CN114273583A - Ti2AlNb-based alloy plate and preparation method and application thereof - Google Patents
Ti2AlNb-based alloy plate and preparation method and application thereof Download PDFInfo
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Abstract
The invention relates to Ti2In particular to a Ti based alloy in the technical field of AlNb based alloy2An AlNb-based alloy plate and a preparation method and application thereof. Ti of the invention2The preparation method of the AlNb-based alloy plate comprises the following steps: (A) mixing Ti2The AlNb-based alloy cast ingot is subjected to three-dimensional reversing forging treatment in the temperature ranges of a B2 single-phase region, a B2+ alpha two-phase region, a B2+ alpha + O three-phase region and a B2+ O two-phase region in sequence, and then is subjected to upsetting to obtain a plate blank; (B) rolling the plate blank at 920-950 ℃ to obtain Ti2AlNb-based alloy sheet material. The method refines Ti2The grain size of the AlNb-based alloy sheet is increased, and Ti is improved2The structural uniformity and plasticity of the AlNb-based alloy sheet material.
Description
Technical Field
The invention relates to the technical field of Ti2 AlNb-based alloy, in particular to Ti2An AlNb-based alloy plate and a preparation method and application thereof.
Background
In recent years, with the further development of material science, particularly the development in the fields of aerospace and the like, higher and higher requirements are made on the performance of materials. Ti2As a light high-temperature-resistant structural material, the AlNb-based alloy has the advantages of high specific strength, high fracture toughness, better oxidation resistance, excellent heat resistance, no magnetism, flame retardance and the like, can be used for a long time within the range of 700 plus materials and 800 ℃, and can be used at a temperature higher than 1100 ℃ for a short time, so that the AlNb-based alloy is widely concerned by people. But Ti2The AlNb alloy is strengthened by an intermediate compound, Ti2The mixed bonding mode of the metal bond and the covalent bond of the AlNb alloy ensures that the AlNb alloy has excellent high-temperature performance and intrinsic brittleness, thereby bringing great difficulty to processing. The intrinsic brittleness of the intermetallic compounds within the alloy limits its use. Therefore, how to increase Ti2The plasticity of the AlNb alloy is gradually becoming the focus of research.
Ti prepared by the prior art2The as-cast structure of the AlNb-based alloy is generally coarse isometric crystals, so that the room-temperature processability of the material is low, and the application of the material is limited. At present, the elongation of 50 percent can be obtained at 800-1000 ℃ by forging, which is far from enough for manufacturing some thin-wall parts.
In view of the above, the present invention is particularly proposed.
Disclosure of Invention
The first object of the present invention is to provide a Ti2A method for preparing AlNb-based alloy plate, which refines Ti2The crystal grains of the AlNb-based alloy plate improve Ti2The structural uniformity and plasticity of the AlNb-based alloy sheet material.
The second object of the present invention is to provide a Ti2The AlNb-based alloy sheet has a grain size of 1-3 μm and excellent plasticity.
It is a third object of the present invention to provide the above Ti2The application of the AlNb-based alloy plate in aerospace equipment.
In order to achieve the above purpose of the present invention, the following technical solutions are adopted:
the invention provides a Ti2The preparation method of the AlNb-based alloy plate comprises the following steps:
(A) mixing Ti2The AlNb-based alloy cast ingot is subjected to three-dimensional reversing forging treatment in the temperature ranges of a B2 single-phase region, a B2+ alpha two-phase region, a B2+ alpha + O three-phase region and a B2+ O two-phase region in sequence, and then is subjected to upsetting to obtain a plate blank;
(B) rolling the plate blank at 920-950 ℃ to obtain Ti2AlNb-based alloy sheet material.
The invention also provides a method for preparing the Ti2Ti prepared by preparation method of AlNb-based alloy plate2AlNb-based alloy sheet material.
The invention also provides the Ti2The application of the AlNb-based alloy plate in aerospace equipment.
Compared with the prior art, the invention has the beneficial effects that:
the invention provides a Ti2The preparation method of the AlNb-based alloy plate is characterized in that Ti with good structure uniformity and grain size of 50-300 mu m is prepared by adopting a method of gradual cooling, multi-fire alternating and large-deformation three-dimensional reversing forging2Rolling the AlNb-based alloy plate blank at 920-950 ℃, and equiaxially crystallizing the precipitated phase to obtain Ti with the grain size of 1-3 mu m2The plasticity of the AlNb-based alloy plate blank at 800-1000 ℃ can reach 800-1000 percent, and the AlNb-based alloy plate blank is Ti2The forming of the thin-wall structural part of the AlNb alloy plate provides an excellent foundation.
Drawings
In order to more clearly illustrate the technical solutions of the embodiments of the present invention, the drawings that are required to be used in the embodiments will be briefly described below, it should be understood that the following drawings only illustrate some embodiments of the present invention and therefore should not be considered as limiting the scope, and for those skilled in the art, other related drawings can be obtained according to the drawings without inventive efforts.
FIG. 1 shows Ti prepared in example 1 of the present invention2SEM images of AlNb-based alloy sheets.
Detailed Description
The technical solutions of the present invention will be described clearly and completely with reference to the following detailed description, but those skilled in the art will understand that the following described examples are some, not all, of the examples of the present invention, and are only used for illustrating the present invention, and should not be construed as limiting the scope of the present invention. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention. The examples, in which specific conditions are not specified, were conducted under conventional conditions or conditions recommended by the manufacturer. The reagents or instruments used are not indicated by the manufacturer, and are all conventional products available commercially.
The following is a Ti2The AlNb-based alloy plate and the preparation method and the application thereof are specifically explained.
Some embodiments of the present invention provide a Ti2The preparation method of the AlNb-based alloy plate comprises the following steps:
(A) mixing Ti2The AlNb-based alloy cast ingot is subjected to three-dimensional reversing forging treatment in the temperature ranges of a B2 single-phase region, a B2+ alpha two-phase region, a B2+ alpha + O three-phase region and a B2+ O two-phase region in sequence, and then is subjected to upsetting to obtain a plate blank;
(B) rolling the plate blank at 920-950 ℃ to obtain Ti2AlNb-based alloy sheet material.
The invention adopts the three-dimensional reversing forging with large deformation by gradually cooling and multiple times of heat alternation to lead the original Ti to be2The beta crystal grains of the AlNb-based alloy ingot are continuously dynamically recrystallizedThe grain size is gradually thinned to 50-300 mu m from 5-8 mm, alternate large-deformation three-dimensional reversing forging is carried out, the same structure in each direction is guaranteed, the good structure uniformity is achieved, then rolling is carried out at 900-1000 ℃, the grain size is further thinned, the precipitated phase is axially equalized, and the prepared Ti is obtained2The AlNb-based alloy plate has the grain size of 1-3 mu m and excellent plasticity, and the plasticity can reach 800-1000% at the highest temperature of 800-1000 ℃.
In some embodiments of the present invention, the temperature of the B2 single-phase region in step (A) is in the range of 1160-1170 ℃.
In some embodiments of the present invention, in step (a), the temperature of three-dimensional reverse forging of the B2 single-phase region may be, for example, 1160 ℃, 1161 ℃, 1162 ℃, 1163 ℃, 1164 ℃, 1165 ℃, 1166 ℃, 1167 ℃, 1168 ℃, 1169 ℃, 1170 ℃, or the like, typically but not limited to.
In some embodiments of the present invention, the temperature of the B2+ alpha two-phase region ranges from 1010 to 1020 ℃.
In some embodiments of the present invention, the temperature of the three-dimensional reverse forging of the B2+ α two-phase region in step (a) may be, for example, typically but not exclusively, 1010 ℃, 1011 ℃, 1012 ℃, 1013 ℃, 1014 ℃, 1015 ℃, 1016 ℃, 1017 ℃, 1018 ℃, 1019 ℃ or 1020 ℃ and the like.
In some embodiments of the present invention, the temperature of the B2+ alpha + O triple-phase region ranges from 990 ℃ to 1000 ℃.
In some embodiments of the present invention, in step (a), the temperature of the three-dimensional reverse forging of the B2+ α + O three-phase region may be, for example, 990 ℃, 991 ℃, 992 ℃, 993 ℃, 994 ℃, 995 ℃, 996 ℃, 997 ℃, 998 ℃, 999 ℃ or 1000 ℃, and the like, typically but not limitedly.
In some embodiments of the present invention, the temperature of the B2+ O two-phase region ranges from 930 ℃ to 940 ℃.
In some embodiments of the present invention, the temperature of the three-dimensional reverse forging of the B2+ O two-phase region in step (a) may be, for example, typically but not limited to 930 ℃, 931 ℃, 932 ℃, 933 ℃, 934 ℃, 935 ℃, 936 ℃, 937 ℃, 938 ℃, 939 ℃, 940 ℃ or the like.
In some embodiments of the invention, step (a), the three-dimensional reverse forging comprises: respectively facing Ti along the first direction, the second direction and the third direction2Upsetting the AlNb-based alloy ingot with deformation of 30-45%; wherein the first direction, the second direction and the third direction mutually form an included angle of 90 degrees +/-5 degrees.
In some embodiments of the invention, in step (A), the number of three-dimensional reversing forgings in each phase region is more than or equal to 2; preferably, the number of times of three-dimensional reversing forging in each phase region is 2-6.
The deformation of the three-dimensional forging of the invention is 30-45%, and if the deformation is large, Ti is caused2Cracking the AlNb-based alloy cast ingot to obtain a plate blank; if the deformation amount is small, the deformation is not uniform, and the texture uniformity of the prepared plate is poor.
In some embodiments of the invention, the temperature of the upsetting in the step (A) is 930-940 ℃; typically, but not limited to, for example, 930 deg.C, 931 deg.C, 932 deg.C, 933 deg.C, 934 deg.C, 935 deg.C, 936 deg.C, 937 deg.C, 938 deg.C, 939 deg.C, 940 deg.C, etc.
In some embodiments of the present invention, in the step (a), the upsetting is performed to obtain a slab having a thickness of 80 to 120mm, and preferably, a slab having a thickness of 100 mm.
In some embodiments of the invention, in step (A), the three-dimensionally reverse forged Ti is2And upsetting the AlNb-based alloy ingot at 930-940 ℃ for several times to obtain a plate blank with the thickness of 80-120 mm.
In some embodiments of the invention, in step (a), Ti is prepared by a method comprising one-time vacuum consumable melting, two-time vacuum skull melting and three-time vacuum consumable melting2And (4) casting an AlNb-based alloy ingot.
In some embodiments of the present invention, step (a) further comprises subjecting Ti to a three-dimensional reverse forging process2Upsetting the AlNb-based alloy ingot to obtain Ti with preset size2An AlNb-based alloy ingot; preferably, the upsetting temperature is 1160-1170 ℃.
In some embodiments of the invention, in the step (B), the plate blank is subjected to first rolling with total deformation of more than or equal to 900% at 920-950 ℃ along the thickness direction, and then is subjected to annealing treatment at 920-950 ℃ for 0.5-2 h.
In some embodiments of the present invention, in step (B), the temperature of the first rolling, typically but not limited to, may be, for example, 920 ℃, 930 ℃, 940 ℃ or 950 ℃, and the like.
In some embodiments of the invention, in step (B), the total deformation of the first rolling is between 900% and 1500%.
In some embodiments of the invention, in step (B), the pass of the first rolling is 15 to 18; typically, but not by way of limitation, the first rolling pass is, for example, 15, 16, 17, or 18.
In some embodiments of the invention, in step (B), the amount of deformation per pass of the first rolling is between 5% and 30%; typically, but not by way of limitation, the first rolling may have a deformation of 5%, 10%, 15%, 20%, 25%, or 30% per pass, for example.
In some embodiments of the present invention, in step (B), the temperature of the annealing treatment, typically but not limited to, may be, for example, 920 ℃, 930 ℃, 940 ℃ or 950 ℃, and the like; the annealing time is typically but not limited to, for example, 0.5h, 1h, 1.5h or 2h, etc., and preferably 1 h.
In some embodiments of the invention, in the step (B), the slab after the first rolling is subjected to a second rolling with total deformation of more than or equal to 900% at 920-950 ℃.
In some embodiments of the invention, the total deformation of the second rolling in step (B) is between 900% and 1500%.
In some embodiments of the present invention, in step (B), the temperature of the second rolling, typically but not limited to, may be, for example, 920 ℃, 930 ℃, 940 ℃ or 950 ℃, and the like.
In some embodiments of the invention, in step (B), the second rolling is clad-rolling.
In some embodiments of the present invention, in the step (B), the direction of the second rolling is perpendicular to the direction of the first rolling.
In some embodiments of the present invention, in step (B), the pass of the second rolling is 8-10; typically, but not by way of limitation, the second rolling pass is, for example, 8, 9, or 10.
In some embodiments of the invention, the amount of deformation per pass of the second rolling is between 10% and 30%; typically, but not by way of limitation, the second pass may have a deformation of, for example, 10%, 12%, 14%, 16%, 18%, 20%, 22%, 24%, 26%, 28%, or 30% per pass, and so forth.
Some embodiments of the present invention also provide methods of using the above Ti2Ti prepared by preparation method of AlNb-based alloy plate2AlNb-based alloy sheet material.
In some embodiments of the invention, Ti2The grain size of the AlNb-based alloy sheet is 1-3 μm.
In some embodiments of the invention, Ti2Equiaxed alpha in AlNb-based alloy sheet2The volume fraction of the/O phase is > 40%.
In some embodiments of the invention, Ti2The AlNb-based alloy plate mainly comprises an O phase and a B2 phase, wherein the volume fraction of the equiaxed O phase is 40-60%, the volume fraction of the B2 phase is 20-30%, and the volume fraction of the lamellar O phase is 20-30%.
In some embodiments of the invention, Ti2Not less than 90% of precipitated phase alpha in AlNb-based alloy sheet2Aspect ratio/O phase < 1.5: 1; typically but not limitatively, e.g. out-of-phase alpha2The aspect ratio of the/O phase is 1.4: 1. 1.3: 1. 1.2: 1. 1.1: 1 or 1: 1, etc.
In some embodiments of the invention, Ti2The plasticity of the AlNb-based alloy plate is 800-1000% at 800-1000 ℃.
Some embodiments of the invention also provide Ti2AlNb-based alloy sheetThe material is applied to aerospace equipment.
The features and properties of the present invention are described in further detail below with reference to examples.
Ti used in the embodiment of the present invention2The alloy composition of AlNb plate is illustrated by taking Ti-22Al-25Nb as an example, but not limited thereto, and the balance is Ti2AlNb-based alloys are acceptable.
Example 1
This example provides Ti2The preparation method of the AlNb-based alloy plate comprises the following steps:
(A) adding Ti at 1170 DEG C2Upsetting AlNb-based alloy ingot to obtain Ti with the size of 160 multiplied by 340mm2After AlNb-based alloy ingot casting, three-dimensional reversing forging is carried out at 1170 ℃, 1020 ℃, 1000 ℃ and 935 ℃ in sequence to obtain Ti with the size of 200 multiplied by 400mm2The three-dimensional reversing forging frequency of each temperature point of the AlNb-based alloy ingot is 3; then upsetting is carried out at 935 ℃ to obtain a plate blank with the size of 420 multiplied by 100 mm; wherein the three-dimensional reverse forging comprises the step of respectively aligning Ti along a first direction, a second direction and a third direction2Upsetting the AlNb-based alloy ingot; the deformation of 3 upsets in the first direction is respectively 30%, 30% and 45%, the deformation of 3 upsets in the second direction is respectively 30%, 45% and 30%, and the deformation of 3 upsets in the third direction is respectively 45%, 30% and 30%; the first direction, the second direction and the third direction are at an angle of 90 ° to each other.
(B) Carrying out 16-pass first rolling (the single-pass reduction is 5-8 mm) on the plate blank along the thickness direction at 935 ℃ to obtain a plate blank with the size of 420 multiplied by 4200 multiplied by 10mm, then annealing at 920 ℃ for 1h, and then evenly dividing the plate blank to obtain a plate blank with the size of 420 multiplied by 1050 multiplied by 10 mm; and then performing double-covering and overlapping rolling on the plate blank, and performing 9-pass second rolling (the single-pass reduction is 2-5 mm) with the total deformation of 935% at 920 ℃ after covering to obtain Ti with the size of 4200 x 1050 x 1mm2AlNb-based alloy sheet material.
In step (A), Ti2The preparation method of the AlNb-based alloy ingot comprises the following steps:
sponge titanium, high-purity aluminum and niobium chips are used as raw materials, and cast ingots are prepared by a smelting method of vacuum self-consumption, skull solidification and self-consumption. The specific process comprises the following steps: material proportioning calculation, electrode pressing, electrode assembly welding, primary vacuum consumable melting, secondary vacuum skull melting and tertiary vacuum consumable melting. The raw materials required for ingot casting include: titanium sponge, high-purity aluminum beans and pure Nb scraps. Firstly, calculating the weight of ingredients required by each electrode according to nominal ingredients, then mixing raw materials and pressing the electrodes to prepare a one-time self-consumption electrode, and performing one-time self-consumption
And secondary skull melting to obtain 3
And (4) solidifying and casting ingots with uniform components. Then, assembling and welding 3 skull cast ingots into a self-consuming electrode in a furnace welding mode, and finally obtaining the self-consuming electrode through vacuum self-consuming smelting
The finished ingot is obtained by turning, peeling and sawing
Ti of (A)2And (4) casting an AlNb-based alloy ingot.
Example 2
This example provides Ti2The preparation method of the AlNb-based alloy plate comprises the following steps:
(A) adding Ti at 1170 DEG C2Upsetting AlNb-based alloy ingot to obtain Ti with the size of 160 multiplied by 340mm2After AlNb-based alloy ingot casting, three-dimensional reversing forging is carried out at 1170 ℃, 1010 ℃, 990 ℃ and 940 ℃ in sequence to obtain Ti with the size of 200 multiplied by 400mm2The three-dimensional reversing forging frequency of each temperature point of the AlNb-based alloy ingot is 3; then upsetting the mixture at 930 ℃ to obtain a slab with the size of 420 multiplied by 100 mm; wherein the three-dimensional reverse forging comprises the step of respectively aligning Ti along a first direction, a second direction and a third direction2Upsetting AlNb-based alloy ingotCoarse; the deformation of 3 upsets in the first direction is respectively 30%, 30% and 45%, the deformation of 3 upsets in the second direction is respectively 30%, 45% and 30%, and the deformation of 3 upsets in the third direction is respectively 45%, 30% and 30%; the first direction, the second direction and the third direction are at an angle of 90 ° to each other.
(B) Carrying out 15-pass first rolling (5-8 mm single-pass reduction) on the plate blank along the thickness direction at 950 ℃ with the total deformation of 900% to obtain a plate blank with the size of 420X 4200X 10mm, then annealing at 950 ℃ for 2h, and then evenly dividing the plate blank to obtain a plate blank with the size of 420X 1050X 10 mm; then the plate blank is subjected to double covering and overlapping rolling, 8-pass second rolling (the single pass rolling is 2-5 mm) with the total deformation of 900% is carried out at 950 ℃ after covering, and Ti with the size of 4200 x 1050 x 1mm is obtained2AlNb-based alloy sheet material.
Ti used in this example2The AlNb-based alloy ingot was the same as in example 1.
Example 3
This example provides Ti2The preparation method of the AlNb-based alloy plate comprises the following steps:
(A) adding Ti at 1165 deg.C2Upsetting AlNb-based alloy ingot to obtain Ti with the size of 160 multiplied by 340mm2After the AlNb-based alloy ingot casting, three-dimensional reversing forging is carried out at 1160 ℃, 1015 ℃, 995 ℃ and 920 ℃ in sequence to obtain Ti with the size of 200 multiplied by 400mm2The AlNb-based alloy ingot casting is carried out, and the three-dimensional reversing forging frequency of each temperature point is 5; then upsetting is carried out at 940 ℃ to obtain a slab with the size of 420 multiplied by 100 mm; wherein, the deformation of 5 times of upsetting in the first direction is respectively 30%, 45%, 30% and 45%, the deformation of 5 times of upsetting in the second direction is respectively 30%, 45%, 30%, 45% and 30%, and the deformation of 5 times of upsetting in the third direction is respectively 45%, 30% and 30%; the first direction, the second direction and the third direction are at an angle of 90 ° to each other.
(B) The slab was subjected to 18 passes of first rolling (single pass reduction of 5 to 8mm) at 920 ℃ in the thickness direction with a total deformation of 900% to obtain a slab having dimensions of 420X 4200X 10mm, and then annealed at 935 ℃ by 0.After 5h, uniformly dividing the slab IV to obtain slabs with the size of 420 multiplied by 1050 multiplied by 10 mm; and then performing double-covering and overlapping rolling on the plate blank, and performing 10-pass second rolling (the single-pass reduction is 2-5 mm) with the total deformation of 900% at 920 ℃ after covering to obtain the Ti with the size of 4200 x 1050 x 1mm2AlNb-based alloy sheet material.
Ti used in this example2The AlNb-based alloy ingot was the same as in example 1.
Comparative example 1
Ti of this comparative example2The method for producing an AlNb-based alloy sheet is as described in example 1, except that: adjusting the rolling temperature to 910 ℃ to obtain Ti2AlNb-based alloy sheet, but the slab broke during rolling.
Comparative example 2
Ti of this comparative example2Production method of AlNb-based alloy sheet referring to example 1, except that three-dimensional reverse forging was performed at 1300 deg.C, 1050 deg.C, 1005 deg.C and 950 deg.C in this order to obtain Ti having a size of 200X 400mm2And (4) casting an AlNb-based alloy ingot.
Comparative example 3
Ti of this comparative example2The method for producing an AlNb-based alloy sheet is as described in example 1, except that the three-dimensional reverse forging in step (a) is performed by: respectively facing Ti along the first direction, the second direction and the third direction2The AlNb-based alloy ingot was upset with a deformation amount of 50%.
Ti2The AlNb-based alloy ingot was broken, and Ti having a size of 200X 400mm could not be obtained2And (4) casting an AlNb-based alloy ingot.
Test examples
For Ti prepared in example 12The AlNb-based alloy sheet was subjected to scanning electron microscope test, and the results are shown in fig. 1.
Grain sizes (test Standard: GBT6494-2017) and equiaxed forms of alpha's in examples 1 to 3 and comparative examples 1 to 22The volume fraction of the/O phase (test standard: image pro plus) and the plasticity (test standard: GB/T228.2, measurement temperature 935. + -. 5 ℃ C.) were measured, and the results are shown in Table 1.
TABLE 1
As can be seen from FIG. 1, Ti prepared by the present invention2The AlNb-based alloy plate has uniform and fine microstructure and good structure uniformity.
As can be seen from Table 1, Ti according to the present invention was used2Ti prepared by preparation method of AlNb-based alloy plate2The AlNb-based alloy plate has the grain size of 1-3 mu m and plasticity of 800-1000 ℃ at 800-1000 ℃.
Finally, it should be noted that: the above embodiments are only used to illustrate the technical solution of the present invention, and not to limit the same; while the invention has been described in detail and with reference to the foregoing embodiments, it will be understood by those skilled in the art that: the technical solutions described in the foregoing embodiments may still be modified, or some or all of the technical features may be equivalently replaced; and the modifications or the substitutions do not make the essence of the corresponding technical solutions depart from the scope of the technical solutions of the embodiments of the present invention.
Claims (10)
1. Ti2The preparation method of the AlNb-based alloy plate is characterized by comprising the following steps:
(A) mixing Ti2The AlNb-based alloy cast ingot is subjected to three-dimensional reversing forging treatment in the temperature ranges of a B2 single-phase region, a B2+ alpha two-phase region, a B2+ alpha + O three-phase region and a B2+ O two-phase region in sequence, and then is subjected to upsetting to obtain a plate blank;
(B) rolling the plate blank at 920-950 ℃ to obtain Ti2AlNb-based alloy sheet material.
2. The Ti of claim 12The preparation method of the AlNb-based alloy plate is characterized in that in the step (A), the temperature range of the B2 single-phase zone is 1160-1170 ℃;
preferably, the temperature range of the B2+ alpha two-phase region is 1010-1020 ℃;
preferably, the temperature range of the B2+ alpha + O three-phase region is 990-1000 ℃;
preferably, the temperature range of the B2+ O two-phase region is 930-940 ℃.
3. The Ti of claim 12The preparation method of the AlNb-based alloy plate is characterized in that in the step (A), the three-dimensional reversing forging comprises the following steps: respectively aligning the Ti along a first direction, a second direction and a third direction2Upsetting the AlNb-based alloy ingot with deformation of 30-45%;
wherein the first direction, the second direction and the third direction mutually form an included angle of 90 degrees +/-5 degrees.
4. The Ti of claim 12The preparation method of the AlNb-based alloy plate is characterized in that in the step (A), the three-dimensional reversing forging frequency in each phase region is more than or equal to 2;
preferably, the number of times of the three-dimensional reversing forging in each phase region is 2-6.
5. The Ti of claim 12The preparation method of the AlNb-based alloy plate is characterized in that in the step (A), the Ti is prepared by adopting a method of one-time vacuum consumable melting, two-time vacuum skull melting and three-time vacuum consumable melting2And (4) casting an AlNb-based alloy ingot.
6. The Ti of claim 12The preparation method of the AlNb-based alloy plate is characterized in that in the step (B), the plate blank is subjected to first rolling with the total deformation amount of more than or equal to 900% at 920-950 ℃ along the thickness direction, and then annealing treatment is carried out at 920-950 ℃ for 0.5-2 h;
preferably, the pass of the first rolling is 15-18;
preferably, the deformation amount of each pass of the first rolling is 5-30%.
7. The Ti of claim 62Preparation method of AlNb-based alloy plateThe method is characterized in that in the step (B), the plate blank subjected to the first rolling is subjected to second rolling with the total deformation amount of more than or equal to 900% at 920-950 ℃;
preferably, the second rolling is clad-rolling;
preferably, the direction of the second rolling is perpendicular to the direction of the first rolling;
preferably, the pass of the second rolling is 8-10;
preferably, the deformation of each pass of the second rolling is 10-30%.
8. Use of Ti as described in any of claims 1 to 72Ti prepared by preparation method of AlNb-based alloy plate2AlNb-based alloy sheet material.
9. The Ti of claim 82An AlNb-based alloy sheet material, characterized in that the Ti2The grain size of the AlNb-based alloy plate is 1-3 mu m;
preferably, the Ti2Equiaxed alpha in AlNb-based alloy sheet2The volume fraction of the/O phase is > 40%;
preferably, the Ti2Not less than 90% of precipitated phase alpha in AlNb-based alloy sheet2Aspect ratio/O phase < 1.5: 1.
10. the Ti of claim 8 or 92The application of the AlNb-based alloy plate in aerospace equipment.
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Cited By (4)
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|---|---|---|---|---|
| CN115971492A (en) * | 2022-09-30 | 2023-04-18 | 北京钢研高纳科技股份有限公司 | Ti2AlNb alloy plate and preparation method and application thereof |
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| CN116987991B (en) * | 2023-09-26 | 2024-01-23 | 成都先进金属材料产业技术研究院股份有限公司 | Regulating Ti 2 Method for preparing AlNb-based alloy with yield ratio |
| CN117696805A (en) * | 2023-12-27 | 2024-03-15 | 北京钢研高纳科技股份有限公司 | Ti3Al alloy thin bar and preparation method thereof |
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