WO2019119711A1 - Ti2AlNb基合金空心薄壁构件热态气压成形与热处理的方法 - Google Patents

Ti2AlNb基合金空心薄壁构件热态气压成形与热处理的方法 Download PDF

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WO2019119711A1
WO2019119711A1 PCT/CN2018/085969 CN2018085969W WO2019119711A1 WO 2019119711 A1 WO2019119711 A1 WO 2019119711A1 CN 2018085969 W CN2018085969 W CN 2018085969W WO 2019119711 A1 WO2019119711 A1 WO 2019119711A1
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Prior art keywords
gas
alnb
based alloy
pipe
hot
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PCT/CN2018/085969
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English (en)
French (fr)
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刘钢
苑世剑
王东君
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哈尔滨工业大学
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Application filed by 哈尔滨工业大学 filed Critical 哈尔滨工业大学
Priority to SG11201907160XA priority Critical patent/SG11201907160XA/en
Priority to US16/095,938 priority patent/US10688552B2/en
Publication of WO2019119711A1 publication Critical patent/WO2019119711A1/zh
Priority to ZA2019/05140A priority patent/ZA201905140B/en

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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D26/00—Shaping without cutting otherwise than using rigid devices or tools or yieldable or resilient pads, i.e. applying fluid pressure or magnetic forces
    • B21D26/02—Shaping without cutting otherwise than using rigid devices or tools or yieldable or resilient pads, i.e. applying fluid pressure or magnetic forces by applying fluid pressure
    • B21D26/033—Deforming tubular bodies
    • B21D26/041—Means for controlling fluid parameters, e.g. pressure or temperature
    • 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
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D26/00—Shaping without cutting otherwise than using rigid devices or tools or yieldable or resilient pads, i.e. applying fluid pressure or magnetic forces
    • B21D26/02—Shaping without cutting otherwise than using rigid devices or tools or yieldable or resilient pads, i.e. applying fluid pressure or magnetic forces by applying fluid pressure
    • B21D26/033—Deforming tubular bodies
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D26/00—Shaping without cutting otherwise than using rigid devices or tools or yieldable or resilient pads, i.e. applying fluid pressure or magnetic forces
    • B21D26/02—Shaping without cutting otherwise than using rigid devices or tools or yieldable or resilient pads, i.e. applying fluid pressure or magnetic forces by applying fluid pressure
    • B21D26/053—Shaping without cutting otherwise than using rigid devices or tools or yieldable or resilient pads, i.e. applying fluid pressure or magnetic forces by applying fluid pressure characterised by the material of the blanks
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • 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
    • B21K21/00—Making hollow articles not covered by a single preceding sub-group
    • B21K21/04—Shaping thin-walled hollow articles, e.g. cartridges
    • 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
    • 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

Definitions

  • the invention belongs to the technical field of plastic forming manufacturing of thin-walled members with difficult-to-deform materials, and in particular relates to a method for forming a hollow thin-walled member of Ti 2 AlNb-based alloy.
  • Hollow variable-section thin-walled components (such as intake pipes, nozzles, etc.) are widely used in aerospace vehicles.
  • Ti 2 AlNb based alloy has high room temperature ductility and fracture toughness, excellent high temperature resistance such as creep resistance, fatigue resistance and oxidation resistance, and also has the advantages of low density, low thermal expansion coefficient and non-magnetic property, so it is used at 600-800 °C.
  • One of the most promising materials for temperature replacement of superalloys is of great significance for aerospace vehicles to further reduce weight, increase payload and flight speed.
  • the key components of the aircraft power system (such as: intake port, nozzle, etc.) need to withstand high-speed high-pressure airflow, the service environment is very harsh, the working temperature of the component body reaches 600-800 ° C; the gas pressure of the component is usually several megapascals Ten atmospheres) up to 20 MPa (200 atmospheres). Therefore, such components are required to have excellent high temperature service properties (including high strength and a certain elongation at break, etc.).
  • the intake flow field control is realized, the risk of penetration of the aerodynamic heat caused by the stagnation point is avoided, and the shape and dimensional accuracy of the components such as the inlet port and the nozzle are very high, especially the inner surface precision. Demanding.
  • the Ti 2 AlNb-based alloy atoms are combined by a mixed bond in which metal bonds and covalent bonds coexist, they have intrinsic brittleness and can only be formed at a high temperature, and at the same time, the hollow thin-walled members cannot After the forming, mechanical machining, especially the inner profile of the component is basically impossible to process, so a high-precision high-temperature forming method is required, which directly meets the dimensional accuracy requirements of the profile during the forming process.
  • the Ti 2 AlNb based alloy In terms of component service performance regulation, the Ti 2 AlNb based alloy consists of ⁇ 2 , B 2 and O phases, wherein the O phase has higher intrinsic ductility than the ⁇ 2 phase, but the internal crack of the component is easily equiaxed O/ under service conditions. O-phase grain boundaries are formed, resulting in intergranular fracture. Therefore, the content and morphology of the O phase have a significant effect on the high temperature serviceability of Ti 2 AlNb based alloy components. Therefore, in order to obtain excellent use properties, the Ti 2 AlNb-based alloy member must be heat-treated after forming to improve microstructure (such as O phase content, morphology, size, etc.).
  • the object of the invention is to solve the problems that the existing Ti 2 AlNb-based alloy hollow thin-walled members are difficult to form, the process steps are complicated, the shape dimensional precision and the structural properties are contradictory, and the thermal state of the Ti 2 AlNb-based alloy hollow thin-walled members is provided.
  • Method of air pressure forming and heat treatment is provided.
  • the invention relates to a method of hot gas pressure forming and heat treatment of a Ti 2 AlNb based alloy hollow thin-walled member, wherein the method comprises the following steps:
  • (1) hot air pressure forming after heating the mold to a forming temperature of 970-990 ° C, the pipe blank is placed in the mold, wherein the mold is provided with a pipe inlet and a pipe outlet;
  • the inlet sealing plug is provided with a pipe for supplying the pipe blank.
  • the outlet seal plug being provided with a gas outlet passage for exhausting gas outward from the pipe of the pipe blank and for Opening or closing an air outlet switch of the gas outlet passage;
  • the temperature is maintained at a temperature of 970-990 ° C for 5 min-30 min, keeping the outlet switch in a closed state, and the intake switch is opened to allow the compressed gas I to enter the pipe of the pipe blank through the gas inlet passage.
  • the hot air pressure forming is carried out under the conditions of an inflation pressure of 5 MPa-70 MPa and a temperature of 970-990 ° C until the tube blank is completely formed, and a hot gas pressure formed tubular member is obtained;
  • Controlled cooling heat treatment opening the gas outlet switch, and then introducing a compressed gas II into the pipe of the hot gas pressure forming pipe from the gas inlet passage to make the hot gas pressure forming pipe fitting
  • the gas pressure in the pipeline is maintained at 1 MPa to 20 MPa, and the hot gas pressure formed pipe is air-cooled at a cooling rate of 0.3 ° C / s - 3.5 ° C / s;
  • the compressed gas II is continuously introduced, so that the gas pressure in the pipe of the pipe after the hot air pressure is formed is maintained at 1 MPa to 20 MPa, and the heat is further cooled at a cooling rate of 0.3 ° C / s - 3.5 ° C / s. After the air pressure is formed, the pipe is air-cooled;
  • the hot air pressure forming principle of the present invention a Ti 2 AlNb-based alloy thin-walled tube blank is used as a pipe blank, and the final shape of the control member is designed and optimized by a mold, and the mold is provided with a pipe inlet and a pipe outlet (also called a pipe outlet).
  • a pipe outlet also called a pipe outlet
  • the mold is provided with a pipe inlet and a pipe outlet (also called a pipe outlet).
  • the pipe exhaust port After the mold is heated to the forming temperature, the pipe billet is placed, and the exhaust port is closed during the bulging process, and the air inlet of the pipe is introduced to maintain the inflation pressure. Under the action of high temperature, the strength of the Ti 2 AlNb-based alloy thin-walled tube blank is reduced, and the plastic deformation ability is increased.
  • the tube blank When the applied atmospheric pressure causes the Ti 2 AlNb-based alloy tube blank to reach the yield condition, the tube blank is plastically deformed to achieve close contact.
  • Microstructure control performance of Ti 2 AlNb based alloy the cooling rate of the high temperature zone after forming is appropriately increased to reduce the size of the precipitated O photo layer, and the appropriate aging heat treatment condition parameters are combined to obtain a fine B 2 phase matrix.
  • the microstructure of a small amount of equiaxed ⁇ 2 phase and an appropriate amount of fine layered O phase is uniformly distributed to obtain excellent comprehensive performance.
  • the present invention completes the aging heat treatment at the same time as the hot air pressure forming, and does not require an additional heat treatment process, thereby improving production efficiency.
  • the aging heat treatment is performed by using the residual heat, and the heating is not required after cooling, thereby reducing the energy consumption.
  • the formed hollow thin-walled member controls the cooling rate in the mold by high-pressure gas circulation, which overcomes the problems of low cooling rate and long cooling time of the component, resulting in excessive O-phase content and coarse structure.
  • the obtained Ti 2 AlNb-based alloy hollow thin-walled member has good microstructure and realizes controllability and control integration.
  • the microstructure of the Ti 2 AlNb-based alloy hollow thin-walled member obtained by the present invention is such that a small amount of fine equiaxed ⁇ 2 phase and an appropriate amount of fine lamellar O phase are uniformly distributed in the B 2 phase matrix, wherein the layered The O photo layer size is 50-300 nm.
  • the mechanical properties of the Ti 2 AlNb-based alloy hollow thin-walled member obtained by the invention are: tensile yield strength ⁇ 1200 MPa, tensile rupture strength ⁇ 1350 MPa, elongation at break ⁇ 14% at room temperature; 750 ° C), tensile yield strength ⁇ 680 MPa (according to 0.2% plastic strain), tensile rupture strength ⁇ 780 MPa, elongation at break ⁇ 15%.
  • the dimensional accuracy index of the Ti 2 AlNb-based alloy hollow thin-walled member obtained by the present invention is: dimensional deviation ⁇ 0.2 mm, angular deviation ⁇ 0.25°.
  • the invention is mainly used for preparing a Ti 2 AlNb-based alloy hollow thin-walled member by hot air pressure forming and heat treatment.
  • the present invention relates to a Ti 2 AlNb based alloy hollow thin-walled member prepared by the above-described hot gas pressure forming and heat treatment method.
  • Fig. 1 is a schematic structural view of a mold according to an exemplary embodiment, in which 1 denotes a mold, 2 denotes a pipe inlet, 3 denotes a pipe outlet, 1-1 denotes an upper die, and 1-2 denotes a lower die. ;
  • 1 represents a mold
  • 4 denotes an inlet sealing plug
  • 5 denotes a gas outlet sealing plug
  • 6 denotes a gas inlet passage
  • 7 denotes a gas outlet passage
  • 8 denotes an intake switch
  • 9 denotes an outlet switch
  • 10 denotes a pipe blank
  • 1-1 denotes an upper die
  • 1-2 denotes a lower die
  • FIG. 3 is a schematic structural view of a mold after hot air pressure forming in an exemplary embodiment, wherein 1 represents a mold, 4 denotes an air inlet sealing plug, 5 denotes a gas outlet sealing plug, and 6 denotes a gas inlet passage, 7 Indicates a gas outlet passage, 8 denotes an intake switch, 9 denotes an outlet switch, 11 denotes a hot gas formed pipe, 1-1 denotes an upper die, and 1-2 denotes a lower die;
  • Figure 4 is a physical photograph of an exemplary tube blank employed in step (1) of Example 1;
  • Example 5 is a physical photograph of an exemplary Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 1;
  • FIG. 6 is a diagram showing the hot gas forming and heat treatment process steps of an exemplary Ti 2 AlNb based alloy hollow thin-walled member in Examples 1 and 2, wherein T1 represents the forming temperature, T2 represents the heat treatment temperature, and P1 represents the forming air expansion pressure. , P2 represents the heat treatment gas pressure;
  • FIG. 7 is a flow chart showing the forming process of the Ti 2 AlNb-based alloy hollow thin-walled members in Examples 3 and 4.
  • T1 represents the forming temperature
  • P1 represents the forming inflation pressure, wherein 1 represents quenching rapid cooling, and 2 represents Slowly cooling with the mold;
  • Example 8 is a microstructure diagram of an exemplary Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 1;
  • Example 9 is a microstructure diagram of an exemplary Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 2 ;
  • Example 10 is a microstructure diagram of a Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 3;
  • Figure 11 is a microstructure diagram of a Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 4.
  • Figure 12 is a tensile test piece of a Ti 2 AlNb-based alloy hollow thin-walled member
  • Figure 13 is a graph showing the tensile properties at room temperature, wherein A represents the room temperature tensile property of the Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 3, and B shows an exemplary Ti 2 AlNb-based alloy obtained in Example 1.
  • the room temperature tensile property curve of the hollow thin-walled member, and C in the figure shows the room temperature tensile property curve of the Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 4;
  • Figure 14 is a graph showing the tensile properties at room temperature, wherein A represents the room temperature tensile property of the Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 3, and B shows an exemplary Ti 2 AlNb-based alloy obtained in Example 1.
  • the room temperature tensile property curve of the hollow thin-walled member, B2 in the figure shows the room temperature tensile property curve of the exemplary Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 2
  • C in the figure shows the Ti 2 AlNb group obtained in Example 4.
  • Figure 15 is a tensile property curve at a temperature of 750 ° C, wherein A shows the tensile properties of the Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 3 at a temperature of 750 ° C, and B shows that Example 1 is obtained.
  • Figure 16 is a tensile property curve at a temperature of 750 ° C, wherein A shows the tensile properties of the Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 3 at a temperature of 750 ° C, and B shows that Example 1 is obtained.
  • Tensile performance curve of an exemplary Ti 2 AlNb based alloy hollow thin-walled member at a temperature of 750 ° C and B2 in the figure shows an exemplary Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 2 at a temperature of 750 ° C
  • the tensile property curve of the graph shows that the tensile properties of the Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 4 at a temperature of 750 ° C.
  • the term “hollow thin-walled member” encompasses “tubing” and means a member having a hollow outer diameter to wall thickness of any shape of not less than 20.
  • hot gas pressure forming may also be referred to as “flat expansion” unless otherwise indicated.
  • (1) hot air pressure forming after the mold 1 is heated to a forming temperature of 970-990 ° C, the pipe blank 10 is placed in the mold 1, wherein the mold 1 is provided with a pipe inlet 2 and a pipe outlet 3;
  • the inlet end of the pipe material 10 and the outlet end of the pipe material 10 (the end of the pipe material 10 near the pipe inlet 2 and the end near the pipe outlet 3 are respectively referred to as the pipe blank 10
  • the inlet end and the outlet end of the pipe blank 10 are sealed by an inlet sealing plug 4 and an outlet sealing plug 5, respectively, wherein the inlet sealing plug 4 is provided with a gas for supplying a pipe to the pipe blank 10.
  • the outlet sealing plug 5 being provided with a gas outlet passage 7 for discharging gas outward from the pipe of the pipe blank.
  • an air outlet switch 9 for opening or closing the gas outlet passage ie, sealing the inlet end of the pipe material 10 with the inlet sealing plug 4, and the gas inlet sealing plug 4 is provided with a gas communicating with the pipe material 10 pipe
  • the intake passage 6, the external opening of the gas inlet passage 6 is provided with an intake switch 8, the outlet end of the pipe blank 10 is sealed by the air outlet sealing plug 5, and the gas outlet of the pipe blank 10 is connected to the air outlet sealing plug 5 aisle 7, the gas outlet channel 7 is provided at the outer opening of the gas outlet switch 9);
  • the temperature is maintained at a temperature of 970-990 ° C for 5 min-30 min, the outlet switch 9 is kept in a closed state, and the intake switch 8 is opened to allow the compressed gas I to enter the pipe blank 10 through the gas inlet passage 6 .
  • the hot air pressure forming is performed under the conditions of an inflation pressure of 5 MPa-70 MPa and a temperature of 970-990 ° C until the tube blank 10 is completely formed, and the hot-bar formed pipe is obtained;
  • Controlled cooling heat treatment opening the gas outlet switch 9, and then introducing a compressed gas II from the gas inlet passage 6 into the pipe of the hot gas formed pipe to form a pipe of the pipe after the hot air pressure is formed
  • the gas pressure inside is maintained at 1 MPa-20 MPa, and the tube after hot state air forming is air-cooled at a cooling rate of 0.3 ° C / s - 3.5 ° C / s;
  • the compressed gas II is continuously introduced, so that the gas pressure in the pipe of the pipe after the hot air pressure is formed is maintained at 1 MPa to 20 MPa, and then the hot air pressure is maintained at a cooling rate of 0.3 ° C / s - 3.5 ° C / s.
  • the pipe is air-cooled;
  • the mold 1 described in the step (1) of the above exemplary embodiment is composed of an upper mold 1-1 and a lower mold 1-2.
  • 1 is a schematic structural view of a mold in the above exemplary embodiment, wherein 1 represents a mold, 2 represents a pipe inlet, 3 represents a pipe outlet, 1-1 represents an upper die, and 1-2 represents a lower die;
  • Figure 2 is a schematic view showing the structure of the mold after the mold clamping in the above exemplary embodiment, wherein 1 is a mold, 4 is an air inlet sealing plug, 5 is a gas outlet sealing plug, and 6 is a gas inlet passage, 7 Indicates a gas outlet passage, 8 denotes an intake switch, 9 denotes an outlet switch, 10 denotes a pipe blank, 1-1 denotes an upper die, and 1-2 denotes a lower die;
  • FIG. 3 is a schematic structural view of a mold after hot air pressure forming in the above exemplary embodiment, wherein 1 represents a mold, 4 denotes an air inlet sealing plug, 5 denotes a gas outlet sealing plug, and 6 denotes a gas inlet passage, 7 denotes a gas outlet passage, 8 denotes an intake switch, 9 denotes an outlet switch, 11 denotes a hot gas formed pipe, 1-1 denotes an upper die, and 1-2 denotes a lower die;
  • the hot gas forming in step (1) above can be accomplished under vacuum conditions.
  • the hot gas pressure forming in the above step (1) can also be carried out under an inert atmosphere.
  • the inert atmosphere includes, but is not limited to, a nitrogen atmosphere, a helium atmosphere, a helium atmosphere, an argon atmosphere, a helium atmosphere, a helium atmosphere, a mixture thereof, and the like.
  • the mold 1 in the above step (1), may be heated to a forming temperature of 970 to 990 ° C at an arbitrary heating rate, for example, at a heating rate of 1 ° C/min to 10 ° C/min. 1 Heat to a forming temperature of 970-990 °C.
  • the tube blank 10 described in step (1) has a circular, elliptical or polygonal cross section.
  • the pipe material 10 described in the step (1) may satisfy the requirement that the ratio of the outer diameter to the wall thickness is not less than 20, and the thickness, outer diameter and length of the pipe material 10 are not particularly affected.
  • the thickness of the pipe material 10 described in the step (1) may be 1 mm to 6 mm
  • the outer diameter of the pipe material may be 20 mm to 3000 mm
  • the length of the pipe material may be 100 mm to 2000 mm.
  • the pipe material 10 described in the step (1) is a Ti 2 AlNb-based alloy pipe material, and the atomic percentage of Ti in the Ti 2 AlNb-based alloy is 41.5% to 58%, and the atomic percentage of Al is 22%-25%, the atomic percentage of Nb is 20%-30%.
  • the Ti 2 AlNb-based alloy further contains Mo, and the atomic percentage of Mo in the Ti 2 AlNb-based alloy is 0.01% to 1.5%.
  • the Ti 2 AlNb-based alloy further contains V, and the atomic percentage of V in the Ti 2 AlNb-based alloy is 0.01% to 2%.
  • the compressed gas I described in the step (1) may be a compressed gas of air, a compressed gas of argon, a compressed gas of nitrogen, a compressed gas of helium or a compressed gas of CO 2 .
  • the compressed gas II described in the step (2) may be a compressed gas of air, a compressed gas of argon, a compressed gas of nitrogen, a compressed gas of helium or a compressed gas of CO 2 .
  • the Ti 2 AlNb-based alloy hollow thin-walled member obtained in the step (2) has a circular, elliptical, polygonal or irregular cross section.
  • the axial shape of the Ti 2 AlNb-based alloy hollow thin-walled member obtained in the step (2) is a straight line, an in-plane curve or a spatial curve.
  • the content of the present invention is not limited to the contents of the above embodiments, and a combination of one or several specific embodiments can also achieve the object of the invention.
  • Example 3 and Example 4 were used as comparative examples.
  • Embodiment 1 Method for hot air pressure forming and heat treatment of Ti 2 AlNb based alloy hollow thin-walled member of the present invention
  • the method of hot air forming and heat treatment of the Ti 2 AlNb-based alloy hollow thin-walled member described in Embodiment 1 comprises the following steps:
  • (1) hot air pressure forming after the mold 1 is heated at a heating rate of 8 ° C / min to a forming temperature of 970 ° C, the pipe material 10 is placed in a mold 1, wherein the mold 1 is provided with a pipe inlet 2 and Pipe outlet 3;
  • the inlet port 2 and the outlet port 3 of the pipe are respectively inserted into the inlet sealing plug 4 and the outlet sealing plug 5 to respectively seal the inlet end of the pipe blank 10 and the outlet end of the pipe blank 10
  • One end of the pipe material 10 near the pipe air inlet 2 and one end near the pipe air outlet 3 are respectively referred to as an inlet end of the pipe material 10 and an outlet end of the pipe material 10, wherein the air inlet
  • the sealing plug 4 is provided with a gas intake passage 6 for supplying a gas to the pipe of the pipe blank 10 and an intake switch 8 for opening or closing the gas intake passage
  • the outlet sealing plug 5 being provided for a gas outlet passage 7 for exhausting gas from the pipe of the pipe blank and an outlet switch 9 for opening or closing the gas outlet passage;
  • the temperature is maintained at 970 ° C for 20 min, keeping the outlet switch 9 in a closed state, and the intake switch 8 is opened to allow the compressed gas I to enter the pipe of the pipe material 10 through the gas inlet passage 6 at the inflation pressure.
  • the hot air pressure forming is carried out under the condition of 15 MPa and a temperature of 970 ° C until the pipe material 10 is completely formed, and the hot gas pressure formed pipe is obtained;
  • Controllable cooling heat treatment opening the gas outlet switch 9, and then introducing a compressed gas II from the gas inlet passage 6 into the pipe of the hot gas formed pipe to form the hot gas pressure
  • the gas pressure in the pipe of the rear pipe is maintained at 2 MPa, and the pipe member after hot air forming is air-cooled at a cooling rate of 0.4 ° C/s;
  • the compressed gas II is continuously introduced, the gas pressure in the pipe of the pipe after the hot air pressure is formed is maintained at 2 MPa, and the hot gas pressure forming pipe is gas-cut at a cooling rate of 0.4 ° C/s. cold;
  • Example 1 The hot air pressure forming in the step (1) of Example 1 was carried out under vacuum.
  • the pipe billet described in the step (1) of Example 1 has a circular cross section.
  • the pipe material described in the step (1) of Example 1 had a thickness of 2 mm, the pipe material had an outer diameter of 40 mm, and the pipe material had a length of 200 mm.
  • the pipe billet described in the step (1) of the embodiment 1 is a Ti 2 AlNb-based alloy pipe billet, the atomic percentage of Ti in the Ti 2 AlNb-based alloy is 53.5%, the atomic percentage of Al is 22%, and the atomic percentage of Nb is 24%, and the Ti 2 AlNb-based alloy further contains Mo, and the atomic percentage of Mo in the Ti 2 AlNb-based alloy is 0.5%.
  • the compressed gas I described in the step (1) of the first embodiment is a compressed gas of argon gas; the compressed gas II described in the step (2) of the first embodiment is a compressed gas of argon gas.
  • FIG. 4 is a photograph of a material of a pipe material used in the step (1) of the first embodiment; and FIG. 5 is a photograph of a material of the Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 1.
  • the present embodiment successfully realizes the pipe blank to be a Ti 2 AlNb-based alloy hollow thin-walled member.
  • FIG. 6 is a diagram showing a hot gas pressure forming and heat treatment process of a Ti 2 AlNb-based alloy hollow thin-walled member in Embodiment 1.
  • T1 represents a forming temperature
  • T2 represents a heat treatment temperature
  • P1 represents a forming inflation pressure
  • P2 represents a heat treatment gas. pressure. It can be seen from FIG. 6 that the present embodiment uses the residual heat to complete the aging heat treatment after forming, and does not need to be cooled and then reheated, thereby reducing energy consumption.
  • Fig. 8 is a microstructure diagram of a Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 1. It can be seen from FIG. 8 that since the Ti 2 AlNb-based alloy hollow thin-walled member is formed by the hot gas pressure forming and the heat treatment forming control integrated technology of the Ti 2 AlNb-based alloy hollow thin-walled member, the microstructure of the obtained Ti 2 AlNb-based alloy hollow thin-walled member is the most excellent. It is shown that the B 2 phase matrix (bright contrast) is distributed with a fine equiaxed ⁇ 2 phase (dark contrast) and a fine lamellar O phase (gray contrast), wherein the O photo layer has a thickness of 100-200 nm.
  • Embodiment 2 Method for hot air pressure forming and heat treatment of Ti 2 AlNb based alloy hollow thin-walled member of the present invention
  • the method of hot air forming and heat treatment of the Ti 2 AlNb based alloy hollow thin-walled member described in Embodiment 2 comprises the following steps:
  • Hot air pressure forming After the mold 1 is heated at a heating rate of 3 ° C / min to a forming temperature of 990 ° C, the pipe blank 10 is placed in a mold 1, wherein the mold 1 is provided with a pipe inlet 2 and Pipe outlet 3;
  • the inlet port 2 and the outlet port 3 of the pipe are respectively inserted into the inlet sealing plug 4 and the outlet sealing plug 5 to respectively seal the inlet end of the pipe blank 10 and the outlet end of the pipe blank 10
  • One end of the pipe material 10 near the pipe air inlet 2 and one end near the pipe air outlet 3 are respectively referred to as an inlet end of the pipe material 10 and an outlet end of the pipe material 10, wherein the air inlet
  • the sealing plug 4 is provided with a gas intake passage 6 for supplying a gas to the pipe of the pipe blank 10 and an intake switch 8 for opening or closing the gas intake passage
  • the outlet sealing plug 5 being provided for a gas outlet passage 7 for exhausting gas from the pipe of the pipe blank and an outlet switch 9 for opening or closing the gas outlet passage;
  • the temperature is maintained at 990 ° C for 10 min, the outlet switch 9 is kept in the closed state, and the air inlet switch 8 is opened to allow the compressed gas I to enter the pipe of the pipe material 10 through the gas inlet passage 6 at the inflation pressure.
  • the hot air pressure forming is carried out under the condition of 50 MPa and a temperature of 990 ° C until the pipe material 10 is completely formed, and the hot gas pressure formed pipe is obtained;
  • Controllable cooling heat treatment opening the gas outlet switch 9, and then introducing a compressed gas II from the gas inlet passage 6 into the pipe of the hot gas formed pipe to form the hot gas pressure
  • the gas pressure in the pipe of the rear pipe member is maintained at 10 MPa, and the pipe member after the hot air pressure forming is air-cooled at a cooling rate of 1.5 ° C/s;
  • the compressed gas II is continuously introduced, the gas pressure in the pipe of the pipe after the hot air pressure is formed is maintained at 10 MPa, and the hot gas formed pipe is gas-cut at a cooling rate of 1.5 ° C/s. cold;
  • Example 2 The hot air pressure forming in the step (1) of Example 2 was carried out under vacuum.
  • the pipe billet described in the step (1) of Example 2 has a circular cross section.
  • the pipe material described in the step (1) of Example 2 had a thickness of 2 mm, the pipe material had an outer diameter of 40 mm, and the pipe material had a length of 200 mm.
  • the pipe billet described in the step (1) of the embodiment 2 is a Ti 2 AlNb-based alloy pipe billet, the atomic percentage of Ti in the Ti 2 AlNb-based alloy is 53.5%, the atomic percentage of Al is 22%, and the atomic percentage of Nb is 24%, and the Ti 2 AlNb-based alloy further contains Mo, and the atomic percentage of Mo in the Ti 2 AlNb-based alloy is 0.5%.
  • the compressed gas I described in the step (1) of the second embodiment is a compressed gas of argon gas; the compressed gas II described in the step (2) of the second embodiment is a compressed gas of argon gas.
  • FIG. 6 is a view showing a hot air pressure forming and heat treatment process of a Ti 2 AlNb-based alloy hollow thin-walled member in Embodiment 2, in which T1 represents a forming temperature, T2 represents a heat treatment temperature, P1 represents a forming air pressure, and P2 represents a heat treatment gas. pressure. It can be seen from FIG. 6 that the present embodiment uses the residual heat to complete the aging heat treatment after forming, and does not need to be cooled and then reheated, thereby reducing energy consumption.
  • Fig. 9 is a microstructure diagram of a Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 2. It can be seen from FIG. 9 that the microstructure of the Ti 2 AlNb-based alloy hollow thin-walled member obtained by using the Ti 2 AlNb-based alloy hollow thin-walled member by hot gas pressure forming and heat treatment forming control integrated technology is superior in this embodiment. It is shown that the B 2 phase matrix (bright contrast) is distributed with a fine equiaxed ⁇ 2 phase (dark contrast) and a fine lamellar O phase (gray contrast), wherein the O photo layer has a thickness of 100-200 nm.
  • Embodiment 3 Method for hot air pressure forming of existing Ti 2 AlNb based alloy hollow thin-walled member
  • the method includes the following steps:
  • Hot air pressure forming firstly, the mold is heated to a forming temperature of 970 ° C at a heating rate of 8 ° C / min, and then placed in a pipe billet; after the mold is closed, the mold is kept at a temperature of 970 ° C for 20 min, and charged. The gas is then subjected to hot gas pressure forming at a pressure of 15 MPa and a temperature of 970 ° C until the tube billet is completely formed, and a hot gas formed tube is obtained;
  • Cooling and heat treatment After quenching and rapid cooling, the hot gas is formed into a tube and then cooled to room temperature, then heated to 800 ° C, heat treated at 800 ° C for 30 min, and then rapidly cooled to room temperature by quenching to obtain Ti 2 AlNb based alloy. Hollow thin-walled members.
  • the hot air pressure forming in the step (1) of Example 3 was carried out under vacuum.
  • the pipe billet described in the step (1) of Example 3 has a circular cross section.
  • the thickness of the pipe material described in the step (1) of Example 3 was 2 mm, the outer diameter of the pipe material was 40 mm, and the length of the pipe material was 200 mm.
  • the pipe billet described in the step (1) of the embodiment 3 is a Ti 2 AlNb-based alloy pipe billet, the atomic percentage of Ti in the Ti 2 AlNb-based alloy is 53.5%, the atomic percentage of Al is 22%, and the atomic percentage of Nb is 24%, and the Ti 2 AlNb-based alloy further contains Mo, and the atomic percentage of Mo in the Ti 2 AlNb-based alloy is 0.5%.
  • the compressed gas described in the step (1) of Example 3 is an argon compressed gas.
  • Embodiment 4 Method for hot air pressure forming of existing Ti 2 AlNb based alloy hollow thin-walled members
  • the method includes the following steps:
  • Hot air pressure forming firstly, the mold is heated to a forming temperature of 970 ° C at a heating rate of 8 ° C / min, and then placed in a pipe billet; after the mold is closed, the mold is kept at a temperature of 970 ° C for 20 min, and charged. The gas is then subjected to hot gas pressure forming at a pressure of 15 MPa and a temperature of 970 ° C until the tube billet is completely formed, and a hot gas formed tube is obtained;
  • Example 4 The hot air pressure forming in the step (1) of Example 4 was completed under vacuum.
  • the pipe billet described in the step (1) of Example 4 has a circular cross section.
  • the tube blank described in the step (1) of Example 4 had a thickness of 2 mm, the outer diameter of the tube material was 40 mm, and the length of the tube material was 200 mm.
  • the pipe billet described in the step (1) of the embodiment 4 is a Ti 2 AlNb-based alloy pipe billet, the atomic percentage of Ti in the Ti 2 AlNb-based alloy is 53.5%, the atomic percentage of Al is 22%, and the atomic percentage of Nb is 24%, and the Ti 2 AlNb-based alloy further contains Mo, and the atomic percentage of Mo in the Ti 2 AlNb-based alloy is 0.5%.
  • the compressed gas described in the step (1) of Example 4 is an argon compressed gas.
  • Figure 7 is a flow chart showing the forming process of the Ti 2 AlNb-based alloy hollow thin-walled members in Examples 3 and 4, wherein T1 represents the forming temperature, P1 represents the forming inflation pressure, and Figure 1 shows the quenching rapid cooling of Example 3. 2 in the figure shows the slow cooling with the mold of Example 4.
  • FIG. 10 is a microstructure diagram of a Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 3; and FIG. 11 is a microstructure diagram of a Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 4.
  • FIG. 10 for the Ti 2 AlNb-based alloy hollow thin-walled member which is quenched and rapidly cooled, since the cooling rate is fast, when the air is swollen at 970 ° C, the O phase dissolved in the B 2 phase matrix is too late to be precipitated.
  • Its microstructure is that the equiaxed ⁇ 2 phase is distributed in the B 2 phase matrix, and no O phase exists. It can be seen from Fig.
  • the Ti 2 AlNb-based alloy hollow thin-walled member which is slowly cooled by the mold has a microstructure in which the equiaxed ⁇ 2 phase and the lamellar O phase are distributed in the B 2 phase matrix, but due to the high temperature region ( 970-850 ° C) The cooling rate is slow, the lamellar O phase is large in size, and the O photo layer has a thickness of 1 ⁇ m to 2 ⁇ m.
  • Fig. 12 is a graph showing the tensile properties of a Ti 2 AlNb-based alloy hollow thin-walled member.
  • FIG. 13 and FIG. 14 are tensile properties at room temperature, in which A represents the room temperature tensile property curve of the Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 3, and B shows the Ti 2 AlNb-based alloy obtained in Example 1.
  • C in the figure shows the Ti 2 AlNb-based alloy hollow thin film obtained in Example 4.
  • FIG. 15 and FIG. 16 are tensile performance curves at a temperature of 750 ° C, and A shows the tensile properties of the Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 3 at a temperature of 750 ° C, and B shows the implementation.
  • the Ti 2 AlNb-based alloy hollow thin-walled members obtained in Examples 1 to 4 were subjected to a tensile test, and the tensile test specimen shown in Fig. 12 was used, and the room temperature tensile test was performed at a strain rate of 0.001 s -1 ;
  • Tensile specimens shown in Figure 12 when the furnace temperature was raised to 750 ° C, placed in a tensile specimen, kept for 5 min to make the specimen temperature uniform, and then subjected to a tensile test at 750 ° C at a strain rate of 0.001 s -1 and recorded until The stress-strain relationship at break gives a tensile curve as shown in Figures 13-16. 13 and FIG.
  • A represents the room temperature tensile property curve of the Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 3
  • B shows the Ti 2 AlNb-based alloy obtained in Example 1.
  • the room temperature tensile property curve of the hollow thin-walled member, B2 in the figure shows the room temperature tensile property curve of the Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 2
  • C in the figure shows the Ti 2 AlNb-based alloy hollow thin film obtained in Example 4.
  • A shows the tensile properties of the Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 3 at a temperature of 750 ° C
  • B shows the implementation.
  • B2 in the figure shows the stretching of the Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 2 at a temperature of 750 ° C
  • the performance curve, C in the figure shows the tensile performance curve of the Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 4 at a temperature of 750 °C.
  • the Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 1 has a yield strength at room temperature of 1214 MPa, a tensile strength of 1378 MPa, and an elongation at break of 14.6%; Ti obtained in Example 2 2
  • the AlNb-based alloy hollow thin-walled member has a yield strength of 1202 MPa at room temperature, a tensile strength of 1413 MPa, and an elongation at break of 14.3%.
  • the Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 1 has a yield strength of 688 MPa at a high temperature (750 ° C), a tensile strength of 801 MPa, and an elongation at break of 22.5%.
  • the Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 2 has a yield strength of 685 MPa under high temperature conditions (750 ° C), a tensile strength of 805 MPa, and a tensile elongation at break of 19.4%.
  • the Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 3 has a low elongation at room temperature of 25.5%, but has a low strength, a yield strength of 1110 MPa, and a tensile strength of 1112 MPa.
  • the Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 4 had the lowest yield strength (855 MPa) at room temperature, a tensile strength of 1124 MPa, and an elongation at break of 14.3%.
  • the Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 3 has a yield strength of 804 MPa at a high temperature (750 ° C), a tensile strength of 906 MPa, but a minimum elongation at break.
  • the Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 4 has a tensile elongation at a high temperature (750 ° C) of 15.1%, but the strength is the lowest, and the yield strength is 511 MPa, and the tensile strength is Only 612 MPa.
  • the Ti 2 AlNb-based alloy hollow thin-walled members obtained in Example 1 and Example 2 have the most excellent comprehensive mechanical properties.
  • the Ti 2 AlNb-based alloy hollow thin-walled members obtained in Examples 1 to 4 were tested for dimensional accuracy according to the following steps: measuring the section height, width and fillet radius dimensions of the hollow thin-walled members, and it was found by the test that Example 1 and the implementation were carried out.
  • the length, width and fillet radius dimensional deviation of the Ti 2 AlNb based alloy hollow thin-walled members obtained in Example 2 are less than 0.2 mm, and the cross-sectional angle deviation is less than 0.2°, which satisfies the design requirements of such components (design requirements are dimensional deviation ⁇ 0.25 mm) ).
  • the Ti 2 AlNb-based alloy hollow thin-walled member obtained in Example 3 has a maximum deviation of 0.27 mm, a maximum deviation of 0.25 mm, and a cross-sectional angular deviation of 0.34°; the Ti 2 AlNb-based alloy hollow thin wall obtained in Example 4
  • the maximum deviation of the length of the member was 0.26 mm, the maximum deviation of the width was 0.22 mm, and the deviation of the section angle was 0.26°.
  • the Ti 2 AlNb-based alloy hollow thin-walled members obtained in Example 1 and Example 2 have the best shape and dimensional accuracy.

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Abstract

Ti2AlNb基合金空心薄壁构件热态气压成形与热处理的方法，包括步骤：(1)热态气压成形：将模具（1）加热至成形温度后，将管材坯料（10）放入模具中，合模后将管材坯料的进气端和出气端分别密封，然后保持出气开关（9）处于关闭状态，打开进气开关（8），使压缩气体I进入管材坯料内，进行热态气压成形，从而得到热态气压成形后的管件；(2)可控冷却热处理：打开出气开关，然后从进气通道（6）向管道内通入压缩气体II，控制管道内的气压和温度，当热态气压成形后管件的温度降至400-500℃时，停止进气，得到Ti2AlNb基合金空心薄壁构件。该方法提高了生产效率，实现了控形控性一体化，得到的管材力学性能优异。以及一种采用热态气压成形与热处理方法制备的Ti2AlNb基合金空心薄壁构件。

Description

Ti 2AlNb基合金空心薄壁构件热态气压成形与热处理的方法 技术领域
本发明属于难变形材料薄壁构件塑性成形制造技术领域，具体涉及一种Ti 2AlNb基合金空心薄壁构件成形方法。
背景技术
随着航空航天工业的迅速发展，对于提高动力系统效率和降低能耗要求越来越迫切，空心变截面薄壁构件(如：进气道、喷管等)是航空航天飞行器中使用广、要求高、难制造的典型代表构件。Ti 2AlNb基合金室温塑性和断裂韧性较高，抗蠕变、抗疲劳和抗氧化性等高温性能优良，还具有低密度、低热膨胀系数和无磁性等优点，因此成为在600-800℃服役温度替代高温合金的最具潜力材料之一，对于航空航天飞行器进一步减重、提高有效载荷和飞行速度具有重要意义。
飞行器动力系统关键部件(如：进气道、喷管等)需承受高速高压气流冲刷，服役环境十分恶劣，构件本体工作温度达600-800℃；构件承受的气体压力通常是数兆帕(数十大气压)，最高可达20兆帕(200大气压)。因此，需要此类构件具有优异的高温服役性能(包括高强度及一定的断裂延伸率等)。同时，为了满足气体动力学要求，实现进气流场控制、避免驻点气动热过高引起的熔穿风险，进气道、喷管等构件的形状尺寸精度要求很高，尤其内型面精度要求苛刻。
在构件形状尺寸精度控制方面，由于Ti 2AlNb基合金原子之间为以金属键和共价键共存的混合键方式结合，具有本征脆性，只能在高温成形，同时由于空心薄壁构件不能在成形后再机械加工，尤其构件内型面基本无法加工，因此需要一种高精度的高温成形方法，在成形过程中直接满足型面尺寸精度要求。
在构件服役性能调控方面，Ti 2AlNb基合金由α 2、B 2和O相组成，其中O相的本征塑性高于α 2相，但在服役条件下构件内部裂纹容易在等轴O/O相晶界处形成，而产生晶间断裂。因此，O相的含量及形貌对Ti 2AlNb基合金构件的高温服役性能影响显著。因此，为了获得优异的使用性能，Ti 2AlNb基合金构件在成形后必须进行热处理，以改善微观组织(如O相含量、形貌和尺寸等)。
但是，Ti 2AlNb基合金空心薄壁构件的服役性能调控与形状尺寸精度控制矛盾非常突出。研制中发现，在热成形后将零件从模具中取出再进行热处理，会由于热处理过程组织演变和温度变化导致严重的形状畸变、尺寸精度超差、产品报废。因此，亟需开发Ti 2AlNb基合金空心薄壁构件成形控性一体化新工艺，以满足航空航天飞行器研制对高性能、高精度Ti 2AlNb基合金空心薄壁构件的迫切需求。
发明内容
本发明的目的是要解决现有Ti 2AlNb基合金空心薄壁构件难成形、工艺步骤复杂、且形状尺寸精度和组织性能调控矛盾的问题，从而提供Ti 2AlNb基合金空心薄壁构件热态气压成形与热处理的方法。
一方面，本发明涉及一种Ti 2AlNb基合金空心薄壁构件热态气压成形与热处理的方法，其中，所述方法包括以下步骤：
(1)热态气压成形：将模具加热至成形温度970-990℃后，将管材坯料放入所述模具中，其中，所述模具设有管材进气口和管材出气口；
合模后，将管材坯料进气端和管材坯料出气端分别用进气口密封塞和出气口密封塞进行密封，其中，所述进气口密封塞设置有用于向所述管材坯料的管道供给气体的气体进气通道以及用于打开或闭合所述气体进气通道的进气开关，所述出气口密封塞设置有用于从所述管材坯料的管道向外排出气体的气体出气通道以及用于打开或闭合所述气体出气通道的出气开关；
然后，在温度970-990℃下保温5min-30min，保持所述出气开关处于关闭状态，打开所述进气开关，使压缩气体Ⅰ通过所述气体进气通道进入所述管材坯料的管道内，在气胀压力为5MPa-70MPa和温度为970-990℃的条件下进行热态气压成形，直至管材坯料完全成形，得到热态气压成形后管件；
(2)可控冷却热处理：打开所述出气开关，然后，从所述气体进气通道向所述热态气压成形后管件的管道内通入压缩气体Ⅱ，使所述热态气压成形后管件的管道内的气体压力保持在1MPa-20MPa，以0.3℃/s-3.5℃/s的冷却速度对所述热态气压成形后管件进行气冷；
当所述热态气压成形后管件的温度降至780-830℃时，停止进气，在温度为780-830℃下保温30min-60min；
然后，继续通入所述压缩气体Ⅱ，使所述热态气压成形后管件的管道内的气体压力保持在1MPa-20MPa，再以0.3℃/s-3.5℃/s的冷却速度对所述热态气压成形后管件进行气冷；
当所述热态气压成形后管件的温度降至400-500℃时，停止进气，在通过所述气体出气通道泄压后开模，得到所述Ti 2AlNb基合金空心薄壁构件。
本发明的技术方案的原理及优点：
(i)本发明热态气压成形原理：以Ti 2AlNb基合金薄壁管坯作为管材坯料，通过模具设计与优化控制构件的最终形状，模具设有管材进气口和管材出气口(也称为“管材排气口”)，将模具加热至成形温度后，放入管材坯料，胀形过程中排气口关闭，由管材进气口进气并维持气胀压力。在高温作用下，Ti 2AlNb基合金薄壁管坯强度降低，塑性变形能力增加；当施加的气压压力使Ti 2AlNb基合金管坯达到屈服条件时，管坯通过塑性变形的方式达到紧贴模具内壁成形的目的。胀形结束后管材进气口和管材排气口均打开，由管材进气口进气，管材排气口排气，通过调节冷却气体来控制成形薄壁件的冷却速度，冷却处理过程中，仍维持一定的气体压力，以保证成形构件的形状尺寸精度。
(ii)Ti 2AlNb基合金微观组织性能调控原理：适当增加成形后高温区的冷却速度，达到减小析出O相片层尺寸的目的，结合适当的时效热处理条件参数，最终获得细小B 2相基体中均匀分布少量等轴α 2相以及适量的细小片层状O相的微观组织，以获得优异的综合使用性能。
(iii)本发明在热态气压成形的同时，完成时效热处理，不需要另外的热处理工序，因此提高了生产效率。
(iv)尺寸精度高：在气压支撑作用下使构件在模具内完成热处理，避免了热处理导致的形状畸变，因此尺寸精度高。
(v)在成形后利用余热完成时效热处理，不需冷却后再次加热，降低能耗。
(vi)成形后的空心薄壁构件在模具内通过高压气体循环控制冷速速度，克服了现有技术冷却速度低、构件降温时间长，导致O相含量过多、组织粗大等问题，所以本发明得到的Ti 2AlNb基合金空心薄壁构件组织性能好，实现了控形控性一体化。
(vii)本发明得到的Ti 2AlNb基合金空心薄壁构件的微观组织为：在B 2相基体中均匀分布少量细小的等轴α 2相以及适量的细小片层状O相，其中层状O相片层尺寸为50-300nm。
(viii)本发明得到的Ti 2AlNb基合金空心薄壁构件的力学性能为：室温条件下，拉伸屈服强度≥1200MPa，拉伸断裂强度≥1350MPa，断裂延伸率≥14％；高温条件下(750℃)，拉伸屈服强度≥680MPa(根据0.2％塑性应变)，拉伸断裂强度≥780MPa，断裂延伸率≥15％。
(ix)本发明得到的Ti 2AlNb基合金空心薄壁构件的形状尺寸精度指标为：尺寸偏差≤0.2mm，角度偏差≤0.25°。
本发明主要用于采用热态气压成形与热处理制备Ti 2AlNb基合金空心薄壁构件。
另一方面，本发明涉及采用上述的热态气压成形与热处理方法制备的Ti 2AlNb基合金空心薄壁构件。
附图说明
图1是示例性的具体实施方式中所述的模具的结构示意图，图中1表示模具，2表示管材进气口，3表示管材出气口，1-1表示上模具，1-2表示下模具；
图2是示例性的具体实施方式中的合模后的模具的结构示意图，图中1表示模具，4表示进气口密封塞，5表示出气口密封塞，6表示气体进气通道，7表示气体出气通道，8表示进气开关，9表示出气开关，10表示管材坯料，1-1表示上模具，1-2表示下模具；
图3是示例性的具体实施方式中的热态气压成形后模具的结构示意图，图中1表示模具，4表示进气口密封塞，5表示出气口密封塞，6表示气体进气通道，7表示气体出气通道，8表示进气开关，9表示出气开关，11表示热态气压成形后管件，1-1表示上模具，1-2表示下模具；
图4是实施例1中步骤(1)采用的示例性的管材坯料的实物照片；
图5是实施例1得到的示例性的Ti 2AlNb基合金空心薄壁构件的实物照片；
图6是实施例1和2中的示例性的Ti 2AlNb基合金空心薄壁构件热态气压成形与热处理工艺步骤图，图中T1表示成形温度，T2表示热处理温度，P1表示成形气胀压力，P2表示热处理气体压力；
图7是实施例3和4中的Ti 2AlNb基合金空心薄壁构件成形工艺步骤图，图中T1表示成形温度，P1表示成形气胀压力，图中①表示淬火快速冷却，图中②表示随模具缓慢冷却；
图8是实施例1得到的示例性的Ti 2AlNb基合金空心薄壁构件的微观组织图；
图9是实施例2得到的示例性的Ti 2AlNb基合金空心薄壁构件的微观组织图；
图10是实施例3得到的Ti 2AlNb基合金空心薄壁构件的微观组织图；
图11是实施例4得到的Ti 2AlNb基合金空心薄壁构件的微观组织图；
图12是Ti 2AlNb基合金空心薄壁构件的拉伸性能试件图；
图13是室温拉伸性能曲线，图中A表示实施例3得到的Ti 2AlNb基合金空心薄壁构件室温拉伸性能曲线，图中B表示实施例1得到的示例性的Ti 2AlNb基合金空心薄壁构件室温拉伸性能曲线，图中C表示实施例4得到的Ti 2AlNb基合金空心薄壁构件室温拉伸性能曲线；
图14是室温拉伸性能曲线，图中A表示实施例3得到的Ti 2AlNb基合金空心薄壁构件室温拉伸性能曲线，图中B表示实施例1得到的示例性的Ti 2AlNb基合金空心薄壁构件室温拉伸性能曲线，图中B2表示实施例2得到的示例性的Ti 2AlNb基合金空心薄壁构件室温拉伸性能曲线，图中C表示实施例4得到的Ti 2AlNb基合金空心薄壁构件室温拉伸性能曲线；
图15是温度750℃下的拉伸性能曲线，图中A表示实施例3得到的Ti 2AlNb基合金空心薄壁构件在温度750℃下的拉伸性能曲线，图中B表示实施例1得到的示例性的Ti 2AlNb基合金空心薄壁构件在温度750℃下的拉伸性能曲线，图中C表示实施例4得到的Ti 2AlNb基合金空心薄壁构件在温度750℃下的拉伸性能曲线；
图16是温度750℃下的拉伸性能曲线，图中A表示实施例3得到的Ti 2AlNb基合金空心薄壁构件在温度750℃下的拉伸性能曲线，图中B表示实施例1得到的示例性的Ti 2AlNb基合金空心薄壁构件在温度750℃下的拉伸性能曲线，图中B2表示实施例2得到的示例性的Ti 2AlNb基合金空心薄壁构件在温度750℃下的拉伸性能曲线，图中C表示实施例4得到的Ti 2AlNb基合金空心薄壁构件在温度750℃下的拉伸性能曲线。
具体实施方式
在本文中，除非另有说明，术语“空心薄壁构件”涵盖“管材”，是指具有任意形状的中空的外径与壁厚的比值不小于20的构件。
在本文中，除非另有说明，术语“热态气压成形”也可称为“气胀成形”。
为了更清楚地说明本发明请求保护的技术方案，在下文中给出了本发明的示例性的具体实施方式，但是本领域技术人员能够理解的是，本发明的保护范围并不仅限于此。
在一个实施方式中，结合图1至3，本发明的示例性的具体实施方式涉及的Ti 2AlNb基合金空心薄壁构件热态气压成形与热处理的方法包括以下步骤：
(1)热态气压成形：将模具1加热至成形温度970-990℃后，将管材坯料10放入模具1中，其中，所述模具1设有管材进气口2和管材出气口3；
合模后，将管材坯料10进气端和管材坯料10出气端(将所述管材坯料10靠近所述管材进气口2的一端和靠近所述管材出气口3的一端分别记为管材坯料10进气端和管材坯料10出气端)分别用进气口密封塞4和出气口密封塞5进行密封，其中，所述进气口密封塞4设置有用于向所述管材坯料10的管道供给气体的气体进气通道6以及用于打开或闭合所述气体进气通道的进气开关8，所述出气口密封塞5设置有用于从所述管材坯料的管道向外排出气体的气体出气通道7以及用于打开或闭合所述气体出气通道的出气开关9(即，利用进气口密封塞4密封管材坯料10进气端，且进气口密封塞4上设置与管材坯料10管道连通的气体进气通道6，气体进气通道6的外界开口处设置进气开关8，利用出气口密封塞5密封管材坯料10出气端，且出气口密封塞5上设置与管材坯料10管道连通的气体出气通道7，气体出气通道7的外界开口处设置出气开关9)；
然后，在温度970-990℃下保温5min-30min，保持所述出气开关9处于关闭状态，打开所述进气开关8，使压缩气体Ⅰ通过所述气体进气通道6进入所述管材坯料10的管道内，在气胀压力为5MPa-70MPa和温度为970-990℃的条件下进行热态气压成形，直至所述管材坯料10完全成形，得到热态气压成形后管件；
(2)可控冷却热处理：打开出气开关9，然后，从所述气体进气通道6向所述热态气压成形后管件的管道内通入压缩气体Ⅱ，使热态气压成形后管件的管道内的气体压力保持在1MPa-20MPa，以0.3℃/s-3.5℃/s的冷却速度对热态气压成形后管件进行气冷；
当所述热态气压成形后管件的温度降至780-830℃时，停止进气，在温度为780-830℃下保温30min-60min；
然后，继续通入所述压缩气体Ⅱ，使所述热态气压成形后管件的管道内的气体压力保持在1MPa-20MPa，再以0.3℃/s-3.5℃/s的冷却速度对热态气压成形后管件进行气冷；
当热态气压成形后管件的温度降至400-500℃时，停止进气，在通过所述气体出气通道7泄压后开模，得到Ti 2AlNb基合金空心薄壁构件。
上述示例性的实施方式的步骤(1)中所述的模具1由上模具1-1和下模具1-2组成。
图1是上述示例性的具体实施方式中的模具的结构示意图，图中1表示模具，2表示管材进气口，3表示管材出气口，1-1表示上模具，1-2表示下模具；
图2是上述示例性的具体实施方式中的合模后的模具的结构示意图，图中1表示模具，4表示进气口密封塞，5表示出气口密封塞，6表示气体进气通道，7表示气体出气通道，8表示进气开关，9表示出气开关，10表示管材坯料，1-1表示上模具，1-2表示下模具；
图3是上述示例性的具体实施方式中的热态气压成形后模具的结构示意图，图中1表示模具，4表示 进气口密封塞，5表示出气口密封塞，6表示气体进气通道，7表示气体出气通道，8表示进气开关，9表示出气开关，11表示热态气压成形后管件，1-1表示上模具，1-2表示下模具；
在另一实施方式中，上述步骤(1)中的热态气压成形可在真空条件下完成。
在另一实施方式中，上述步骤(1)中的热态气压成形还可在非活性气氛下完成。所述非活性气氛包括但不限于：氮气气氛、氦气气氛、氖气气氛、氩气气氛、氪气气氛、氙气气氛及它们的混合物等。
在另一实施方式中，在上述步骤(1)中，可采用任意的升温速率将模具1加热至成形温度970-990℃，例如，以1℃/min-10℃/min的升温速率将模具1加热至成形温度970-990℃。
在另一实施方式中，步骤(1)中所述的管材坯料10的截面呈圆形、椭圆形或多边形。
在另一实施方式中，步骤(1)中所述的管材坯料10只要满足外径与壁厚的比值不小于20的要求即可，而管材坯料10的厚度、外径和长度并不受到特别的限制，例如，步骤(1)中所述的管材坯料10的厚度可为1mm-6mm，管材坯料的外径可为20mm-3000mm，管材坯料的长度可为100mm-2000mm。
在另一实施方式中，步骤(1)中所述的管材坯料10为Ti 2AlNb基合金管材坯料，Ti 2AlNb基合金中的Ti的原子百分数为41.5％-58％，Al的原子百分数为22％-25％，Nb的原子百分数为20％-30％。
在另一实施方式中，所述Ti 2AlNb基合金还含有Mo，且Ti 2AlNb基合金中的Mo的原子百分数为0.01％-1.5％。
在另一实施方式中，所述Ti 2AlNb基合金还含有V，且Ti 2AlNb基合金中的V的原子百分数为0.01％-2％。
在另一实施方式中，步骤(1)中所述的压缩气体Ⅰ可为空气的压缩气体、氩气的压缩气体、氮气的压缩气体、氦气的压缩气体或CO 2的压缩气体。
在另一实施方式中，步骤(2)中所述的压缩气体Ⅱ可为空气的压缩气体、氩气的压缩气体、氮气的压缩气体、氦气的压缩气体或CO 2的压缩气体。
在另一实施方式中，步骤(2)中得到的Ti 2AlNb基合金空心薄壁构件的截面呈圆形、椭圆形、多边形或异形。
在另一实施方式中，步骤(2)中得到的Ti 2AlNb基合金空心薄壁构件的轴线形状为直线、平面内曲线或空间曲线。
本发明内容不仅限于上述各实施方式的内容，其中一个或几个具体实施方式的组合同样也可以实现发明的目的。
采用下述试验验证本发明效果，其中，实施例3和实施例4是用作对比的实施例。
实施例1：本发明的Ti 2AlNb基合金空心薄壁构件热态气压成形与热处理的方法
结合图1至3，实施例1所述的Ti 2AlNb基合金空心薄壁构件热态气压成形与热处理的方法包括以下步骤：
(1)热态气压成形：将模具1以升温速率8℃/min加热至成形温度970℃后，将管材坯料10放入模具1中，其中，所述模具1设有管材进气口2和管材出气口3；
合模后，向所述管材进气口2和所述管材出气口3分别塞入进气口密封塞4和出气口密封塞5以分别密封管材坯料10进气端和管材坯料10出气端(将所述管材坯料10靠近所述管材进气口2的一端和靠近所述管材出气口3的一端分别记为管材坯料10进气端和管材坯料10出气端)，其中，所述进气口密封塞4设置有用于向所述管材坯料10的管道供给气体的气体进气通道6以及用于打开或闭合所述气体进气通道的进气开关8，所述出气口密封塞5设置有用于从所述管材坯料的管道向外排出气体的气体出气通道7以及用于打开或闭合所述气体出气通道的出气开关9；
然后，在温度970℃下保温20min，保持所述出气开关9处于关闭状态，打开所述进气开关8，使压缩气体Ⅰ通过气体进气通道6进入管材坯料10的管道内，在气胀压力为15MPa和温度为970℃的条件下进行热态气压成形，直至管材坯料10完全成形，得到热态气压成形后管件；
(2)可控冷却热处理：打开所述出气开关9，然后，从所述气体进气通道6向所述热态气压成形后管件的管道内通入压缩气体Ⅱ，使所述热态气压成形后管件的管道内的气体压力保持在2MPa，以0.4℃/s的冷却速度对热态气压成形后管件进行气冷；
当上述热态气压成形后管件的温度降至800℃时，停止进气，在温度为800℃下保温30min；
然后，继续通入所述压缩气体Ⅱ，使所述热态气压成形后管件的管道内的气体压力保持在2MPa，再以0.4℃/s的冷却速度对所述热态气压成形后管件进行气冷；
当热态气压成形后管件的温度降至500℃时，停止进气，在通过所述气体出气通道7泄压后开模，得到Ti 2AlNb基合金空心薄壁构件。
实施例1步骤(1)中的热态气压成形在真空条件下完成。
实施例1步骤(1)中所述的管材坯料的截面呈圆形。
实施例1步骤(1)中所述的管材坯料的厚度为2mm，管材坯料的外径为40mm，管材坯料的长度为200mm。
实施例1步骤(1)中所述的管材坯料为Ti 2AlNb基合金管材坯料，Ti 2AlNb基合金中的Ti的原子百分数为53.5％，Al的原子百分数为22％，Nb的原子百分数为24％，且所述Ti 2AlNb基合金还含有Mo，Ti 2AlNb基合金中的Mo的原子百分数为0.5％。
实施例1步骤(1)中所述的压缩气体Ⅰ为氩气的压缩气体；实施例1步骤(2)中所述的压缩气体Ⅱ为氩气的压缩气体。
图4是实施例1中步骤(1)采用的管材坯料的实物照片；图5是实施例1得到的Ti 2AlNb基合金空心薄壁构件的实物照片。通过图5与图4对比可知，本实施例成功实现了将管材坯料制成Ti 2AlNb基合金空心薄壁构件。
图6是实施例1中的Ti 2AlNb基合金空心薄壁构件热态气压成形与热处理工艺步骤图，图中T1表示成形温度，T2表示热处理温度，P1表示成形气胀压力，P2表示热处理气体压力。通过图6可知本实施例在成形后利用余热完成时效热处理，不需冷却后再次加热，由此降低能耗。
图8是实施例1得到的Ti 2AlNb基合金空心薄壁构件的微观组织图。通过图8可以看出：由于本实施例采用Ti 2AlNb基合金空心薄壁构件热态气压成形与热处理成形控性一体化技术，获得的Ti 2AlNb基合金空心薄壁构件的微观组织最为优异，表现为B 2相基体(亮衬度)中分布着细小等轴α 2相(暗衬度)和细小片层状O相(灰色衬度)，其中O相片层厚度为100-200nm。
实施例2：本发明的Ti 2AlNb基合金空心薄壁构件热态气压成形与热处理的方法
结合图1至3，实施例2所述的Ti 2AlNb基合金空心薄壁构件热态气压成形与热处理的方法包括以下步骤：
(1)热态气压成形：将模具1以升温速率3℃/min加热至成形温度990℃后，将管材坯料10放入模具1中，其中，所述模具1设有管材进气口2和管材出气口3；
合模后，向所述管材进气口2和所述管材出气口3分别塞入进气口密封塞4和出气口密封塞5以分别密封管材坯料10进气端和管材坯料10出气端(将所述管材坯料10靠近所述管材进气口2的一端和靠近所述管材出气口3的一端分别记为管材坯料10进气端和管材坯料10出气端)，其中，所述进气口密封塞4设置有用于向所述管材坯料10的管道供给气体的气体进气通道6以及用于打开或闭合所述气体进气通道的进气开关8，所述出气口密封塞5设置有用于从所述管材坯料的管道向外排出气体的气体出气通道7以及用于打开或闭合所述气体出气通道的出气开关9；
然后，在温度990℃下保温10min，保持所述出气开关9处于关闭状态，打开所述进气开关8，使压缩气体Ⅰ通过气体进气通道6进入管材坯料10的管道内，在气胀压力为50MPa和温度为990℃的条件下进行热态气压成形，直至管材坯料10完全成形，得到热态气压成形后管件；
(2)可控冷却热处理：打开所述出气开关9，然后，从所述气体进气通道6向所述热态气压成形后管件的管道内通入压缩气体Ⅱ，使所述热态气压成形后管件的管道内的气体压力保持在10MPa，以1.5℃/s的冷却速度对热态气压成形后管件进行气冷；
当上述热态气压成形后管件的温度降至810℃时，停止进气，在温度为810℃下保温45min；
然后，继续通入所述压缩气体Ⅱ，使所述热态气压成形后管件的管道内的气体压力保持在10MPa，再以1.5℃/s的冷却速度对所述热态气压成形后管件进行气冷；
当热态气压成形后管件的温度降至500℃时，停止进气，在通过所述气体出气通道7泄压后开模，得到Ti 2AlNb基合金空心薄壁构件。
实施例2步骤(1)中的热态气压成形在真空条件下完成。
实施例2步骤(1)中所述的管材坯料的截面呈圆形。
实施例2步骤(1)中所述的管材坯料的厚度为2mm，管材坯料的外径为40mm，管材坯料的长度为200mm。
实施例2步骤(1)中所述的管材坯料为Ti 2AlNb基合金管材坯料，Ti 2AlNb基合金中的Ti的原子百分数为53.5％，Al的原子百分数为22％，Nb的原子百分数为24％，且所述Ti 2AlNb基合金还含有Mo，Ti 2AlNb基合金中的Mo的原子百分数为0.5％。
实施例2步骤(1)中所述的压缩气体Ⅰ为氩气的压缩气体；实施例2步骤(2)中所述的压缩气体Ⅱ为氩气的压缩气体。
图6是实施例2中的Ti 2AlNb基合金空心薄壁构件热态气压成形与热处理工艺步骤图，图中T1表示成形温度，T2表示热处理温度，P1表示成形气胀压力，P2表示热处理气体压力。通过图6可知本实施例在成形后利用余热完成时效热处理，不需冷却后再次加热，由此降低能耗。
图9是实施例2得到的Ti 2AlNb基合金空心薄壁构件的微观组织图。通过图9可以看出：由于本实施例采用Ti 2AlNb基合金空心薄壁构件热态气压成形与热处理成形控性一体化技术，获得的Ti 2AlNb基合金空心薄壁构件的微观组织较为优异，表现为B 2相基体(亮衬度)中分布着细小等轴α 2相(暗衬度)和细小片层状O相(灰色衬度)，其中O相片层厚度为100-200nm。
实施例3：现有的Ti 2AlNb基合金空心薄壁构件热态气压成形的方法
所述方法包括以下步骤：
(1)热态气压成形：先将模具以升温速率8℃/min加热至成形温度970℃，然后放入管材坯料；合模后，将所述模具在温度970℃下保温20min，充入压缩气体，然后在气胀压力为15MPa和温度为970℃条件下进行热态气压成形，直至管材坯料完全成形，得到热态气压成形后管件；
(2)冷却及热处理：采用淬火快速冷却将热态气压成形后管件冷却至室温，然后升温至800℃，在温度800℃下热处理30min，再采用淬火快速冷却至室温，得到Ti 2AlNb基合金空心薄壁构件。
实施例3步骤(1)中的热态气压成形在真空条件下完成。
实施例3步骤(1)中所述的管材坯料的截面呈圆形。
实施例3步骤(1)中所述的管材坯料的厚度为2mm，管材坯料的外径为40mm，管材坯料的长度为200mm。
实施例3步骤(1)中所述的管材坯料为Ti 2AlNb基合金管材坯料，Ti 2AlNb基合金中的Ti的原子百分数为53.5％，Al的原子百分数为22％，Nb的原子百分数为24％，且所述Ti 2AlNb基合金还含有Mo，Ti 2AlNb基合金中的Mo的原子百分数为0.5％。
实施例3步骤(1)中所述的压缩气体为氩气的压缩气体。
实施例4：现有的Ti 2AlNb基合金空心薄壁构件热态气压成形的方法
所述方法包括以下步骤：
(1)热态气压成形：先将模具以升温速率8℃/min加热至成形温度970℃，然后放入管材坯料；合模后，将所述模具在温度970℃下保温20min，充入压缩气体，然后在气胀压力为15MPa和温度为970℃条件下进行热态气压成形，直至管材坯料完全成形，得到热态气压成形后管件；
(2)随模具缓慢冷却(也称为“自然冷却”)及热处理：热态气压成形后管件随模具缓慢冷却至室温，然后升温至800℃，在温度800℃下热处理30min，再随模具缓慢冷却至室温，得到Ti 2AlNb基合金空心薄壁构件。
实施例4步骤(1)中的热态气压成形在真空条件下完成。
实施例4步骤(1)中所述的管材坯料的截面呈圆形。
实施例4步骤(1)中所述的管材坯料的厚度为2mm，管材坯料的外径为40mm，管材坯料的长度为200mm。
实施例4步骤(1)中所述的管材坯料为Ti 2AlNb基合金管材坯料，Ti 2AlNb基合金中的Ti的原子百分数为53.5％，Al的原子百分数为22％，Nb的原子百分数为24％，且所述Ti 2AlNb基合金还含有Mo，Ti 2AlNb基合金中的Mo的原子百分数为0.5％。
实施例4步骤(1)中所述的压缩气体为氩气的压缩气体。
图7是实施例3和4中的Ti 2AlNb基合金空心薄壁构件成形工艺步骤图，图中T1表示成形温度，P1表示成形气胀压力，图中①表示实施例3的淬火快速冷却，图中②表示实施例4的随模具缓慢冷却。
图10是实施例3得到的Ti 2AlNb基合金空心薄壁构件的微观组织图；图11是实施例4得到的Ti 2AlNb基合金空心薄壁构件的微观组织图。通过图10可知，对于淬火快速冷却处理的Ti 2AlNb基合金空心薄壁构件而言，由于冷却速度较快，在970℃气胀时，溶入B 2相基体中的O相来不及析出，因此其显微组织为B 2相基体中分布着等轴α 2相，无O相存在。通过图11可知，随模具缓慢冷却处理的Ti 2AlNb基合金空心薄壁构件，其微观组织为B 2相基体中分布着等轴α 2相和片层状O相，但由于在高温区(970-850℃)冷却速度较慢，片层状O相尺寸较大，O相片层厚度为1μm-2μm。
图12是Ti 2AlNb基合金空心薄壁构件的拉伸性能试件图。
图13和图14是室温拉伸性能曲线，图中A表示实施例3得到的Ti 2AlNb基合金空心薄壁构件室温拉伸性能曲线，图中B表示实施例1得到的Ti 2AlNb基合金空心薄壁构件室温拉伸性能曲线，图中B2表示 实施例2得到的Ti 2AlNb基合金空心薄壁构件室温拉伸性能曲线，图中C表示实施例4得到的Ti 2AlNb基合金空心薄壁构件室温拉伸性能曲线；
图15和图16是温度750℃下的拉伸性能曲线，图中A表示实施例3得到的Ti 2AlNb基合金空心薄壁构件在温度750℃下的拉伸性能曲线，图中B表示实施例1得到的Ti 2AlNb基合金空心薄壁构件在温度750℃下的拉伸性能曲线，图中B2表示实施例2得到的Ti 2AlNb基合金空心薄壁构件在温度750℃下的拉伸性能曲线，图中C表示实施例4得到的Ti 2AlNb基合金空心薄壁构件在温度750℃下的拉伸性能曲线。
对实施例1至4得到的Ti 2AlNb基合金空心薄壁构件进行拉伸测试，采用图12所示拉伸试样，在0.001s -1应变速率下进行室温拉伸测试；另外，采用图12所示拉伸试样，当炉温升至750℃放入拉伸试样，保温5min以使试样温度均匀，然后在应变速率0.001s -1下进行750℃拉伸试验，并记录直至断裂时的应力-应变关系，得到拉伸曲线，如图13至图16所示。图13和图14是室温拉伸性能曲线，图中A表示实施例3得到的Ti 2AlNb基合金空心薄壁构件室温拉伸性能曲线，图中B表示实施例1得到的Ti 2AlNb基合金空心薄壁构件室温拉伸性能曲线，图中B2表示实施例2得到的Ti 2AlNb基合金空心薄壁构件室温拉伸性能曲线，图中C表示实施例4得到的Ti 2AlNb基合金空心薄壁构件室温拉伸性能曲线。图15和图16是温度750℃下的拉伸性能曲线，图中A表示实施例3得到的Ti 2AlNb基合金空心薄壁构件在温度750℃下的拉伸性能曲线，图中B表示实施例1得到的Ti 2AlNb基合金空心薄壁构件在温度750℃下的拉伸性能曲线，图中B2表示实施例2得到的Ti 2AlNb基合金空心薄壁构件在温度750℃下的拉伸性能曲线，图中C表示实施例4得到的Ti 2AlNb基合金空心薄壁构件在温度750℃下的拉伸性能曲线。通过图13和图14可知，实施例1得到的Ti 2AlNb基合金空心薄壁构件在室温下的屈服强度为1214MPa，抗拉强度为1378MPa，断裂延伸率为14.6％；实施例2得到的Ti 2AlNb基合金空心薄壁构件在室温下的屈服强度为1202MPa，抗拉强度为1413MPa，断裂延伸率为14.3％。通过图15和图16可知，实施例1得到的Ti 2AlNb基合金空心薄壁构件在高温条件下(750℃)的屈服强度为688MPa，抗拉强度可以达到801MPa，同时断裂延伸率为22.5％；实施例2得到的Ti 2AlNb基合金空心薄壁构件在高温条件下(750℃)的屈服强度为685MPa，抗拉强度可以达到805MPa，同时断裂延伸率为19.4％。通过图13和图14可知，实施例3得到的Ti 2AlNb基合金空心薄壁构件在室温下的断裂延伸率尽管为25.5％，但其强度较低，屈服强度为1110MPa，抗拉强度为1112MPa；实施例4得到的Ti 2AlNb基合金空心薄壁构件在室温下的屈服强度最低(855MPa)，抗拉强度为1124MPa，断裂延伸率为14.3％。通过图15和图16可知，实施例3得到的Ti 2AlNb基合金空心薄壁构件在高温条件下(750℃)的屈服强度为804MPa，抗拉强度可以达到906MPa，但断裂延伸率却最小，仅为4.3％；实施例4得到的Ti 2AlNb基合金空心薄壁构件在高温条件下(750℃)的断裂延伸率尽管为15.1％，但其强度最低，屈服强度为511MPa，而抗拉强度仅为612MPa。通过对比，实施例1及实施例2得到的Ti 2AlNb基合金空心薄壁构件具有最为优异的综合力学性能。
对实施例1至4得到的Ti 2AlNb基合金空心薄壁构件按照以下步骤测试形状尺寸精度：测量空心薄壁构件的截面高度、宽度和圆角半径尺寸，通过测试可知，实施例1及实施例2得到的Ti 2AlNb基合金空心薄壁构件的长度、宽度和圆角半径尺寸偏差均小于0.2mm，截面角度偏差小于0.2°，满足此类构件设计要求(设计要求为尺寸偏差≤0.25mm)。而实施例3得到的Ti 2AlNb基合金空心薄壁构件的长度最大偏差为0.27mm、宽度最大偏差为0.25mm，截面角度偏差为0.34°；实施例4得到的Ti 2AlNb基合金空心薄壁构件的长度最大偏差为0.26mm、宽度最大偏差为0.22mm，截面角度偏差为0.26°。通过对比可知，实施例1及实施例2得到的Ti 2AlNb基合金空心薄壁构件具有最佳的形状尺寸精度。

Claims (10)

  1. 一种Ti 2AlNb基合金空心薄壁构件热态气压成形与热处理的方法，其特征在于，所述方法包括以下步骤：
    (i)热态气压成形：将模具(1)加热至成形温度970-990℃后，将管材坯料(10)放入所述模具(1)中，其中，所述模具(1)设有管材进气口(2)和管材出气口(3)；
    合模后，将管材坯料(10)进气端和管材坯料(10)出气端分别用进气口密封塞(4)和出气口密封塞(5)进行密封，其中，所述进气口密封塞(4)设置有用于向所述管材坯料(10)的管道供给气体的气体进气通道(6)以及用于打开或闭合所述气体进气通道的进气开关(8)，所述出气口密封塞(5)设置有用于从所述管材坯料的管道向外排出气体的气体出气通道(7)以及用于打开或闭合所述气体出气通道的出气开关(9)；
    然后，在温度970-990℃下保温5min-30min，保持所述出气开关(9)处于关闭状态，打开所述进气开关(8)，使压缩气体Ⅰ通过所述气体进气通道(6)进入所述管材坯料(10)的管道内，在气胀压力为5MPa-70MPa和温度为970-990℃的条件下进行热态气压成形，直至所述管材坯料(10)完全成形，得到热态气压成形后管件；
    (ii)可控冷却热处理：打开所述出气开关(9)，然后，从所述气体进气通道(6)向所述热态气压成形后管件的管道内通入压缩气体Ⅱ，使所述热态气压成形后管件的管道内的气体压力保持在1MPa-20MPa，以0.3℃/s-3.5℃/s的冷却速度对所述热态气压成形后管件进行气冷；
    当所述热态气压成形后管件的温度降至780-830℃时，停止进气，在温度为780-830℃下保温30min-60min；
    然后，继续通入所述压缩气体Ⅱ，使所述热态气压成形后管件的管道内的气体压力保持在1MPa-20MPa，再以0.3℃/s-3.5℃/s的冷却速度对所述热态气压成形后管件进行气冷；
    当所述热态气压成形后管件的温度降至400-500℃时，停止进气，在通过所述气体出气通道(7)泄压后开模，得到Ti 2AlNb基合金空心薄壁构件。
  2. 根据权利要求1所述的Ti 2AlNb基合金空心薄壁构件热态气压成形与热处理的方法，其特征在于，步骤(i)中的热态气压成形在真空条件下完成。
  3. 根据权利要求1或2所述的Ti 2AlNb基合金空心薄壁构件热态气压成形与热处理的方法，其特征在于，步骤(i)中的热态气压成形在非活性气氛下完成，所述非活性气氛优选为选自氮气气氛、氦气气氛、氖气气氛、氩气气氛、氪气气氛和氙气气氛中的至少一种。
  4. 根据权利要求1-3中任一项所述的Ti 2AlNb基合金空心薄壁构件热态气压成形与热处理的方法，其特征在于，在步骤(i)中，以1℃/min-10℃/min的升温速率将所述模具(1)加热至成形温度970-990℃。
  5. 根据权利要求1-4中任一项所述的Ti 2AlNb基合金空心薄壁构件热态气压成形与热处理的方法，其特征在于，步骤(i)中的所述管材坯料(10)的截面呈圆形、椭圆形或多边形
  6. 根据权利要求1-5中任一项所述的Ti 2AlNb基合金空心薄壁构件热态气压成形与热处理的方法，其特征在于，步骤(i)中的所述管材坯料(10)的外径与壁厚的比值不小于20；优选，所述管材坯料(10)的厚度为1mm-6mm，管材坯料的外径为20mm-3000mm，管材坯料的长度为100mm-2000mm。
  7. 根据权利要求1-6中任一项所述的Ti 2AlNb基合金空心薄壁构件热态气压成形与热处理的方法，其特征在于，步骤(i)中的所述管材坯料(10)为Ti 2AlNb基合金管材坯料，Ti 2AlNb基合金中的Ti的原子百分数为41.5％-58％，Al的原子百分数为22％-25％，Nb的原子百分数为20％-30％；
    优选地，所述Ti 2AlNb基合金还含有Mo，且所述Ti 2AlNb基合金中的Mo的原子百分数为0.01％-1.5％；
    另外优选地，所述Ti 2AlNb基合金还含有V，且所述Ti 2AlNb基合金中的V的原子百分数为0.01％-2％。
  8. 根据权利要求1-7中任一项所述的Ti 2AlNb基合金空心薄壁构件热态气压成形与热处理的方法，其特征在于，步骤(i)中的所述压缩气体Ⅰ为空气的压缩气体、氩气的压缩气体、氮气的压缩气体、氦气的压缩气体或CO 2的压缩气体；优选，步骤(ii)中的所述压缩气体Ⅱ为空气的压缩气体、氩气的压缩气体、氮气的压缩气体、氦气的压缩气体或CO 2的压缩气体。
  9. 根据权利要求1-8中任一项所述的Ti 2AlNb基合金空心薄壁构件热态气压成形与热处理的方法，其特征在于，步骤(ii)中得到的所述Ti 2AlNb基合金空心薄壁构件的截面呈圆形、椭圆形、多边形或异形；
    优选地，步骤(ii)中得到的所述Ti 2AlNb基合金空心薄壁构件的轴线形状为直线、平面内曲线或空间曲线。
  10. 采用权利要求1-9中任一项所述的热态气压成形与热处理方法制备的Ti 2AlNb基合金空心薄壁构件。
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