CN114346137B - Hot working preparation method of large-size titanium alloy bar with uniform ribbon-shaped structure - Google Patents

Hot working preparation method of large-size titanium alloy bar with uniform ribbon-shaped structure Download PDF

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CN114346137B
CN114346137B CN202111478959.2A CN202111478959A CN114346137B CN 114346137 B CN114346137 B CN 114346137B CN 202111478959 A CN202111478959 A CN 202111478959A CN 114346137 B CN114346137 B CN 114346137B
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deformation
titanium alloy
forging
temperature
fire
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CN114346137A (en
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刘建荣
王清江
赵子博
朱绍祥
李文渊
王磊
陈志勇
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Institute of Metal Research of CAS
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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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C37/00—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
    • B21C37/04—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of bars or wire
    • 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
    • B21J5/02—Die forging; Trimming by making use of special dies ; Punching during forging
    • 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
    • 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

Abstract

The invention belongs to the field of titanium-based material hot working, and particularly relates to a hot working preparation method of a large-size titanium alloy bar with uniform fine strip-shaped structures. The method comprises the components of applicable alloy types, hot working process, application range and the like. By adopting the hot working process, the rod blank with the cross section low-power structure of 1-3 grades of fuzzy crystals and the longitudinal section low-power structure of uniform thin strip-shaped structure can be obtained. The total deformation firing time of the rod blank thermal processing can be controlled within 8 fires, the yield can be improved by more than 10 percent, and the method has the technical advantages of short flow, high efficiency and low cost. The bar stock prepared by the invention is directly used for preparing part blanks such as frames, beams, columns, shafts and the like with the main bearing direction parallel or nearly parallel to the banded structure after simple hot and cold processing, or is used as forging blanks of various forgings, and the forging blanks are formed into forging structures with fine and uniform grain sizes after thermal deformation of 2-4 fire, thereby meeting the requirements of high-quality and low-cost titanium alloy forgings in the high-tech fields such as aerospace and the like.

Description

Hot working preparation method of large-size titanium alloy bar with uniform ribbon-shaped structure
Technical Field
The invention belongs to the field of titanium-based material hot working, and particularly relates to a hot working preparation method of a large-size titanium alloy bar (with the diameter or equivalent diameter of more than or equal to 150 mm) with uniform fine-strip-shaped structures.
Background
The titanium alloy has the advantages of high specific strength, corrosion resistance, heat resistance and the like, so that the titanium alloy is widely applied to the fields of aviation, aerospace, petroleum, chemical industry, energy, automobiles, medical treatment, sports and leisure and the like. With the development of aviation and aerospace technology, the demand for high-end titanium materials is increasing. However, the high material and processing cost limit the wide application of titanium alloy, especially for titanium alloy with high brittleness tendency, the high-efficiency preparation process which reduces the hot processing firing time, improves the material yield, and does not reduce the quality of the product, especially the semi-finished product (such as bar) directly determines the quality stability, price and application.
The quality of the semi-finished product and the finished product of the titanium alloy material is mainly characterized in the following aspects: 1) The ingot metallurgy quality refers to defects and control degrees of high-low density inclusion, oxide, nitride, shrinkage cavity, porosity, macroscopic component segregation, segregation and the like which possibly occur in a titanium alloy ingot, and the higher the control degree is, the lower the probability of occurrence of the defects is, and the better the ingot metallurgy quality is; 2) Microstructure and uniformity and consistency control thereof. On the premise that the metallurgical quality of the cast ingot meets the requirement, the quality of a finished product or a semi-finished product mainly depends on target microstructure control, uniformity of grain size and difference of grain morphology/size of different parts (namely, tissue consistency). It is generally considered that the more uniform the grain size and the more discrete the crystallographic orientation of the grains, the less the microstructural differences in the different parts, and the higher the quality of the finished or semi-finished titanium alloy product, provided that the microstructure type meets the control requirements.
The reason for the high price of titanium alloy semi-finished products is mainly represented by the following aspects: 1) Raw material price. The raw materials of the titanium alloy mainly comprise sponge titanium and various intermediate alloys, the price of the sponge titanium at home and abroad fluctuates up and down at 80 yuan/kg, the price of the intermediate alloy is several times to tens times of that of the sponge titanium, and the price of the raw materials is tens times or even tens times of that of common steel; 2) And (5) alloy smelting. The titanium alloy has high activity, O in a molten state and in air 2 、N 2 、CO 2 The reaction of steam and the like is intense and almost all refractory materials contacted with the steam and the steam react chemically, so that the smelting of the titanium alloy can only be completed under the vacuum or inert gas protection environment, therefore, a water-cooled copper crucible or a condensation shell is required to be used as a container, and induction, vacuum consumable, plasma and electron beam are adoptedThe smelting method has higher smelting cost; 3) And (5) heat processing cost. According to different alloy types and requirements, the heat processing fire time of the currently domestic forged titanium alloy products is between a few fires and tens of fires, and some products even reach more than twenty fires, and each fire adopts an electric furnace for heating; surface oxidation in the heating process, surface polishing after forging and the like, and not only has raw material loss, but also has energy power loss, so that the cost is further increased; so that the price of the titanium alloy is high for a long time. Among the three factors affecting the cost of titanium alloys, the link with a large cost compression space is the cost of hot working. The heat processing fire is reduced, the raw material loss is reduced, the qualification rate is improved, the cost can be obviously reduced, and the method is a key for reducing the production cost of titanium alloy products in the present stage.
In conclusion, the microstructure of the titanium alloy semi-finished product and the microstructure of the finished product are stable and controllable, and the titanium alloy semi-finished product and the finished product have good uniformity and consistency, which are important means for reducing the heat, improving the heat deformation efficiency, reducing the energy and material loss in the heat deformation process and reducing the production cost.
The titanium alloy hot working process has more patents, and similar patents to the invention have about 20. Such as:
chinese patent publication No. CN109371268A discloses a method for preparing a high-temperature, high-thermal-stability and high-creep-resistance titanium alloy bar, which comprises heating a Ti55 titanium alloy ingot to 1150-1200 ℃, and then cogging and forging in a beta phase region by using a rapid forging machine or a hydraulic press; repeatedly upsetting and drawing-out forging by using a quick forging machine or a hydraulic press at 1050-1100 ℃, and heating the forged blank to T β -100℃～T β -20℃（T β The Ti55 titanium alloy is subjected to alpha+beta/beta phase transition temperature), and is repeatedly upsetting, drawing and forging to the required size by using a rapid forging machine or a hydraulic press, so that the titanium alloy bar with a fuzzy crystal low-power structure and a uniform high-power structure is obtained. The maximum difference between the reference example and the hot working process used in the invention is that each fire forging of the reference example adopts a repeated upsetting and drawing process, and the obtained low-power tissue with fuzzy crystals is not uniform strip tissue because of the repeated upsetting effect; in addition, the forging temperature is selected so that the invention can avoid the occurrence of large surface The temperature range of the product recrystallization, therefore, the thermal deformation temperature range below the transformation point is shifted down as a whole, which is significantly different from the forging process and pursuing the final effect of the present invention.
Chinese patent publication No. CN111390081a discloses a process for preparing a high creep resistance, high fracture toughness TC25G titanium alloy forging, which includes heating a TC25G bar blank to 50-30 ℃ below the beta transition temperature, upsetting and shaping to obtain a forging stock; then forming the forging stock at the temperature of 10-40 ℃ above the phase transition point, and controlling the deformation to 40-80%; finally, the forging blank microstructure is obtained after solid solution and aging dual heat treatment and is a basket structure. The target product of the comparative example is a disc forging, the last fire forging is completed above the beta transformation point, the target structure is a basket structure, and the final fire forging is completed at 30-200 ℃ below the beta transformation temperature and the target structure is a ribbon structure which is obviously different from the final fire forging of the invention.
Chinese patent publication No. CN101104898A discloses a novel high-temperature titanium alloy with high heat resistance and high heat stability, and provides a hot working process of the alloy, which is characterized in that a low-high-low process of heating forging in an α+β two-phase region, heating forging in a β single-phase region, and heating forging in an α+β two-phase region is adopted, and the intermediate "heating forging in a β single-phase region" process causes the hot working structure of the previous process to be completely recrystallized, thus contrary to the design of the fine band-shaped structure of the present invention. The reference example also provides a process for preparing the thin bar by adopting the process of 'beta single-phase zone heating forging + precision forging + rolling'. The product specification, application, deformation mode and metal flow under precision forging and rolling conditions are completely different from those of the hydraulic press forging of the invention, and are not comparable with the production process for preparing large-size bars by adopting the hydraulic press.
Chinese patent publication No. CN104018027a discloses a novel heat-resistant titanium alloy, and a processing method and application thereof, including alloy components, smelting, heat processing, heat treatment, and other constituent elements. The alloy can obtain different matches of tensile strength and plasticity, durability and creep strength and thermal stability through different heat processing and heat treatment process combinations, and can be used for manufacturing parts such as blades, disc parts and the like of high-temperature parts of an advanced aeroengine. The thermal processing temperature range above the beta phase transition point is +20 to +150 ℃, and the deformation heat is required to be 2-4 times; the temperature range of the hot working process below the phase transition point is 10-60 ℃, the deformation temperature is gradually reduced along with the increase of deformation heat, and the microstructure morphology is not clarified. The thermal processing technology of the invention requires that the deformation temperature below the beta transformation point is selected to avoid the temperature interval where large-area recrystallization occurs in the thermal deformation tissue, and avoid the recrystallization and growth of crystal grains, so the control of the deformation temperature below the beta transformation point is very critical, and the operation of 'increasing with the deformation heat and gradually reducing the deformation temperature' is not suitable for obtaining uniform and fine banded tissues in the invention in terms of technical principle.
Chinese patent publication No. CN111235506a discloses a hot working process for TC25G titanium alloy forging, which specifically comprises: 1) Cogging forging of cast ingots: heating and preserving heat of an alloy cast ingot, discharging the alloy cast ingot from a furnace for forging, and heating the cast ingot to a certain temperature for upsetting and drawing deformation to obtain a blank after cogging in a beta phase region; 2) Preparing forging stock: deforming the blank at 100-20 ℃ below the beta phase transition point; heating to 15-40 ℃ above the beta phase transition point, homogenizing at high temperature, and deforming; cooling to 100-30 ℃ below the beta phase transition point, and deforming to a bar with the target size; 3) And (5) die forging and forming: forging the forging stock; 4) And (3) heat treatment: and carrying out solid solution and aging double heat treatment to obtain a TC25G titanium alloy forging blank, wherein the obtained TC25G forging structure is a double-state structure. The comparative example is characterized in that a low-high-low process is adopted in the preparation process of forging stock, namely, after deformation at 100-20 ℃ below a phase transition point, the forging stock is heated to 15-40 ℃ above the phase transition point for high-temperature homogenization treatment, then deformation is carried out, and then the forging stock is deformed to a target size at 100-30 ℃ below a beta phase transition point. After the thermal deformation temperature of the invention is below the beta phase transition point, the phase transition point is not deformed in the subsequent process, thereby avoiding the occurrence of complete recrystallization of deformed crystal grains and further influencing the formation of fine-ribbon-shaped tissues and the control of the size and the shape.
Chinese patent publication No. CN109234554A discloses a method for preparing a high-temperature titanium alloy bar, which comprises heating a prepared Ti60 titanium alloy cast ingot to 1150-1200 ℃, and then benefitingCogging and forging in a beta phase region by using a rapid forging machine or a hydraulic press; repeatedly upsetting and drawing-out forging by using a quick forging machine or a hydraulic press at 1080-1150 ℃, and heating the forged blank to T β -120℃～T β -30℃（T β The transformation temperature of alpha+beta/beta phase of Ti60 titanium alloy) is repeatedly upsetted, drawn and forged to the required size by a rapid forging machine or a hydraulic press, and the titanium alloy bar with a fuzzy crystal low-power structure and a uniform high-power structure is obtained. The comparative example is characterized in that repeated upsetting and drawing are emphasized, and finally, a forging structure with a fuzzy microstructure and a uniform high-power microstructure is obtained, which is completely different from the technical original purpose and the implementation scheme of the invention that the unidirectional drawing deformation and the obtaining of the ribbon-shaped tissue bar are required under the phase change point.
Chinese patent publication No. CN101967581a discloses a titanium alloy with fine lamellar microstructure and a method for manufacturing the same, which is characterized in that: 1) Based on the particular alloy composition; 2) The thermal deformation temperature is selected below the silicide dissolution temperature rather than the beta transformation point, so that the existence of silicide which prevents the growth of grains in the thermal deformation process is ensured; 3) And carrying out heat treatment above the beta-phase transition point and below the silicide dissolution temperature to obtain the fine lamellar structure with the original beta-grain size below 300 mu m. Quite different from the ribbon-like target tissue and control method sought by the present invention.
Chinese patent publication No. CN109252061a discloses a method for preparing a high temperature, high thermal stability, high fracture toughness titanium alloy bar. Heating a TC25G titanium alloy cast ingot to 1100-1200 ℃, and then cogging and forging in a beta phase region by using a rapid forging machine or a hydraulic press; repeatedly upsetting and drawing-out forging by using a quick forging machine or a hydraulic press at 1030-1100 ℃, and heating the forged blank to T β -110℃～T β -20℃（T β Is TC25G titanium alloy alpha+beta/beta phase transition temperature) is repeatedly upsetted and drawn by a rapid forging machine or a hydraulic press, and finally the forged forging stock is heated to T β -110℃～T β And drawing the titanium alloy bar to the required size by using a rapid forging machine or a hydraulic press at the temperature of 30 ℃ below zero to obtain the titanium alloy bar with a uniform low-power structure of fuzzy crystals and a uniform high-power structure. The comparative example is characterized by a specific temperature above and below the phase transition pointRepeated upsetting and pulling in the degree interval can obtain bars with fuzzy low-power tissues and uniform high-power tissues. Because the microstructure control target is quite different from the ribbon-like structure to which the present invention is directed, the corresponding control means, process paths, and deformation patterns have significant differences.
Chinese patent publication No. CN111318581a discloses a method for manufacturing a large-sized titanium alloy ring with basket structure, which is characterized in that a titanium alloy blank is upset, punched and shaped at 20-50 ℃ below the beta phase transition point to obtain a ring blank; reaming the ring blank at 20-50 ℃ below the phase transition point; ring rolling and forming the ring blank after reaming at the temperature of 25-80 ℃ above the phase transition point; finally, carrying out solid solution and aging dual heat treatment to obtain the titanium alloy ring piece with the basket structure characteristics. The comparative example is characterized in that the blank is manufactured under the phase transition point, the deformation of the final stage is above the phase transition point, the aim is to obtain a rolling ring with a basket structure, and the aim is to obtain a bar stock with a fine-ribbon-shaped structure and related products thereof, which are completely different from the deformation of the final stage of the invention, which is below the phase transition point.
Chinese patent publication No. CN111235505a discloses a process for preparing a high-strength and high-toughness TC25G titanium alloy ring, which comprises the following specific steps: 1) Cogging: heating the alloy cast ingot to a certain temperature for upsetting forging, and then heating the cast ingot to a temperature 10-50 ℃ above the beta phase transformation point for deformation to obtain a blank after cogging in the beta phase region. 2) Preparing forging stock: fully deforming the blank at 100-20 ℃ below the beta phase transition point, and then heating to 10-40 ℃ above the beta phase transition point to perform high-temperature homogenization treatment; fully deforming at 100-30 ℃ below the beta phase transition point to obtain the forging stock. 3) Preparing a ring blank: punching and reaming at 60-35 ℃ below the beta transition temperature; 4) Ring rolling and forming: rolling and forming to the size at the temperature of 60-35 ℃ below the phase transition point; 5) And (3) heat treatment: the ring member is subjected to solid solution and aging heat treatment through an alpha+beta two-phase region. The TC25G titanium alloy ring prepared by the process is of a double-state structure. The remarkable characteristic of this comparative example is that after the cogging above the beta transformation point, a ring-making process of thermal deformation under the transformation point, homogenization heat treatment on the transformation point, thermal deformation under the transformation point, solid solution and aging heat treatment of the alpha + beta two-phase region is performed, and the target structure is a two-state structure. Since the homogenization heat treatment at the transformation point completely recrystallizes the thermally deformed structure, it is contrary to the object of the fine band-like structure of the present invention.
Chinese patent publication No. CN106947887a discloses a method for preparing a high temperature titanium alloy forging stock, the high temperature titanium alloy forging stock comprises the following elements in percentage by mass: al:6.5 to 7.5 percent, sn: 2-3%, zr: 6-9%, mo:0.2 to 1 percent, W:0.5 to 1.4 percent, nb:0.5 to 1.5 percent, si:0.2 to 0.3 percent of Er:0.1 to 0.3 percent and the balance of Ti; the method is characterized by comprising the following steps of: cutting an alloy cast ingot into a forging stock with the size of a mm multiplied by b mm, spraying an anti-oxidation coating, performing three-vertical multidirectional die forging, taking out the treated cast ingot after heat preservation for a min to b min at 20 to 50 ℃ above a phase transition point in a heat treatment furnace, putting the cast ingot into a heated die for forging, heating the die to a forging temperature before each forging, putting the forging stock a mm multiplied by a mm downwards each time, putting the cast ingot into a top die after the casting is put, and forming the cast ingot at a deformation rate of 0.01 to 0.03s -1 Forging the forging stock into a transverse a mm multiplied by b mm; after each die forging, heating the alloy to 20-50 ℃ above the phase transition point, and carrying out heat preservation (a-b)/tempering treatment for 2min, and sequentially forging the alloy in three vertical directions. The comparative example is characterized by multi-directional forging, i.e., deformation operations are alternately performed in three perpendicular directions of x, y, and z, while the deformation of the present invention has a significant difference in the deformation manner along a certain direction of x or y or z.
Chinese patent publication No. CN104762576a discloses a method for preparing ultra-long bars with medium specification in TC18 titanium alloy whole basket structure, which is characterized in that: 1) Cogging and forging the cast ingot at 900-1150 ℃ with forging ratio of 5.6-8.4 to obtain primary forging stock; 2) The primary forging stock is split off in step one and then fed in (T β -50)℃～(T β Forging by upsetting and drawing at the temperature of 15 ℃ below zero for 2 to 3 times, wherein the forging ratio of each forging by forging is 5.6 to 7.5, and obtaining an intermediate forging stock; t (T) β Beta phase transition temperature in degrees celsius; 3) Intermediate forging stock is in (T) β -50)℃～(T β Performing finish forging for one time at the temperature of 20 ℃ below zero to obtain a finish-forged bar; 4) Beta-zone high-temperature solid solution treatment is carried out on the precision forging bar, and the temperature is (T β +5)℃～(T β +50) DEG C, preserving heat for 0.5-2 h; 5) The finish forging bar after the beta region solid solution treatment is within the range of 300 ℃ to 450 DEG CAir cooling is carried out after heat preservation is carried out for 6 to 24 hours; 6) The finish forging bar after low-temperature aging pretreatment is subjected to a thermal deformation treatment in an alpha+beta region, and specifically comprises the steps of placing the finish forging bar in a heating furnace, and firstly (T β -40)℃～(T β And (3) preserving heat for 1-3 h within the range of-10) DEG C, cooling to 720-760 ℃ along with a furnace, preserving heat for 1-3 h, and drawing out the furnace to deform with a small deformation amount of 1-5% to obtain a bar with the whole basket structure characteristics, wherein the diameter is 50-90 mm, and the length is 2700-3800 mm. Compared with the process of the invention, the diameter of the bar is smaller, the target tissue is a basket tissue, and the steps of cogging, upsetting forging, finish forging, high-temperature solution treatment in a beta phase region, low-temperature aging pretreatment, small deformation amount elongation deformation and the like are adopted, so that the deformation process, the target tissue, bar specifications and the like are obviously different from the process of the invention.
Chinese patent publication No. CN106734796a discloses a forging method of high temperature resistant titanium alloy large-sized bar for engine, which is implemented according to the following steps: firstly, cogging and forging an ingot with three fires, wherein the first fire is used for drawing and deforming, the heating temperature is 1150-1250 ℃, the heat preservation time is 8-10 hours, and the forging ratio is controlled between 1.4-1.6; the second and third fires are upsetting and drawing deformation, the second firing heating temperature is 1090-1110 ℃, the third firing heating temperature is 1070-1090 ℃, the heating temperature is kept for 6-8 hours, the upsetting-drawing forging ratio is controlled between 2.2-3.2, and water quenching is adopted after forging; secondly, performing multi-firing equal-temperature forging on the cast ingot after the blank forging in a two-phase region, further refining and homogenizing the structure of the blank, and performing air cooling after forging; thirdly, heating the forging stock at 60-80 ℃ below the phase transition point, throwing round, and air cooling after forging to obtain the WSTi64311SC titanium alloy bar. The important effect of cogging and forging for 3 fires is emphasized in the comparative example, deformation dead zones and deformation non-uniformity are avoided by adopting inverted octave treatment, and cracking is avoided by adopting asbestos wrapping materials. The upsetting and drawing process adopted for the isothermal forging change of the two-phase region with multiple fires is completely different from the unidirectional drawing process under specific conditions and the deformation mode and effect aiming at obtaining the fine band-shaped tissue.
Chinese patent publication No. CN105734339a discloses a high temperature resistant titanium alloy bar and a method for preparing the same, wherein the bar is prepared by "three one" upsetting deformation, and the uniform and consistent ribbon-like structure of the present invention cannot be obtained due to the upsetting deformation adopted in the whole process.
Chinese patent publication No. CN106862451a discloses a titanium alloy variable temperature speed control forging method, under the variable temperature condition in the large forging blank free forging process, through comprehensive matching control of the temperature, deformation rate and deformation amount of "high temperature, high speed, large deformation", "low temperature, low speed and small deformation", dynamic recrystallization of the blank is ensured during each deformation of fire, and simultaneously, the core and edge of large thick section and multidirectional deformation uniformity and deformation grains with enough deformation can generate recrystallization and grain growth are realized through controlling the deformation amount of each hammer and the total deformation amount of each fire, thereby achieving the purposes of tissue uniformity and tissue refinement of the large thick section blank. The comparison scheme utilizes the ' that the deformed crystal grains have enough deformation to generate recrystallization and crystal grain growth ' to realize the purposes of realizing the structure uniformity and the structure refinement of a large-scale thick-section blank ', but the invention needs to avoid the effect that the deformed structure generates large-scale recrystallization and crystal grain growth so as to damage the uniformity and the continuity of the banded structure, so that the comparison example is quite opposite to the process principle of the invention, and is also south-beam north rut in specific operation.
Chinese patent publication No. CN106903249a discloses a forging method of a high-structure uniform titanium alloy cake material, which comprises performing high-temperature homogenization treatment on a titanium alloy ingot, and performing forging by forging with 1 firing; and then forging by upsetting and drawing at a temperature above and below the beta phase transition temperature, cooling by water after forging, and finally forging and forming the blank by upsetting and drawing for 2-3 times at a temperature of 30-50 ℃ below the beta phase transition temperature to obtain the cake material with the diameter of 400-700 mm and the thickness of 100-200 mm. The invention adopts the means of high-temperature homogenization treatment, water cooling after forging, reversing upsetting, diagonal drawing and the like to be matched with each other, and has reasonable design of heating and heat preservation coefficients, thereby ensuring the uniformity of the blank to the greatest extent; and the problem that a single display signal is easy to appear in finished product flaw detection can be obviously improved by adopting a two-phase region high-low-high forging process with the temperature of between 30 and 50 ℃ and between 50 and 70 ℃ and between 30 and 50 ℃ below the beta phase transition temperature. Compared with the invention, the biggest characteristic of the comparative example is that upsetting forging and two-phase zone 'high-low-high' forging processes are adopted, and means such as reversing upsetting and diagonal drawing are adopted, and the technological principle of single-direction drawing below the beta phase transition temperature is adopted, namely, the south bridge north track, the starting point and the technological path are completely different.
Chinese patent publication No. CN106180251a discloses a method for preparing TC20 titanium alloy fine grain bar, which is characterized in that heating is performed at high temperature below the phase transition point, and one-fire multi-pass precision forging is adopted; heating the blank subjected to finish forging in the step 1 below the phase transition point, and performing single-fire multi-pass rolling; finally, carrying out heat treatment, straightening and polishing to obtain the TC20 titanium alloy fine crystal bar. The method can produce the fine crystal TC20 bar with uniform transverse structure of phi 8-phi 15 mm. The comparative example is to produce the wire rod with the diameter phi 8-phi 15mm by adopting the precision forging and rolling process, and the product specification, the deformation mode, the pass deformation and the deformation efficiency are not comparable with those of the process for preparing the bar with the diameter phi 150mm by adopting a hydraulic press or a quick forging machine.
Chinese patent publication No. CN110508731a discloses a forging method for improving the structural uniformity of a TC4 titanium alloy large-size forging, which comprises selecting an ingot, peeling, cutting off a riser, and then testing the phase transition temperature; heating the treated ingot to T β Performing forging at a temperature of between 50 and 150 ℃ with two to three fires; then at a temperature T β Completing one-two fire forging at the temperature of (20-30); then at temperature T β Completing a fire at a temperature of between 30 and 50 ℃; then at temperature T β Completing three-four fire forging at 30-50 deg.c; then at T β And (5) forming and forging at the temperature of 40-50 ℃. It is characterized in that at T β The following thermal deformation intermediate process increases a heat T β Forging at a temperature of between plus and minus 30 and 50 ℃ to reduce the difference of the structure of the forging from the outside to the inside, homogenize the structure, and can be summarized as a low-high-low process, wherein the deformation structure is completely recrystallized by high fire in the middle, and the T of the invention β The following deformations are completely different until the starting point, the process strategy and the path of the bar with the ribbon-like structure are formed.
Chinese patent publication No. CN108262435a discloses a method for drawing and forging a titanium alloy bar blank, comprising the following steps: determining the feeding size L of each drawing; drawing and forging for the first time; feeding a titanium alloy bar blank; rotary forging according to the forging method described in the step 1.2 until the deformation of the L-length titanium alloy rod blank reaches A; repeating the steps 1.3 to 1.4 until the deformation of the whole titanium alloy rod blank reaches A. The comparative example shows a special titanium alloy rod blank drawing forging method, which enhances the deformation controllability, ensures the consistency of the deformation of the end part and the middle part of the rod blank, improves the process stability and is irrelevant to the deformation temperature. The invention adopts the forging method of the transformation point upper cogging forging and the transformation point lower drawing forging, the forging heating temperature under the transformation point is selected to avoid the temperature interval of large-area recrystallization and large recrystallization grain growth, thereby obtaining the titanium alloy bar with the characteristic of fine ribbon-shaped structure, and the invention has the key point of controlling the temperature and the deformation and has small drawing relation with the specific adopted mode.
Disclosure of Invention
The invention aims to provide a hot working preparation method of a large-size titanium alloy bar with uniform ribbon-shaped tissue, and the technical principle is applicable to most titanium alloys and Ti 2 And materials such as AlNb. The method is characterized in that: 1) The primary crushing of coarse columnar grains in the titanium alloy ingot is realized through thermal deformation above the beta transformation point, and meanwhile, a blank with a specific specification is prepared according to the specification of a finished bar and the control requirement of the total deformation below the beta transformation point; 2) Carrying out unidirectional drawing thermal deformation below the beta phase transition point to obtain a fine band-shaped structure with the width less than or equal to 300 mu m; 3) In order to control the size and shape of the band-shaped tissue, the heating temperature below the beta-phase transition point is selected to meet the basic condition that large-area recrystallization does not occur in the heating and thermal deformation processes; 4) The low-power tissues of the cross section and the longitudinal section of the finished bar are respectively a fuzzy tissue and a fine belt tissue, but are observed to be uniform tissues in any direction of the cross section and the longitudinal section; 5) The bar stock produced by the process has a certain degree of anisotropy, and can be directly used for preparing parts with the main stress direction parallel or approximately parallel to the ribbon-shaped tissue after simple processing; 6) The bar stock produced by the process can also be used as forging blanks of disc forgings and ring forgings; 7) Simple process and easy operation The operation is short, the flow is short, the loss is small, and the cost is low.
The technical scheme of the invention is as follows:
a hot working preparation method of a large-size titanium alloy bar with uniform thin strip-shaped tissue sequentially completes thermal deformation in two characteristic temperature ranges above and below a beta phase transition point; when deformation is carried out below the beta phase transition point, the heating temperature is selected to avoid a temperature interval in which the deformed tissue is fully recrystallized, the deformation mode is one-way drawing and the minimum deformation requirement is ensured; according to the conversion of the cross-sectional area, the diameter or equivalent diameter of the bar stock prepared by the method is more than or equal to 150mm, the cross-section low-power tissue is 1-3 grade fuzzy crystal, the longitudinal section low-power tissue is a fine band-shaped tissue, the average width of the band-shaped tissue is less than or equal to 300 mu m, and the inside of the band-shaped tissue is equiaxed, rod-shaped or elongated alpha particles plus residual beta phase.
According to the hot processing preparation method of the large-size titanium alloy bar with the uniform ribbon-shaped structure, firstly, cogging is carried out on the titanium alloy bar at a temperature of 100-200 ℃ above a beta transformation point, and forging is carried out at a temperature of 20-100 ℃ above the beta transformation point for 1-3 fires; then transferring to one-way drawing at the temperature of 30-100 ℃ under the phase change point, wherein the drawing deformation amount per time is more than or equal to 35%, and the sum of the deformation amounts under the phase change point is more than or equal to 160%; the forging equipment adopts a hydraulic press or an oil press or a quick forging machine, and the heating equipment adopts a resistance furnace with the temperature control precision of +/-10 ℃.
According to the hot processing preparation method of the large-size titanium alloy bar with the uniform ribbon-shaped structure, firstly, cogging is carried out on the titanium alloy bar at 120-200 ℃ above the beta transformation point, and 2 fires are forged at 20-100 ℃ above the beta transformation point; then transferring to one-way drawing at the temperature of 30-100 ℃ under the phase change point, wherein the drawing deformation amount per time is more than or equal to 35%, and the sum of the deformation amounts under the phase change point is more than or equal to 160%; the forging equipment adopts a hydraulic press or an oil press or a quick forging machine, and the heating equipment adopts a resistance furnace with the temperature control precision of +/-10 ℃.
According to the hot processing preparation method of the large-size titanium alloy bar with the uniform ribbon-shaped structure, firstly, cogging is carried out on the titanium alloy bar at 140-200 ℃ above the beta transformation point, and 1 fire is forged at 20-100 ℃ above the beta transformation point; then transferring to one-way drawing at the temperature of 40-100 ℃ under the phase change point, wherein the drawing deformation amount per time is more than or equal to 35%, and the sum of the deformation amounts under the phase change point is more than or equal to 160%; the forging equipment adopts a hydraulic press or an oil press or a quick forging machine, and the heating equipment adopts a resistance furnace with the temperature control precision of +/-10 ℃.
According to the hot working preparation method of the large-size titanium alloy bar with the uniform ribbon-shaped structure, firstly, forging deformation of the titanium alloy bar at 140-200 ℃ above a beta transformation point is carried out, wherein the forging deformation is not less than one forging and one drawing; then transferring to one-way drawing at the temperature of 30-100 ℃ under the phase change point, wherein the drawing deformation amount per time is more than or equal to 35%, and the sum of the deformation amounts under the phase change point is more than or equal to 160%; the forging equipment adopts a hydraulic press or an oil press or a quick forging machine, and the heating equipment adopts a resistance furnace with the temperature control precision of +/-10 ℃.
According to the hot processing preparation method of the large-size titanium alloy bar with the uniform fine strip-shaped structure, the titanium alloy bar is divided into a plurality of sections, deformation operation perpendicular to the strip-shaped structure is applied within the range of 30-100 ℃ below a phase change point, the cross section and/or the axial shape of the titanium alloy bar are changed, and a frame, beam, column or shaft part blank with linear characteristics is prepared; the heating equipment adopts a resistance furnace with the temperature control precision of +/-10 ℃.
The hot working preparation method of the large-size titanium alloy bar with the uniform ribbon-shaped tissue comprises the steps of deforming, flattening or bending, wherein the cross section is round or square, and the axial shape is straight or curved.
According to the hot working preparation method of the large-size titanium alloy bar with the uniform fine strip-shaped structure, the titanium alloy bar is divided into a plurality of sections, and alternate thermal deformation parallel to and perpendicular to the strip-shaped structure is applied within the range of 30-100 ℃ at a phase change point, and the deformation is carried out for 2-5 times, so that a disc part blank with plane characteristics is obtained; the heating equipment adopts a resistance furnace with the temperature control precision of +/-10 ℃.
According to the hot processing preparation method of the large-size titanium alloy bar with the uniform fine strip-shaped structure, the titanium alloy bar is divided into a plurality of sections, flattening, punching, reaming or ring rolling operation which is parallel or perpendicular to the strip-shaped structure is applied within the temperature range of 30-100 ℃ below the phase change point, and the deformation fire is 2-5, so that a ring part blank is prepared; the heating equipment adopts a resistance furnace with the temperature control precision of +/-10 ℃.
The design idea of the invention is as follows:
the invention provides a hot working preparation method of a large-size titanium alloy bar with a ribbon-shaped structure by taking two key control elements as main grippers. By adopting a special control process, the ribbon-shaped tissue parallel to the length direction of the bar stock is obtained. The bar material has the advantages of simple preparation process, short flow, small material loss in the hot working process, good uniformity and consistency of microstructure along the length direction, good mechanical property matching with the direction parallel to the ribbon-shaped structure, and can be used for manufacturing parts such as frames, beams, shafts, columns and the like with main stress direction parallel to the ribbon-shaped structure after simple processing; the material can also be used as a raw material of disc forgings and ring rolling pieces, and after alternating thermal deformation in the parallel-vertical strip direction for 2-5 times, high-quality forgings or ring rolling pieces can be obtained.
In a word, the forging of the high-temperature titanium alloy at home and abroad at present mainly controls parameters such as heating temperature, deformation quantity, strain rate, deformation mode, deformation heat and the like, and different combinations of the factors can form a large number of specific thermal deformation processes. Therefore, the core difference of different heat deformation processes is the design concept of the heat deformation process, namely, what kind of products are to be obtained and what kind of technical effects are to be achieved. The invention surrounds a titanium alloy bar with a ribbon-shaped structure, and is characterized in that the transverse section and the longitudinal section have a large difference in low-power structures and are high-uniformity structures, and the technical scheme is simple, easy to operate and high in efficiency, so that the problems of difficult processing, easy cracking of the titanium alloy bar, too much hot processing fire, high microstructure uniformity and uniformity control difficulty, high cost and the like of the existing titanium alloy bar can be effectively solved, and a solution is provided for the production and the expansion application of high-quality titanium alloy.
The invention has the advantages and beneficial effects that:
1. the invention has the functions of crushing the coarse as-cast structure in the cast ingot, preparing the forging blank with specified specification and forming the microstructure of the forging blank with long alpha phase, thus being convenient for subsequent process to refine crystal grains and obtain fine band-shaped structure.
2. In order to obtain a uniform banded structure, the invention avoids a temperature interval in which beta grains are recrystallized in a large range and the grains are obviously grown up when the beta phase change point is subjected to heat processing, and ensures the uniformity of the banded structure.
3. In order to obtain uniform fine ribbon-like structure, the invention ensures enough deformation when being thermally processed below beta phase transition point, so that the uniform average width of the ribbon-like structure is within 300 mu m, and the inside of the ribbon-like structure is a mixed structure composed of fine equiaxed alpha, short rod-like alpha, elongated ribbon-like alpha and residual beta phases.
4. The deformation process is simple and the efficiency is high. When the invention is used for hot working below the beta phase transition point, a single drawing deformation process is adopted instead of a upsetting process, so that the invention has the advantages of less fire, high efficiency and low cost.
5. The bar stock with the ribbon-shaped structure can be directly used for parts with the main stress direction parallel or nearly parallel to the ribbon-shaped structure after being deformed by simple processing such as changing the cross section shape, bending and the like, and the manufacturing cost of the parts is greatly reduced by utilizing good toughness matching of the direction of the parallel ribbon-shaped structure.
6. The bar stock with the ribbon-shaped structure can also be used as a disc forging blank, and the blank is manufactured after alternating thermal deformation in the directions of parallel and perpendicular ribbon-shaped structures, so that the disc part blank with low cost and high quality stability is prepared.
7. The bar stock with the ribbon-shaped structure can also be used as a blank of a ring part, and the blank of the ring part with low cost is prepared by adopting blank making, punching, reaming and ring rolling processes.
Drawings
FIGS. 1 (a) and (b) are, respectively, a bar longitudinal section ribbon-like macrostructure and a cross-section fuzzy macrostructure of the present invention.
FIGS. 2 (a) and (b) are, respectively, an insufficiently recrystallized forged high-power structure and a fully recrystallized high-power structure of a conventional process of the present invention.
Detailed Description
In a specific implementation process, the invention provides a hot working preparation method of a large-size titanium alloy bar (the diameter or equivalent diameter is more than or equal to 150 mm) with a uniform ribbon-shaped structure, and the method comprises the components of applicable alloy types, hot working process, application range and the like. The hot working process comprises the components of deformation mode, forging equipment, forging temperature, deformation amount, strain rate and the like. The hot working process comprises the following specific steps:
1) Heating the cast ingot at 100-200 ℃ above the beta phase transition point, forging for 1 time by adopting a hydraulic press or an oil press, wherein the nominal deformation is not less than 60%, and cooling by air after forging;
2) Heating the forging blank at 20-150 ℃ above the beta transformation point, forging for 1-3 times by adopting a hydraulic press or an oil press, wherein the nominal deformation of each time is not less than 60%, and cooling by air after forging;
3) Before the last fire deformation above the beta transformation point is finished, calculating the section size of the blank according to the diameter of the finished bar and the deformation requirement below the beta transformation point, and finishing the preparation of the qualified forging blank;
4) The alpha and beta two-phase regions are deformed by single elongation. Heating at 30-100 ℃ below the alpha+beta/beta phase transition point, wherein the nominal deformation of each firing time is not less than 35%, adopting a hydraulic press or a quick forging machine for hot working, and performing air cooling after forging;
5) Repeating the 4) operation until the bar control size is approached; at the final stage, small surface deformation is adopted for drawing until the diameter of a finished bar is +10-30 mm, and the surface is polished after cooling to room temperature in air;
6) Finally, forging by 1-2 fires, namely forging by a precision forging machine until the forging is close to a finished product, cooling the product in air to room temperature, and polishing the surface;
7) The bar stock prepared by the steps 1) to 6) can be divided into a plurality of sections, heated at 30-100 ℃ below the alpha+beta/beta phase transition point, subjected to flattening, bending and other operations perpendicular to the banded tissue, and changed in section and/or axial shape (straight line or curve) to prepare part blanks with linear characteristics, such as frames, beams, columns, shafts and the like;
8) The bar stock prepared by the steps 1) to 6) can be divided into a plurality of sections, alternating thermal deformation parallel to and perpendicular to the strip-shaped tissue is applied within the range of 30 ℃ to 100 ℃ at the phase change point, and the deformation heat is 2 to 5 times, so that a disc part blank with plane characteristics is prepared;
9) The bar stock prepared by adopting the steps 1) to 6) can be divided into a plurality of sections, flattening, punching, reaming, ring rolling and other operations which are parallel or perpendicular to the banded tissue are applied within the range of 30 ℃ to 100 ℃ under the phase change point, and the deformation heat is 2 to 5 heats, so that the ring part blank is prepared.
Wherein, the strain rate control is to avoid local temperature rise in the forging blank exceeding 20 ℃, and the deformation rate control upper limit can be determined through deformation simulation. By adopting the hot working process, the rod blank with the cross section of 1-3-level fuzzy crystal (rated according to GJB 2220A-2018) and the longitudinal section of uniform thin strip structure can be obtained. The total deformation firing time of the rod blank thermal processing can be controlled within 8 fires, the yield can be improved by more than 10 percent, and the method has the technical advantages of short flow, high efficiency and low cost. The bar stock prepared by the technology of the invention can be directly used for preparing part blanks of frames, beams, columns, shafts and the like with the main bearing direction parallel or nearly parallel to the banded structure after simple hot and cold processing, can also be used as forging blanks of various forgings, and can form forging structures with fine and uniform grain size after thermal deformation of 2-4 fire, thereby meeting the requirements of high-quality and low-cost titanium alloy forgings in the high-tech fields of aerospace and the like.
The invention is further elucidated below by means of examples and figures.
Example 1
The phi 710mm alloy cast ingot obtained by smelting 3 times by adopting a vacuum consumable electrode arc furnace comprises 5.8wt.% of Al, 4.0wt.% of Sn, 3.5wt.% of Zr, 0.5wt.% of Mo, 0.40wt.% of Si, 0.3wt.% of Nb, 1.0wt.% of Ta, 0.8wt.% of W, 0.05wt.% of C, less than or equal to 0.05wt.% of Fe, less than or equal to 0.15wt.% of O and the balance of Ti (alloy mark is Ti 65), and a phase transition point (T) measured by adopting a metallographic method β ) 1040 ℃. After removing surface oxide skin and cutting riser, the ingot is prepared into bar stock according to the following process: fire 1, heating temperature 1200 ℃, upsetting by a hydraulic press, drawing or drawing and upsetting, wherein phi 720mm circle, and the opposite side distance is 720mm octagon, and the nominal deformation of upsetting or drawing is more than or equal to 40%; 2 nd fire, heating temperature 1120 ℃, and obtaining octagons with opposite side distance 1160 mm after upsetting-drawing-upsetting operation of octagons with opposite side distance 720mm, wherein the nominal deformation of upsetting or drawing is more than or equal to 40%; 3 rd fire, heating temperature 1060 ℃, drawing and upsetting by a hydraulic press to obtain octagons or squares with opposite side distances of 1260mm, and upsetting or drawing nominal deformation by 40%; fire 4, heating temperature 990 ℃, drawing by a hydraulic press, and having an opposite side distance 1260mm octagon or square-900 mm octagon Or square, with a deformation of 49%; fire 5, heating temperature 990 ℃, drawing by a hydraulic press, wherein the opposite side distance is 900 mm octagon or square, the opposite side distance is 700 mm octagon or square, and the deformation is 40%; 6 th fire, heating temperature 990 ℃, drawing by a hydraulic press, wherein the distance between opposite sides is 700 mm octagons or square, the distance between opposite sides is 540 mm octagons or square, and the nominal deformation of drawing is 40%; 7 th fire, heating temperature 990 ℃, drawing by a hydraulic press, and setting the opposite side distance of 540 mm octagon or square-phi 420 mm circle with deformation amount of 40%; after cooling, the skin was removed by machining to 400mm. The final forging temperature per fire is controlled at T in consideration of the surface temperature drop in the deformation process β -200 ℃, 840 ℃.
Description: in the embodiment of the invention, the specifications of the forged blank are divided into three types of circles and octagons or squares, wherein the specifications of the circular blank are expressed by 'number + mm', and the section sizes of the octagons or squares are uniformly expressed by the distance between any two opposite sides; upsetting deformation calculation formula is delta= fatter L/L 0 The calculation formula of the elongation deformation is delta= fatter L/L 1 Wherein fatly L is the length L of the blank before deformation 0 Length L of blank after deformation 1 A difference between; the final bar section can be round, square or rectangular, and the bar section shape does not have a substantial effect on the ribbon-like texture characteristics and the deformation process. The heating mode is resistance furnace heating, and the temperature control precision is +/-10 ℃; in the following examples, the relevant expressions apply to the present description unless otherwise specified.
Example 2
The phi 710mm alloy cast ingot obtained by smelting 3 times by adopting a vacuum consumable electrode arc furnace comprises 5.8wt.% of Al, 4.0wt.% of Sn, 3.5wt.% of Zr, 0.5wt.% of Mo, 0.40wt.% of Si, 0.3wt.% of Nb, 1.0wt.% of Ta, 0.8wt.% of W, 0.05wt.% of C, less than or equal to 0.05wt.% of Fe, less than or equal to 0.15wt.% of O and the balance of Ti (alloy mark is Ti 65), and a phase transition point (T) measured by adopting a metallographic method β ) 1040 ℃. After removing surface oxide skin and cutting riser, the ingot is prepared into bar stock according to the following process: fire 1, heating temperature 1200 ℃, upsetting by a hydraulic press, drawing or drawing and upsetting, phi 710mm circle, 710mm octagon, and the nominal deformation of the upsetting or drawing is more than or equal to 40%; fire 2, heating temperature 1120 ℃, upsetting by a hydraulic press, drawing and upsetting to obtain 1200 mm octagon, wherein the upsetting or drawing deformation is more than or equal to35%; 3 rd fire, heating temperature 980 ℃, drawing by a hydraulic press, and obtaining 1200 mm octagons, 880 mm octagons or squares with deformation of 46%; fire 4, heating temperature 990 ℃, drawing out by a hydraulic press, namely 880 mm octagon or square, 640 mm octagon or square, and dividing the deformation amount into 47 percent; fire 5, heating temperature 990 ℃, drawing by a hydraulic press, and obtaining 640 mm octagons or squares 480mm octagons, wherein the deformation is 44%; heating at 990 ℃ by a 6 th fire, drawing by a hydraulic press, and forming a 480mm octagon-phi 370 mm circle with the deformation amount of 40%; after cooling, the skin was peeled off until a thickness of 350mm. Phase transition point (T) β ) The sum of total deformation of the lower 4 times of fire drawing is 177%. The final forging temperature per fire is controlled at T in consideration of the surface temperature drop in the deformation process β -200 ℃, 840 ℃.
Example 3
The phi 710mm alloy cast ingot obtained by smelting 3 times by adopting a vacuum consumable electrode arc furnace comprises 5.8wt.% of Al, 4.0wt.% of Sn, 3.5wt.% of Zr, 0.5wt.% of Mo, 0.40wt.% of Si, 0.3wt.% of Nb, 1.0wt.% of Ta, 0.8wt.% of W, 0.05wt.% of C, less than or equal to 0.05wt.% of Fe, less than or equal to 0.15wt.% of O and the balance of Ti (alloy mark is Ti 65), and a phase transition point (T) measured by adopting a metallographic method β ) 1040 ℃. After removing surface oxide skin and cutting riser, the ingot is prepared into bar stock according to the following process: fire 1, heating temperature 1200 ℃, upsetting by a hydraulic press, drawing or drawing and upsetting, wherein phi 720mm circle, and the opposite side distance is 720mm octagon, and the upsetting or drawing deformation is more than or equal to 40%; fire 2, heating temperature 1100 ℃, upsetting by a hydraulic press, drawing and upsetting, 720mm octagon, 1160 mm octagon or square, and the deformation of upsetting and drawing is more than or equal to 40%; 3 rd fire, heating temperature 980 ℃, drawing out by a hydraulic press, 1160 mm octagons or squares, 880 mm octagons or squares, and deformation amount 40%; fire 4, heating temperature 990 ℃, drawing 880 mm octagon or square to 690 mm octagon or square by a hydraulic press, and the deformation is 40%; fire 5, heating temperature 990 ℃, drawing 690 and mm octagon or square by a hydraulic press, 530 and mm octagon or square, and the deformation is 40 percent, and dividing; fire 6, heating temperature 990 ℃, drawing by a hydraulic press, wherein the deformation is 40% from 530 mm octagons or square to 410 mm octagons; 7 th fire, heating temperature 990 ℃, drawing by a hydraulic press, wherein the deformation is 40% from 410 mm octagon to phi 320 mm circle; mechanically skinning after cooling 300mm. Phase transition point (T) β ) The deformation of the steel is about 200% after 5 times of heat drawing. The final forging temperature per fire is controlled at T in consideration of the surface temperature drop in the deformation process β -200 ℃, 840 ℃.
Example 4
Using 410 mm octagon blank obtained by fire 6 in example 3, applying fire 7 for deformation, heating to 990 ℃, and drawing the octagon blank with 320 mm by a hydraulic press, wherein the deformation is 40%; applying 8 th fire deformation, heating to 980 ℃, and drawing the steel plate by a hydraulic press to form a phi 270 mm circle, wherein the deformation is 30%; after cooling, the skin is removed to a thickness of 250mm. The final forging temperature per fire is controlled at T in consideration of the surface temperature drop in the deformation process β -200 ℃, 840 ℃.
Example 5
The phi 710mm alloy cast ingot is obtained by smelting 3 times by adopting a vacuum consumable electrode arc furnace, and the components are 5.8wt.% of Al, 4.0wt.% of Sn, 3.5wt.% of Zr, 0.5wt.% of Mo and 0.40wt.% of Si; 0.3wt.% of Nb, 1.0wt.% of Ta, 0.8wt.% of W, 0.05wt.% of C, less than or equal to 0.05wt.% of Fe, less than or equal to 0.15wt.% of O and the balance of Ti (alloy brand Ti 65), and a phase transition point (T) measured by a metallographic method β ) 1040 ℃. After removing surface oxide skin and cutting riser, the ingot is prepared into bar stock according to the following process: fire 1, heating temperature 1160 ℃, upsetting by a hydraulic press, drawing and upsetting to obtain 1030 mm octagon or square, wherein the deformation of upsetting or drawing is more than or equal to 35%; fire 2, heating temperature 980 ℃, drawing out by a hydraulic press, and measuring 1030 and mm octagons or squares to 790 and mm octagons or squares, wherein the deformation is 40%; 3 rd fire, heating temperature 990 ℃, drawing by a hydraulic press, 790 mm octagon or square, 610 mm octagon or square, and deformation amount 40%; fire 4, heating temperature 990 ℃, drawing by a hydraulic press, forming 610 mm octagons or squares, forming 470 mm octagons or squares, and dividing into middle parts, wherein the deformation is 40%; fire 5, heating temperature 990 ℃, drawing by a hydraulic press, 470 mm octagons or squares, 370 mm octagons or squares, and deformation 46%; fire 6, heating temperature 990 ℃, drawing by a hydraulic press, 370 mm octagons or squares 280 mm octagons, and deformation 40%; 7 th fire, heating temperature 990 ℃, drawing by a hydraulic press, wherein the deformation is 40% from 280 mm octagons to phi 220 mm circles; after cooling, the skin was peeled off to 200mm. Phase transition point (T) β ) The sum of total deformation of 6-time heat elongation is about 240Percent of the total weight of the composition. The final forging temperature per fire is controlled at T in consideration of the surface temperature drop in the deformation process β -200 ℃, 840 ℃.
Example 6
The phi 610mm alloy cast ingot obtained by smelting 3 times by adopting a vacuum consumable electrode arc furnace comprises 5.8wt.% of Al, 4.0wt.% of Sn, 3.5wt.% of Zr, 0.5wt.% of Mo, 0.40wt.% of Si, 0.3wt.% of Nb, 1.0wt.% of Ta, 0.8wt.% of W, 0.05wt.% of C, less than or equal to 0.05wt.% of Fe, less than or equal to 0.15wt.% of O and the balance of Ti (alloy mark is Ti 65), and a phase transition point (T) measured by adopting a metallographic method β ) 1040 ℃. After removing surface oxide skin and cutting riser, the ingot is prepared into bar stock according to the following process: 1 st fire, heating to 1200 ℃, upsetting, drawing and upsetting by a hydraulic press, wherein the upsetting or drawing deformation is formed by phi 610mm round 790 mm octagon or square, and the upsetting or drawing deformation is more than or equal to 35%; fire 2, heating temperature 990 ℃, drawing by a hydraulic press, 790 and mm octagon or square, 610 and mm octagon or square, and deformation amount 40%; fire 3, heating temperature 990 ℃, drawing by a hydraulic press, and forming into a shape of 610mm octagon or square, 470 mm octagon or square, wherein the deformation is 40%; fire 4, heating temperature 990 ℃, drawing by a hydraulic press, wherein the deformation is 40% and the length is 470 and mm octagons or squares to 370mm octagons or squares, and the middle is divided; fire 5, heating temperature 990 ℃, drawing by a hydraulic press, 370mm octagons or squares 280 mm octagons, and deformation 40%; fire 6, heating temperature 990 ℃, drawing by a hydraulic press, forming a 280-mm octagon-phi 220-mm circle, and deforming 40%; after cooling, the skin was peeled off to 200mm. Phase transition point (T) β ) The deformation of the steel is about 200% after 5 times of heat drawing. The final forging temperature per fire is controlled at T in consideration of the surface temperature drop in the deformation process β -200 ℃, 840 ℃.
Example 7
The phi 610mm alloy cast ingot obtained by smelting 3 times by adopting a vacuum consumable electrode arc furnace comprises 5.8wt.% of Al, 4.0wt.% of Sn, 3.5wt.% of Zr, 0.5wt.% of Mo, 0.40wt.% of Si, 0.3wt.% of Nb, 1.0wt.% of Ta, 0.8wt.% of W, 0.05wt.% of C, less than or equal to 0.05wt.% of Fe, less than or equal to 0.15wt.% of O and the balance of Ti (alloy mark is Ti 65), and a phase transition point (T) measured by adopting a metallographic method β ) 1040 ℃. After removing surface oxide skin and cutting riser, the ingot is prepared into bar stock according to the following process: fire 1, heating temperature 1200 ℃, heading by a hydraulic pressCoarse, long or drawing and upsetting, phi 610mm circle, 610mm octagon or square, and the upsetting or drawing deformation is more than or equal to 35%; fire 2, heating temperature 990 ℃, drawing by a hydraulic press, 610mm octagons or squares to 470 mm octagons or squares, and deformation amount 40%; fire 3, heating temperature 990 ℃, drawing by a hydraulic press, wherein the deformation amount is 38% from 470 mm octagon or square to 370 mm octagon or square; fire 4, heating temperature 990 ℃, drawing by a hydraulic press, wherein the deformation is 42% and the length is 370 and mm octagons or squares to 280mm octagons or squares; fire 5, heating temperature 980 ℃, drawing by a hydraulic press, wherein the deformation is 40% from 280mm octagons or square to phi 220 mm octagons; and 6, heating at 990 ℃, drawing by a hydraulic press or rolling by a rolling mill, wherein the deformation is 40% from 220 mm octagon to phi 160-170 mm circle. After cooling, the skin is removed by peeling to 150mm. Phase transition point (T) β ) The deformation of the steel is about 200% after 5 times of heat drawing. The final forging temperature per fire is controlled at T in consideration of the surface temperature drop in the deformation process β -200 ℃, 840 ℃.
Example 8
The phi 710mm alloy cast ingot obtained by smelting 3 times by adopting a vacuum consumable electrode arc furnace comprises 5.5wt.% of Al, 3.5wt.% of Sn, 3.0wt.% of Zr, 0.8wt.% of Mo, 0.3wt.% of Si, 0.4wt.% of Nb, 0.4wt.% of Ta, less than or equal to 0.10wt.% of Fe, less than or equal to 0.15wt.% of O and the balance of Ti (alloy brand is TA 32), and the phase transition point (T) is measured by adopting a metallographic method β ) Is 1010 ℃. After removing surface oxide skin and cutting riser, the ingot is prepared into bar stock according to the following process: fire 1, heating temperature 1200 ℃, upsetting by a hydraulic press, drawing and upsetting, phi 710mm round, 940 mm octagonal or square, and upsetting or drawing deformation more than or equal to 40%; fire 2, heating temperature 960 ℃, drawing by a hydraulic press, wherein the deformation is 44% from 940 mm octagon or square to 700 mm octagon or square; fire 3, heating temperature 970 ℃, drawing by a hydraulic press, wherein the deformation amount is 43% from 700 mm octagon or square to 530 mm octagon or square; fire 4, heating temperature 970 ℃, drawing by a hydraulic press, 530 mm octagons or squares to 390mm octagons or squares, and dividing the deformation amount into 45 percent; fire 5, heating temperature 960 ℃, drawing by a hydraulic press, 390mm octagons or square-290 mm octagons, and deformation 44%; fire 6, heating temperature 970 ℃, hydraulic press drawing, 290-mm octagon → Phi 220 mm circles, deformation 44%; phase transition point (T) β ) The deformation of the steel is about 220% after 5 times of heat drawing. After cooling, the skin was peeled off mechanically to 200mm.
Example 9
The phi 710mm alloy cast ingot obtained by smelting 3 times by adopting a vacuum consumable electrode arc furnace comprises 5.8wt.% of Al, 4.0wt.% of Sn, 3.5wt.% of Zr, 0.5wt.% of Mo, 0.4wt.% of Si, 0.7wt.% of Nb, 0.05wt.% of C, less than or equal to 0.015wt.% of Fe, less than or equal to 0.075 and less than or equal to 0.15wt.% of O and the balance of Ti (alloy brand is Ti 150), and the phase transition point (T) is measured by adopting a metallographic method β ) Is 1042 ℃. After removing surface oxide skin and cutting riser, the ingot is prepared into bar stock according to the following process: fire 1, heating to 1200 ℃, applying upsetting, drawing and upsetting deformation by a hydraulic press, wherein phi 710mm round-710 mm octagonal or square, and the upsetting or drawing deformation is more than or equal to 40%; 2 nd fire, heating temperature 1070 ℃, upsetting by a hydraulic press, drawing and upsetting, wherein phi 710mm round-900 mm octagonal or square, and the upsetting or drawing deformation is more than or equal to 40%; 3 rd fire, heating temperature 980 ℃, drawing by a hydraulic press, and changing the shape of the octagon or square 900 mm to 690 mm octagon or square, wherein the deformation is 41%; fire 4, heating temperature 990 ℃, drawing 690 and mm octagon or square by a hydraulic press, 540 and mm octagon or square, and deformation 40%; fire 5, heating temperature 990 ℃, drawing by a hydraulic press, wherein the deformation is 40% and the length is 540, mm, 420, mm, and the middle part; fire 6, heating temperature 980 ℃, drawing by a hydraulic press, namely, 420 mm octagon or square 320 mm octagon, and deformation 40%; and 7 th fire, heating temperature 990 ℃, drawing by a hydraulic press, and forming 320 mm octagons to 250 mm circles, wherein the deformation is 40%. After cooling, the skin was peeled off mechanically to 230mm. Phase transition point (T) β ) The deformation of the steel is about 200% after 5 times of heat drawing.
Example 10
The phi 610mm alloy cast ingot obtained by smelting 3 times by adopting a vacuum consumable electrode arc furnace comprises 6.7wt.% of Al, 1.0wt.% of V, 2.0wt.% of Zr, 1.0wt.% of Mo and the balance of Ti (alloy brand is TA 15), and a phase change point (T) measured by adopting a metallographic method β ) Is 980 ℃. After removing surface oxide skin and cutting riser, the ingot is prepared into bar stock according to the following process: fire 1, heating temperature 1180deg.C, hydraulic press upsetting+drawing+upsetting, phi 610mm round → 840 mmThe deformation of the octagon or square shape, upsetting or drawing is more than or equal to 40%; fire 2, heating temperature 935 ℃, drawing by a hydraulic press, and obtaining 840, mm, 560, mm, or square octagon with deformation of 45%; 3 rd fire, heating temperature to 930 ℃, drawing by a hydraulic press, 560 mm octagon or square, 380 mm octagon or square, deformation of 45%, and halving; fire 4, heating temperature 930 ℃, drawing by a hydraulic press, and changing 380 mm octagon or square to 250mm octagon or square, wherein the deformation is 45%; the 5 th fire, the heating temperature is 930 ℃, the drawing is carried out by a hydraulic press or the rolling is carried out by a rolling mill, the octagon or square shape of 250mm is formed, the circle diameter is 160-170 mm, and the deformation is 45%; phase transition point (T) β ) The sum of the elongation deformation amount of the lower 4 times is about 180 percent. After cooling, the skin is removed by peeling to 150mm.
Example 11
The phi 710mm alloy cast ingot obtained by smelting 3 times by adopting a vacuum consumable electrode arc furnace comprises 6.0wt.% of Al, 2.0wt.% of Sn, 4.0wt.% of Zr, 2.0wt.% of Mo, 0.08wt.% of Si and the balance of Ti (alloy mark is TA 19), and the phase change point (T) is measured by adopting a metallographic method β ) 1002 ℃. After removing surface oxide skin and cutting riser, the ingot is prepared into bar stock according to the following process: fire 1, heating temperature 1180 ℃, upsetting by a hydraulic press, drawing or drawing and upsetting, phi 710mm round, 1030 mm octagonal or square, and upsetting or drawing deformation more than or equal to 40%; fire 2, heating temperature 950 ℃, drawing out by a hydraulic press, and measuring 1030 and mm octagons or squares to 800 and mm octagons or squares, wherein the deformation is 40%; 3 rd fire, heating temperature 950 ℃, drawing by a hydraulic press, 800 mm octagon or square, 600 mm octagon or square, and deformation 43%; fire 4, heating temperature 960 ℃, drawing by a hydraulic press, 600 mm octagons or squares to 400 mm octagons or squares, and dividing the deformation amount into about 45 percent; fire 5, heating temperature 950 ℃, drawing by a hydraulic press, 400 mm octagons or squares 270mm octagons, and deformation amount 45%; and 6, heating to 950 ℃, drawing by a hydraulic press, wherein the deformation is 34% from 270mm octagon to 220 mm circle. Phase transition point (T) β ) Pulling out about 207% of deformation amount after 4 times of fire, cooling, and peeling to 200mm.
Example 12
The round bar stock with the thickness of 200-400 mm obtained in the embodiments 1-6 and 8-11 is cut into blanks with specific length according to the requirement, then the blanks are heated at the temperature of 30-100 ℃ under the phase change point, 2-4 groups of alternating thermal deformation of vertical strip-shaped tissues and parallel strip-shaped tissues is applied, and the single deformation of the vertical and/or parallel strip-shaped tissues is more than or equal to 35%, so that prefabricated blanks of disc-shaped parts are obtained; heating at the transformation point of 30-100 ℃, and carrying out isothermal forging or hot forging or free forging to obtain a part blank.
Example 13
After the round bar stock with the diameter of 200-400 mm obtained in the embodiments 1-6 and 8-11 is cut into bar blanks with specific lengths according to the requirement, heating at 30-100 ℃ at a first fire phase transition point, applying thermal deformation of a vertical strip-shaped structure, flattening the outer side surface of the circumference, controlling the single deformation to be more than 30%, and punching when the round bar stock is hot or punching after furnace returning heating; and heating at the second fire transformation point of 30-100 ℃, and reaming or reaming and ring rolling or direct ring rolling to obtain the annular part blank.
Example 14
After the 150 mm round bar stock obtained in the embodiment 7 and/or 10 is cut into bar blanks with specific length according to the requirement, heating is carried out at the temperature of 30-100 ℃ below the phase transition point, and radial deformation of the bar stock or bending deformation perpendicular to the strip-shaped tissue is applied, wherein the deformation can be adjusted according to the size of the part blank, so that bar-shaped blank with different section shapes can be obtained; the bar-shaped blank is bent along the length direction by adopting a specific tool to manufacture part blanks with different curvatures and with the characteristics of frames, beams and columns.
As can be seen from the low-power tissue of the longitudinal section of the bar in the invention shown in the figure 1 (a), the bar has a characteristic of a fine banded tissue along the length direction of the bar, namely, the microstructure is uniformly elongated into a banded shape along the length direction of the bar, and the width of the banded tissue is within 300 mu m; as can be seen from the cross-sectional low-power tissue of fig. 1 (b), no trace of He Bianxing is seen in the cross-section perpendicular to the strip-like tissue because the longitudinal-sectional low-power tissue is an elongated fine strip-like tissue; in addition, the width of the band-shaped tissue is controlled within 300 mu m, so that the cross section macrostructure is completely blurred crystal, and clear crystal or semi-clear crystal phenomenon caused by coarse crystal or incomplete deformation coarse crystal is not found.
FIG. 2 (a) is a typical microstructure of a bar according to the invention, which is seen to consist of elongated or equiaxed fine alpha grains and a residual beta phase, the as-forged microstructure being free of significant recrystallization; fig. 2 (b) shows a high-power structure of a bar in the conventional process, because of the influence of higher deformation temperature, more deformation heat, lower deformation efficiency and the like, the forged high-power structure is very similar to the heat-treated high-power structure, and is a more typical two-state structure, which indicates that the bar undergoes more obvious recrystallization and grain growth in the deformation process and the cooling process after deformation.
In summary, from the viewpoints of efficient connection between titanium alloy ingots and finished part blanks, simplification of the process, cost reduction, improvement of product quality stability and the like, the invention provides a hot working manufacturing method of a titanium alloy bar with uniform fine strip structure characteristics according to the low-cost and high-quality stability requirements of the fields of aviation, aerospace and the like on the basis of experiments and theoretical exploration through research and analysis of the conventional titanium alloy hot working process and product application reported in application and/or literature, wherein the hot working process is tightly designed around the aim of obtaining the fine strip structure, and the aim of the deformation process above a phase change point is to convert the conventional refined columnar crystal structure and original beta crystal grains into broken columnar crystal structures, so that a forging blank meeting the minimum deformation requirement is provided for thermal deformation below the phase change point; the deformation characteristics below the phase transition point are simple elongation, the premise of deformation temperature selection is that large-area recrystallization does not occur, the obvious growth of crystal grains is avoided, the deformation process is obviously simplified, the process control is simpler, the controllable degree of the quality stability of the bar is higher, and the obtained bar can be directly used for preparing a bar part blank with the main stress direction parallel or nearly parallel to a strip-shaped tissue after simple processing; the blank can also be used as an original blank for preparing cake-shaped forging blanks represented by aerospace disc parts and annular part blanks represented by parts such as a casing, a drum and the like, and has wide application. The hot working manufacturing method of the titanium alloy bar stock with the uniform ribbon-shaped tissue characteristic is suitable for most of titanium-based materials which can be hot worked by forging and rolling methods currently and in the future in technical principle.

Claims (8)

1. A hot working preparation method of a large-size titanium alloy bar with uniform thin strip-shaped tissue is characterized in that the thermal deformation is completed in two characteristic temperature intervals above and below a beta phase transition point in sequence; when deformation is carried out below the beta phase transition point, the heating temperature is selected to avoid a temperature interval in which the deformed tissue is fully recrystallized, the deformation mode is one-way drawing and the minimum deformation requirement is ensured; according to the conversion of the cross-sectional area, the diameter or equivalent diameter of a bar stock prepared by the method is more than or equal to 150mm, the cross-section macroscopic tissue is 1-3 grade fuzzy crystal, the longitudinal section macroscopic tissue is a fine band-shaped tissue, the average width of the fine band-shaped tissue is less than or equal to 300 mu m, and the interior of the fine band-shaped tissue is equiaxed, rod-shaped or elongated alpha particles and residual beta phase;
firstly, cogging a titanium alloy bar at 100-200 ℃ above a beta transformation point, and forging for 1-3 fires at 20-100 ℃ above the beta transformation point; then transferring to one-way drawing at the temperature of 30-100 ℃ under the beta phase transition point, wherein the drawing deformation amount per fire is more than or equal to 35%, and the sum of the deformation amounts under the beta phase transition point is more than or equal to 160%; the forging equipment adopts a hydraulic press or an oil press, and the heating equipment adopts a resistance furnace with the temperature control precision of +/-10 ℃.
2. The hot working preparation method of the large-size titanium alloy bar with the uniform ribbon-shaped structure, which is characterized in that firstly, the titanium alloy bar is cogged at 120-200 ℃ above the beta transformation point, and is forged at 20-100 ℃ above the beta transformation point for 2 fire; then the steel is transferred into a beta phase transformation point for unidirectional drawing at 30-100 ℃, the drawing deformation amount per fire is more than or equal to 35%, and the sum of the deformation amounts under the beta phase transformation point is more than or equal to 160%.
3. The hot working preparation method of the large-size titanium alloy bar with the uniform ribbon-shaped structure according to claim 1, which is characterized in that firstly, the titanium alloy bar is cogged at 140-200 ℃ above a beta transformation point, and is forged at 1 fire at 20-100 ℃ above the beta transformation point; then the single-way drawing is carried out at the temperature of 40-100 ℃ under the beta phase transition point, the drawing deformation amount per fire is more than or equal to 35%, and the sum of the deformation amounts under the beta phase transition point is more than or equal to 160%.
4. The hot working method for preparing a large-size titanium alloy bar with uniform and fine strip-shaped structures according to claim 1, wherein the titanium alloy bar is firstly subjected to forging deformation of at least one heading and one drawing at 140-200 ℃ above a beta transformation point; then the steel is transferred into a beta phase transformation point for unidirectional drawing at 30-100 ℃, the drawing deformation amount per fire is more than or equal to 35%, and the sum of the deformation amounts under the beta phase transformation point is more than or equal to 160%.
5. A method of hot working a large-size titanium alloy bar having a uniform fine ribbon-like structure according to any one of claims 1 to 4, wherein the titanium alloy bar is divided into a plurality of segments, and a deformation operation perpendicular to the fine ribbon-like structure is applied at a β -transformation point within a range of 30 ℃ to 100 ℃ to change the cross section and/or axial shape thereof, thereby producing a frame, beam, column or shaft part blank having linear characteristics; the heating equipment adopts a resistance furnace with the temperature control precision of +/-10 ℃.
6. The method for hot working a large-sized titanium alloy bar having a uniform ribbon-like structure according to claim 5, wherein the deforming operation is flattening or bending, the cross section is circular or square, and the axial shape is a straight line or curve.
7. The hot working preparation method of the large-size titanium alloy bar with uniform fine-ribbon-like structure according to one of claims 1 to 4, wherein the titanium alloy bar is divided into a plurality of sections, and alternating heat deformation parallel to and perpendicular to the fine-ribbon-like structure is applied within the range of 30 ℃ to 100 ℃ below a beta phase transition point, and the deformation is carried out for 2 to 5 times, so as to obtain a disc part blank with plane characteristics; the heating equipment adopts a resistance furnace with the temperature control precision of +/-10 ℃.
8. The hot working preparation method of the large-size titanium alloy bar with uniform fine-ribbon-like structure according to one of claims 1 to 4, which is characterized in that the titanium alloy bar is divided into a plurality of sections, flattening, punching or reaming operation which is parallel or perpendicular to the fine-ribbon-like structure is applied within the range of 30 ℃ to 100 ℃ below the beta phase transition point, and the deformation fire is 2 to 5 fires, so as to prepare a ring part blank; the heating equipment adopts a resistance furnace with the temperature control precision of +/-10 ℃.
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