CN108441705B - High-strength nickel-based wrought superalloy and preparation method thereof - Google Patents
High-strength nickel-based wrought superalloy and preparation method thereof Download PDFInfo
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/056—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 10% but less than 20%
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- C22B9/00—General processes of refining or remelting of metals; Apparatus for electroslag or arc remelting of metals
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- C22B9/18—Electroslag remelting
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- C22B9/00—General processes of refining or remelting of metals; Apparatus for electroslag or arc remelting of metals
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- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/055—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 20% but less than 30%
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- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
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Abstract
The invention belongs to the technical field of nickel-based high-temperature alloys, and relates to a high-strength nickel-based wrought high-temperature alloy and a preparation method thereof. The high-strength nickel-based wrought superalloy comprises the following main elements in percentage by mass: cr: 10.0% -25.0%; co: 10.0% -20.0%; mo: 0.1 to 6.0 percent; w: 0.1 to 6.0 percent; al: 0.1 to 6.0 percent; ti: 0.1 to 6.0 percent; nb: 0.05 percent to 1.5 percent; fe: 0.1% -2.0%; c: 0.001% -0.10%; b: 0.001% -0.05%; zr: 0.01 to 0.1 percent; ce: 0.001% -0.10%; mg: 0.001% -0.10%; hf: 0.01 to 0.5 percent; ni: the balance; and unavoidable impurity elements; the preparation method of the alloy comprises the steps of obtaining a high-purity cast ingot by adopting vacuum induction smelting, electroslag remelting and vacuum consumable remelting, carrying out high-temperature diffusion homogenization annealing on the cast ingot within the range of 1170-1190 ℃, heating the annealed cast ingot to 1130-1160 ℃, preserving heat for 2-4 h, forging the annealed cast ingot into a required bar by using a quick forging machine, and carrying out heat treatment on a bar sample to obtain the alloy material meeting the design requirement of the invention.
Description
Technical Field
The invention belongs to the technical field of nickel-based high-temperature alloys, and relates to a high-strength nickel-based wrought high-temperature alloy and a preparation method thereof.
Background
High temperature alloys are a class of materials that have a high degree of alloying by adding various elements and can operate for a long period of time at temperatures above about 600 c, compared to stainless steels and heat resistant steels. The high-temperature alloy mainly comprises nickel-base high-temperature alloy, iron-base high-temperature alloy and cobalt-base high-temperature alloy according to a matrix, and is generally divided into three types according to a forming process, including wrought high-temperature alloy, casting high-temperature alloy and powder metallurgy high-temperature alloy. The nickel-based wrought superalloy becomes an indispensable key material for rotating parts such as turbine disks and compressor disks of aero-engines. GH4169 is a nickel-base wrought superalloy with a service temperature of 650 ℃. With the development of high thrust ratio aircraft engines, the inlet temperature of the turbine is higher and higher, and accordingly, the requirements on high-temperature mechanical performance indexes such as high-temperature strength, heat strength and the like of the high-temperature alloy of the turbine disc are higher and higher. Although powder Metallurgy superalloys (such as FGH4097 alloy) are a material option for future high-thrust-ratio engine turbine disk manufacturing, they are expensive to produce compared to wrought Superalloy turbine disks manufactured by the cast + wrought deformation process route (document 1: DeviaxA, stress A, Cormier J, Villechaise P, Douin J, Handcherli M and Petriari-stator F. Effect of making a turbine-mechanical-performance of AD730M metals.20148th International Symposium on superior 718and Derivatives, separator 28-30,2014, Pittsburgh, USA, 485-499; document 2: Raisson G. key of silicon metals, PM, 2008. 13. metals, 2008. pp.). According to the research progress of the turbine disc high temperature alloy in recent years (document 3: Chinese patent: CN 102443721A; document 4: Francis R.Preli, David Fuel, Lessons left from the development, application and advance of alloy 718.20148 th International Symposium on superior 718and Derivatives, September 28-30,2014Pittsburgh, USA, pp.3-14.), the preparation of the high performance wrought high temperature alloy by the short-flow low-cost casting and forging process technology is the direction and trend of the key development in the future at home and abroad. Therefore, there is a need to develop a high strength wrought superalloy with higher high temperature strength than the GH4169 alloy, comparable to the combination properties of powder superalloys (e.g., FGH4097), to meet the use requirements and low cost manufacturing requirements for aircraft engine turbine disks with higher mechanical performance requirements.
Disclosure of Invention
The invention aims to provide a high-strength nickel-based wrought superalloy and a preparation method thereof, which meet the use requirement and low-cost manufacturing requirement of a turbine disc with higher mechanical property requirement.
The technical scheme for realizing the invention is as follows: the high-strength nickel-based wrought superalloy comprises the following elements in percentage by mass: cr: 10.0% -25.0%; co: 10.0% -20.0%; mo: 0.1 to 6.0 percent; w: 0.1 to 6.0 percent; al: 0.1 to 6.0 percent; ti: 0.1 to 6.0 percent; nb: 0.05 percent to 1.5 percent; fe: 0.1% -2.0%; c: 0.001% -0.10%; b: 0.001% -0.05%; zr: 0.01 to 0.1 percent; ce: 0.001% -0.10%; mg: 0.001% -0.10%; hf: 0.01 to 0.5 percent; ni: and (4) the balance.
The mass percentages of the main elements are respectively as follows: cr: 14 percent; co: 13 percent; mo: 3.8 percent; w: 4.5 percent; al: 2.0 percent; ti: 3.5 percent; nb: 1.0 percent; fe: 1.0 percent; c: 0.03 percent; b: 0.02 percent; zr: 0.02 percent; ce: 0.01 percent; mg: 0.01 percent; hf: 0.1 percent; ni: and (4) the balance.
The mass percentages of the main elements are respectively as follows: cr: 16 percent; co: 12 percent; mo: 4.3 percent; w: 3.5 percent; al: 1.8 percent; ti: 3.8 percent; nb: 0.8 percent; fe: 0.8 percent; c: 0.02 percent; b: 0.015 percent; zr: 0.04 percent; ce: 0.01 percent; mg: 0.01 percent; hf: 0.15 percent; ni: and (4) the balance.
The mass percentages of the main elements are respectively as follows: cr: 15 percent; co: 11.5 percent; mo: 4.5 percent; w: 3.0 percent; al: 2.5 percent; ti: 3.3 percent; nb: 0.6 percent; fe: 0.9 percent; c: 0.01 percent; b: 0.018%; zr: 0.03 percent; ce: 0.01 percent; mg: 0.01 percent; hf: 0.2 percent; ni: and (4) the balance.
The preparation method of the high-strength nickel-based wrought superalloy comprises the following steps:
step A: preparing an alloy according to the element proportion, then smelting in a vacuum induction furnace, wherein the smelting process controls the total melting temperature: 1510 ℃ -1570 ℃; controlling the molten steel refining temperature: 1500-1560 ℃; tapping at the last stage of smelting, and pouring the solution into an alloy electrode;
and B: b, carrying out electroslag remelting on the alloy electrode obtained in the step A to obtain an electroslag ingot; the electroslag remelting adopts premelting slag, and the slag system and the proportion are CaF2:Al2O3:CaO:TiO2:MgO＝67±2.0:13±2.0:13±2.0:3±0.5:6±2.0；
And C: b, carrying out vacuum consumable remelting on the electroslag ingot obtained in the step B to obtain a consumable ingot; controlling the melting speed to be 3.0-4.0 Kg/min when in vacuum consumable remelting;
step D: c, performing high-temperature diffusion homogenization annealing on the consumable ingot obtained in the step C within the range of 1170-1190 ℃ to obtain a homogenization annealed ingot;
step E: heating the homogenized annealing ingot obtained in the step D to 1130-1160 ℃, preserving heat for 2-4 h, and forging the homogenized annealing ingot into a required bar on a quick forging machine;
step F: and E, cutting a sample from the head of the bar obtained in the step E in a linear cutting mode, and carrying out heat treatment on the sample, wherein the heat treatment process system of the sample is as follows: heating to 1060 ℃, preserving heat for 4h, cooling the oil to room temperature, then heating the sample to 760 ℃, preserving heat for 8h, and cooling in air to room temperature to obtain the high-strength nickel-based wrought superalloy bar.
The rated pressure of the rapid forging machine is 4500T.
The invention has the beneficial effects that: the high-strength nickel-based wrought superalloy is obtained by adding a plurality of elements and reasonably proportioning to perform composite multi-element strengthening, and compared with a standard heat-treated comparative alloy GH4169, the high-strength nickel-based wrought superalloy has higher room-temperature tensile strength, wherein the room-temperature tensile strength is improved by 20%; higher high temperature tensile strength, wherein the tensile strength at 700 ℃ is improved by 33 percent. Meanwhile, the alloy has longer lasting service life than GH4169 alloy under the condition of 650 ℃ and 700 ℃ and bearing higher load, so the alloy has higher heat resistance and service temperature than the GH4169 alloy. In addition, the high-temperature endurance performance of the alloy is equivalent to that of FGH4097 alloy at 650 ℃ and 700 ℃, but the tensile strength of the alloy is higher than that of FGH4097 alloy, wherein the tensile strength at room temperature is improved by 10% than that of FGH4097 alloy, and the tensile strength at 700 ℃ is improved by 12%, namely the alloy has more excellent comprehensive performance than that of FGH4097 alloy, and can meet the use requirement of a turbine disk with higher mechanical property requirement; in addition, a proper amount of Fe is added into the alloy, and the return material of the high-temperature alloy (such as GH4169) containing Fe can be used as furnace charge in smelting, so that the smelting cost is reduced from the source; more importantly, the alloy is prepared by adopting a casting and forging process route, compared with a complicated process manufacturing route of powder high-temperature alloy, the process flow is short, the total production cost is reduced, the mechanical property is comparable to or superior to that of the powder high-temperature alloy, the low-cost manufacturing requirement of advanced aeroengine turbine discs can be met, and the alloy has good economic and social benefits and is suitable for popularization and use.
The high-strength nickel-based wrought superalloy has the following component characteristics in consideration:
cr mainly plays a role in improving oxidation resistance and corrosion resistance in the high-temperature alloy, when the content of Cr in the alloy is not less than 10%, the oxidation resistance and corrosion resistance of Cr can be fully exerted, meanwhile, Cr is a main component element of a harmful phase sigma phase in the nickel-based high-temperature alloy, and has a strong tendency of promoting the sigma phase to form at high temperature, so that the service performance of the alloy is directly deteriorated. On the basis of comprehensively considering factors of improving the oxidation resistance, inhibiting the content of harmful phases and the like, the Cr is controlled within the range of 10.0-25.0 percent, and preferably within the range of 14-17 percent.
Co can form a continuous replacement solid solution with Ni, is an important constituent element for forming a matrix solid solution and plays a role in solid solution strengthening. Co also reduces the stacking fault energy of the matrix and thus improves the creep properties of the alloy. However, the addition of Co in an excessive amount is not sufficient, and on the one hand, the addition of Co in an excessive amount increases the tendency of the harmful phase to precipitate from the matrix, and on the other hand, Co is a strategic resource, and is expensive, which increases the production cost. Therefore, the control range of Co is designed to be 10.0% to 20.0%, and preferably, the control range is 11% to 15%.
Mo and W can play a role in solid solution strengthening of a matrix Ni, and importantly, Mo and W can improve the diffusion activation energy of creep of the high-temperature alloy, slow down the creep softening speed of the high-temperature alloy, improve the creep and endurance properties of the high-temperature alloy and improve the service temperature of the alloy. However, too much Mo promotes the precipitation of a harmful phase μ phase, and too much W increases notch sensitivity of the alloy. Therefore, in view of the similar effects of the two elements in the superalloy, Mo and W are controlled in the ranges of 0.1% to 6.0%, respectively, and preferably in the ranges of 3.0% to 4.5%, respectively, at a 1:1 equilibrium ratio.
The addition of Al and Ti is an important way to realize high strength of the high-temperature alloy, because Al and Ti are the forming elements of a gamma 'phase which is the main strengthening phase of the alloy, the higher the content of Al and Ti is, the more the number of the gamma' phase is, the better the precipitation strengthening effect is, and the strength of the alloy is correspondingly increased. However, too high Al and Ti contents also increase the solution temperature of the γ' phase in the alloy, reduce the hot working process window of the alloy, and increase the hot working difficulty of the alloy, so the ranges of Al and Ti are controlled to be 0.1% to 6.0%, preferably 1.0% to 3.0%, and 2.0% to 4.0%, respectively.
The main function of Nb is to enter the gamma ' phase, and a proper amount of Nb has the strengthening and stabilizing effects on the gamma ' phase, increases the phase reversal domain boundary energy when the gamma ' phase is cut by dislocation, and improves the precipitation strengthening effect.
The addition of Fe is beneficial to the utilization of high-temperature alloy return materials containing Fe including GH4169 alloy, and the cost of smelting furnace materials is reduced; however, since the addition of too much Fe causes the formation of a harmful phase in the nickel-base superalloy, the Fe is controlled in the range of 0.1 to 2.0%, preferably 0.1 to 1.0%.
C. B, Zr, Ce, Mg and Hf are grain boundary strengthening elements, and the trace addition of the elements can improve and improve the comprehensive properties of the alloy, such as plasticity, durability, processing forming property and the like.
The reasonable proportion of the alloy elements is the guarantee of the high strength of the alloy.
Detailed Description
The high-strength nickel-based wrought superalloy comprises the following elements in percentage by mass: cr: 10.0% -25.0%; co: 10.0% -20.0%; mo: 0.1 to 6.0 percent; w: 0.1 to 6.0 percent; al: 0.1 to 6.0 percent; ti: 0.1 to 6.0 percent; nb: 0.05 percent to 1.5 percent; fe: 0.1% -2.0%; c: 0.001% -0.10%; b: 0.001% -0.05%; zr: 0.01 to 0.1 percent; ce: 0.001% -0.10%; mg: 0.001% -0.10%; hf: 0.01 to 0.5 percent; ni: and (4) the balance.
The preparation method of the high-strength nickel-based wrought superalloy comprises the following steps:
step A: preparing an alloy according to the element proportion, then smelting in a vacuum induction furnace, wherein the smelting process controls the total melting temperature: 1510 ℃ -1570 ℃; controlling the molten steel refining temperature: 1500-1560 ℃; tapping at the last stage of smelting, and pouring the solution into an alloy electrode;
and B: b, carrying out electroslag remelting on the alloy electrode obtained in the step A to obtain an electroslag ingot;
and C: b, carrying out vacuum consumable remelting on the electroslag ingot obtained in the step B to obtain a consumable ingot;
step D: c, performing high-temperature diffusion homogenization annealing on the consumable ingot obtained in the step C within the range of 1170-1190 ℃ to obtain a homogenization annealed ingot;
step E: heating the homogenized annealing ingot obtained in the step D to 1130-1160 ℃, preserving heat for 2-4 h, and forging the homogenized annealing ingot into a required bar on a quick forging machine;
step F: and E, cutting a sample from the head of the bar obtained in the step E in a wire cutting mode, carrying out heat treatment on the sample, and carrying out surface finishing on the bar with the sample removed to obtain the alloy material meeting the design requirement of the invention.
In the step B, pre-melted slag is adopted for electroslag remelting, and the slag system and the proportion are CaF2:Al2O3:CaO:TiO2:MgO＝67±2.0:13±2.0:13±2.0:3±0.5:6±2.0。
And C, controlling the melting speed to be (3.0-4.0) Kg/min when the vacuum consumable remelting is carried out in the step C.
The rated pressure of the rapid forging machine in the step E is 4500T.
And F, carrying out heat treatment on the sample, wherein the heat treatment process system is as follows: heating to 1060 ℃, keeping the temperature for 4h, cooling the oil to room temperature, then heating the sample to 760 ℃, keeping the temperature for 8h, and cooling the sample to room temperature in air.
Example 1
A method for preparing the high-strength nickel-based wrought superalloy of the present invention comprises the steps of:
step A: according to Cr: 22 percent; co: 13 percent; mo: 3.8 percent; w: 5.0 percent; al: 2.0 percent; ti: 3.5 percent; nb: 1.0 percent; fe: 1.0 percent; c: 0.06 percent; b: 0.02 percent; zr: 0.02 percent; ce: 0.03 percent; mg: 0.01 percent; hf: 0.1 percent; ni: preparing alloy according to the balance weight percentage, then smelting in a vacuum induction furnace, wherein the smelting process controls the total smelting temperature: 1553 deg.C; controlling the molten steel refining temperature: 1550 ℃; tapping at the last stage of smelting, and pouring the solution into an alloy electrode;
and B: b, carrying out electroslag remelting on the alloy electrode obtained in the step A to obtain an electroslag ingot;
and C: b, carrying out vacuum consumable remelting on the electroslag ingot obtained in the step B to obtain a consumable ingot;
step D: c, performing high-temperature diffusion homogenization annealing on the consumable ingot obtained in the step C at 1170 ℃ to obtain a homogenization annealed ingot;
step E: heating the homogenized annealing ingot obtained in the step D to 1130 ℃, preserving heat for 4 hours, and forging the homogenized annealing ingot into a required bar on a quick forging machine;
step F: and E, cutting a sample from the head of the bar obtained in the step E in a wire cutting mode, carrying out heat treatment on the sample, and carrying out surface finishing on the bar with the sample removed to obtain the alloy material meeting the design requirement of the invention.
The electroslag remelting adopts premelting slag, and the slag system and the proportion are CaF2：Al2O3：CaO：TiO2: MgO 65: 13: 13: 3: 6; when the vacuum consumable remelting is carried out, the melting speed is controlled to be 3.0 Kg/min; the rated pressure of the rapid forging machine is 4500T; the heat treatment of the sample comprises the following steps: heating to 1060 ℃, keeping the temperature for 4h, cooling the oil to room temperature, then heating the sample to 760 ℃, keeping the temperature for 8h, and cooling the sample to room temperature in air.
Example 2
The method for preparing the high-strength nickel-based wrought superalloy comprises the following steps:
step A: according to Cr: 16 percent; co: 15 percent; mo: 5.5 percent; w: 4.5 percent; al: 1.5 percent; ti: 4.0 percent; nb: 0.8 percent; fe: 0.8 percent; c: 0.03 percent; b: 0.015 percent; zr: 0.04 percent; ce: 0.002%; mg: 0.002%; hf: 0.15 percent; ni: preparing alloy according to the balance weight percentage, then smelting in a vacuum induction furnace, wherein the smelting process controls the total smelting temperature: 1552 deg.C; controlling the molten steel refining temperature: 1560 deg.C; tapping at the last stage of smelting, and pouring the solution into an alloy electrode;
and B: b, carrying out electroslag remelting on the alloy electrode obtained in the step A to obtain an electroslag ingot;
and C: b, carrying out vacuum consumable remelting on the electroslag ingot obtained in the step B to obtain a consumable ingot;
step D: c, performing high-temperature diffusion homogenization annealing on the consumable ingot obtained in the step C at 1180 ℃ to obtain a homogenization annealed ingot;
step E: heating the homogenized annealing ingot obtained in the step D to 1140 ℃, preserving heat for 3 hours, and forging the homogenized annealing ingot into a required bar on a quick forging machine;
step F: and E, cutting a sample from the head of the bar obtained in the step E in a wire cutting mode, carrying out heat treatment on the sample, and carrying out surface finishing on the bar with the sample removed to obtain the alloy material meeting the design requirement of the invention.
The electroslag remelting adopts premelting slag, and the slag system and the proportion are CaF2：Al2O3：CaO：TiO2: MgO 65: 13: 13: 3: 6; when the vacuum consumable remelting is carried out, the melting speed is controlled to be 3.5 Kg/min; the rated pressure of the rapid forging machine is 4500T; the heat treatment of the sample comprises the following steps: heating to 1060 ℃, keeping the temperature for 4h, cooling the oil to room temperature, then heating the sample to 760 ℃, keeping the temperature for 8h, and cooling the sample to room temperature in air.
Example 3
A method for preparing the high-strength nickel-based wrought superalloy of the present invention comprises the steps of:
step A: according to Cr: 12 percent; co: 18.5 percent; mo: 4.5 percent; w: 3.0 percent; al: 3.0 percent; ti: 2.5 percent; nb: 0.6 percent; fe: 1.2 percent; c: 0.01 percent; b: 0.01 percent; zr: 0.03 percent; ce: 0.01 percent; mg: 0.015 percent; hf: 0.3 percent; ni: preparing alloy according to the balance weight percentage, then smelting in a vacuum induction furnace, wherein the smelting process controls the total smelting temperature: 1550 ℃; controlling the molten steel refining temperature: 1555 deg.C; tapping at the last stage of smelting, and pouring the solution into an alloy electrode;
and B: b, carrying out electroslag remelting on the alloy electrode obtained in the step A to obtain an electroslag ingot;
and C: b, carrying out vacuum consumable remelting on the electroslag ingot obtained in the step B to obtain a consumable ingot;
step D: c, performing high-temperature diffusion homogenization annealing on the consumable ingot obtained in the step C at 1190 ℃ to obtain a homogenization annealed ingot;
step E: heating the homogenized annealing ingot obtained in the step D to 1150 ℃, preserving heat for 2.5 hours, and forging the homogenized annealing ingot into a required bar on a quick forging machine;
step F: and E, cutting a sample from the head of the bar obtained in the step E in a wire cutting mode, carrying out heat treatment on the sample, and carrying out surface finishing on the bar with the sample removed to obtain the alloy material meeting the design requirement of the invention.
The electroslag remelting adopts premelting slag, and the slag system and the proportion are CaF2：Al2O3：CaO：TiO2: MgO 65: 13: 13: 3: 6; when the vacuum consumable remelting is carried out, the melting speed is controlled to be 3.8 Kg/min; the rated pressure of the rapid forging machine is 4500T; the heat treatment of the sample comprises the following steps: heating to 1060 ℃, keeping the temperature for 4h, cooling the oil to room temperature, then heating the sample to 760 ℃, keeping the temperature for 8h, and cooling the sample to room temperature in air.
The high-strength nickel-based wrought superalloy also inevitably contains impurity elements, and the types and the mass percentages are respectively as follows: p is less than or equal to 0.010 percent; s is less than or equal to 0.0015 percent; si is less than or equal to 0.1 percent; mn is less than or equal to 0.1 percent; pb is less than or equal to 0.0005 percent; ag is less than or equal to 0.0005 percent; te is less than or equal to 0.00005 percent; tl is less than or equal to 0.00005 percent; bi is less than or equal to 0.00003 percent.
The above description is only an embodiment of the present invention, and not intended to limit the scope of the present invention, and all modifications of equivalent structures and equivalent processes, or direct or indirect applications in other related fields, which are made by the present disclosure, are included in the scope of the present invention.
After the alloy of the invention is subjected to the steps, the alloy has excellent mechanical properties, and the specific properties are shown in the following tables 1, 2 and 3:
TABLE 1 tensile Properties at room temperature of the alloys
TABLE 2 high temperature tensile Properties of the alloys
TABLE 3 high temperature endurance of the alloys
Claims (3)
1. A high-strength nickel-based wrought superalloy, comprising: the mass percentages of the elements are respectively as follows: cr: 10.0% -16.0%; co: 18.5% -20.0%; mo: 0.1 to 3.8 percent; w: 0.1 to 6.0 percent; al: 2.0% -6.0%; ti: 2.5% -6.0%; nb: 1.0% -1.5%; fe: 0.1% -2.0%; c: 0.001% -0.10%; b: 0.02% -0.05%; zr: 0.01 to 0.1 percent; ce: 0.001% -0.10%; mg: 0.001% -0.10%; hf: 0.01 to 0.5 percent; ni: the balance; the high-strength nickel-based wrought superalloy is prepared by the following steps:
step A: preparing an alloy according to the element proportion, then smelting in a vacuum induction furnace, wherein the smelting process controls the total melting temperature: 1510 ℃ -1570 ℃; controlling the refining temperature of the alloy liquid: 1500-1560 ℃; alloy is produced at the last stage of smelting, and the molten liquid is poured into an alloy electrode;
and B: b, carrying out electroslag remelting on the alloy electrode obtained in the step A to obtain an electroslag ingot; the electroslag remelting adopts premelting slag, and the slag system and the proportion are CaF2:Al2O3:CaO:TiO2:MgO＝67±2.0:13±2.0:13±2.0:3±0.5:6±2.0；
And C: b, carrying out vacuum consumable remelting on the electroslag ingot obtained in the step B to obtain a consumable ingot; when the vacuum consumable remelting is carried out, controlling the melting speed to be 3.0-4.0 kg/min;
step D: c, performing high-temperature diffusion homogenization annealing on the consumable ingot obtained in the step C within the range of 1170-1190 ℃ to obtain a homogenization annealed ingot;
step E: heating the homogenized annealing ingot obtained in the step D to 1130-1160 ℃, preserving heat for 2-4 h, and forging the homogenized annealing ingot into a required bar on a quick forging machine;
step F: and E, cutting a sample from the head of the bar obtained in the step E in a linear cutting mode, and carrying out heat treatment on the sample, wherein the heat treatment process system of the sample is as follows: heating to 1060 ℃, preserving heat for 4h, cooling the oil to room temperature, then heating the sample to 760 ℃, preserving heat for 8h, and cooling in air to room temperature to obtain the high-strength nickel-based wrought superalloy.
2. A method of making a high strength nickel-base wrought superalloy as in claim 1, comprising the steps of:
step A: preparing an alloy according to the element proportion, then smelting in a vacuum induction furnace, wherein the smelting process controls the total melting temperature: 1510 ℃ -1570 ℃; controlling the refining temperature of the alloy liquid: 1500-1560 ℃; alloy is produced at the last stage of smelting, and the molten liquid is poured into an alloy electrode;
and B: b, carrying out electroslag remelting on the alloy electrode obtained in the step A to obtain an electroslag ingot; the electroslag remelting adopts premelting slag, and the slag system and the proportion are CaF2:Al2O3:CaO:TiO2:MgO＝67±2.0:13±2.0:13±2.0:3±0.5:6±2.0；
And C: b, carrying out vacuum consumable remelting on the electroslag ingot obtained in the step B to obtain a consumable ingot; when the vacuum consumable remelting is carried out, controlling the melting speed to be 3.0-4.0 kg/min;
step D: c, performing high-temperature diffusion homogenization annealing on the consumable ingot obtained in the step C within the range of 1170-1190 ℃ to obtain a homogenization annealed ingot;
step E: heating the homogenized annealing ingot obtained in the step D to 1130-1160 ℃, preserving heat for 2-4 h, and forging the homogenized annealing ingot into a required bar on a quick forging machine;
step F: and E, cutting a sample from the head of the bar obtained in the step E in a linear cutting mode, and carrying out heat treatment on the sample, wherein the heat treatment process system of the sample is as follows: heating to 1060 ℃, preserving heat for 4h, cooling the oil to room temperature, then heating the sample to 760 ℃, preserving heat for 8h, and cooling in air to room temperature to obtain the high-strength nickel-based wrought superalloy bar.
3. The method of making a high strength nickel-base wrought superalloy according to claim 2, wherein the rapid forging machine has a pressure rating of 4500 t.
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