CN110468361B - Preparation method of deformed high-temperature alloy fine-grain bar - Google Patents
Preparation method of deformed high-temperature alloy fine-grain bar Download PDFInfo
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- CN110468361B CN110468361B CN201910665041.5A CN201910665041A CN110468361B CN 110468361 B CN110468361 B CN 110468361B CN 201910665041 A CN201910665041 A CN 201910665041A CN 110468361 B CN110468361 B CN 110468361B
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
- B21J5/002—Hybrid process, e.g. forging following casting
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
- B21J5/06—Methods for forging, hammering, or pressing; Special equipment or accessories therefor for performing particular operations
- B21J5/08—Upsetting
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/023—Alloys based on nickel
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- 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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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- 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
Abstract
The invention belongs to the technical field of advanced processing of high-temperature alloy, and relates to a preparation method of a deformed high-temperature alloy fine-grain bar, which comprises the following steps: the method comprises the following steps of raw material proportioning, smelting in a vacuum induction furnace, vacuum consumable remelting, high-temperature diffusion homogenization annealing, upsetting and blank making, hot sheathing, sheathing blank sand blasting, coating glass lubricant, preparing a bar by extrusion, and sheathing and removing. The invention organically combines the upsetting and the extrusion cogging processes, innovatively adopts small-specification ingots to prepare large-specification bars, solves the problems of large process deformation difficulty and difficult processing and forming of the materials, has fine and uniform bar grain structure, produces high-quality compound hybrid alloying deformation high-temperature alloy bars, has ideal microstructure control, improves and improves mechanical properties, has high material qualification rate and obvious economic benefit.
Description
Technical Field
The invention belongs to the technical field of advanced processing of high-temperature alloy, and particularly relates to a preparation method of a composite alloy alloying deformation high-temperature alloy uniform fine-grain bar.
Background
The high-temperature alloy is widely applied to the industrial fields of aviation, aerospace, ships, nuclear power, petroleum, chemical engineering and the like. High temperature alloys can be generally classified into wrought high temperature alloys and cast high temperature alloys according to the forming process. Wrought superalloys are an important class of materials from which aircraft engine turbine disks are fabricated.
The preparation of the deformed high-temperature alloy uniform fine-grain bar or uniform fine-grain billet for the turbine disc is the premise and the basis for the development and production of advanced engine turbine discs. The uniformity and the refining characteristics of the grain structure of the deformed high-temperature alloy bar can ensure the uniformity and the good service performance of the structure of the disc, so that the reliability and the safety of the disc are improved.
Smelting and hot forming are two most important processes for producing deformed high-temperature alloy bars for turbine disks. In order to obtain a bar material with the diameter of phi 200 mm-phi 280mm for a turbine disc, in the traditional smelting preparation of an ingot, the selected ingot type is a large ingot type with the diameter of phi 508mm, but the ingot type with a large specification can cause serious segregation phenomenon of an alloy ingot casting solidification structure, and is not beneficial to obtaining a uniform structure of the bar material.
Hot working cogging is an important part of the production process of the deformed high-temperature alloy bar, and is a thermal deformation process method for changing a deformed high-temperature alloy ingot into a bar. Forging cogging is one way of hot working cogging. Forging cogging is suitable for wrought superalloys having low levels of alloying, which typically have low heat distortion resistance and high thermoplasticity, and are therefore easily forged. However, with the development of advanced aero-engines, the thrust-weight ratio of aero-engines is required to be continuously improved, which requires that a large amount of alloying elements must be added to the wrought superalloy for manufacturing turbine disks to obtain good comprehensive performance, thereby meeting the use requirements of high thrust-ratio engine turbine disks, the addition of a large amount of alloying elements leads to the complex alloying degree of the wrought superalloy for turbine disks, and the complex alloyed wrought superalloy has high hot-working deformation resistance and low thermoplasticity, so that ingots are difficult to deform, and the complex alloyed wrought alloy has the defects of high cracking degree of bars, high forming difficulty of bars, uneven forged structure, coarse grains, mixed grains and large grain size difference.
Hot extrusion is another hot forming method for producing metal materials. Compared with forging cogging process, the stress state borne by the material in the two processes is completely different, and the hot extrusion process has a three-way compression stress state, so that the deformation capacity of the material is improved to the maximum extent, the process plasticity and the allowable deformation degree are improved, fine and uniform dynamic recrystallization grains can be formed, and the hot extrusion process is favorable for forming low-plasticity alloys and materials difficult to deform.
The preparation of the low-alloying deformation high-temperature alloy bar has more domestic research and mature technology. However, the preparation of the compound hybrid alloying deformation superalloy uniform fine-grain bar for the turbine disc is lack of research in China, has high technical difficulty, and is a problem to be solved urgently.
Disclosure of Invention
The purpose of the invention is: the preparation method of the deformed high-temperature alloy fine-grain bar is provided to solve the technical problems that the segregation phenomenon of the alloy cast ingot solidification structure is serious and the bar is not favorable for obtaining a uniform structure in the conventional method due to the fact that the ingot with a large specification is large.
In order to solve the technical problem, the technical scheme of the invention is as follows:
a preparation method of a deformed high-temperature alloy fine-grain bar comprises the following steps:
step one, raw material blending: weighing and batching Cr, Co, Mo, W, Al, Ti, Nb, C and Ni as raw materials according to chemical components of the deformed high-temperature alloy;
step two, smelting in a vacuum induction furnace: putting a certain weight of prepared raw materials into a vacuum induction furnace for smelting to prepare an electrode rod;
step three, vacuum consumable remelting: the electrode bar prepared by smelting in the vacuum induction furnace is put into a vacuum consumable furnace for consumable remelting to prepare consumable ingots with medium specifications; the specification of the consumable ingot is phi 320 mm-phi 360 mm;
step four, high-temperature diffusion homogenization annealing: carrying out high-temperature diffusion homogenization annealing on the consumable ingot to obtain a homogenization annealed ingot;
step five, upsetting and blank making: machining two ends of the homogenized annealing ingot to enable two end surfaces to be flat and parallel and to be rounded; then, putting the annealing ingot into a high-temperature electric furnace for heating, taking the annealing ingot out of the high-temperature electric furnace, putting the annealing ingot into an upsetting die, upsetting the annealing ingot on a hydraulic machine to form an intermediate blank, and cooling the intermediate blank to room temperature;
step six, hot covering: putting the intermediate blank into a preheated stainless steel sleeve to obtain a sleeve blank;
step seven, covering blank sand blasting: placing the sheathed blank into a sand blasting machine for sand blasting treatment; forming a certain roughness on the outer surface of the sheath blank;
step eight, painting glass lubricant: uniformly brushing a glass lubricant on the outer surface of the sheathed blank subjected to sand blasting; the uniformity, firmness and compactness are realized;
step nine, extruding and preparing a bar stock: putting the sheathed blank coated with the glass lubricant into a high-temperature electric furnace for heating; taking out the ladle sleeve blank from the high-temperature electric furnace, putting the ladle sleeve blank into an extrusion cylinder of an extruder, extruding the ladle sleeve blank into a rod-shaped material with the diameter phi of 200 mm-280 mm, and cooling the extruded rod-shaped material to room temperature;
step ten, sheath removal: and removing the stainless steel sheath outside the extruded bar-shaped material by adopting a machining or wire cutting mode to obtain the deformed high-temperature alloy uniform fine-grain bar material.
And in the second step, the diameter of the electrode rod is phi 270 mm-phi 290 mm.
And step four, annealing the consumable ingot at 1170-1250 ℃.
And fifthly, the annealing ingot is heated in a high-temperature electric furnace in the following specific heating process: the charging temperature of the heating annealing ingot is less than or equal to 300 ℃, the heating is carried out to 800-850 ℃, the heat preservation is carried out for 30-60 min, the temperature is continuously raised to 1100-1130 ℃, and the heat preservation is carried out for 240-300 min.
The sixth step comprises the following specific steps: putting a stainless steel sleeve with the inner diameter being 0.5-1 mm smaller than the outer diameter of the intermediate blank into a high-temperature electric furnace, heating to 500 ℃ or above, preserving the heat for 45-60 min, taking the stainless steel sleeve out of the high-temperature electric furnace, quickly sleeving the intermediate blank into the stainless steel sleeve, and obtaining a ladle blank after air cooling; the stainless steel sleeve with the inner diameter smaller than the outer diameter of the intermediate billet is heated to more than 500 ℃ and is kept warm for 45-60 min, and the intermediate billet can be sleeved in the stainless steel sleeve at high temperature by utilizing the difference that the linear expansion coefficient of the stainless steel at high temperature is higher than that of the deformed high-temperature alloy intermediate billet, and the purpose of tightly combining the stainless steel sleeve and the deformed high-temperature alloy intermediate billet is realized.
The heating process of the tundish sleeve blank in the ninth step is specifically as follows: the temperature of the sheathed blank is less than or equal to 300 ℃, the sheathed blank is heated to 700-750 ℃, the temperature is kept for 60-120 min, the temperature is continuously raised to 900-950 ℃, the temperature is kept for 60-120 min, the temperature is continuously raised to 1050-1100 ℃, and the temperature is kept for 240-360 min;
the extrusion process parameters in the ninth step are as follows: the extrusion ratio was 3: 1-8: 1, the extrusion speed is 65 mm/s-95 mm/s.
Preferably, the step five further comprises the step of preheating the upsetting die; the preheating temperature is 200-300 ℃.
Preferably, in the step five, the two rounded end surfaces have the rounding radii R10 mm-R20 mm.
And fifthly, the specification of the intermediate billet is consistent with that of the upsetting die, and the diameter phi of the intermediate billet is preferably 400 mm-500 mm.
Preferably, the intermediate blank in the fifth step is cooled by covering heat-insulating cotton; and step nine, cooling the extruded rod-shaped material by covering heat preservation cotton.
The invention has the beneficial effects that:
(1) according to the technical scheme, the hot processing cogging combined process of upsetting and extruding is adopted, so that the hot processing forming preparation of the composite hybrid alloying deformation high-temperature alloy bar is realized, the problems of high difficulty in process deformation and difficulty in processing forming of the material are solved, and the yield of the bar is greatly improved;
(2) according to the technical scheme, the process of combining upsetting and extruding can obtain larger hot working deformation, and can effectively crush dendritic crystal structures of cast ingots, so that the crystal grain structures of the bars are very uniform and fine, the grain size can reach ASTM 10-14 grade, and an effective and feasible method is provided for controlling the homogenization and grain refining of the complex alloying deformation high-temperature alloy bar structures for the turbine disc;
(3) the technical scheme of the invention aims at the characteristics of complex alloying deformation high-temperature alloy, innovatively adopts small-specification ingot type to realize the preparation of large-specification bar, thereby reducing or eliminating the phenomenon of serious segregation structure of ingot casting caused by large-ingot type smelting, improving the uniformity of the casting structure of the complex alloying deformation high-temperature alloy, and creating a precondition for obtaining the uniformity of the bar hot processing structure.
(4) The compound hybrid alloying deformation high-temperature alloy bar prepared by the process method has good comprehensive properties such as room-temperature tensile property, high-temperature tensile property and the like.
(5) The invention provides a reliable preparation method by strictly controlling process parameters and matching processes, and the high-quality composite alloy-transformation high-temperature alloy bar is manufactured, so that the service life of the material is prolonged, the production cost is reduced, and the economic benefit is obvious.
Drawings
In order to more clearly illustrate the technical solution of the present invention, the drawings used in the embodiment of the present invention will be briefly explained. It is obvious that the drawings described below are only some embodiments of the invention, and that for a person skilled in the art, other drawings can be obtained from these drawings without inventive effort.
FIG. 1 is a typical uniform fine grain structure of a wrought superalloy bar prepared by the method of the present invention;
FIG. 2 is a comparison of typical tensile strength (UTS) and Yield Strength (YS) obtained from tensile testing at different temperatures for bars prepared using both the inventive process and a conventional forging process;
wherein the scale bar in fig. 1 is 100 μm.
Detailed Description
In order to make the objects, technical solutions and advantages of the embodiments of the present invention clearer, the technical solutions in the embodiments of the present invention will be clearly and completely described below with reference to the drawings in the embodiments of the present invention. It is to be understood that the embodiments described are only a few embodiments of the present invention, and not all embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
Features of various aspects of embodiments of the invention will be described in detail below. In the following detailed description, numerous specific details are set forth in order to provide a thorough understanding of the present invention. It will be apparent, however, to one skilled in the art that the present invention may be practiced without these specific details. The following description of the embodiments is merely intended to better understand the present invention by illustrating examples thereof. The present invention is not limited to any particular arrangement or method provided below, but rather covers all product structures, any modifications, alterations, etc. of the method covered without departing from the spirit of the invention.
In the drawings and the following description, well-known structures and techniques are not shown to avoid unnecessarily obscuring the present invention.
Example 1
A preparation method of a deformed superalloy fine-grained bar material comprises the following chemical components in percentage by weight: cr: 10.12 percent; co: 15.78 percent; mo: 4.05 percent; w: 3.42 percent; al: 3.65 percent; ti: 2.96 percent; nb: 3.07 percent; c: 0.045%; the balance being Ni and unavoidable impurities. Weighing and batching the raw materials of Cr, Co, Mo, W, Al, Ti, Nb, C and Ni according to the chemical components of the compound alloy alloying deformation superalloy; putting a certain weight of prepared raw materials into a vacuum induction furnace for smelting to prepare a phi 270mm electrode rod; loading the composite alloy alloying deformation high-temperature alloy electrode bar prepared by smelting in a vacuum induction furnace into a vacuum consumable furnace for consumable remelting to prepare a consumable ingot with the diameter of phi 320 mm; carrying out high-temperature diffusion homogenization annealing on the compound alloy alloying deformation high-temperature alloy phi 320mm consumable ingot at 1170 ℃ to obtain a homogenization annealed ingot; machining two ends of the homogenized annealing ingot to enable the two end surfaces to be flat and parallel and to be rounded, wherein the radius of the rounded corner of the two end surfaces is R10 mm; then, putting the trimmed annealing ingot into a high-temperature electric furnace for heating, wherein the charging temperature of the annealing ingot is less than or equal to 300 ℃, heating to 800 ℃, keeping the temperature for 30min, continuously heating to 1100 ℃, and keeping the temperature for 240 min; preheating an upsetting die to 300 ℃ in a resistance furnace; taking out the annealed ingot from the high-temperature electric furnace, putting the annealed ingot into a preheated upsetting die, upsetting the ingot into an intermediate blank with the diameter phi of 400mm on a hydraulic press with the rated pressure not lower than 5000T, covering heat-insulating cotton on the intermediate blank, and cooling the intermediate blank to room temperature; putting the austenitic stainless steel sleeve with the wall thickness of 10mm into a high-temperature electric furnace, heating to 500 ℃, preserving heat for 45min, taking out the austenitic stainless steel sleeve from the high-temperature electric furnace, quickly sleeving the intermediate blank into the austenitic stainless steel sleeve, and air-cooling to obtain a ladle blank; placing the sheathed blank into a sand blasting machine for sand blasting treatment; forming a certain roughness on the outer surface of the sheath blank; coating a glass lubricant with the melting temperature of 1100 ℃ on the outer surface of the sheathed blank subjected to sand blasting, and coating the glass lubricant for 3 times to achieve uniformity, firmness and compactness; heating the sheathed blank coated with the glass lubricant in a high-temperature electric furnace, wherein the furnace charging temperature of the sheathed blank is less than or equal to 300 ℃, heating to 700 ℃, keeping the temperature for 60min, continuously heating to 900 ℃, keeping the temperature for 60min, continuously heating to 1050 ℃, and keeping the temperature for 240 min; taking out the sleeve blank from the high-temperature electric furnace, putting the sleeve blank into an extrusion cylinder of an extruder with rated pressure not lower than 6000T, and adopting an extrusion ratio of 4.0: 1, extruding the mixture into a rod material with the diameter phi of 200mm at the extrusion speed of 80mm/s, covering heat preservation cotton on the extruded rod material, and cooling the extruded rod material to the room temperature. And removing the stainless steel sheath outside the extruded bar-shaped material by adopting a machining mode to obtain the composite alloy-deformed high-temperature alloy uniform fine-grained bar material.
Example 2
A preparation method of a deformed superalloy fine-grained bar material comprises the following chemical components in percentage by weight: cr: 11.35 percent; co: 14.52 percent; mo: 4.95 percent; w: 2.82 percent; al: 3.81 percent; ti: 2.79 percent; nb: 3.10 percent; c: 0.065%; the balance being Ni and unavoidable impurities. Weighing and batching the raw materials of Cr, Co, Mo, W, Al, Ti, Nb, C and Ni according to the chemical components of the compound alloy alloying deformation superalloy; putting a certain weight of prepared raw materials into a vacuum induction furnace for smelting to prepare an electrode rod with phi of 280 mm; loading the composite alloy alloying deformation high-temperature alloy electrode bar prepared by smelting in a vacuum induction furnace into a vacuum consumable furnace for consumable remelting to prepare a consumable ingot with phi of 340 mm; carrying out high-temperature diffusion homogenization annealing on the complex hybrid alloying deformation high-temperature alloy phi 340mm consumable ingot at 1200 ℃ to obtain a homogenization annealed ingot; machining two ends of the homogenized annealing ingot to enable the two end surfaces to be flat and parallel, and rounding off, wherein the radius of the fillet of the two end surfaces is R15 mm; then, putting the trimmed annealing ingot into a high-temperature electric furnace for heating, wherein the charging temperature of the annealing ingot is less than or equal to 300 ℃, heating to 850 ℃, keeping the temperature for 30min, continuously heating to 1120 ℃, and keeping the temperature for 270 min; preheating an upsetting die to 300 ℃ in a resistance furnace; taking out the annealed ingot from the high-temperature electric furnace, putting the annealed ingot into a preheated upsetting mold, upsetting the ingot into an intermediate blank with the diameter phi of 450mm on a hydraulic press with the rated pressure not lower than 5000T, covering heat-insulating cotton on the intermediate blank, and cooling the intermediate blank to room temperature; putting the austenitic stainless steel sleeve with the wall thickness of 15mm into a high-temperature electric furnace, heating to 600 ℃, preserving heat for 50min, taking out the austenitic stainless steel sleeve from the high-temperature electric furnace, quickly sleeving the intermediate blank into the austenitic stainless steel sleeve, and air-cooling to obtain a ladle blank; placing the sheathed blank into a sand blasting machine for sand blasting treatment; forming a certain roughness on the outer surface of the sheath blank; coating a glass lubricant with the melting temperature of 1100 ℃ on the outer surface of the sheathed blank subjected to sand blasting, and coating the glass lubricant for 3 times to achieve uniformity, firmness and compactness; heating the sheathed blank coated with the glass lubricant in a high-temperature electric furnace, wherein the furnace charging temperature of the sheathed blank is less than or equal to 300 ℃, heating to 750 ℃, keeping the temperature for 80min, continuously heating to 900 ℃, keeping the temperature for 60min, continuously heating to 1080 ℃, and keeping the temperature for 300 min; taking out the sleeve blank from the high-temperature electric furnace, putting the sleeve blank into an extrusion cylinder of an extruder with rated pressure not lower than 6000T, and adopting an extrusion ratio of 3.5: 1, extruding the mixture into a rod-shaped material with the diameter of 250mm at the extrusion speed of 65mm/s, covering heat preservation cotton on the extruded rod-shaped material, and cooling the extruded rod-shaped material to the room temperature. And removing the stainless steel sheath outside the extruded bar-shaped material by adopting a machining mode to obtain the composite alloy-deformed high-temperature alloy uniform fine-grained bar material.
Example 3
A preparation method of a deformed superalloy fine-grained bar material comprises the following chemical components in percentage by weight: cr: 11.96 percent; co: 14.89 percent; mo: 4.13 percent; w: 2.96 percent; al: 3.79 percent; ti: 2.92 percent; nb: 3.46 percent; c: 0.07 percent; the balance being Ni and unavoidable impurities. Weighing and batching the raw materials of Cr, Co, Mo, W, Al, Ti, Nb, C and Ni according to the chemical components of the compound alloy alloying deformation superalloy; putting a certain weight of prepared raw materials into a vacuum induction furnace for smelting to prepare an electrode rod with phi 290 mm; loading the composite alloy alloying deformation high-temperature alloy electrode bar prepared by smelting in a vacuum induction furnace into a vacuum consumable furnace for consumable remelting to prepare a consumable ingot with phi of 360 mm; carrying out high-temperature diffusion homogenization annealing on the compound hybrid alloying deformation high-temperature alloy phi 360mm consumable ingot at 1250 ℃ to obtain a homogenization annealed ingot; machining two ends of the homogenized annealing ingot to enable the two end surfaces to be flat and parallel, and rounding off, wherein the radius of the fillet of the two end surfaces is R15 mm; then, putting the trimmed annealing ingot into a high-temperature electric furnace for heating, wherein the charging temperature of the annealing ingot is less than or equal to 300 ℃, heating to 850 ℃, keeping the temperature for 60min, continuously heating to 1130 ℃, and keeping the temperature for 300 min; preheating an upsetting die to 300 ℃ in a resistance furnace; taking out the annealed ingot from the high-temperature electric furnace, putting the annealed ingot into a preheated upsetting die, upsetting the ingot into an intermediate blank with the diameter phi of 500mm on a hydraulic press with the rated pressure not lower than 5000T, covering heat-insulating cotton on the intermediate blank, and cooling the intermediate blank to room temperature; putting the austenitic stainless steel sleeve with the wall thickness of 20mm into a high-temperature electric furnace, heating to 700 ℃, preserving heat for 60min, taking out the austenitic stainless steel sleeve from the high-temperature electric furnace, quickly sleeving the intermediate blank into the austenitic stainless steel sleeve, and air-cooling to obtain a ladle blank; placing the sheathed blank into a sand blasting machine for sand blasting treatment; forming a certain roughness on the outer surface of the sheath blank; coating a glass lubricant with the melting temperature of 1100 ℃ on the outer surface of the sheathed blank subjected to sand blasting, and coating the glass lubricant for 3 times to achieve uniformity, firmness and compactness; heating the sheathed blank coated with the glass lubricant in a high-temperature electric furnace, wherein the furnace charging temperature of the sheathed blank is less than or equal to 300 ℃, heating to 750 ℃, keeping the temperature for 120min, continuously heating to 950 ℃, keeping the temperature for 120min, continuously heating to 1100 ℃, and keeping the temperature for 360 min; taking out the sleeve blank from the high-temperature electric furnace, putting the sleeve blank into an extrusion cylinder of an extruder with rated pressure not lower than 6000T, and adopting an extrusion ratio of 3.2: 1, extruding the mixture into a rod-shaped material with the diameter phi of 280mm at the extrusion speed of 90mm/s, covering heat preservation cotton on the extruded rod-shaped material, and cooling the rod-shaped material to the room temperature. And removing the stainless steel sheath outside the extruded bar-shaped material by adopting a machining mode to obtain the composite alloy-deformed high-temperature alloy uniform fine-grained bar material.
According to the technical scheme, the process of combining upsetting and extruding can obtain larger hot working deformation, and the dendritic crystal structure of the ingot can be effectively crushed, so that the crystal grain structure of the bar is very uniform and fine, the grain size can reach ASTM 10-14 grade, as shown in figure 1, and an effective and feasible method is provided for controlling the homogenization and grain refining of the structure of the compound hybrid alloying deformation high-temperature alloy bar for the turbine disc.
The wrought high-temperature alloy bar prepared by the process method has good comprehensive properties such as room-temperature tensile property, high-temperature tensile property and the like, wherein compared with the traditional single forging process, the room-temperature tensile yield strength of the alloy bar is improved by about 22% on average, and the tensile strength of the alloy bar is improved by about 10% on average; compared with the traditional single forging process, the tensile yield strength at 650 ℃ is improved by about 20% on average, and the tensile strength is improved by about 8% on average. See fig. 2.
Finally, it should be noted that: the above embodiments are only for illustrating the technical solutions of the present invention, but the scope of the present invention is not limited thereto, and any person skilled in the art can easily conceive various equivalent modifications or substitutions within the technical scope of the present invention, and these modifications or substitutions should be covered within the scope of the present invention.
Claims (6)
1. A preparation method of a deformed high-temperature alloy fine-grain bar is characterized by comprising the following steps: the preparation method comprises the following steps:
step one, raw material blending: weighing and batching Cr, Co, Mo, W, Al, Ti, Nb, C and Ni as raw materials according to chemical components of the deformed high-temperature alloy;
step two, smelting in a vacuum induction furnace: putting the prepared raw materials into a vacuum induction furnace for smelting to prepare an electrode rod; the diameter of the electrode rod is phi 270 mm-phi 290 mm;
step three, vacuum consumable remelting: the electrode bar prepared by smelting in the vacuum induction furnace is put into a vacuum consumable furnace for consumable remelting to prepare consumable ingots with medium specifications; the specification of the consumable ingot is phi 320 mm-phi 360 mm;
step four, high-temperature diffusion homogenization annealing: carrying out high-temperature diffusion homogenization annealing on the consumable ingot to obtain a homogenization annealed ingot; annealing the consumable ingot at 1170-1250 ℃;
step five, upsetting and blank making: machining two ends of the homogenized annealing ingot until the two end surfaces are flat and parallel and are rounded; then, putting the annealing ingot into a high-temperature electric furnace for heating, taking the annealing ingot out of the high-temperature electric furnace, putting the annealing ingot into an upsetting die, upsetting the annealing ingot on a hydraulic machine to form an intermediate blank, and cooling the intermediate blank to room temperature;
the specific heating process of the annealed ingot in a high-temperature electric furnace is as follows: heating the annealed ingot to 800-850 ℃ at the charging temperature of less than or equal to 300 ℃, keeping the temperature for 30-60 min, continuously heating to 1100-1130 ℃, and keeping the temperature for 240-300 min;
step six, hot covering: putting the intermediate blank into a preheated stainless steel sleeve to obtain a sleeve blank;
step seven, covering blank sand blasting: placing the sheathed blank into a sand blasting machine for sand blasting treatment;
step eight, painting glass lubricant: uniformly brushing a glass lubricant on the outer surface of the sheathed blank subjected to sand blasting;
step nine, extruding and preparing a bar stock: putting the sheathed blank coated with the glass lubricant into a high-temperature electric furnace for heating; taking out the ladle sleeve blank from the high-temperature electric furnace, putting the ladle sleeve blank into an extrusion cylinder of an extruder, extruding the ladle sleeve blank into a rod-shaped material with the diameter phi of 200 mm-280 mm, and cooling the extruded rod-shaped material to room temperature; the extrusion ratio was 3: 1-8: 1, the extrusion speed is 65 mm/s-95 mm/s;
step ten, sheath removal: and removing the stainless steel sheath outside the extruded bar-shaped material by adopting a machining or wire cutting mode to obtain the deformed high-temperature alloy uniform fine-grain bar material.
2. The method of claim 1, wherein: and step five, rounding radii of two end surfaces of the rounded corner R10 mm-R20 mm.
3. The method of claim 1, wherein: the sixth step comprises the following specific steps: and (3) putting the stainless steel sleeve into a high-temperature electric furnace, heating to more than 500 ℃, preserving heat for 45-60 min, taking out the stainless steel sleeve from the high-temperature electric furnace, quickly sleeving the intermediate blank into the stainless steel sleeve, and carrying out air cooling to obtain a ladle blank.
4. The method of claim 1, wherein: the heating process of the tundish sleeve blank in the ninth step is specifically as follows: the temperature of the sheathed blank is less than or equal to 300 ℃, the sheathed blank is heated to 700-750 ℃, the temperature is kept for 60-120 min, the temperature is continuously raised to 900-950 ℃, the temperature is kept for 60-120 min, the temperature is continuously raised to 1050-1100 ℃, and the temperature is kept for 240-360 min.
5. The method of claim 1, wherein: step five, cooling the intermediate blank by covering heat preservation cotton; and step nine, cooling the extruded rod-shaped material by covering heat preservation cotton.
6. The method of claim 1, wherein: the step five also comprises the step of preheating the upsetting die; the preheating temperature is 200-300 ℃.
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| CN201910665041.5A CN110468361B (en) | 2019-07-22 | 2019-07-22 | Preparation method of deformed high-temperature alloy fine-grain bar |
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