cogging can be realized.

The nickel-based wrought superalloy obtained in any one of embodiments 1 to 16 can be used for preparing a wheel disc forging with the diameter of 100-1200 mm by adopting the smelting, forging and cogging, forging and heat treatment processes provided by the invention, can realize industrial production by adopting conventional equipment, and has good casting-forging process performance.

In summary, the nickel-based wrought superalloy wheel disc material which can be used at 850 ℃ and above and obtained in any of embodiments 1 to 16 of the present invention can be used for preparing a wheel disc forging with a diameter of 100-1200 mm through reasonable component design and a preparation method, has excellent tensile and durability properties at 850 ℃, has good long-term structure stability, and has an industrial mass production capability.

Comparative example 1, nickel-based wrought superalloy wheel disc forging piece with diameter of 900mm and capable of being used at 850 DEG C

The nickel-based wrought superalloy wheel disc forging piece with the diameter of 900mm, which can be used at the temperature of 850 ℃, is prepared according to the comparative example, the alloy components are shown in a table 1, namely the comparative example 1, and the content of trace elements such as B, Zr, Ce, Mg and the like is lower than that of the embodiment 3.

The preparation process of the alloy wheel disc forging comprises the following steps:

the smelting adopts a duplex process, vacuum induction smelting and vacuum consumable remelting, the diameter of an alloy ingot subjected to vacuum induction smelting once is 355mm, the diameter of an electroslag remelting alloy ingot is 440mm, and the diameter of the vacuum consumable remelting alloy ingot is 508 mm. The vacuum induction melting comprises the following steps: weighing raw materials according to the element proportion of the alloy, wherein the metal raw materials comprise: metallic nickel, metallic chromium or nickel-chromium alloy, metallic titanium, metallic aluminum, metallic molybdenum, ferroboron, metallic cobalt, metallic tungsten, nickel-tungsten alloy, niobium-nickel alloy, ferrovanadium, carbon electrode, return material, and the like. The vacuum induction smelting process comprises the steps of evacuation, smelting period, refining, tapping and the like, wherein the vacuum degree in the evacuation period is 20Pa, the temperature in the smelting period is 1550 ℃, the temperature in the refining period is 1500 ℃, the vacuum degree in the refining period is 4Pa, the tapping temperature is 1480 ℃, 20000Pa argon is filled for protection during tapping, and after casting is completed, the ingot is cooled for 3 hours, demoulded and cooled to obtain a primary alloy ingot. And machining the primary alloy ingot to prepare a consumable remelting electrode, wherein the filling ratio of the electrode to a crystallizer is 0.85, the melting speed is 3.5kg/min, the cooling time after the three times of alloy ingot melting is 2 hours, and then demolding and cooling to obtain the alloy ingot.

The high-temperature diffusion homogenization annealing of the alloy ingot comprises the processes of heating, heat preservation and cooling, wherein the heating speed is controlled to be 35 ℃/h, the heat preservation temperature is 1190 ℃, the heat preservation time is 50h, and the cooling speed is controlled to be 25 ℃/h. After carrying out homogenizing annealing on the alloy ingot, machining the alloy ingot, heating the alloy ingot to a forging temperature, keeping the temperature, then discharging the alloy ingot out of a furnace for forging, controlling the heating speed to be 35 ℃/h before forging, the heat preservation temperature to be 1170 ℃, the heat preservation time to be 6h, carrying out forging cogging process including upsetting and drawing out, returning the alloy ingot to the furnace for heat preservation for 2h after single-fire forging time exceeds 15min, coating asbestos on the surface of the alloy ingot before forging each time for heat preservation, and controlling the total forging ratio to be 15 to obtain the bar.

Cutting a bar with a proper length according to the weight of the wheel disc forging, controlling the height-diameter ratio of the bar to be 2.5, upsetting the bar after heating the bar to form a blank, controlling the heating speed before forging to be 35 ℃/h, the heat preservation temperature to be 1120 ℃, the heat preservation time to be 4h, and the upsetting deformation to be 40%. And heating the disc blank, and then performing die forging forming, wherein the heating temperature rise speed before forging is controlled to be 35 ℃/h, the heat preservation temperature is 1120 ℃, the heat preservation time is 4h, the die forging deformation is 40%, and the die heating temperature is 650 ℃, so that the wheel disc forging is obtained.

The wheel disc forging is subjected to heat treatment through machining, wherein the heat treatment comprises solid solution treatment, intermediate aging treatment and aging treatment, the solid solution treatment system is 1180 ℃ and is kept warm for 5 hours, the intermediate aging treatment system is 1050 ℃ and is kept warm for 4 hours, and the aging treatment system is 910 ℃ and is kept warm for 12 hours.

In the low power inspection of the alloy bar prepared by the comparative example 1, black spot metallurgical defects are found, the cracking is obvious in the forging and cogging process, and the cracking tendency is larger than that of the example 3.

Comparative example 2 Nickel-based wrought superalloy wheel disc forging with diameter of 900mm capable of being used at 850 DEG C

The comparative example prepares a nickel-based wrought superalloy wheel disc forging piece with the diameter of 900mm, which can be used at the temperature of 850 ℃, the alloy components are shown in a table 1 and a comparative example 2, and compared with an example 3, the content of Mo is increased, the content of W is reduced, and the content of Fe is increased.

The preparation process of the alloy wheel disc forging comprises the following steps:

the smelting adopts a duplex process, namely vacuum induction smelting, electroslag remelting and vacuum consumable remelting, wherein the diameter of an alloy ingot subjected to vacuum induction smelting once is 355mm, the diameter of the electroslag remelting alloy ingot is 423mm, and the diameter of the vacuum consumable remelting alloy ingot is 508 mm. The vacuum induction melting comprises the following steps: weighing raw materials according to the element proportion of the alloy, wherein the metal raw materials comprise: metallic nickel, metallic chromium or nickel-chromium alloy, metallic titanium, metallic aluminum, metallic molybdenum, ferroboron, metallic cobalt, metallic tungsten, nickel-tungsten alloy, niobium-nickel alloy, ferrovanadium, carbon electrode, return material, and the like. The vacuum induction smelting process comprises the steps of evacuation, smelting period, refining, tapping and the like, wherein the vacuum degree in the evacuation period is 20Pa, the temperature in the smelting period is 1550 ℃, the temperature in the refining period is 1500 ℃, the vacuum degree in the refining period is 4Pa, the tapping temperature is 1480 ℃, 20000Pa argon is filled for protection during tapping, and after casting is completed, the ingot is cooled for 3 hours, demoulded and cooled to obtain a primary alloy ingot. Machining the primary alloy ingot to prepare an electroslag remelting electrode, wherein the filling ratio of the electrode to a crystallizer is 0.8, and the electroslag ratio is CaF 2: CaO: MgO: al2O 3: TiO2 ═ 65%: 15%: 1%: 15%: 4 percent, the steady-state melting speed is 5.0kg/min, the cooling time after the secondary alloy ingot is melted is 2 hours, and then the ingot is demoulded and cooled. And machining the secondary alloy ingot to prepare an electroslag remelting electrode, wherein the filling ratio of the electrode to a crystallizer is 0.83, the melting speed is 2.8kg/min, the cooling time after the third alloy ingot is melted is 2 hours, and then demolding and cooling are carried out to obtain the alloy ingot.

The high-temperature diffusion homogenization annealing of the alloy ingot comprises the processes of heating, heat preservation and cooling, wherein the heating speed is controlled to be 35 ℃/h, the heat preservation temperature is 1190 ℃, the heat preservation time is 50h, and the cooling speed is controlled to be 25 ℃/h. After carrying out homogenizing annealing on the alloy ingot, machining the alloy ingot, heating the alloy ingot to a forging temperature, keeping the temperature, then discharging the alloy ingot out of a furnace for forging, controlling the heating speed to be 35 ℃/h before forging, the heat preservation temperature to be 1170 ℃, the heat preservation time to be 6h, carrying out forging cogging process including upsetting and drawing out, returning the alloy ingot to the furnace for heat preservation for 2h after single-fire forging time exceeds 15min, coating asbestos on the surface of the alloy ingot before forging each time for heat preservation, and controlling the total forging ratio to be 15 to obtain the bar.

Cutting a bar with a proper length according to the weight of the wheel disc forging, controlling the height-diameter ratio of the bar to be 2.5, upsetting the bar after heating the bar to form a blank, controlling the heating speed before forging to be 35 ℃/h, the heat preservation temperature to be 1120 ℃, the heat preservation time to be 4h, and the upsetting deformation to be 40%. And heating the disc blank, and then performing die forging forming, wherein the heating temperature rise speed before forging is controlled to be 35 ℃/h, the heat preservation temperature is 1120 ℃, the heat preservation time is 4h, the die forging deformation is 40%, and the die heating temperature is 650 ℃, so that the wheel disc forging is obtained.

The wheel disc forging is subjected to heat treatment through machining, wherein the heat treatment comprises solid solution treatment, intermediate aging treatment and aging treatment, the solid solution treatment system is 1180 ℃ and is kept warm for 5 hours, the intermediate aging treatment system is 1050 ℃ and is kept warm for 4 hours, and the aging treatment system is 910 ℃ and is kept warm for 12 hours.

The alloy wheel disc forging piece prepared by the comparative example is used for taking a sample to carry out high-temperature long-term tissue stability test, and after the sample is aged for 3000 hours at 850 ℃, more harmful phases sigma phase and mu phase are separated out, and the tissue stability at 850 ℃ is poor.

Comparative example 3 and other prior art comparative analyses

To investigate whether the prior art has an accelerating effect on the technology of the present invention, the inventors conducted experiments of the technical processes of the following patents:

the test result shows that the comparative patent CN110241331A alloy is also a high-alloying nickel-base high-temperature alloy, the component proportion of the alloy is similar to that of the alloy of the invention, and the alloy is manufactured by adopting a powder metallurgy process. However, the inventors have found through experimental comparison that the alloy of the present invention contains a high content of Ti element and a low content of W element, and further contains alloy elements such as Hf and Ta. For the deformed high-temperature alloy produced by adopting the casting-forging process, Ti element is easy to segregate, and the high content of Ti element can increase the forming probability of point deviation defect in the vacuum consumable remelting process; the Hf element is an element which is very easy to oxidize, is very easy to oxidize into HfO2 particles in the casting process, and is mixed into a molten pool to cause adverse effects on the purity of a steel ingot.

Similarly, the results of comparative tests show that the comparative patent CN110205523A is also a high-alloyed Ni-based superalloy with a similar composition ratio to the alloy of the present invention, which is manufactured by a powder metallurgy process. Compared with the alloy of the invention, the content of W element is low, the content of Mo element is high, and the high Mo element is not beneficial to the thermal stability of the alloy at 850 ℃, and is easy to separate out harmful mu phase; the alloy is also added with Hf element, and is not suitable for being produced by adopting a casting-forging process.

Similarly, the results of comparative tests show that the comparative patent CN108441705A is also a high-alloyed Ni-based superalloy with a similar composition ratio to the alloy of the present invention, and the alloy is manufactured by a cast-forging process. Compared with the alloy of the 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 the use requirement of 850 ℃ can not be met; a small amount of Hf element is also added into the alloy, so that the risk of oxide inclusion is high for production by adopting a casting-forging process.

Similarly, the results of comparative tests show that the comparative patent CN108425037A is also a high-alloyed Ni-based superalloy with a similar composition ratio to the alloy of the present invention, which is manufactured by a powder metallurgy process. Compared with the alloy of the invention, the content of Ti element is high, Ti element increases the formation risk of metallurgical defects, and expensive Ta element is added for strengthening, which can not achieve the aim of developing a low-cost alloy which can be produced by adopting a casting-forging process.

Similarly, the results of comparative tests show that the comparative patent CN108315599A is also a high-alloyed Ni-based superalloy with a similar composition ratio to the alloy of the present invention, and the alloy is manufactured by a cast-forging process. Compared with the alloy of the invention, the W element content is low, a large amount of Nb element and Fe element are added, the Nb element is an element with strong segregation tendency, the black spot defect is easy to form in the content process, and the harmful sigma phase is easy to precipitate in the alloy at high temperature due to the high content of Fe element, so that the use requirement of the alloy at the high temperature of 850 ℃ cannot be met.

Similarly, the results of comparative tests show that the comparative patent CN107760926A is also a high-alloyed nickel-base superalloy with a similar composition ratio to the alloy of the present invention, which is manufactured by a casting process. Compared with the alloy of the invention, the content of Co is low, which is not beneficial to the structural stability and the forging process performance of the alloy; in addition, beneficial trace elements such as Mg, Zr, Ce and the like are not added in the grain boundary, so that the method is not suitable for improving the performance of the wrought superalloy with equiaxed grains.

The above description is only for the preferred embodiment of the present invention, but the scope of the present invention is not limited thereto, and any changes or substitutions that can be easily conceived by those skilled in the art within the technical scope of the present invention are also included in the scope of the present invention.

Claims (10)

1. The nickel-based wrought superalloy with high aluminum content is characterized by comprising the following components in percentage by mass: c: 0.004-0.1%, W: 6.0-9.0%, 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%, and the balance of Ni.

2. The nickel-base wrought superalloy according to claim 1, wherein the nickel-base wrought superalloy comprises, in mass percent: 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% of Ni; the nickel-based wrought superalloy also comprises impurity elements, wherein P is less than or equal to 0.015%, Mn is less than or equal to 0.5%, Si is less than or equal to 0.5%, S is less than or equal to 0.015%, O is less than or equal to 0.005%, N is less than or equal to 0.01%, Ag is less than or equal to 0.005%, Ca is less than or equal to 0.01%, Sn is less than or equal to 0.01%, Pb is less than or equal to 0.001%, Cu is less than or equal to 0.5%, Ta is less than or equal to 0.5%, and V is.

3. The nickel-base wrought superalloy according to claim 1, wherein the nickel-base wrought superalloy comprises, in mass percent: c: 0.01-0.06%, W: 6.5-7.5%, 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% of Ni; the nickel-based wrought superalloy also comprises impurity elements, wherein P is less than or equal to 0.010%, Mn is less than or equal to 0.15%, Si is less than or equal to 0.15%, S is less than or equal to 0.005%, O is less than or equal to 0.002%, N is less than or equal to 0.005%, Ag is less than or equal to 0.0005%, Ca is less than or equal to 0.005%, Sn is less than or equal to 0.005%, Pb is less than or equal to 0.0005%, Cu is less than or equal to 0.1%, Ta is less than or equal to 0.1%, and V is.

4. The nickel-based wrought superalloy according to claim 1, wherein gamma austenite is used as a matrix, the mass percentage of a gamma' phase of a strengthening phase reaches 55-65%, and the chemical composition of the strengthening phase is (Ni, Co)₃(Al，Ti，Nb)。

5. The nickel-base wrought superalloy according to claim 1, further comprising a second phase, wherein the second phase comprises: MC type carbide, M6C type carbide, M23C6 type carbide, MB2 type boride, and M3B2 type boride.

6. The nickel-base wrought superalloy according to claim 1, wherein the content of a gamma' phase in the nickel-base wrought superalloy is 55-65% by mass, the nickel-base wrought superalloy is aged for more than 5000 hours at a temperature of 650-900 ℃ for a long time, and the content of a precipitated harmful phase μ phase is not more than 1%.

7. The preparation method of the nickel-based wrought superalloy with high aluminum content is characterized by comprising the following steps:

step 1: smelting the metal raw material components of any claim 1 to 5 into a primary alloy ingot by vacuum induction smelting, remelting and refining the primary alloy ingot by electroslag to obtain a secondary alloy ingot, and remelting and refining the secondary alloy ingot by vacuum consumable melting to obtain a third alloy ingot to obtain an alloy ingot;

step 2: after the alloy ingot obtained in the step 1 is subjected to high-temperature diffusion homogenization annealing, heating, forging and cogging to form a bar;

and step 3: performing blanking and die forging on the bar obtained in the step 2 to obtain an alloy wheel disc forging;

and 4, step 4: and (4) carrying out heat treatment on the alloy wheel disc forged piece obtained in the step (3) to obtain the nickel-based deformation high-temperature alloy wheel disc forged piece used at the long time of 850 ℃.

8. The method according to claim 7, wherein the vacuum induction melting in step 1 comprises the following processing steps: evacuating, smelting period, refining and tapping;

in the vacuumizing treatment process, the vacuum degree is 10-100 Pa;

in the treatment process in the smelting period, the temperature is controlled to be 1300-1650 ℃;

in the refining treatment process, the temperature is controlled to be 1400-1600 ℃, and the vacuum degree is 1-20 Pa;

in the tapping treatment process, the temperature is controlled to be 1420-1590 ℃, and 10000-50000 Pa argon gas is filled for protection, after casting, the cast ingot is cooled for 0.5-3 h, and then demoulding and cooling are carried out, so that a primary alloy ingot is obtained.

9. The method as claimed in claim 7, wherein the step 1 further comprises: preparing the primary alloy ingot into an I electroslag remelting electrode, wherein the filling ratio of the I electroslag remelting electrode to the crystallizer is 0.75-0.9; in the electroslag remelting process, the adopted electroslag has the component proportion of CaF 2: CaO: MgO: al2O 3: TiO2= 65-75%: 10-20%: 0.5-5%: 10-20%: 0.5-5%, the steady-state melting speed is 1.0-6.0 kg/min, the cooling time after the secondary alloy ingot is melted is 0.5-6 h, and then demoulding and cooling are carried out.

10. The method as claimed in claim 7, wherein the step 1 further comprises: and preparing the secondary alloy ingot into an II electroslag remelting electrode, wherein the filling ratio of the II electroslag remelting electrode to the crystallizer is 0.75-0.95, the melting speed is 1.0-5.0 kg/min, the cooling time after the alloy ingot is melted for three times is 0.5-3 h, and then demolding and cooling.

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