CN114101556B - Processing method for preparing TB8 titanium alloy sheet in short process - Google Patents
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- B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
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- B21B1/38—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling sheets of limited length, e.g. folded sheets, superimposed sheets, pack rolling
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- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
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- B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
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- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J1/00—Preparing metal stock or similar ancillary operations prior, during or post forging, e.g. heating or cooling
- B21J1/06—Heating or cooling methods or arrangements specially adapted for performing forging or pressing operations
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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
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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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- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21K—MAKING FORGED OR PRESSED METAL PRODUCTS, e.g. HORSE-SHOES, RIVETS, BOLTS OR WHEELS
- B21K29/00—Arrangements for heating or cooling during processing
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
- C21D1/30—Stress-relieving
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- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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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
- C22F1/02—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working in inert or controlled atmosphere or vacuum
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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
- C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
- C22F1/18—High-melting or refractory metals or alloys based thereon
- C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/38—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling sheets of limited length, e.g. folded sheets, superimposed sheets, pack rolling
- B21B2001/386—Plates
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- B21B2261/02—Transverse dimensions
- B21B2261/04—Thickness, gauge
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- B21B2261/20—Temperature
Abstract
The invention relates to a processing method for preparing a TB8 titanium alloy sheet in a short process, which comprises the following steps: the method comprises the following steps: heating the cast ingot to 1100-1200 ℃, forging for one time by one fire, and cooling by water to obtain a forged blank after cogging; step two: heating the blank in the step one to 1050-1100 ℃, and performing reverse forging for one fire to obtain a plate blank for hot rolling; step three: carrying out first hot rolling, and obtaining a first hot rolled plate blank after water cooling; step four: performing second hot rolling to obtain a second hot-rolled plate blank; step five: carrying out intermediate recrystallization annealing treatment; step six: carrying out third hot rolling to obtain a third hot-rolled plate blank; step seven: carrying out intermediate annealing treatment; step eight: performing cold rolling to obtain a cold-rolled sheet; step nine: and carrying out finished product annealing treatment to obtain the TB8 titanium alloy sheet with the thickness of 0.3-1.0 mm. The preparation method has the advantages that the technical scheme is complete, the integral preparation process of the TB8 titanium alloy sheet is simplified by the processes of cogging forging, hot rolling, recrystallization annealing, cold rolling and the like from the beginning of ingot casting, the process is stable and reliable, the prepared TB8 titanium alloy sheet has uniform structure, fine crystal grains and good performance consistency, and the sheet meeting the requirements of related technical indexes can be produced in batches.
Description
Technical Field
The invention discloses a short-process machining method for preparing a TB8 titanium alloy sheet, and belongs to the technical field of titanium alloy material machining.
Background
The TB8 (Ti-15 Mo-2.7Nb-3A1-0.2 Si) titanium alloy is a novel metastable beta-type titanium alloy, adopts more Mo element instead of V element, greatly improves the oxidation resistance and corrosion resistance of the alloy, and has better cold rolling and cold forming capabilities similar to those of the Ti-15-3 (Ti-15V-3 Cr-3Sn-3A 1) alloy. The TB8 titanium alloy has high oxidation resistance and hot oil corrosion resistance, compared with Ti-15-3, the oxidation resistance of the TB8 titanium alloy is improved by about 100 times, and the TB8 titanium alloy has good high-temperature performance and can work for a long time at 540 ℃. From the aspects of reducing wood formation, reducing weight, improving performance and the like, the beta-21S titanium Alloy is used for replacing part of anti-combustion titanium Alloy C (nominal component: ti-35V-15 Cr) for an F119 engine in the United states, and the maximum working temperature of the engine can reach 550 ℃. In addition, boeing has chosen the beta-21S alloy as the liner and nozzle material for 777.
Compared with the common beta titanium alloy, the TB8 titanium alloy has a plurality of outstanding advantages, firstly, the TB8 titanium alloy has high strength and good strength-toughness matching performance, and the tensile strength can reach above 1450MPa through aging strengthening. And the cold working property is excellent, the cold working property can be rolled into sheets and foils, and the cold deformation can reach 72 to 85 percent under the condition of no intermediate annealing. At the same time, cold rolling with deformation amount over 80% can be performed under the condition of solid solution.
Therefore, the TB8 titanium alloy can be used for manufacturing airplane structural parts or engine structural parts with temperature requirements, honeycombs, fastening hydraulic pipes and the like, and can also be used as matrixes, castings and the like of metal matrix composite materials.
At present, the domestic research on the TB8 titanium alloy mainly focuses on the influence of different thermomechanical processes, such as forging temperature, deformation degree, cooling speed after forging and the like, on the structure performance of the alloy. In the aspect of plate processing, the method focuses on the process method of hot rolling and cold rolling of the plate to prepare the sheet, and the adopted rolled plate blank is usually subjected to repeated drawing deformation for 3-5 times of fire so as to achieve the purpose of refining the plate blank structure, so that the process flow is increased, the yield of the material is low, and the cost is high.
Disclosure of Invention
The invention provides a processing method for preparing a TB8 titanium alloy sheet in a short process aiming at the defects in the prior art, and aims to shorten the preparation process, effectively reduce the cost, simultaneously ensure simple operation and stable and controllable process and meet the requirements of related technical indexes by effectively combining the cogging forging and the subsequent rolling process of ingot casting.
The technical scheme of the invention is determined on the basis that:
the processing method for preparing the TB8 titanium alloy sheet by the short process, which is disclosed by the technical scheme of the invention, comprises the following steps of:
heating a TB8 titanium alloy ingot to 1100-1200 ℃, forging for one time in the streamline direction of the ingot, cooling by water, and then carrying out surface grinding treatment to obtain a forged blank after cogging, wherein the finish forging temperature is not lower than 850 ℃;
step two, heating the forging stock in the step one to 1050-1100 ℃, and performing one-time reverse forging on the forging stock in a direction vertical to the flow line of the forging stock, wherein the finish forging temperature is not lower than 800 ℃ to obtain a hot-rolled plate blank with the thickness of 120-200 mm;
step three, directly keeping the hot rolled plate blank in the step two at the temperature of 950-1000 ℃ for 50-80 min without cooling, then carrying out first fire rolling, carrying out surface grinding treatment after water cooling to obtain a first fire rolled plate blank with the thickness of 25-50 mm; the rolling direction of the first hot rolling is one-way rolling;
step four, preserving the heat of the first hot rolled plate blank in the step three in a heating furnace at the temperature of 900-950 ℃ for 30-60 min, then carrying out second hot rolling, and carrying out surface grinding treatment after air cooling to obtain a second hot rolled plate blank with the thickness of 6-15 mm; the rolling direction of the second hot rolling is alternately vertical and parallel to the rolling direction of the first hot rolling;
step five, carrying out recrystallization annealing treatment on the second hot-rolled plate blank in the step four;
step six, preserving the second hot rolled plate blank subjected to the recrystallization annealing treatment in the step five in a heating furnace at the temperature of 850-900 ℃ for 5-15 min, then carrying out third hot rolling, and carrying out surface grinding treatment after water cooling to obtain a third hot rolled plate blank with the thickness of 1.5-4.0 mm; the rolling direction of the third hot rolling is parallel to that of the first hot rolling;
step seven, performing intermediate argon-filling on-line continuous annealing treatment on the third hot rolled plate blank in the step six;
step eight, sending the third rolled plate blank subjected to the intermediate annealing treatment in the step seven into a cold rolling mill for cold rolling to obtain a cold-rolled plate with the thickness of 0.3-1.0 mm; the rolling direction of the cold rolling is parallel to that of the third hot rolling.
And step nine, carrying out argon-filling on-line continuous annealing treatment on the cold-rolled sheet obtained in the step eight to obtain the TB8 titanium alloy sheet with the thickness of 0.3-1.0 mm, the room-temperature tensile strength of not less than 900MPa and the elongation of not less than 12%.
In the implementation, the upsetting times of the one-time forging in the step one are three-upsetting and three-drawing, the single-time upsetting deformation amount is 35-50%, the elongation deformation amount per hammer is 10-20%, and the reduction rate is 10-15 mm/s.
In the implementation, the upsetting and drawing times of the one-time forging in the step two are two upsetting and two-time drawing, the single-time upsetting deformation amount is 50-65%, the elongation deformation amount per hammer is 15-25%, and the reduction rate is 15-20 mm/s.
In the implementation, in the third step, the number of passes of the first hot rolling is 5-8, and the deformation amount of each pass is 10-25%.
In the fourth step, the number of passes of the second hot rolling is 5-7, the deformation of each pass is 10% -30%, wherein the rolling direction of the first 2-3 passes is vertical to the rolling direction of the first hot rolling, and the rolling direction of the subsequent passes is parallel to the rolling direction of the first hot rolling.
In the implementation, the temperature of the recrystallization annealing treatment in the fifth step is 800-900 ℃, and the heat preservation time is 10-20 min.
In the implementation, in the sixth step, the number of times of the third hot rolling is 4-6 times, and the deformation amount of each time is 15-30%.
In the implementation, the annealing temperature of the argon-filled online annealing treatment in the step seven is 850-900 ℃, the traveling speed of the plate is 0.05-0.15 m/min, the purity of the argon filled in the furnace is more than or equal to 99.99%, and the micro positive pressure of the inert gas on the basis of overflowing is kept.
In the eighth step, the cold rolling is completed by 5 to 8 passes, and the deformation amount of each pass is 10 to 30 percent.
In the implementation, the annealing temperature of the finished product argon-filling online annealing treatment in the ninth step is 820-850 ℃, the traveling speed of the plate is 0.05-0.15 m/min, the purity of the argon filled in the furnace is more than or equal to 99.99%, and the micro positive pressure of the inert gas overflow is kept.
In the technical scheme of the invention, in view of the requirement that the deformation of the TB8 titanium alloy sheet can reach more than 99% from an initial cast ingot with a diameter close to phi 600mm to a sheet with a diameter within 1mm, the cogging forging and the subsequent rolling process of the cast ingot are combined, the process steps are reduced and the preparation process is optimized by controlling the process parameters of heating temperature, upsetting deformation, rolling pass deformation, reverse rolling and the like and reasonably utilizing the action mechanism of dynamic recrystallization grain refinement, on the basis of ensuring the texture performance of the TB8 titanium alloy sheet, so that the integral yield is improved, and the argon-filled online annealing treatment is adopted, so that the surface oxidation problem of the sheet in the annealing process is avoided, the subsequent alkali, acid pickling and other processes are saved, the environment is effectively protected, and the production cost is saved. Therefore, the technology for preparing the TB8 titanium alloy from the ingot to the sheet, which is provided by the technical scheme of the invention, shortens the preparation process, solves the bottleneck problem of high price of the TB8 titanium alloy sheet, and meets the urgent need of domestic industrial production. The features and functions of the technical measures in the technical solution of the present invention are explained as follows:
(1) In the first step, the ingot is heated to a high-temperature area of 1100-1200 ℃, and repeated upsetting deformation is carried out for one fire in the flow line direction, so that the coarse beta grain structure of the ingot is crushed and homogenized, the difference of structure and performance caused by ingot smelting is eliminated, and the consistency and stability of the process are improved. And after the forging is finished, water cooling quenching is rapidly carried out, coarsening of the strip alpha phase which is crushed preliminarily in the cooling process is inhibited, and a fine and uniform lamellar structure is obtained. Considering that the titanium alloy has poor plasticity, the pier drawing frequency is strictly controlled not to exceed three piers and three piers, and simultaneously the single pier upsetting deformation, the per-hammer pressing amount and the pressing rate are matched;
(2) In the second step, repeated upsetting deformation is carried out on the cast ingot in the direction vertical to the streamline direction of the forging stock, so that crystal grains vertical to the flow direction of the forging stock are crushed and refined, the anisotropy of the titanium alloy forging stock is avoided, the forging temperature is reduced, and the comprehensive balance of dynamic recrystallization and crystal grain nucleation length is controlled;
(3) In the third step, the plate blank is subjected to one-time large deformation rolling in a high-temperature area, the coarse grain structure is further crushed, and meanwhile, the plate blank is subjected to water cooling in the third step. The thickness of the rolled plate blank is 40-50 mm, so that the thickness range can meet the requirement of better hardenability of water-cooling quenching, can ensure that the water-cooling quenching can not generate buckling deformation, does not need to additionally increase complicated procedures such as shape correction, grinding, shearing and the like, greatly simplifies the production procedures, reduces the workload and improves the yield of the plate.
(4) In the fourth step, the reversing rolling process is adopted in the first 2-3 passes of the plate blank, the conventional rolling process is carried out in the subsequent passes, the effect is to fully crush the crystal boundary alpha phase and the strip-shaped alpha phase of the plate to obtain the equiaxial fine crystal structure, the anisotropy of the titanium alloy plate blank is eliminated through the reversing rolling of 2-3 passes, the deformation in two rolling directions is completed through the rolling of one fire, and the comprehensive balance of dynamic recrystallization and the nucleation length of crystal grains is controlled in the two directions.
(5) In the fifth step, the titanium alloy plate blank is subjected to recrystallization annealing treatment, so that relatively coarse deformation grains generated by large deformation of the plate blank rolled in the previous two times are converted into distortion-free grains again through static recrystallization, the grain structure is further refined, the process plasticity is improved, and the deformation cogging tendency and the buckling deformation of the plate are reduced. Meanwhile, the residual stress generated by uneven cooling, uneven deformation and the like after the first two times of fire rolling is eliminated, and the surface quality and the dimensional accuracy of the plate blank are improved.
(6) And step six, the rolling temperature is further reduced, the equiaxial alpha is more fully refined and homogenized, equiaxial fine-grained structures are obtained, and meanwhile, the size requirement required by cold rolling is met.
(7) And seventhly, performing intermediate argon-filled on-line continuous annealing treatment on the plate blank, so that on one hand, a distortion-free equiaxial structure required by subsequent cold rolling and plate finished products can be obtained, and the residual stress in the plate is eliminated. On the other hand, because the argon-filling online annealing treatment is adopted, the surface oxidation problem of the plate in the annealing process is avoided, the subsequent processes of alkali, acid washing and the like are saved, the environment is effectively protected, and the production cost is saved.
The technical measures are based on good fracture toughness and excellent cold processing performance of the TB8 titanium alloy, cogging forging and subsequent rolling processes of the TB8 titanium alloy are combined, repeated upsetting forging cogging and 2 hot rolling which need 3-5 fire times of a hot rolling plate blank in the traditional process are reduced to 2 repeated upsetting forging cogging and 2 hot rolling, the purpose of equally refining the crystal grain structure of the plate blank is achieved, the crystal grain structure is further refined through subsequent recrystallization annealing, the process steps are reduced, the preparation flow is optimized, and therefore the integral yield is improved. Meanwhile, the annealing processes before and after the subsequent cold-rolled sheet adopt argon-filled on-line annealing treatment, so that the surface oxidation problem of the sheet in the annealing process is avoided, the subsequent processes of alkali, acid washing and the like are saved, the environment is effectively protected, the preparation process is shortened, and the production cost is greatly saved.
Drawings
FIG. 1 is a photograph showing the microstructure of a thin TB8 titanium alloy sheet obtained in example 1
FIG. 2 is a microstructure photograph of a thin TB8 titanium alloy plate obtained in example 2
FIG. 3 is a microstructure photograph of a thin TB8 titanium alloy plate obtained in example 3
Detailed Description
The technical scheme of the invention is further detailed in the following by combining the drawings and the embodiment:
example 1
The method for preparing the TB8 titanium alloy plate with the thickness of 0.7mm comprises the following specific steps:
the method comprises the following steps: heating the qualified TB8 titanium alloy ingot to 1180 ℃, and performing three-pier three-drawing forging in the streamline direction of the ingot, wherein the single-pier upsetting deformation amounts are 45%, 45% and 40% respectively, the drawing reduction per hammer is 15%, and the drawing reduction rate is 13mm/s. The finish forging temperature is 920 ℃, then the steel plate is soaked in water and rapidly cooled to the room temperature, and a cogging forged blank is obtained through surface grinding treatment;
and step two, heating the forging stock in the step one to 1070 ℃, and performing two-pier two-drawing reverse forging in the direction vertical to the streamline direction of the forging stock, wherein the single-time upsetting deformation is 55 percent and 60 percent respectively, the drawing reduction per hammer is 20 percent, and the pressing rate is 18mm/s. The final forging temperature is 850 ℃, and a hot rolled plate blank with the thickness of 180mm is obtained;
step three, directly keeping the forging stock in the step two in a heating furnace at 980 ℃ for 70min without cooling, carrying out first hot rolling for 7 times, keeping the rolling direction of the first hot rolling as unidirectional rolling, and respectively keeping the deformation of each time as follows: 12%,18%,18%,20%,20%,16%,16%, then soaking in water to rapidly cool to room temperature, and obtaining a first hot-rolled plate blank with the thickness of 48mm through surface grinding treatment;
step four: and (3) preserving the heat of the first hot-rolled plate blank in the step (III) in a heating furnace at 920 ℃ for 50min, and performing 6-pass second fire rolling, wherein the rolling direction of the first 3 passes is vertical to that of the first hot rolling, the rolling directions of the other 3 passes are parallel to that of the first hot rolling, and the deformation of each pass is respectively as follows: 16%,20%, 22%,25%,20%,20%, air cooling, and then performing surface grinding treatment to obtain a second hot-rolled slab with the thickness of 12 mm;
step five: placing the fourth hot-rolled plate blank in the step four into an annealing furnace, preserving heat for 18min at the temperature of 850 ℃, and cooling in the air;
step six: and (4) preserving the heat of the second hot-rolled plate blank in the fifth step in a heating furnace at 880 ℃ for 12min, performing 5-pass third hot rolling, keeping the rolling direction of the third hot rolling parallel to the rolling direction of the first hot rolling, and respectively setting the deformation of each pass as follows: 20%,22%,24%,20%,16%, air cooling, and then performing surface grinding treatment to obtain a third hot-rolled plate blank with the thickness of 3.8 mm;
step seven: and sixthly, annealing the third hot-rolled plate blank in the step six in a continuous annealing furnace filled with high-purity argon, wherein the annealing temperature is 860 ℃, and the plate traveling speed is 0.10m/min.
Step eight: and (4) feeding the third hot-rolled plate blank in the step seven into a cold rolling mill, carrying out 6-pass cold rolling, keeping the cold rolling direction parallel to the rolling direction of the third hot rolling, and respectively setting the deformation of each pass as follows: 20%,25%, 28%,29%,25%,20% to obtain a cold-rolled sheet having a thickness of 0.7 mm.
Step nine: and (5) annealing the finished product of the cold-rolled sheet obtained in the step eight in a continuous annealing furnace filled with high-purity argon, wherein the annealing temperature is 840 ℃ and the traveling speed of the sheet is 0.08m/min.
The tensile strength of the TB8 titanium alloy sheet prepared by the embodiment at room temperature is 953MPa, the elongation is 14.1%, and the microstructure is shown in figure 1 and meets the requirements of related technical standards.
Example 2
The method for preparing the TB8 titanium alloy plate with the thickness of 0.5mm comprises the following specific steps:
the method comprises the following steps: heating the qualified TB8 titanium alloy ingot to 1150 ℃, and performing three-pier three-drawing forging in the streamline direction of the ingot, wherein the single-pier upsetting deformation amounts are 40%, 45% and 45%, the drawing reduction per hammer is 12%, and the pressing rate is 12mm/s. The finish forging temperature is 930 ℃, then the steel plate is soaked in water and rapidly cooled to room temperature, and a forged blank after cogging is obtained through surface grinding treatment;
and step two, heating the forging stock in the step one to 1080 ℃, and performing two-pier two-drawing reverse forging in the direction vertical to the streamline direction of the forging stock, wherein the single-pier upsetting deformation amounts are 50% and 60%, the drawing reduction per hammer amount is 22%, and the drawing reduction rate is 18mm/s. The finish forging temperature is 820 ℃, and a hot rolled plate blank with the thickness of 160mm is obtained;
step three, directly keeping the forging stock in the step two in a heating furnace at 960 ℃ for 60min without cooling, carrying out first hot rolling for 6 times, keeping the rolling direction of the first hot rolling as unidirectional rolling, and respectively keeping the deformation of each time as follows: 18%,20%,22%,22%,22%,16%, then soaking in water to rapidly cool to room temperature, and carrying out surface grinding treatment to obtain a first hot-rolled plate blank with the thickness of 42 mm;
step four: and (3) preserving the heat of the first hot-rolled plate blank in the step (III) for 45min in a heating furnace at 920 ℃, and performing 7-pass second fire rolling, wherein the rolling direction of the first 3 passes is vertical to that of the first hot rolling, the rolling directions of the other 4 passes are parallel to that of the first hot rolling, and the deformation of each pass is respectively as follows: 15%, 18%,22%,24%,20%,20%,10%, air cooling, and performing surface grinding treatment to obtain a second hot-rolled slab with the thickness of 10 mm;
step five: placing the fourth hot-rolled plate blank in the step four into an annealing furnace, preserving heat for 16min at the temperature of 860 ℃, and cooling in the air;
step six: and (4) preserving the heat of the second hot-rolled plate blank in the fifth step for 10min in a heating furnace at 880 ℃, performing 6-pass third hot rolling, keeping the rolling direction of the third hot rolling parallel to the rolling direction of the first hot rolling, and respectively setting the deformation of each pass as follows: 15%,20%,22%,25%,20%,12%, air cooling, and performing surface grinding treatment to obtain a third hot-rolled plate blank with the thickness of 2.8 mm;
step seven: and sixthly, annealing the third hot-rolled plate blank in the step six in a continuous annealing furnace filled with high-purity argon, wherein the annealing temperature is 870 ℃, and the plate traveling speed is 0.10m/min.
Step eight: and (3) feeding the third hot-rolled plate blank in the step seven into a cold rolling mill, carrying out 6-pass cold rolling, keeping the cold rolling direction parallel to the rolling direction of the third hot rolling, and respectively setting the deformation of each pass as follows: 20%,23%, 28%,28%,25%,25% to obtain a cold-rolled sheet having a thickness of 0.5 mm.
Step nine: and (5) annealing the finished product of the cold-rolled sheet obtained in the step eight in a continuous annealing furnace filled with high-purity argon, wherein the annealing temperature is 830 ℃, and the running speed of the sheet is 0.10m/min.
The tensile strength of the TB8 titanium alloy sheet prepared by the embodiment at room temperature is 964MPa, the elongation is 15.6%, and the microstructure is shown in FIG. 2, so that the sheet meets the requirements of related technical standards.
Example 3
The method for preparing the TB8 titanium alloy plate with the thickness of 0.3mm comprises the following specific steps:
the method comprises the following steps: heating the qualified TB8 titanium alloy ingot to 1190 ℃, and performing three-pier three-drawing forging in the streamline direction of the ingot, wherein the single-pier upsetting deformation amounts are respectively 38%, 45% and 40%, the drawing reduction per hammer amount is 16%, and the pressing rate is 12mm/s. The finish forging temperature is 900 ℃, then the steel plate is soaked in water and rapidly cooled to room temperature, and a cogging forged blank is obtained through surface grinding treatment;
and step two, heating the forging stock in the step one to 1060 ℃, and performing two-pier two-drawing reverse forging in the direction vertical to the streamline direction of the forging stock, wherein the single-pier upsetting deformation amounts are 60% and 55%, the drawing reduction amount per hammer is 20%, and the drawing reduction rate is 16mm/s. The final forging temperature is 840 ℃, and a hot rolled plate blank with the thickness of 130mm is obtained;
step three, directly preserving the temperature of the forging stock in the step two for 50min in a 980 ℃ heating furnace without cooling, carrying out 8-pass first hot rolling, and keeping the rolling direction of the first hot rolling as unidirectional rolling, wherein the deformation of each pass is respectively as follows: 12%,15%,16%,20%,20%,20%,16%,15%, then soaking in water to rapidly cool to room temperature, and performing surface grinding treatment to obtain a first hot-rolled plate blank with the thickness of 30 mm;
step four: and (3) preserving the heat of the first hot-rolled plate blank obtained in the step (three) for 45min in a heating furnace at 900 ℃, and performing 6-pass second fire rolling, wherein the rolling direction of the first 2 passes is vertical to the rolling direction of the first hot rolling, the rolling directions of the other 6 passes are parallel to the rolling direction of the first hot rolling, and the deformation of each pass is respectively as follows: 16%,20%, 25%,25%,28%,14%, air cooling, and then performing surface grinding treatment to obtain a second hot-rolled slab with the thickness of 7 mm;
step five: placing the fourth hot-rolled plate blank in the step four into an annealing furnace, preserving heat for 18min under the condition that the temperature is 880 ℃, and then cooling in the air;
step six: and (4) preserving the heat of the second hot-rolled plate blank in the fifth step in a heating furnace at 880 ℃ for 12min, performing 6-pass third hot rolling, keeping the rolling direction of the third hot rolling parallel to the rolling direction of the first hot rolling, and respectively setting the deformation of each pass as follows: 20%,23%,23%,20%,20%,20%, air cooling, and then performing surface grinding treatment to obtain a third hot-rolled plate blank with the thickness of 1.7 mm;
step seven: and sixthly, annealing the third hot-rolled plate blank in the step six in a continuous annealing furnace filled with high-purity argon, wherein the annealing temperature is 860 ℃, and the plate traveling speed is 0.12m/min.
Step eight: and (3) feeding the third hot-rolled plate blank in the step seven into a cold rolling mill, carrying out 6-pass cold rolling, keeping the cold rolling direction parallel to the rolling direction of the third hot rolling, and respectively setting the deformation of each pass as follows: 20%,28%, 23%,25%,25%,28% to obtain a cold-rolled sheet having a thickness of 0.3 mm.
Step nine: and (5) annealing the finished product of the cold-rolled sheet obtained in the step eight in a continuous annealing furnace filled with high-purity argon, wherein the annealing temperature is 825 ℃, and the running speed of the sheet is 0.10m/min.
The tensile strength of the TB8 titanium alloy sheet prepared by the embodiment at room temperature is 986MPa, the elongation is 14.8%, and the microstructure is shown in FIG. 3 and meets the requirements of related technical standards.
Claims (3)
1. A processing method for preparing a TB8 titanium alloy sheet in a short process is characterized by comprising the following steps: the method comprises the following steps:
heating a TB8 titanium alloy ingot to 1100-1200 ℃, forging for one time in the streamline direction of the ingot, cooling by water, and then carrying out surface grinding treatment to obtain a forged blank after cogging, wherein the finish forging temperature is not lower than 850 ℃;
step two, heating the forging stock in the step one to 1050-1100 ℃, and performing reverse forging for one fire time in the direction vertical to the streamline direction of the forging stock, wherein the finish forging temperature is not lower than 800 ℃, so as to obtain a hot rolling plate blank with the thickness of 120-200 mm;
step three, directly keeping the hot rolled plate blank in the step two at the temperature of 950-1000 ℃ for 50-80 min without cooling, then carrying out first fire rolling for 5-8 times, wherein the deformation of each time is 10-25%, carrying out surface grinding treatment after water cooling to obtain a first fire rolled plate blank with the thickness of 25-50 mm; the rolling direction of the first hot rolling is unidirectional rolling;
step four, preserving the heat of the first hot rolled plate blank in the step three in a heating furnace at the temperature of 900-950 ℃ for 30-60 min, then carrying out second hot rolling, wherein the number of passes is 5-7, and the deformation of each pass is 10-30%, wherein the rolling direction of the first 2-3 passes is vertical to that of the first hot rolling, the rolling direction of the subsequent passes is parallel to that of the first hot rolling, and carrying out surface polishing treatment after air cooling to obtain the second hot rolled plate blank with the thickness of 6-15 mm; the rolling direction of the second hot rolling is alternately vertical and parallel to the rolling direction of the first hot rolling;
step five, carrying out recrystallization annealing treatment on the second hot rolled plate blank in the step four, wherein the temperature is 800-900 ℃, and the heat preservation time is 10-20 min;
sixthly, preserving the second hot rolling plate blank subjected to the recrystallization annealing treatment in the step five in a heating furnace at the temperature of 850-900 ℃ for 5-15 min, then carrying out third hot rolling for 4-6 times, wherein the deformation of each time is 15-30%, and carrying out surface grinding treatment after water cooling to obtain a third hot rolling plate blank with the thickness of 1.5-4.0 mm; the rolling direction of the third hot rolling is parallel to that of the first hot rolling;
seventhly, carrying out intermediate argon-filled on-line continuous annealing treatment on the third fire-rolled plate blank in the sixth step, wherein the annealing temperature is 850-900 ℃, the plate traveling speed is 0.05-0.15 m/min, the purity of the argon filled in the furnace is more than or equal to 99.99%, and the micro-positive pressure of the inert gas overflowing as a standard is kept;
step eight, sending the third rolling plate blank subjected to the intermediate annealing treatment in the step seven into a cold rolling mill for cold rolling, wherein the cold rolling is completed by 5-8 passes, the deformation of each pass is 10% -30%, and a cold-rolled plate with the thickness of 0.3-1.0 mm is obtained; the rolling direction of the cold rolling is parallel to that of the third hot rolling;
and step nine, carrying out argon-filled on-line continuous annealing treatment on the cold-rolled sheet obtained in the step eight, wherein the annealing temperature is 820-850 ℃, the traveling speed of the sheet is 0.05-0.15 m/min, the purity of the argon filled in the furnace is more than or equal to 99.99%, and micro-positive pressure with inert gas overflowing as the standard is kept, so that the TB8 titanium alloy sheet with the thickness of 0.3-1.0 mm, the room-temperature tensile strength of not less than 900MPa and the elongation of not less than 12% is obtained.
2. The processing method for preparing the TB8 titanium alloy sheet in the short process according to claim 1, wherein the processing method comprises the following steps: in the step one, the pier drawing frequency of one-time forging is three piers and three-drawing, the single-time upsetting deformation is 35-50%, the drawing deformation per hammer is 10-20%, and the pressing rate is 10-15 mm/s.
3. The processing method for preparing the TB8 titanium alloy sheet in the short process according to claim 1, wherein the processing method comprises the following steps: in the second step, the upsetting times of the first-time forging is two upsetting and two-time drawing, the single upsetting deformation is 50-65%, the elongation deformation per hammer is 15-25%, and the pressing rate is 15-20 mm/s.
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Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2002155349A (en) * | 2000-11-17 | 2002-05-31 | Sumitomo Metal Ind Ltd | Method for producing titanium plate |
| CN106955893A (en) * | 2017-03-17 | 2017-07-18 | 中国航发北京航空材料研究院 | A kind of superplastic forming processing method of SP700 titanium-alloy thin-plates |
| CN110592508A (en) * | 2019-09-12 | 2019-12-20 | 中国航发北京航空材料研究院 | Low-cost and high-performance titanium alloy short-process forging process |
| CN112517659A (en) * | 2020-11-17 | 2021-03-19 | 中国航发北京航空材料研究院 | Processing method of titanium alloy wire for plasma arc/electric arc additive manufacturing |
| CN112517633A (en) * | 2020-11-17 | 2021-03-19 | 中国航发北京航空材料研究院 | Low-cost titanium alloy short-process rolling process |
| CN112795798A (en) * | 2019-11-13 | 2021-05-14 | 新疆大学 | Preparation method of titanium alloy plate |
-
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- 2021-09-30 CN CN202111168032.9A patent/CN114101556B/en active Active
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2002155349A (en) * | 2000-11-17 | 2002-05-31 | Sumitomo Metal Ind Ltd | Method for producing titanium plate |
| CN106955893A (en) * | 2017-03-17 | 2017-07-18 | 中国航发北京航空材料研究院 | A kind of superplastic forming processing method of SP700 titanium-alloy thin-plates |
| CN110592508A (en) * | 2019-09-12 | 2019-12-20 | 中国航发北京航空材料研究院 | Low-cost and high-performance titanium alloy short-process forging process |
| CN112795798A (en) * | 2019-11-13 | 2021-05-14 | 新疆大学 | Preparation method of titanium alloy plate |
| CN112517659A (en) * | 2020-11-17 | 2021-03-19 | 中国航发北京航空材料研究院 | Processing method of titanium alloy wire for plasma arc/electric arc additive manufacturing |
| CN112517633A (en) * | 2020-11-17 | 2021-03-19 | 中国航发北京航空材料研究院 | Low-cost titanium alloy short-process rolling process |
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