CN115679153A - High-strength and high-toughness short-time high-temperature titanium alloy plate and preparation method and application thereof - Google Patents
High-strength and high-toughness short-time high-temperature titanium alloy plate and preparation method and application thereof Download PDFInfo
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Abstract
The invention discloses a high-strength and high-toughness short-time high-temperature titanium alloy plate and a preparation method and application thereof, and relates to the technical field of titanium alloy materials. The element composition comprises, by mass, 7-8% of Al, 3-4% of Sn, 10-12% of Zr, 2-3% of Mo, 2-3% of Nb, 1-2% of W, 0.5-0.7% of Si, the balance Ti and trace inevitable impurity elements. According to the invention, a thermal mechanical treatment process comprising solution quenching, forging cogging, double-liner rolling and aging annealing is adopted, so that the large-size titanium alloy plate which is fine in crystal grains, has second-phase nano-dispersion distribution, is free from edge cracks, has excellent room-temperature process plasticity and high-temperature instantaneous strength and meets the requirements of aerospace and military equipment industries on the comprehensive performance of the alloy material is obtained.
Description
Technical Field
The invention relates to the technical field of titanium alloy materials, in particular to a high-strength and high-toughness short-time high-temperature titanium alloy plate and a preparation method and application thereof.
Background
The high-temperature titanium alloy widely used at present, such as IMI834, ti1100, BT36, ti60, ti600 and the like, has excellent high-temperature strength and structure stability at 600 ℃, high oxidation resistance and creep resistance, and can stably work for a long time at 600 ℃. However, when the temperature exceeds the above range, the mechanical properties and oxidation resistance of these conventional high temperature titanium alloys will be rapidly reduced, and the service requirements cannot be met, so that it is a critical problem to be solved urgently to develop a 650-700 ℃ high temperature titanium alloy capable of meeting the rapid development requirements in the fields of aerospace, military industry and the like. And for materials with special working conditions, such as the fuselage of a space craft, the compressor disk, military weapon parts and the like, the service time is short, the performances of high-temperature creep, fatigue and the like of the alloy can be ignored to a certain extent, and the attention is paid to the room temperature process plasticity and instantaneous high-temperature strength, so that a wider thought is provided for developing a novel high-temperature-resistant short-time high-temperature titanium alloy. At present, some researches are carried out on short-time high-temperature titanium alloys at 650-700 ℃, such as Ti65, ti650, BTi-6431S, BTi-62421S and the like, but the researches are in a research and development stage, and large-scale engineering application reports are not seen, particularly for titanium alloy plates with large size (the width is more than or equal to 400mm, the length is more than or equal to 1000mm, and the thickness is 0.2-4 mm), the titanium alloy plates are used as sheet metal component blanks and high-temperature bearing elements, and the room temperature plasticity and the high-temperature mechanical property at 650-700 ℃ still need to be further improved. A large number of researches show that the thermal deformation is an important means for refining a coarse initial structure, regulating and controlling the precipitation and distribution of a second phase and effectively improving the comprehensive mechanical property of the high-temperature titanium alloy. However, because titanium alloys have large deformation resistance and the structure evolution is sensitive to thermal process parameters, the conventional hot working modes such as extrusion, rolling and forging are difficult to eliminate inherent defects and realize precise regulation and control of microstructures. Therefore, how to prepare the large-size short-time high-temperature titanium alloy plate at 650-700 ℃ is a technical problem which needs to be solved urgently in the prior art.
Disclosure of Invention
Based on the content, the invention provides the high-strength and high-toughness short-time high-temperature titanium alloy plate and the preparation method and application thereof, and the large-size titanium alloy plate which is fine in crystal grains, has the advantages of second-phase nano dispersion distribution, no edge crack and excellent room-temperature process plasticity and high-temperature instantaneous strength and is prepared by adopting a thermal mechanical treatment process of solution quenching, forging cogging, double-lining-plate rolling and aging annealing, so that the problems of insufficient room-temperature plasticity and high-temperature strength and serious edge crack of the novel short-time high-temperature titanium alloy plate at 650-700 ℃ in the prior art are solved.
In order to achieve the purpose, the invention provides the following scheme:
according to one technical scheme, the high-strength and high-toughness short-time high-temperature titanium alloy plate comprises, by mass, 7% -8% of Al, 3% -4% of Sn, 10% -12% of Zr, 2% -3% of Mo, 2% -3% of Nb, 1% -2% of W, 0.5% -0.7% of Si, the balance Ti and trace inevitable impurity elements.
According to the second technical scheme, the preparation method of the high-strength, high-toughness and short-time high-temperature titanium alloy plate comprises the following steps:
melting, mixing and casting the raw materials of the alloy elements according to the mass percentage to obtain an alloy ingot;
carrying out solution quenching, forging and cogging, double-liner rolling and aging treatment on the alloy cast ingot in sequence to obtain the high-strength and high-toughness short-time high-temperature titanium alloy plate;
the solid solution quenching specifically comprises the following steps: placing the alloy ingot at a temperature above the silicide dissolution temperature for solution treatment, and then quenching with a NaCl aqueous solution;
the forging cogging specifically comprises the following steps: forging and upsetting the alloy sample in one pass along the height direction of the alloy sample, wherein the deformation temperature is lower than the alpha + beta/beta phase transition temperature of the alloy cast ingot, the temperature is kept before forging, the process deformation is 60-80%, and the strain rate is 0.05s -1 ～0.1s -1 Air cooling after forging;
the rolling of the double lining plates is specifically as follows: respectively paving a hard alloy lining plate on the upper surface and the lower surface of a sample to be rolled, preserving heat at a temperature lower than the alpha + beta/beta phase transition temperature of the alloy cast ingot, synchronously conveying the alloy cast ingot into rollers for 4-6 times of rolling, and performing furnace returning and heat preservation between the times of rolling;
the aging treatment specifically comprises the following steps: and carrying out aging annealing treatment in a vacuum environment at 650-750 ℃, and then air cooling.
Further, the alloy ingot is a Widmannstatten structure and comprises initial beta grains and lamellar alpha beam domains inside the beta grains.
Further, the solution quenching specifically comprises: and (3) putting the alloy ingot into a temperature condition of 5-20 ℃ above the silicide dissolution temperature for solid solution for 2-4 h, and then quenching by using 5-15 wt.% of NaCl aqueous solution.
Furthermore, in the forging and cogging process, the deformation temperature is 80-100 ℃ below the alpha + beta/beta phase transition temperature of the alloy cast ingot, and the temperature is kept for 20-30 min before forging.
Further, the rolling of the double lining plates specifically comprises the following steps: and respectively paving a hard alloy lining plate on the upper surface and the lower surface of a sample to be rolled, preserving heat for 20-40 min at the temperature of 20-50 ℃ below the alpha + beta/beta phase transition temperature of the alloy ingot, synchronously feeding the alloy ingot into rollers for 4-6 times of rolling, wherein the reduction amount of each time is 15%, the total reduction amount of the rolling is 60-90%, carrying out furnace returning and heat preservation between the times of rolling, and the temperature and the time for furnace returning and heat preservation of each time are the same.
Further, the aging treatment specifically comprises: aging annealing treatment is carried out for 4 to 8 hours in a vacuum environment at the temperature of between 650 and 750 ℃, and the vacuum degree is 10 -1 ～10 -2 Pa, and then air cooling.
In the third technical scheme of the invention, the high-strength high-toughness short-time high-temperature titanium alloy plate is applied to preparation of aerospace craft bodies, compressor disks and military weapon parts.
The technical idea of the invention is as follows:
(1) Selecting alloy components: the design principle of 'critical Al equivalent' and 'critical valence electron concentration' is broken through in component design. Based on the components of the existing Ti-Al-Sn-Zr-Mo-Nb-W-Si series short-time high-temperature titanium alloy, 1) the Al equivalent is improved, and the subsequent aging treatment regulates and controls the brittleness alpha 2 The phase is separated out in nanometer size, the dispersion strengthening effect is exerted, and the alpha is reasonably utilized 2 High temperature strengthening effect of the phases; 2) The content of beta stable elements (Mo, nb, W and Si) is increased, the beta stable elements can effectively strengthen the beta phase, the heat strength of the alloy is improved, more beta phases can be obtained in the alloy structure, and the manufacturability of the alloy is improved. The addition of excessive beta-stabilizing elements will deteriorate the thermal stability of the alloy, but for short-time high-temperature titanium alloys, the requirement on the thermal stability of the alloy is low due to the short service time. In addition, si exceeding the solid solution limit is precipitated in the form of silicide, which has a strong pinning effect on dislocations and can effectively strengthen grain boundaries and phase boundaries.
(2) Alloy ingot casting: the as-cast alloy is widmannstatten structure, including initial beta grains, and lamellar alpha beam domains inside the beta grains.
(3) Solution quenching: because the Zr content in the alloy is high (10-12 wt.%), the solid solubility of Si in the matrix is obviously reduced, that is, the silicide dissolution temperature is greatly increased, according to the phase diagram simulation result, the silicide dissolution temperatures of the series of alloys are all higher than the alpha + beta/beta phase transition temperature by more than 150 ℃, so that some coarse silicides precipitated along the initial beta grain boundary in the solidification process may exist in the as-cast alloy structure, and the large-size silicides precipitated along the grain boundary obviously have adverse effects on the alloy performance, so the as-cast alloy is designed to be fully dissolved at the temperature of 5-20 ℃ above the silicide dissolution temperature (Ts) so that the precipitated silicides are re-dissolved in the matrix. In order to retain the high temperature morphology and obtain a fine martensitic structure, a solution post-quenching treatment is performed. The NaCl aqueous solution is selected as the quenching medium, so that the alloy can be cooled at a high cooling speed and uniformly, and the oxide on the surface of the alloy can be crushed and peeled off.
(4) Forging and cogging: the martensite phase α' obtained after quenching is a supersaturated solid solution of α -Ti, and is decomposed when heated or deformed at high temperatures. Thus, at wrought deformations above the recrystallization temperature, the acicular α' martensite will fracture and recrystallize to form a localized equiaxed fine grain structure. It is worth noting that a great number of defects exist inside the alpha' martensite sheet layer, and the defects can provide energy and serve as nucleation sites when being recrystallized, so that the refinement of matrix grains is effectively promoted. The equiaxial fine-grained structure has small deformation resistance and provides a good structure foundation for subsequent rolling deformation.
(5) Rolling double lining plates: compared with common rolling, the double-liner rolling can effectively reduce or even eliminate the edge crack phenomenon of the rolled plate, which is proved in the test, and the edge crack is hardly generated around the rolled plate. The rolling temperature is 20-50 ℃ below the alpha + beta/beta phase transition temperature, is positioned at the upper end of an alpha + beta two-phase region, and a two-state structure with fine crystal grains is obtained under the condition of large deformation. In addition, under the rolling deformation condition, silicide is precipitated again in a micro-nano size, and the silicide has a good dislocation strengthening effect when the alloy deforms under stress.
(6) Aging annealing: to fully exert alpha 2 Phase dispersion strengthening, aging the rolled plate to regulate alpha 2 And separating out the phase nanometer dispersion. In addition, in order to avoid oxidation of the plate, the whole aging process is carried out in a vacuum environment. The tensile strength at room temperature of the plate obtained in example 1 is 1370MPa, and the elongation is 14.2%; the tensile strength is 642MPa at 700 ℃, the elongation is 22.4 percent, and the comprehensive performance is obviously superior to that of Ti65 and BTi-6431S alloy.
The invention discloses the following technical effects:
(1) According to the invention, a thermal mechanical treatment process comprising solution quenching, forging and cogging, double-liner rolling and aging annealing is adopted, so that the large-size titanium alloy plate which is fine in crystal grains, has second-phase nano-dispersion distribution, has no edge crack, has excellent room-temperature process plasticity and high-temperature instantaneous strength and meets the requirement of aerospace and military equipment industries on the comprehensive performance of the alloy material is obtained.
(2) The invention has simple process steps and is suitable for large-scale industrial production.
Drawings
In order to more clearly illustrate the embodiments of the present invention or the technical solutions in the prior art, the drawings needed in the embodiments will be briefly described below, and it is obvious that the drawings in the following description are only some embodiments of the present invention, and it is obvious for those skilled in the art to obtain other drawings without creative efforts.
FIG. 1 is a macroscopic view, a microscopic SEM view and a dot scan result of precipitated phases of the titanium alloy sheet prepared in example 1; wherein, (a) macroscopic view, (b) microscopic SEM image, and (c) dot scanning result of precipitated phase.
FIG. 2 is an as-cast OM picture, an as-cast SEM picture and an as-cast quenched OM picture of an alloy ingot of step 2 and an OM picture after forging and cogging of step 4 of example 1; wherein, (a) an as-cast OM diagram; (b) an as-cast SEM image; (c) an as-cast post-quench OM map; and (d) OM picture after cogging and forging.
Detailed Description
Reference will now be made in detail to various exemplary embodiments of the invention, the detailed description should not be construed as limiting the invention but rather as a more detailed description of certain aspects, features and embodiments of the invention.
It is to be understood that the terminology used herein is for the purpose of describing particular embodiments only and is not intended to be limiting of the invention. Further, for numerical ranges in this disclosure, it is understood that each intervening value, between the upper and lower limit of that range, is also specifically disclosed. Every smaller range between any stated value or intervening value in a stated range and any other stated or intervening value in that stated range is encompassed within the invention. The upper and lower limits of these smaller ranges may independently be included or excluded in the range.
Unless defined otherwise, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this invention belongs. Although only preferred methods and materials are described herein, any methods and materials similar or equivalent to those described herein can be used in the practice or testing of the present invention. All documents mentioned in this specification are incorporated herein by reference to disclose and describe the methods and/or materials in connection with which the documents are cited. In case of conflict with any incorporated document, the present specification will control.
It will be apparent to those skilled in the art that various modifications and variations can be made in the specific embodiments of the present disclosure without departing from the scope or spirit of the disclosure. Other embodiments will be apparent to those skilled in the art from consideration of the specification. It is intended that the specification and examples be considered as exemplary only.
As used herein, the terms "comprising," "including," "having," "containing," and the like are open-ended terms that mean including but not limited to.
The invention provides a high-strength high-toughness short-time high-temperature titanium alloy plate, which comprises, by mass, 7% -8% of Al, 3% -4% of Sn, 10% -12% of Zr, 2% -3% of Mo, 2% -3% of Nb, 1% -2% of W, 0.5% -0.7% of Si, the balance Ti and trace inevitable impurity elements.
The invention also provides a preparation method of the high-strength and high-toughness short-time high-temperature titanium alloy plate, which comprises the following steps:
step 1, weighing raw materials: calculating and weighing sponge titanium, high-purity aluminum, pure tin particles, sponge zirconium, crystalline silicon, al-Mo, al-Nb and Al-W intermediate alloy as raw materials. Wherein, the mass percentages of all the components are respectively 7-8% of Al, 3-4% of Sn, 10-12% of Zr, 2-3% of Mo, 2-3% of Nb, 1-2% of W, 0.5-0.7% of Si, the balance of Ti and trace inevitable impurity elements;
the Widmannstatten structure of the alloy ingot is obtained based on two conditions of element content limitation and a preparation method. The alloy component proportion provided by the invention belongs to near-alpha high-temperature titanium alloy, and the as-cast structures of the titanium alloy obtained by vacuum induction melting are Widmannstatten structures. However, if the alloy of this composition is made by other means, such as additive manufacturing, the initial structure obtained may not be widmannstatten.
The alloy cast structures with different element component ratios in the above range are widmannstatten structures, and the difference lies in the size of initial beta crystal grains and the thickness of alpha sheet layers.
Step 3, solution quenching: solid dissolving the alloy ingot for 2-4 h at 5-20 ℃ above the silicide dissolution temperature (Ts), and then quenching the alloy ingot by using 5-15 wt.% NaCl aqueous solution;
step 5, rolling the double lining plates: cutting the sample obtained in the step (4) into a cuboid thick plate, and then rolling by using a hot rolling mill; before rolling, respectively paving hard alloy (301 stainless steel or stainless steel of other types) lining plates on the upper surface and the lower surface of a thick plate, wherein the thickness of each lining plate is 1-2 mm, and the lining plates and a test sample are synchronously stressed and deformed during rolling; the method specifically comprises the following steps: firstly, uniformly coating a high-temperature lubricant on the upper and lower surfaces of a lining plate and an alloy sample, then putting the lining plate and the alloy sample together into a heat treatment furnace for heating, setting the furnace temperature to be 20-50 ℃ below the alpha + beta/beta phase transition temperature, synchronously feeding the lining plate and the alloy sample into a roller room for 4-6 times of rolling after the temperature is kept for 20-40 min, wherein the rolling reduction of each time is 15%, and the total rolling reduction is 60-90%; carrying out furnace returning and heat preservation among the passes, wherein the parameters are the same as those of the above steps;
The invention also provides application of the high-strength high-toughness short-time high-temperature titanium alloy plate in preparation of aerospace vehicle bodies, compressor disks and military weapon parts.
The "room temperature" in the present invention means 15 to 30 ℃ unless otherwise specified.
Example 1
The preparation method of the short-time high-temperature titanium alloy plate Ti-7.5Al-3Sn-10Zr-2Mo-2Nb-1W-0.5Si comprises the following steps:
step 1, weighing raw materials: 50kg of sponge titanium, high-purity aluminum, pure tin particles, sponge zirconium, crystalline silicon, al-Mo, al-Nb and Al-W master alloy are sequentially weighed according to the weight percentage of each component as raw materials.
Step 3, solution quenching: the solution quenching treatment was performed for 0.5h at different temperatures (1120 ℃, 1140 ℃, 1160 ℃, 1180 ℃, 1200 ℃) on cast samples of 10mm × 10mm × 6mm, and the silicide dissolution temperature was determined to be about 1190 ℃ by observing the structure. Therefore, the alloy ingot prepared in step 2 was solutionized at 1200 ℃ for 4h, followed by quenching treatment with 15wt.% NaCl aqueous solution.
Step 5, rolling the double lining plates: the sample obtained in step 4 was cut into a thick plate of 320mm × 150mm × 20mm, followed by rolling with a hot rolling mill. Before rolling, hard alloy (301 stainless steel) lining plates are respectively paved on the upper surface and the lower surface of a thick plate, the thickness of each lining plate is 2mm, and the lining plates and the test samples are synchronously stressed and deformed during rolling. The method specifically comprises the following steps: firstly, uniformly coating a high-temperature lubricant on the upper and lower surfaces of a lining plate and an alloy sample, then putting the lining plate and the alloy sample together into a heat treatment furnace for heating, setting the furnace temperature to 980 ℃, synchronously feeding the lining plate and the alloy sample into a roller room for 6-pass rolling after keeping the temperature for 40min, wherein the rolling reduction of each pass is 15%, and the total rolling reduction is 90%. And carrying out furnace returning and heat preservation among the passes, wherein the parameters are the same as those of the above. After rolling, a 1500mm 400mm 2mm high temperature titanium alloy thin plate without edge crack is obtained.
The short-time high-temperature titanium alloy plate prepared by the embodiment has the dimensions of 1500mm multiplied by 400mm multiplied by 2mm, has no edge crack, and has the room-temperature tensile strength of 1370MPa and the elongation of 14.2 percent; the tensile strength at 700 ℃ was 642MPa, and the elongation was 22.4%.
FIG. 1 is a macroscopic view, a microscopic SEM view and a point scan result of precipitated phases of the titanium alloy sheet prepared in example 1; wherein, (a) is a macroscopic view, (b) is a microscopic SEM image, and (c) is a dot scanning result of precipitated phase. In the figure, (a) shows the alloy sheet obtained in example 1, the macroscopic size of the sheet reaches 1500mm × 400mm × 2mm, and no edge crack occurs around the sheet. From (b) in the figure, it can be seen that the microstructure of the plate is a two-state structure including equiaxed alpha grains and beta transition structure. White granular precipitates were found to be uniformly distributed in the matrix structure and had a size of about 60 to 500nm, and the EDS result (FIG. (c)) showed that the precipitates were silicides.
FIG. 2 is an as-cast OM picture, an as-cast SEM picture and an as-cast quenched OM picture of an alloy ingot of step 2 and an OM picture after forging and cogging of step 4 of example 1; wherein, (a) is an as-cast OM diagram; (b) as-cast SEM picture; (c) is OM picture after as-cast quenching; and (d) is OM picture after cogging forging. FIG. 2 shows the alloy structure corresponding to the different steps of example 1. The alloy is widmannstatten structure in the as-cast state, and the trigeminal grain boundary of the initial beta grains is clearly visible (in the figures, (a), (b)). The alloy is transformed into a fine acicular α' martensite structure after solution quenching at 1200 ℃ (fig. (c)). This alpha' martensite is broken and recrystallized after forging deformation to form a partially equiaxed fine-grained and refined alpha-lamellar structure (fig. (d)).
Example 2
The preparation method of the short-time high-temperature titanium alloy plate Ti-8Al-3Sn-12Zr-2Mo-2Nb-1W-0.7Si comprises the following steps:
step 1, weighing raw materials: according to the weight percentage of each component, 10kg of sponge titanium, high-purity aluminum, pure tin particles, sponge zirconium, crystalline silicon, al-Mo, al-Nb and Al-W master alloy are sequentially weighed and used as raw materials.
Step 3, solution quenching: the 10mm × 10mm × 6mm as-cast samples were subjected to solution quenching treatment for 0.5h at various temperatures (1200 deg.C, 1220 deg.C, 1240 deg.C, 1260 deg.C, 1280 deg.C), and the silicide dissolution temperature was determined to be about 1270 deg.C by observing the structure. Therefore, the alloy ingot prepared in step 2 was solutionized at 1290 ℃ for 2h, followed by a quench treatment with 5wt.% aqueous NaCl solution.
Step 5, rolling the double lining plates: the sample obtained in step 4 was cut into a thick plate of 100mm × 60mm × 20mm, followed by rolling using a hot rolling mill. Before rolling, hard alloy (301 stainless steel) lining plates are paved on the upper surface and the lower surface of the thick plate respectively, the thickness of each lining plate is 2mm, and the lining plates and the test samples are stressed and deformed synchronously during rolling. The method specifically comprises the following steps: firstly, uniformly coating a high-temperature lubricant on the upper and lower surfaces of a lining plate and an alloy sample, then putting the lining plate and the alloy sample together into a heat treatment furnace for heating, setting the furnace temperature to 962 ℃, keeping the temperature for 20min, and then synchronously feeding the lining plate and the alloy sample into a roller for 6-pass rolling, wherein the rolling reduction of each pass is 15%, and the total rolling reduction is 90%. And carrying out furnace returning and heat preservation among the passes, wherein the parameters are the same as those of the above. After rolling, a 510mm × 150mm × 2mm high-temperature titanium alloy thin plate without edge crack is obtained.
The short-time high-temperature titanium alloy plate prepared by the embodiment has the dimensions of 510mm multiplied by 150mm multiplied by 2mm, has no edge crack, and has the room-temperature tensile strength of 1427MPa and the elongation of 9.8 percent; the tensile strength at 700 ℃ was 655MPa, and the elongation was 17.3%.
Example 3
The preparation method of the short-time high-temperature titanium alloy plate Ti-7Al-3Sn-10Zr-3Mo-3Nb-2W-0.5Si comprises the following steps:
step 1, weighing raw materials: according to the weight percentage of each component, 10kg of sponge titanium, high-purity aluminum, pure tin particles, sponge zirconium, crystalline silicon, al-Mo, al-Nb and Al-W master alloy are sequentially weighed and used as raw materials.
Step 3, solution quenching: the solution quenching treatment was performed for 0.5h at various temperatures (1140 deg.C, 1160 deg.C, 1180 deg.C, 1200 deg.C, 1220 deg.C) on cast samples of 10mm × 10mm × 6mm, and the silicide dissolution temperature was determined to be about 1220 deg.C by observing the structure. Therefore, the alloy ingot prepared in step 2 was solutionized at 1225 ℃ for 2h, followed by quenching with 10wt.% aqueous NaCl.
Step 5, rolling the double lining plates: the sample obtained in step 4 was cut into a thick plate of 100mm × 60mm × 20mm, followed by rolling using a hot rolling mill. Before rolling, hard alloy (301 stainless steel) lining plates are respectively paved on the upper surface and the lower surface of a thick plate, the thickness of each lining plate is 2mm, and the lining plates and the test samples are synchronously stressed and deformed during rolling. The method specifically comprises the following steps: firstly, uniformly coating a high-temperature lubricant on the upper and lower surfaces of a lining plate and an alloy sample, then putting the lining plate and the alloy sample together into a heat treatment furnace for heating, setting the furnace temperature at 922 ℃, keeping the temperature for 20min, and then synchronously feeding the lining plate and the alloy sample into a roller for 6-pass rolling, wherein the rolling reduction per pass is 15%, and the total rolling reduction is 90%. And carrying out furnace returning and heat preservation among the passes, wherein the parameters are the same as those of the above. After rolling, a 510mm × 150mm × 2mm high temperature titanium alloy thin plate without edge crack is obtained.
The short-time high-temperature titanium alloy plate prepared by the embodiment has the dimensions of 510mm multiplied by 150mm multiplied by 2mm, has no edge crack, and has the room-temperature tensile strength of 1223MPa and the elongation of 13.4 percent; the tensile strength at 700 ℃ was 567MPa, and the elongation was 25.6%.
Example 4
The preparation method of the short-time high-temperature titanium alloy plate Ti-7Al-3.5Sn-11Zr-2Mo-3Nb-1W-0.6Si comprises the following steps:
step 1, weighing raw materials: according to the weight percentage of each component, 20kg of sponge titanium, high-purity aluminum, pure tin particles, sponge zirconium, crystalline silicon, al-Mo, al-Nb and Al-W master alloy are sequentially weighed and used as raw materials.
Step 3, solution quenching: the solution quenching treatment is carried out on cast samples of 10mm multiplied by 6mm for 0.5h at different temperatures (1200 ℃, 1220 ℃, 1240 ℃, 1260 ℃ and 1280 ℃), and the dissolution temperature of the silicide is determined to be about 1270 ℃ by observing the structure. Therefore, the alloy ingot prepared in step 2 was solutionized at 1280 ℃ for 3h, followed by quenching with 10wt.% aqueous NaCl solution.
Step 5, rolling the double lining plates: the sample obtained in step 4 was cut into a thick plate of 200mm × 100mm × 10mm, followed by rolling using a hot rolling mill. Before rolling, hard alloy (301 stainless steel) lining plates are respectively paved on the upper surface and the lower surface of a thick plate, the thickness of each lining plate is 1mm, and the lining plates and the test samples are synchronously stressed and deformed during rolling. The method specifically comprises the following steps: firstly, uniformly coating a high-temperature lubricant on the upper and lower surfaces of a lining plate and an alloy sample, then putting the lining plate and the alloy sample together into a heat treatment furnace for heating, setting the furnace temperature at 920 ℃, keeping the temperature for 25min, and then synchronously feeding the lining plate and the alloy sample into a roller for 4-pass rolling, wherein the rolling reduction per pass is 15%, and the total rolling reduction is 60%. And (4) carrying out furnace returning and heat preservation among the passes, wherein the parameters are the same as those of the above steps. After rolling, a high-temperature titanium alloy thin plate with 350mm multiplied by 180mm multiplied by 4mm and no edge crack is obtained.
The short-time high-temperature titanium alloy plate prepared by the embodiment has the dimensions of 350mm multiplied by 180mm multiplied by 4mm, has no edge crack, and has the room-temperature tensile strength of 1156MPa and the elongation of 12.9%; the tensile strength at 700 ℃ was 589MPa, and the elongation was 21.4%.
The above-described embodiments are merely illustrative of the preferred embodiments of the present invention, and do not limit the scope of the present invention, and various modifications and improvements of the technical solutions of the present invention can be made by those skilled in the art without departing from the spirit of the present invention, and the technical solutions of the present invention are within the scope of the present invention defined by the claims.
Claims (8)
1. The high-strength high-toughness short-time high-temperature titanium alloy plate is characterized by comprising, by mass, 7% -8% of Al, 3% -4% of Sn, 10% -12% of Zr, 2% -3% of Mo, 2% -3% of Nb, 1% -2% of W, 0.5% -0.7% of Si, the balance Ti and trace inevitable impurity elements.
2. The preparation method of the high-strength and high-toughness short-time high-temperature titanium alloy plate as claimed in claim 1, which is characterized by comprising the following steps:
melting, mixing and casting the raw materials of the alloy elements according to the mass percentage to obtain an alloy ingot;
carrying out solution quenching, forging and cogging, double-liner rolling and aging treatment on the alloy cast ingot in sequence to obtain the high-strength and high-toughness short-time high-temperature titanium alloy plate;
the solid solution quenching specifically comprises the following steps: placing the alloy ingot at a temperature above the silicide dissolution temperature for solution treatment, and then quenching with a NaCl aqueous solution;
the forging cogging specifically comprises the following steps: forging and upsetting the alloy sample in one pass along the height direction of the alloy sample, wherein the deformation temperature is lower than the alpha + beta/beta phase transition temperature of the alloy cast ingot, the temperature is kept before forging, the process deformation is 60-80%, and the strain rate is 0.05s -1 ～0.1s -1 Air cooling after forging;
the rolling of the double lining plates is specifically as follows: respectively paving a hard alloy lining plate on the upper surface and the lower surface of a sample to be rolled, carrying out heat preservation under the temperature condition lower than the alpha + beta/beta phase transition temperature of the alloy cast ingot, then carrying out 4-6 times of rolling, and carrying out furnace returning and heat preservation between the times of rolling;
the aging treatment specifically comprises the following steps: and carrying out aging annealing treatment in a vacuum environment at 650-750 ℃, and then air cooling.
3. The method for preparing the high-toughness short-time high-temperature titanium alloy plate as claimed in claim 2, wherein the alloy ingot is a widmannstatten structure comprising initial beta grains and lamellar alpha beam domains inside the beta grains.
4. The preparation method of the high-strength high-toughness short-time high-temperature titanium alloy plate as claimed in claim 2, wherein the solution quenching is specifically as follows: and (3) putting the alloy ingot into a temperature condition of 5-20 ℃ above the silicide dissolution temperature for solid solution for 2-4 h, and then quenching by using 5-15 wt.% of NaCl aqueous solution.
5. The preparation method of the high-strength and high-toughness short-time high-temperature titanium alloy plate according to claim 2, wherein in the forging and cogging process, the deformation temperature is 80-100 ℃ below the alpha + beta/beta transformation temperature of the alloy ingot, and the temperature is kept for 20-30 min before forging.
6. The method for preparing the high-strength high-toughness short-time high-temperature titanium alloy plate according to claim 2, wherein the double-liner rolling specifically comprises the following steps: respectively paving a hard alloy lining plate on the upper surface and the lower surface of a sample to be rolled, preserving heat for 20-40 min at the temperature of 20-50 ℃ below the alpha + beta/beta phase transition temperature of the alloy cast ingot, then synchronously feeding the alloy cast ingot into rollers for 4-6 times of rolling, wherein the reduction amount of each time is 15%, the total reduction amount of rolling is 60-90%, returning heat preservation is carried out between the times of rolling, and the temperature and time for returning heat preservation of each time are the same.
7. The preparation method of the high-strength and high-toughness short-time high-temperature titanium alloy plate as claimed in claim 2, wherein the aging treatment is specifically as follows: aging annealing treatment is carried out for 4 to 8 hours in a vacuum environment at the temperature of between 650 and 750 ℃, and the vacuum degree is 10 -1 ～10 -2 Pa, and then air cooling.
8. The use of the high toughness, short duration, high temperature titanium alloy sheet material of claim 1 in the manufacture of aerospace vehicle fuselages, compressor disks, and military weapon parts.
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| ZA2023/03062A ZA202303062B (en) | 2022-08-25 | 2023-02-28 | The preparation method and application of a short-time high-temperature titanium alloy sheet with high-strength and high-toughness |
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Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CA882041A (en) * | 1971-09-28 | Reactive Metals | Balanced titanium alloy | |
| US4229216A (en) * | 1979-02-22 | 1980-10-21 | Rockwell International Corporation | Titanium base alloy |
| CN105925844A (en) * | 2016-06-08 | 2016-09-07 | 太原理工大学 | Micro and nano double-scale particle reinforced titanium-based composite material and preparation method thereof |
| CN108165820A (en) * | 2016-12-08 | 2018-06-15 | 北京有色金属研究总院 | A kind of strong heat-resistant titanium alloy of superelevation and sheet alloy and preparation method in short-term |
| CN109811193A (en) * | 2019-03-13 | 2019-05-28 | 北京工业大学 | A kind of excellent boron micro-alloyed high-temperature titanium alloy and preparation method thereof of high-temperature behavior |
| CN111188001A (en) * | 2020-03-17 | 2020-05-22 | 山东理工大学 | Method for controlling silicide characteristics of high-temperature titanium-based composite material |
| CN114836651A (en) * | 2022-05-17 | 2022-08-02 | 太原理工大学 | Ultrahigh-strength and toughness beta titanium alloy and preparation method thereof |
| JP7180782B2 (en) * | 2019-07-30 | 2022-11-30 | 日本製鉄株式会社 | Titanium alloy plate and automobile exhaust system parts |
-
2022
- 2022-08-25 CN CN202211029554.5A patent/CN115679153B/en active Active
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- 2023-02-28 ZA ZA2023/03062A patent/ZA202303062B/en unknown
Patent Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CA882041A (en) * | 1971-09-28 | Reactive Metals | Balanced titanium alloy | |
| US4229216A (en) * | 1979-02-22 | 1980-10-21 | Rockwell International Corporation | Titanium base alloy |
| CN105925844A (en) * | 2016-06-08 | 2016-09-07 | 太原理工大学 | Micro and nano double-scale particle reinforced titanium-based composite material and preparation method thereof |
| CN108165820A (en) * | 2016-12-08 | 2018-06-15 | 北京有色金属研究总院 | A kind of strong heat-resistant titanium alloy of superelevation and sheet alloy and preparation method in short-term |
| CN109811193A (en) * | 2019-03-13 | 2019-05-28 | 北京工业大学 | A kind of excellent boron micro-alloyed high-temperature titanium alloy and preparation method thereof of high-temperature behavior |
| JP7180782B2 (en) * | 2019-07-30 | 2022-11-30 | 日本製鉄株式会社 | Titanium alloy plate and automobile exhaust system parts |
| CN111188001A (en) * | 2020-03-17 | 2020-05-22 | 山东理工大学 | Method for controlling silicide characteristics of high-temperature titanium-based composite material |
| CN114836651A (en) * | 2022-05-17 | 2022-08-02 | 太原理工大学 | Ultrahigh-strength and toughness beta titanium alloy and preparation method thereof |
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| ZA202303062B (en) | 2023-05-31 |
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