WO2023016143A1 - 提高两相钛合金抗高速冲击性能的热加工方法 - Google Patents

提高两相钛合金抗高速冲击性能的热加工方法 Download PDF

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WO2023016143A1
WO2023016143A1 PCT/CN2022/103831 CN2022103831W WO2023016143A1 WO 2023016143 A1 WO2023016143 A1 WO 2023016143A1 CN 2022103831 W CN2022103831 W CN 2022103831W WO 2023016143 A1 WO2023016143 A1 WO 2023016143A1
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titanium alloy
rolling
phase titanium
impact resistance
speed impact
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PCT/CN2022/103831
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English (en)
French (fr)
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杨柳
王莹
刘昕
吴静怡
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成都先进金属材料产业技术研究院股份有限公司
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Publication of WO2023016143A1 publication Critical patent/WO2023016143A1/zh

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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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
    • B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B45/00—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
    • B21B45/004—Heating the product
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B45/00—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
    • B21B45/02—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills for lubricating, cooling, or cleaning
    • B21B45/0203—Cooling
    • B21B45/0209—Cooling devices, e.g. using gaseous coolants
    • B21B45/0215—Cooling devices, e.g. using gaseous coolants using liquid coolants, e.g. for sections, for tubes
    • B21B45/0218—Cooling devices, e.g. using gaseous coolants using liquid coolants, e.g. for sections, for tubes for strips, sheets, or plates
    • 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
    • C21D8/0226—Hot rolling
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C14/00—Alloys based on titanium
    • 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
    • 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

Definitions

  • the invention belongs to the technical field of titanium alloy material preparation, relates to a special vehicle titanium alloy plate, and in particular relates to a thermal processing method for improving the high-speed impact resistance of a two-phase titanium alloy.
  • CN109590330A disclosed a rolling method of TC4ELI titanium alloy wide and thick plate.
  • the TC4ELI wide and thick plate is rolled by two-fire rolling.
  • the heating system, total deformation, and final Parameters such as rolling temperature are stipulated, which is characterized in that the temperature in the heating process is controlled stepwise, and the temperature is raised above the phase transition temperature for heating in the last 1/3 of the heating time, and the basket structure can be obtained, but the impact toughness of this structure type is relatively low. Low, not conducive to ballistic protection.
  • CN104874604A disclosed a method for rolling a wide-width titanium alloy thick plate.
  • the heating temperature, deformation amount, final rolling temperature and post-rolling cooling method of the two-phase titanium alloy wide-width thick plate rolling process were carried out. It is characterized by the fact that the final rolling temperature is not lower than 200°C below the phase transition point, and the water cooling method is used for rapid cooling after rolling. It does not involve the control of the deformation temperature during the rolling process, and the plate will undergo thermal deformation during the water cooling process after rolling. , the plate type cannot be guaranteed.
  • CN103230936A disclosed a rolling method of TC4 titanium alloy wide and medium-thick plate. Through the control of the rolling process, a TC4 wide and thick plate with small anisotropy and high comprehensive performance was obtained. After the temperature of the rolling process is reduced to 910-900°C, it is returned to the furnace and reheated for temperature compensation, and then rolled after being raised to 930-950°C. In order to reduce the requirements of the equipment capacity of the rolling mill, the method of high temperature rolling is adopted. However, performance will be adversely affected.
  • CN102172638A disclosed a method for rolling titanium and titanium alloy thin plate sickle bending. After high-temperature rush rolling, multi-pass small-variable deviation-correction rolling is performed after the temperature drops below 650°C. In order to correct the plate shape, because the deformation temperature is too low, the improvement of the tissue performance will not have a significant effect.
  • the technical problem to be solved by the invention is that the existing two-phase titanium alloy plate has low strength and poor high-speed impact resistance.
  • the technical solution adopted by the present invention to solve the technical problem is: a thermal processing method for improving the anti-high-speed impact performance of a two-phase titanium alloy, comprising the following steps:
  • the preheating section is ⁇ 850°C for 10-20min
  • the heating section is 1050-1070°C for 10-20min
  • the soaking section is 1040-1060°C Keep warm for 60-90min
  • the rough rolling temperature is 990-1030 °C, and the reduction ratio is 15-25%;
  • the two-phase titanium alloy is Ti-4Al-1.5Cr-0.5Mo series special bulletproof armor titanium alloy for special vehicles, and the slab is obtained by forging the titanium alloy through high and low temperature upsetting + elongation process .
  • a walking electric heating furnace is used for heating.
  • the size of the two-phase titanium alloy slab is: thickness 100-140mm ⁇ width 800-1200mm ⁇ length 1200-2500mm.
  • the size of the above two-phase titanium alloy slab after transverse rough rolling is: thickness 60-90mm ⁇ width 1200-2200mm ⁇ length 1200-2500mm.
  • the size of the above-mentioned two-phase titanium alloy slab after longitudinal rolling is: thickness 6-20mm ⁇ width 1200-2500mm ⁇ length 4000-12000mm.
  • step b a reversing rolling mill is used for rolling.
  • step c the solution heat treatment is carried out at 850-900° C. for 1-2 hours.
  • step c the aging treatment is carried out at 500-600° C. for 8-12 hours.
  • the beneficial effect of the present invention is that: the present invention adopts the method of section heating, and sets the temperature of the lower preheating section ( ⁇ 850°C) in order to avoid cracking caused by the large temperature difference between the inside and outside of the slab during the heating process from room temperature; the heating section Raising the temperature to 1050-1070°C can raise the overall temperature of the slab to the temperature required for deformation, which is conducive to the progress of structural changes during rolling; the soaking section 1040-1060°C can further homogenize the temperature of each part of the slab.
  • the rolling process of the present invention that is, the two-stage rolling method of the ⁇ -phase region and the ⁇ + ⁇ two-phase region after segmental heating, the transverse and longitudinal property anisotropy of the finished plate can be reduced.
  • the first stage of the rolling process of the present invention adopts large-reduction rolling, and the rolling temperature range is the ⁇ -phase region of 990-1030°C. Due to the high temperature, it can ensure that the rolling mill has the conditions for large-reduction rolling, and at the same time, the large-reduction Quantitative deformation can also effectively break the coarse grain structure of the whole section; the second stage adopts rolling deformation in the two-phase region, and the deformation temperature range is 900-990°C in the ⁇ + ⁇ two-phase region. The deformation in this temperature range can make the structure change from Wei The transformation of the structure to the basket + lamellar structure is conducive to the improvement of high-speed impact resistance.
  • the present invention adopts rapid cooling after rolling to avoid the formation of secondary ⁇ phase and guarantee the strength of the material; adopts solid solution aging strengthening heat treatment to further improve the strength of the material; the rolling process cooperates with rapid cooling after rolling and solid solution aging strengthening heat treatment , can ensure the high strength and excellent high-speed impact resistance of the product, and greatly improve the protective performance of the material.
  • the titanium alloy for special vehicles processed by the thermal processing method of the present invention has a strength ⁇ 1200 MPa and a strain rate greater than 3000s-1 Under certain conditions, the dynamic compressive strength is ⁇ 1700MPa.
  • Fig. 1 is a sheet structure diagram of Example 1 of the present invention.
  • Fig. 2 is a target test result diagram of Example 1 of the present invention.
  • Fig. 3 is a plate structure diagram of Example 2 of the present invention.
  • Fig. 4 is a target test result diagram of Example 2 of the present invention.
  • Fig. 5 is a sheet structure diagram of Example 3 of the present invention.
  • Fig. 6 is a target test result diagram of Example 3 of the present invention.
  • a thermal processing method for improving the high-speed impact resistance of a two-phase titanium alloy comprises the following steps:
  • the preheating section is ⁇ 850°C for 10-20min
  • the heating section is 1050-1070°C for 10-20min
  • the soaking section is 1040-1060°C Keep warm for 60-90min
  • the rough rolling temperature is 990-1030 °C, and the reduction ratio is 15-25%; then the slab is reversed, and longitudinal rolling is carried out, and the rolling temperature is 900 -990°C, the reduction rate is 10-20%;
  • the two-phase titanium alloy described in the present invention is a Ti-4Al-1.5Cr-0.5Mo series special bulletproof armor titanium alloy, and the slab is obtained by forging the titanium alloy through high and low temperature upsetting + stretching and drawing processes.
  • a walking electric heating furnace is used for heating.
  • the size of the forged slab is calculated from the size of the finished product and the deformation required for thermal processing. Therefore, preferably, in the above step a, the size of the two-phase titanium alloy slab is: thickness 100-140mm ⁇ width 800-1200mm ⁇ length 1200mm -2500mm; size control is to control the amount of deformation in each stage of thermal processing, which is an important means to control the microstructure and properties. Therefore, it is preferable that the size of the above-mentioned two-phase titanium alloy slab after transverse rough rolling is: thickness 60-90mm ⁇ Width 1200-2200mm ⁇ length 1200-2500mm; after longitudinal rolling, the size is: thickness 6-20mm ⁇ width 1200-2500mm ⁇ length 4000-12000mm.
  • step b the rolling is carried out by using a reversing rolling mill.
  • the solution heat treatment is 850-900° C. for 1-2 hours; the aging treatment is 500-600° C. for 8-12 hours.
  • This application provides a high and low temperature upsetting + elongation process, which is not a limitation of this application.
  • the original size of the ingot ( ⁇ 600 ⁇ 650)mm) ⁇ (1900 ⁇ 2100)mm), the high and low temperature upsetting + stretching process is as follows:
  • the first high-temperature two-upsetting and two-drawing forging the ingot heating and holding temperature is 1010-1200°C, the holding time is 4h-8h, the starting forging temperature is ⁇ 1000°C, and the final forging temperature is ⁇ 780°C.
  • Process control first upsetting to the ingot height of 950-1050mm, then pulling it back to the original height, returning to the furnace for 2h-4h, and then pulling it out again, first upsetting to the ingot height of 950-1050mm, and then pulling it back to the original height , Pull and hold down the "Eight Direction Deformation" button, the amount of unilateral reduction ⁇ 50mm, throw out after forging to clean the surface;
  • the second low-temperature upsetting + upsetting and elongation forging billet heating and holding temperature 900-980°C, holding time 4h-8h, starting forging temperature ⁇ 900°C, final forging temperature ⁇ 720°C, the process is one upsetting and one Pulling, stretching after upsetting again: the first upsetting and pulling process control: first upsetting to a height of 1050-1150mm, returning to the furnace to keep warm for 2h-4h, and then pulling out to the original height, pulling and long pressing "Bafang deformation", single Side reduction ⁇ 50mm.
  • the second upsetting and stretching and elongation first upsetting to a height of 1250-1300mm, returning to the furnace for 2h-4h, then stretching and elongating after being out of the furnace, pressing "square deformation" for elongation, the size is controlled as thickness 100-140mm ⁇ width 800 -1200mm x length 1200-2500mm.
  • the dimensions and specifications of titanium alloy rolling slabs for special vehicles are: thickness 111mm ⁇ width 990mm ⁇ length 1500mm, and the stepping electric heating furnace is used to heat the slab.
  • the temperature and holding time of each section meet: the preheating section 800°C Keep warm for 20 minutes, keep warm for 15 minutes at 1050°C in the heating section, and keep warm for 80 minutes at 1050°C in the soaking section;
  • the billet size after rolling is: thickness 55mm ⁇ width 2000mm ⁇ length 1550mm; then the slab is reversed, and the temperature of the slab is tested with a hand-held infrared thermometer.
  • the temperature is 970°C, carry out Two-phase area rolling, the billet size after rolling: thickness 8mm ⁇ width 2000mm ⁇ length 12000mm;
  • the rolled armor titanium alloy plate is rapidly cooled to 190°C by water cooling, followed by solution heat treatment at 850°C for 2 hours, and then aging treatment at 500°C for 8 hours after solution heat treatment.
  • the rolled slab in step a can be obtained, but not limited to, by the following forging process:
  • the original size of the ingot is ⁇ 630mm ⁇ 2020mm
  • the first high-temperature two-upsetting and two-drawing forging the heating and holding temperature of the ingot is 1100°C
  • the holding time is 6h
  • the starting forging temperature is 1050°C
  • the final forging temperature is 820°C.
  • Upsetting process control first upsetting to the ingot height of 1050mm, then pulling back to a height of 2020mm, returning to the furnace for 4 hours, and then pulling out again, first upsetting to a height of 950mm, and then pulling back to a height of 2020mm, the shape is square , unilateral reduction 30mm, throw out after forging to clean the surface;
  • the second low-temperature upsetting + upsetting and elongation forging billet heating and holding temperature 950 ° C, holding time 6 hours, starting forging temperature 920 ° C, final forging temperature 750 ° C, the process is one upsetting and one pulling, after upsetting again
  • Stretching and drawing the first upsetting and drawing process control: first upsetting to a height of 1150mm, returning to the furnace for 4 hours, and then drawing out of the furnace to a height of 2020mm, pressing "Octolateral deformation" for drawing and pressing, and the amount of unilateral reduction is 50mm.
  • the second upsetting and stretching and elongation first upsetting to a height of 1300mm, returning to the furnace for 3 hours, then stretching and elongating after being out of the furnace, pressing "square deformation" for elongation, the thickness of the slab after forging is 120mm ⁇ width 1050mm ⁇ length 4800mm, After milling the oxide skin on the surface and dividing it into thirds along the length, a rolled slab with dimensions of thickness 111mm ⁇ width 990mm ⁇ length 1500mm was obtained.
  • the structure of the titanium alloy sheet material for special vehicles finally obtained in Example 1 is shown in Figure 1.
  • the structure obtained in Example 1 is a lamellar structure with a thickness of 2-3 ⁇ m; the material is subjected to a target test (target Test condition: plate thickness 8mm, 53 formula 7.62mm steel core bomb 100 meters 0 ° incident angle), the result is as shown in Figure 2, as can be seen from Figure 2, the plate of embodiment 1 can be to 53 formula 100 meters 0 ° incident angle 7.62mm steel core bullet for effective protection, the tissue has good high-speed impact resistance.
  • target Test condition plate thickness 8mm, 53 formula 7.62mm steel core bomb 100 meters 0 ° incident angle
  • the dimensions and specifications of titanium alloy rolled slabs for special vehicles are: thickness 120mm ⁇ width 1000mm ⁇ length 1300mm, and the stepping electric heating furnace is used to heat the billet.
  • the temperature and holding time of each section meet: the preheating section 750°C Keep warm for 20 minutes, keep warm for 20 minutes at 1050°C in the heating section, and keep warm for 90 minutes at 1050°C in the soaking section;
  • the billet size after rolling is: thickness 50mm ⁇ width 2200mm ⁇ length 1350mm; then the slab is reversed, and the temperature of the slab is tested with a hand-held infrared thermometer.
  • the temperature is 950°C, carry out Two-phase area rolling, the billet size after rolling: thickness 8mm ⁇ width 2200mm ⁇ length 9000mm;
  • the rolled armor titanium alloy plate is rapidly cooled to 185°C by water cooling, followed by solution heat treatment at 900°C for 2 hours, and then aging treatment at 600°C for 12 hours after solution heat treatment.
  • the rolled slab in step a can be obtained, but not limited to, by the following forging process:
  • the original size of the ingot is ⁇ 610mm ⁇ 1950mm
  • the first high-temperature two-upsetting and two-drawing forging the heating and holding temperature of the ingot is 1150°C
  • the holding time is 5h
  • the starting forging temperature is 1100°C
  • the final forging temperature is 870°C.
  • the process is two upsetting and two Pulling, upsetting and pulling process control: first upsetting to the ingot height of 1000mm, then pulling back to a height of 1950mm, returning to the furnace for 4 hours, and then pulling out again, first upsetting to a height of 1000mm, and then pulling back to a height of 1950mm, the shape It is square, with a reduction of 50mm on one side, and it is thrown out to clean the surface after forging;
  • the second low-temperature upsetting + upsetting and elongation forging billet heating and holding temperature 980°C, holding time 5h, starting forging temperature 930°C, final forging temperature 780°C, the process is one upsetting and one pulling, and upsetting again Stretching after roughing: Control of the first upsetting process: first upsetting to a height of 1050mm, returning to the furnace for 4 hours, and then pulling out to a height of 1950mm, pressing "Octolateral deformation" for a long time, and a single-sided reduction of 50mm.
  • the second upsetting and stretching and elongation first upsetting to a height of 1250mm, returning to the furnace for 3 hours, then stretching and elongating after being out of the furnace, pressing "square deformation” for elongation, after forging, the thickness of the slab is 130mm ⁇ width 1100mm ⁇ length 4200mm, After milling the oxide skin on the surface and dividing it into thirds along the length, a rolled slab with a size of 120mm in thickness ⁇ 1000mm in width ⁇ 1300mm in length was obtained.
  • the structure of the titanium alloy sheet material for special vehicles finally obtained in embodiment 2 is shown in Figure 3, as can be seen from the figure, the structure obtained in embodiment 2 is a lamellar structure with a thickness of 1-2 ⁇ m; the material is subjected to a target test (target test Condition: plate thickness 8mm, 53 formula 7.62mm steel core bomb 100 meters 0 ° incident angle), the result is as shown in Figure 4, as can be seen from the figure, the plate of embodiment 2 can be to 53 formula 100 meters 0 ° incident angle 7.62mm Steel core bullets are used for effective protection, and the tissue has good high-speed impact resistance.
  • target test target test Condition: plate thickness 8mm, 53 formula 7.62mm steel core bomb 100 meters 0 ° incident angle
  • the dimensions and specifications of titanium alloy rolling slabs for special vehicles are: thickness 100mm ⁇ width 1100mm ⁇ length 1400mm.
  • Stepping electric heating furnace is used to heat the billet.
  • the temperature and holding time of each section meet: preheating section 670°C Keep warm for 20 minutes, keep warm for 15 minutes at 1050°C in the heating section, and keep warm for 80 minutes at 1040°C in the soaking section;
  • the billet size after rolling is: thickness 50mm ⁇ width 2200mm ⁇ length 1450mm; then the slab is reversed, and the temperature of the slab is tested with a hand-held infrared thermometer.
  • the temperature is 950°C, carry out Two-phase area rolling, the billet size after rolling: thickness 8mm ⁇ width 2200mm ⁇ length 9500mm;
  • the rolled armor titanium alloy plate is rapidly cooled to 150°C by water cooling, followed by solution heat treatment at 850°C for 2 hours, and then aging treatment at 550°C for 12 hours after solution heat treatment.
  • the rolled slab in step a can be obtained, but not limited to, by the following forging process:
  • the original size of the ingot is ⁇ 630mm ⁇ 2000mm
  • the first high-temperature two-upsetting and two-drawing forging the heating and holding temperature of the ingot is 1050°C
  • the holding time is 6h
  • the starting forging temperature is 1000°C
  • the final forging temperature is 820°C.
  • Pulling, upsetting and pulling process control first upsetting to the ingot height of 1000mm, then pulling back to a height of 2000mm, returning to the furnace for 6 hours, and then pulling out again after being out of the furnace, first upsetting to a height of 1000mm, and then pulling back to a height of 2000mm, the shape It is square, with a reduction of 30mm on one side, and it is thrown out to clean the surface after forging;
  • the second low-temperature upsetting + upsetting and elongation forging billet heating and holding temperature 950°C, holding time 6h, starting forging temperature 920°C, final forging temperature 750°C, the process is one upsetting and one pulling, and upsetting again Stretching after roughing: Control of the first upsetting process: first upsetting to a height of 950mm, returning to the furnace for 4 hours, and then pulling out to a height of 2000mm, pressing "Octolateral deformation" for a long time, and a single-sided reduction of 50mm.
  • the second upsetting and stretching and elongation first upsetting to a height of 1200mm, returning to the furnace for 3 hours, then stretching and elongating after being out of the furnace, pressing "square deformation” for elongation, after forging, the thickness of the slab is 110mm ⁇ width 1200mm ⁇ length 4500mm, After milling the oxide skin on the surface and dividing it into thirds along the length, a rolled slab with a size of 100mm in thickness ⁇ 1100mm in width ⁇ 1400mm in length was obtained.
  • the structure of the titanium alloy sheet material for special vehicles finally obtained in embodiment 3 is shown in Figure 5.
  • the structure obtained in embodiment 3 is a lamellar structure with a thickness of 2-3 ⁇ m; the material is subjected to target test (target test Condition: plate thickness 8mm, 53 formula 7.62mm steel core bomb 100 meters 0 ° incident angle), the result is as shown in Figure 6, as can be seen from the figure, the plate of embodiment 3 can be 7.62mm to 53 formula 100 meters 0 ° incident angle Steel core bullets are used for effective protection, and the tissue has good high-speed impact resistance.
  • Table 1 embodiment obtains the mechanical property of plate
  • the average tensile strength of the sheet in Example 1 is 1286MPa, and under the condition that the strain rate is greater than 3000s-1, the average dynamic compressive strength reaches 1883MPa; the average tensile strength of the sheet in Example 2 is 1350MPa, and at the strain rate Under the condition of greater than 3000s-1, the average dynamic compressive strength reaches 2023MPa; the average tensile strength of the plate in Example 3 is 1232MPa, and under the condition of strain rate greater than 3000s-1, the average dynamic compressive strength reaches 1809MPa.
  • the two-phase titanium alloy for special vehicles prepared by adopting the thermal processing technology of the invention has high strength and excellent high-speed impact resistance, and greatly improves the protective performance of the material.

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Abstract

本发明公开了一种提高两相钛合金抗高速冲击性能的热加工方法，属于钛合金材料制备技术领域。提高两相钛合金抗高速冲击性能的热加工方法，包括如下步骤：a.对两相钛合金扁坯坯料进行步进式加热；b.采用换向轧制方式，首先进行横向粗轧，随后将板坯换向，进行纵向轧制；c.将轧制后的板材水冷，随后进行固溶热处理和时效处理。本发明采用β相区和α+β两相区两阶段轧制的方法可减小成品板材横向和纵向的性能各向异性，配合轧后快速冷却和固溶时效强化热处理，可以保障产品的高强度和优异抗高速冲击性能，大幅提升材料的防护性能，本发明的热加工方法可有效解决现有两相钛合金板材强度低，抗高速冲击性能较差的问题。

Description

提高两相钛合金抗高速冲击性能的热加工方法 技术领域
本发明属于钛合金材料制备技术领域，涉及一种特种车辆钛合金中厚板，具体涉及一种提高两相钛合金抗高速冲击性能的热加工方法。
背景技术
为提高特种车辆的机动性、燃油效率和运输性，对于减少坦克、直升机等各种应用中使用的装甲结构重量的需求日益提升。因具有高的比强度、优异的力学性能及良好的抗弹性能，钛合金装甲的应用得到越来越多的重视。为了使特种车辆用钛合金板材保持高强度同时，最大限度提升材料的抗高速冲击性能，因此需要在热加工过程中对热成型工艺和热处理工艺进行严格控制。
2019年4月9日CN109590330A公开了一种TC4ELI钛合金宽幅厚板的轧制方法，采用两火轧制方式轧制TC4ELI宽厚板，对两火次轧制的加热制度、总变形量、终轧温度等参数进行了规定，特征在于对加热过程中的温度进行阶梯式控制，后1/3加热时间将温度提高到相变温度以上加热，可以获得网篮组织，但是该组织类型冲击韧性较低，不利于抗弹防护。
2015年9月2日CN104874604A公开了一种宽幅钛合金厚板轧制方法，对两相钛合金宽幅厚板轧制过程中的加热温度、变形量、终轧温度以及轧后冷却方式进行了规定，特征在于终轧温度不低于相变点以下200℃，轧制后采用水冷方式快速冷却，对于轧制过程中变形温度的控制没有涉及，且轧制后水冷过程板材将发生热变形，板型无法得到保障。
2013年8月7日CN103230936A公开了一种TC4钛合金宽幅中厚板材的轧制方法，通过对轧制工艺的控制，获得了各向异性小、综合性能高的TC4宽厚板，特征在于轧制过程温度将至910-900℃后，回炉再加热进行温度补偿，提高到930-950℃后再进行轧制，该方法为了降低轧机设备能力的要求，采用了补温高温轧制的方法，但对性能将产生不利影响。
2011年9月7日CN102172638A公开了一种轧制钛及钛合金薄板镰刀弯的方法，采用高温抢温轧制后，待温度降低到650℃以下再进行多道次小变量纠偏轧制，作用为矫正板型，由于变形温度太低，对组织性能的改善提高不会起到明显效果。
发明内容
本发明所要解决的技术问题是现有两相钛合金板材强度低，抗高速冲击性能较差的问题。
本发明解决其技术问题所采用的技术方案是：提高两相钛合金抗高速冲击性能的热加工方法，包括如下步骤：
a.对两相钛合金扁坯坯料进行加热，各段温度及保温时间满足：预热段＜850℃保温10-20min，加热段1050-1070℃保温10-20min，均热段1040-1060℃保温60-90min；
b.采用换向轧制方式，首先进行横向粗轧，粗轧温度为990-1030℃，压下率为15-25％；
c.将轧制后的板材水冷至＜200℃，随后进行固溶热处理和时效处理。
上述步骤a中，所述两相钛合金为Ti-4Al-1.5Cr-0.5Mo系特种车辆专用防弹装甲钛合金，所述扁坯由该钛合金经过高低温镦拔+延展拔长工艺锻造得到。
上述步骤a中，加热使用步进式电加热炉。
上述步骤a中，所述两相钛合金扁坯坯料尺寸为：厚度100-140mm×宽度800-1200mm×长度1200-2500mm。
上述两相钛合金扁坯坯料经横向粗轧后尺寸为：厚度60-90mm×宽度1200-2200mm×长度1200-2500mm。
上述两相钛合金扁坯坯料经纵向轧制后尺寸为：厚度6-20mm×宽度1200-2500mm×长度4000-12000mm。
上述步骤b中，采用可逆式轧机进行轧制。
上述步骤c中，固溶热处理为850-900℃保温1-2h。
上述步骤c中，时效处理为500-600℃保温8-12h。
本发明的有益效果是：本发明采用分段加热的方式，设定较低预热段温度(＜850℃)，是为了避免板坯从室温升温过程中，内外温差太大导致开裂；加热段升温至1050-1070℃可以使板坯整体升温至变形所需温度，有利于轧制时组织变化的进行；均热段1040-1060℃可以使板坯各部位温度进一步均匀化。结合本发明的轧制工艺，即分段加热后采用β相区和α+β两相区两阶段轧制的方法，可减小成品板材横向和纵向的性能各向异性。
本发明轧制工艺第一阶段采用大压下量轧制，轧制温度区间为990-1030℃的β相区，由于温度高，可以保障轧机具备大压下轧制的条件，同时大压下量变形也可以有效破碎全断面粗大晶粒组织；第二阶段采用两相区轧制变形，变形温度区间为900-990℃的α+β两相区，该温度区间变形可以使组织由魏氏组织向网篮+片层组织转变，有利于抗高速冲击性能的提高。
同时，本发明采用轧后快速冷却可以避免次生α相的形成，保障材料强度；采用固溶时效强化热处理，可以进一步提升材料的强度；轧制工艺配合轧后快速冷却和固溶时效强化热处理，可以保障产品的高强度和优异抗高速冲击性能，大幅提升材料的防护性能，使用本发 明的热加工方法处理后的特种车辆用钛合金，强度≥1200MPa的同时，在应变速率大于3000s-1的条件下，动态压缩强度≥1700MPa。
附图说明
图1为本发明实施例1的板材组织图。
图2为本发明实施例1的靶试结果图。
图3为本发明实施例2的板材组织图。
图4为本发明实施例2的靶试结果图。
图5为本发明实施例3的板材组织图。
图6为本发明实施例3的靶试结果图。
具体实施方式
本发明的技术方案，具体可以按照以下方式实施。
提高两相钛合金抗高速冲击性能的热加工方法，包括如下步骤：
a.对两相钛合金扁坯坯料进行加热，各段温度及保温时间满足：预热段＜850℃保温10-20min，加热段1050-1070℃保温10-20min，均热段1040-1060℃保温60-90min；
b.采用换向轧制方式，首先进行横向粗轧，粗轧温度为990-1030℃，压下率为15-25％；随后将板坯换向，进行纵向轧制，轧制温度为900-990℃，压下率为10-20％；
c.将轧制后的板材水冷至＜200℃，随后进行固溶热处理和时效处理。
本发明所述两相钛合金为Ti-4Al-1.5Cr-0.5Mo系特种车辆专用防弹装甲钛合金，所述扁坯由该钛合金经过高低温镦拔+延展拔长工艺锻造得到。为了更好的控制加热温度，因此优选的是，上述步骤a中，加热使用步进式电加热炉。
锻造板坯尺寸由成品尺寸和热加工需求变形量计算获得，因此优选的是，上述步骤a中，所述两相钛合金扁坯坯料尺寸为：厚度100-140mm×宽度800-1200mm×长度1200-2500mm；控制尺寸就是控制热加工各阶段的变形量，是实现组织性能控制的重要手段，因此优选的是，上述两相钛合金扁坯坯料经横向粗轧后尺寸为：厚度60-90mm×宽度1200-2200mm×长度1200-2500mm；经纵向轧制后尺寸为：厚度6-20mm×宽度1200-2500mm×长度4000-12000mm。
为了方便实现换向轧制，因此优选的是，上述步骤b中，采用可逆式轧机进行轧制。
为了进一步强化两相钛合金的性能，因此优选的是，上述步骤c中，固溶热处理为850-900℃保温1-2h；时效处理为500-600℃保温8-12h。
本申请提供一种高低温镦拔+延展拔长工艺,并非对本申请的限制。
铸锭原始尺寸(Φ600～Φ650)mm)Φ×(1900～2100)mm)，高低温镦拔+延展拔长工艺如下：
⑴第一次高温两镦两拔锻造：铸锭加热保温温度1010～1200℃，保温时间4h～8h，开锻温度≥1000℃，终锻温度≥780℃，工艺为两镦两拔，镦拔过程控制：先镦粗至铸锭高度950～1050mm，再拔长回原来高度，回炉保温2h～4h后，出炉再次墩拔，先镦粗至铸锭高度950～1050mm，再拔长回原来高度，拔长按“八方变形”，单边压下量≤50mm，锻造后甩出清理表面；
⑵第二次低温镦拔+镦粗及延展拔长锻造：坯料加热保温温度900～980℃，保温时间4h～8h，开锻温度≥900℃，终锻温度≥720℃，工艺为一镦一拔，再次镦粗后延展拔长：第一次镦拔过程控制：先镦粗至高度1050～1150mm，回炉保温2h～4h，再出炉拔长至原高度，拔长按“八方变形”，单边压下量≤50mm。第二次镦粗及延展拔长：先镦粗至高度1250～1300mm，回炉保温2h～4h，再出炉后延展拔长，拔长按“四方变形”，尺寸控制为厚度100-140mm×宽度800-1200mm×长度1200-2500mm。
下面通过实际的例子对本发明的技术方案和效果做进一步的说明。
实施例
实施例1
a.选用特种车辆用钛合金轧制板坯尺寸规格为：厚度111mm×宽度990mm×长度1500mm，采用步进式电加热炉对坯料进行加热，各段温度及保温时间满足：预热段800℃保温20min，加热段1050℃保温15min，均热段1050℃保温80min；
b.将配料冷却至轧制温度后，关闭辊道冷却水以及除磷水，快速将坯料传送至可逆式轧机进行换向轧制，首先进行横向宽展大压下量粗轧β相区，轧制温度为1000℃，轧制后的坯料尺寸：厚度55mm×宽度2000mm×长度1550mm；随后将板坯换向，采用手持式红外测温仪测试板坯温度，当温度为970℃后，进行两相区轧制，轧制后的坯料尺寸：厚度8mm×宽度2000mm×长度12000mm；
c.对轧制后的装甲钛合金板材进行水冷快速冷却至190℃，随后进行850℃保温时间2h的固溶热处理，完成固溶热处理后再进行500℃保温8h的时效处理。
步骤a中的轧制板坯可以但不限于通过以下锻造工艺获得：
⑴铸锭原始尺寸Φ630mm×2020mm，第一次高温两镦两拔锻造：铸锭加热保温温度1100℃，保温时间6h，开锻温度1050℃，终锻温度820℃，工艺为两镦两拔，镦拔过程控制：先镦粗 至铸锭高度1050mm，再拔长回高度2020mm，回炉保温4h后，出炉再次墩拔，先镦粗至铸锭高度950mm，再拔长回高度2020mm，形状为八方，单边压下量30mm，锻造后甩出清理表面；
⑵第二次低温镦拔+镦粗及延展拔长锻造：坯料加热保温温度950℃，保温时间6h，开锻温度920℃，终锻温度750℃，工艺为一镦一拔，再次镦粗后延展拔长：第一次镦拔过程控制：先镦粗至高度1150mm，回炉保温4h，再出炉拔长至高度2020mm，拔长按“八方变形”，单边压下量50mm。第二次镦粗及延展拔长：先镦粗至高度1300mm，回炉保温3h，再出炉后延展拔长，拔长按“四方变形”，锻造后板坯尺寸厚度120mm×宽度1050mm×长度4800mm，铣削表面氧化皮，沿长度三等分后，获得尺寸厚度111mm×宽度990mm×长度1500mm的轧制板坯。
实施例1最终获得的特种车辆用钛合金板材组织如图1所示，由图1可知，实施例1获得的组织为片层组织，片层厚度2-3μm；对材料进行靶试测试(靶试条件：板厚8mm，53式7.62mm钢芯弹100米0°入射角)，结果如图2所示，由图2可知，实施例1的板材能够对53式100米0°入射角的7.62mm钢芯弹进行有效防护，该组织具有良好的抗高速冲击性能。
实施例2
a.选用特种车辆用钛合金轧制板坯尺寸规格为：厚度120mm×宽度1000mm×长度1300mm，采用步进式电加热炉对坯料进行加热，各段温度及保温时间满足：预热段750℃保温20min，加热段1050℃保温20min，均热段1050℃保温90min；
b.将配料冷却至轧制温度后，关闭辊道冷却水以及除磷水，快速将坯料传送至可逆式轧机进行换向轧制，首先进行横向宽展大压下量粗轧β相区，轧制温度为1000℃，轧制后的坯料尺寸：厚度50mm×宽度2200mm×长度1350mm；随后将板坯换向，采用手持式红外测温仪测试板坯温度，当温度为950℃后，进行两相区轧制，轧制后的坯料尺寸：厚度8mm×宽度2200mm×长度9000mm；
c.对轧制后的装甲钛合金板材进行水冷快速冷却至185℃，随后进行900℃保温时间2h的固溶热处理，完成固溶热处理后再进行600℃保温12h的时效处理。
步骤a中的轧制板坯可以但不限于通过以下锻造工艺获得：
(1)铸锭原始尺寸Φ610mm×1950mm，第一次高温两镦两拔锻造：铸锭加热保温温度1150℃，保温时间5h，开锻温度1100℃，终锻温度870℃，工艺为两镦两拔，镦拔过程控制：先镦粗至铸锭高度1000mm，再拔长回高度1950mm，回炉保温4h后，出炉再次墩拔，先镦粗至铸锭高度1000mm，再拔长回高度1950mm，形状为八方，单边压下量50mm，锻造后甩出清 理表面；
(2)第二次低温镦拔+镦粗及延展拔长锻造：坯料加热保温温度980℃，保温时间5h，开锻温度930℃，终锻温度780℃，工艺为一镦一拔，再次镦粗后延展拔长：第一次镦拔过程控制：先镦粗至高度1050mm，回炉保温4h，再出炉拔长至高度1950mm，拔长按“八方变形”，单边压下量50mm。第二次镦粗及延展拔长：先镦粗至高度1250mm，回炉保温3h，再出炉后延展拔长，拔长按“四方变形”，锻造后板坯尺寸厚度130mm×宽度1100mm×长度4200mm，铣削表面氧化皮，沿长度三等分后，获得尺寸厚度120mm×宽度1000mm×长度1300mm的轧制板坯。
实施例2最终获得的特种车辆用钛合金板材组织如图3所示，由图可知，实施例2获得的组织为片层组织，片层厚度1-2μm；对材料进行靶试测试(靶试条件：板厚8mm，53式7.62mm钢芯弹100米0°入射角)，结果如图4所示，由图可知，实施例2的板材能够对53式100米0°入射角的7.62mm钢芯弹进行有效防护，该组织具有良好的抗高速冲击性能。
实施例3
a.选用特种车辆用钛合金轧制板坯尺寸规格为：厚度100mm×宽度1100mm×长度1400mm，采用步进式电加热炉对坯料进行加热，各段温度及保温时间满足：预热段670℃保温20min，加热段1050℃保温15min，均热段1040℃保温80min；
b.将配料冷却至轧制温度后，关闭辊道冷却水以及除磷水，快速将坯料传送至可逆式轧机进行换向轧制，首先进行横向宽展大压下量粗轧β相区，轧制温度为1000℃，轧制后的坯料尺寸：厚度50mm×宽度2200mm×长度1450mm；随后将板坯换向，采用手持式红外测温仪测试板坯温度，当温度为950℃后，进行两相区轧制，轧制后的坯料尺寸：厚度8mm×宽度2200mm×长度9500mm；
c.对轧制后的装甲钛合金板材进行水冷快速冷却至150℃，随后进行850℃保温时间2h的固溶热处理，完成固溶热处理后再进行550℃保温12h的时效处理。
步骤a中的轧制板坯可以但不限于通过以下锻造工艺获得：
(1)铸锭原始尺寸Φ630mm×2000mm，第一次高温两镦两拔锻造：铸锭加热保温温度1050℃，保温时间6h，开锻温度1000℃，终锻温度820℃，工艺为两镦两拔，镦拔过程控制：先镦粗至铸锭高度1000mm，再拔长回高度2000mm，回炉保温6h后，出炉再次墩拔，先镦粗至铸锭高度1000mm，再拔长回高度2000mm，形状为八方，单边压下量30mm，锻造后甩出清 理表面；
(2)第二次低温镦拔+镦粗及延展拔长锻造：坯料加热保温温度950℃，保温时间6h，开锻温度920℃，终锻温度750℃，工艺为一镦一拔，再次镦粗后延展拔长：第一次镦拔过程控制：先镦粗至高度950mm，回炉保温4h，再出炉拔长至高度2000mm，拔长按“八方变形”，单边压下量50mm。第二次镦粗及延展拔长：先镦粗至高度1200mm，回炉保温3h，再出炉后延展拔长，拔长按“四方变形”，锻造后板坯尺寸厚度110mm×宽度1200mm×长度4500mm，铣削表面氧化皮，沿长度三等分后，获得尺寸厚度100mm×宽度1100mm×长度1400mm的轧制板坯。
实施例3最终获得的特种车辆用钛合金板材组织如图5所示，由图可知，实施例3获得的组织为片层组织，片层厚度2-3μm；对材料进行靶试测试(靶试条件：板厚8mm，53式7.62mm钢芯弹100米0°入射角)，结果如图6所示，由图可知，实施例3的板材能够对53式100米0°入射角的7.62mm钢芯弹进行有效防护，该组织具有良好的抗高速冲击性能。
对实施例1-3得到的板材进行力学性能测试(按国标规定测定双样)，其力学性能测试结果如表1所示。
表1实施例获得板材的力学性能
Figure PCTCN2022103831-appb-000001
由表1可知，实施例1的板材平均抗拉强度为1286MPa，在应变速率大于3000s-1的条件下，平均动态压缩强度达到1883MPa；实施例2的板材平均抗拉强度为1350MPa，在应变速率大于3000s-1的条件下，平均动态压缩强度达到2023MPa；实施例3的板材平均抗拉强度为1232MPa，在应变速率大于3000s-1的条件下，平均动态压缩强度达到1809MPa。采用本发明热加工工艺制备的特种车辆用两相钛合金，具有高强度和优异抗高速冲击性能，大幅提升了材料的防护性能。

Claims (7)

  1. 提高两相钛合金抗高速冲击性能的热加工方法，其特征在于包括如下步骤：
    a.对两相钛合金扁坯坯料进行加热，各段温度及保温时间满足：预热段＜850℃保温10-20min，加热段1050-1070℃保温10-20min，均热段1040-1060℃保温60-90min；
    b.采用换向轧制方式，首先进行横向粗轧，粗轧温度为990-1030℃，压下率为15-25％；随后将板坯换向，进行纵向轧制，轧制温度＜990℃，压下率为10-20％；
    c.将轧制后的板材水冷至＜200℃，随后进行固溶热处理和时效处理。
  2. 根据权利要求1所述的提高两相钛合金抗高速冲击性能的热加工方法，其特征在于：步骤a中，所述两相钛合金为Ti-4Al-1.5Cr-0.5Mo系特种车辆专用防弹装甲钛合金，所述扁坯由该钛合金经过高低温镦拔+延展拔长工艺锻造得到。
  3. 根据权利要求1所述的提高两相钛合金抗高速冲击性能的热加工方法，其特征在于：步骤a中，所述两相钛合金扁坯坯料尺寸为：厚度100-140mm×宽度800-1200mm×长度1200-2500mm。
  4. 根据权利要求3所述的提高两相钛合金抗高速冲击性能的热加工方法，其特征在于：所述两相钛合金扁坯坯料经横向粗轧后尺寸为：厚度60-90mm×宽度1200-2200mm×长度1200-2500mm。
  5. 根据权利要求4所述的提高两相钛合金抗高速冲击性能的热加工方法，其特征在于：所述两相钛合金扁坯坯料经纵向轧制后尺寸为：厚度6-20mm×宽度1200-2500mm×长度4000-12000mm。
  6. 根据权利要求1所述的提高两相钛合金抗高速冲击性能的热加工方法，其特征在于：步骤c中，固溶热处理为850-900℃保温1-2h。
  7. 根据权利要求1所述的提高两相钛合金抗高速冲击性能的热加工方法，其特征在于：步骤c中，时效处理为500-600℃保温8-12h。
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