CN115178598A - Hot processing method for improving high-temperature tensile strength of titanium alloy rolled bar - Google Patents
Hot processing method for improving high-temperature tensile strength of titanium alloy rolled bar Download PDFInfo
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- CN115178598A CN115178598A CN202210811072.9A CN202210811072A CN115178598A CN 115178598 A CN115178598 A CN 115178598A CN 202210811072 A CN202210811072 A CN 202210811072A CN 115178598 A CN115178598 A CN 115178598A
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- 229910001069 Ti alloy Inorganic materials 0.000 title claims abstract description 21
- 238000003672 processing method Methods 0.000 title abstract description 4
- 238000005096 rolling process Methods 0.000 claims abstract description 33
- 238000010438 heat treatment Methods 0.000 claims abstract description 30
- 238000000034 method Methods 0.000 claims abstract description 30
- 239000000463 material Substances 0.000 claims abstract description 18
- 238000005242 forging Methods 0.000 claims abstract description 17
- 230000009466 transformation Effects 0.000 claims abstract description 15
- 238000001816 cooling Methods 0.000 claims abstract description 9
- 230000007547 defect Effects 0.000 claims abstract description 8
- 230000008569 process Effects 0.000 claims description 22
- 238000000227 grinding Methods 0.000 claims description 4
- 230000000052 comparative effect Effects 0.000 description 12
- 241000446313 Lamella Species 0.000 description 9
- 238000000137 annealing Methods 0.000 description 6
- 238000002360 preparation method Methods 0.000 description 5
- 238000004321 preservation Methods 0.000 description 5
- 239000013078 crystal Substances 0.000 description 4
- 238000004519 manufacturing process Methods 0.000 description 4
- 238000009826 distribution Methods 0.000 description 3
- 238000005498 polishing Methods 0.000 description 3
- 238000010586 diagram Methods 0.000 description 2
- 238000011160 research Methods 0.000 description 2
- 230000007704 transition Effects 0.000 description 2
- 238000003723 Smelting Methods 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000001808 coupling effect Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000005272 metallurgy Methods 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C37/00—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
- B21C37/04—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of bars or wire
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/16—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling wire rods, bars, merchant bars, rounds wire or material of like small cross-section
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
Abstract
The invention provides a hot processing method for improving high-temperature tensile strength of a titanium alloy rolled bar, which comprises the steps of heating and deforming a bar material obtained by cogging and intermediate billet forging in a beta single-phase region to obtain a final rolled bar blank, wherein the heating temperature is set to be more than a phase transformation point by 30-50 DEG C o C, keeping the temperature for 1min/mm, then performing radial forging or roll forming, wherein the deformation amount is 40-70%, and performing air cooling after deformation; then the obtained bar blank is polished to remove surface defects and then is heated and rolled in an alpha + beta two-phase region low-temperature section to obtain the bar blankThe heating temperature of the final rolling bar billet is set to be 60 to 100 below the transformation point o And C, keeping the temperature for 1min/mm, then rolling and forming, wherein the rolling deformation is 60-90%, and air cooling is carried out after deformation. The rolling structure with uniform and fine alpha phase can be obtained by the method of the invention, and the tensile strength of the rolled bar containing the structure is obviously improved and the value is stable at room temperature and high temperature of 600 ℃ after the rolled bar is subjected to conventional heat treatment.
Description
The technical field is as follows:
the invention belongs to the field of metallurgy, relates to the technical field of hot processing of titanium alloy bars, and particularly relates to a hot processing method for improving the high-temperature tensile strength of a titanium alloy rolled bar.
The background art comprises the following steps:
the titanium alloy has higher specific strength and excellent corrosion resistance, and is widely applied in the fields of aerospace and the like. The near-alpha alloy has good high-temperature strength and structure stability, and is used as a high-temperature titanium alloy used at the temperature of more than 500 ℃.
The traditional hot working process of the high-temperature titanium alloy small-size bar is to forge or roll and deform an alpha + beta two-phase region to prepare an intermediate billet, and then to form the bar in the alpha + beta two-phase region (30-50 ℃ below a phase transformation point), wherein the process route is shown in figure 1. However, a large number of practical results show that the size distribution of the primary alpha phase of the bar obtained by the traditional process is not uniform, and large blocks of alpha exist at local positions. Cracks are easy to be initiated at the interface of the large block alpha and the matrix in the process of stretching the material, so that the tensile strength of the material is reduced, and the dispersity of the tensile property, especially the high-temperature tensile strength, is improved. Therefore, reducing the size of the alpha phase after rolling in the two-phase region and improving the size uniformity are technical bottlenecks to be solved by the near-alpha type high-temperature titanium alloy rolled bar.
The invention content is as follows:
aiming at the technical problems in the prior art, the invention provides a hot working method for improving the high-temperature tensile strength of a titanium alloy rolled bar, and the hot working method for improving the high-temperature tensile strength of the titanium alloy rolled bar aims to solve the technical problems that the tensile strength of a material is reduced and the dispersity of tensile properties, especially the high-temperature tensile strength, is increased when a bar is obtained by a process in the prior art.
The invention provides a hot working method for improving high-temperature tensile strength of a titanium alloy rolled bar, which comprises the following steps:
1) Heating and deforming the bar material obtained by cogging and intermediate billet forging in a beta single-phase region to obtain a final rolled bar blank, setting the heating temperature to be 30-50 ℃ above a transformation point in the process of heating and deforming the bar material in the beta single-phase region to obtain the final rolled bar blank, calculating the heat preservation time according to 1min/mm, then performing radial forging or roll forming, wherein the deformation amount is 40-70%, and performing air cooling after deformation;
2) Grinding the bar blank obtained in the step 1) to remove surface defects, then heating and rolling in an alpha + beta two-phase region low-temperature section, setting the heating temperature of the finally rolled bar blank to be 60-100 ℃ below the phase transition point in the process of heating and rolling in the alpha + beta two-phase region low-temperature section, calculating the heat preservation time according to 1min/mm, then rolling and forming, wherein the rolling deformation is 60-90%, and cooling after deformation.
The preparation process of the titanium alloy bar generally comprises the following steps: the invention relates to ingot casting smelting, cogging, intermediate billet forging, radial forging/rolling, finish rolling and heat treatment, and mainly aims at a preparation process and a finish rolling process of a titanium alloy finish rolled bar blank.
After the titanium alloy bar is prepared by the method, the alpha phase in the rolled state of the titanium alloy bar exists in a uniform, fine isometric state or a worm state, the size is 1-3um, and no large alpha exists. After double annealing heat treatment, the structure is a two-state structure, the primary alpha is uniformly distributed, the size is 5-8um, and no large alpha exists. The material with the structure prepared by the method of the invention has obviously improved tensile strength at room temperature and 600 ℃ and stable numerical value.
The process design principle for optimizing the alpha grain size and uniformity of the high-temperature titanium alloy is as follows:
(1) In the traditional 'alpha + beta two-phase zone blank making' + 'alpha + beta two-phase zone rolling' process, the blank is a typical alpha + beta two-state structure and contains a primary alpha phase and beta transformation structure; during the subsequent heating in the alpha + beta phase region (30-50 ℃ below the transformation point), primary alpha crystal grains grow, alpha lamella in the beta transformation structure is also coarsened, and during the rolling process, the alpha lamella in the primary alpha phase and the beta transformation structure start to be crushed, but the crushing degree is different. Alpha sheets of smaller thickness are susceptible to fracture, but coarse primary alpha phase has limited effectiveness in fracturing, especially the large blocks of alpha present in the billet. The non-uniformity of the deformation causes non-uniformity of the structure of the finish rolled bar, thereby affecting the tensile strength.
(2) In the process of 'beta-phase region blank making' + 'alpha + beta two-phase region rolling', the coupling effect and the tissue evolution of the front and back hot working links are fully utilized. The blank is heated and deformed in a beta region to prepare an intermediate blank, and a Widmannstatten structure with uniform lamella thickness can be formed by controlling the heating temperature and the deformation. The beta heating temperature is not easy to be too high, the time is not easy to be too long, and a certain deformation amount is required, otherwise, the beta crystal grains grow large, and a straight and continuous crystal boundary alpha phase amount is easy to form in the air cooling process after deformation, so that the subsequent crushing is not facilitated. Research and practice show that the heating temperature of the beta region is 30-50 ℃ above the transformation point, the heat preservation time is calculated according to 1min/mm, the deformation is 40-70%, and the obtained Widmannstatten tissue lamella is uniform without straight and continuous crystal boundary alpha. During the subsequent heating in the alpha + beta phase region, the lamella grows to a certain extent, and the transitional growth can be avoided by controlling the heating temperature and time. During the deformation process of the uniform lamella, alpha phases of the lamella at different positions are uniformly crushed, uniform and fine equiaxial or worm-shaped alpha can be formed, and no large blocks alpha exist in the whole observation range. Research and practice show that the rolling heating temperature of the alpha + beta two-phase region is 60-100 ℃ below the phase transformation point, the heat preservation time is calculated according to 1min/mm, the rolling deformation is 60-90%, and the alpha lamella in the obtained tissue is fully crushed. The heating temperature of the two-phase region is too low, and the rolling is cracked; too high alpha phase redissolves and participates in the deformation of the alpha phase of the crushed lamella with limitation. The alpha sheet layer can not be broken when the deformation is too small, and the risk of excessive temperature rise exists when the deformation is too large.
During the subsequent double annealing heat treatment, part of alpha is coarsened to form primary alpha, and the other part forms beta transition structure. Because no large alpha exists and the size and the distribution of the primary alpha are uniform, the room-temperature tensile strength and the high-temperature tensile strength of the material are obviously improved, and the fluctuation of a plurality of measurement results is small.
Compared with the prior art, the invention has remarkable technical progress. The high-temperature titanium alloy rolled bar prepared by the process technology of 'beta phase zone blank manufacturing' + 'alpha + beta two-phase zone rolling' provided by the invention has the advantages that alpha phase exists in a uniform, fine and equiaxial or worm shape in a rolling state, the size is 1-3 mu m, and no large alpha blocks exist. After double annealing heat treatment, the structure is a two-state structure, the size of primary alpha is 5-8um, and no large alpha exists. The material with the structure has high tensile strength at room temperature and 600 ℃ and stable numerical value. The method of the invention improves the strength and reduces the dispersity of the strength, especially the high-temperature tensile strength, by optimizing the size and the uniformity of the alpha phase.
Description of the drawings:
FIG. 1 is a schematic diagram of the conventional "α + β two-phase zone blank-making" + "α + β two-phase zone rolling" process route.
FIG. 2 is a schematic diagram of the process route of "beta-phase zone blank manufacturing" + "alpha + beta two-phase zone rolling" proposed by the present invention.
FIG. 3 is a microstructure morphology obtained in the comparative example using the conventional process route.
FIG. 4 is the microstructure morphology obtained in example 1 using the proposed fabrication process of the present invention.
FIG. 5 is the microstructure morphology obtained in example 2 using the proposed fabrication process of the present invention.
The specific implementation mode is as follows:
the high temperature titanium alloy in the comparative example and example was of Ti-Al-Sn-Zr-Mo-Nb system, containing small amounts of Si and Ce. For other near-alpha high-temperature titanium alloys, the preparation process provided by the invention can also achieve the same effect.
Comparative example:
and performing three times of vacuum consumable melting to obtain a phi 760mm ingot, wherein the phase transformation point is 1020 ℃. Cogging the ingot into phi 220mm by adopting a quick forging machine, and forging at 1050-1150 ℃; then forging into bar with the diameter of 80mm, wherein the forging temperature is 950-970 ℃. The bar is polished and then put into an electric furnace, the temperature is 990 ℃, the heat preservation is 80 minutes, and then the bar is radially forged into a blank, and the deformation is 60 percent. After the surface defects of the blank are removed by grinding, the blank is put into an electric furnace, the temperature is 980 ℃, the temperature is kept for 40 minutes, and the blank is rolled into a bar with the deformation of 75 percent. And (3) carrying out double annealing on the rolled bar, specifically, carrying out air cooling at the temperature of 960 ℃/1h and at the temperature of 570 ℃/2h, and carrying out air cooling.
FIG. 3 shows the microstructure morphology obtained in the comparative example using the conventional two-phase rolling route. As can be seen, the primary alpha phase in the blank before finish rolling is thick and has the size of 10-20um, and the primary alpha phases at local positions are connected to form a large alpha. After final rolling, the primary alpha-phase has different crushing degrees, and some of the primary alpha-phase become fine equiaxial and have the size of 2-10um; some are formed with slightly reduced dimensions, 8-15um in size; some of the original large α pieces were not sufficiently crushed and inherited. Upon subsequent double annealing heat treatment, the fine equiaxed α resolubilizes away, and the bulk α remains. Table 1 shows the room temperature and 600 ℃ high temperature tensile properties of the rolled bar, the high temperature properties of the rolled bar have obvious fluctuation due to the uneven distribution of the alpha phase size and the existence of large blocks of alpha after rolling, and most of the values do not meet the relevant material specifications (the yield strength requirement is not less than 550MPa, and the tensile strength requirement is not less than 650 MPa).
Example 1:
a bar of phi 80mm after cogging + forging in the comparative example was used. The rod material is polished and then put into an electric furnace, the temperature is 1070 ℃, the temperature is kept for 80 minutes, and then the rod material is radially forged into a blank with the deformation of 60 percent. After the surface defects of the rolled blank are removed by polishing, the rolled blank is put into an electric furnace, the temperature is 920 ℃, the temperature is kept for 40 minutes, and the rolled blank is rolled into a bar with the deformation of 70 percent.
FIG. 4 is the microstructure morphology of the bar obtained by the preparation process proposed by the present invention in example 1. Therefore, the bar billet before finish rolling is of a basket structure, the thickness of the alpha sheet layer is uniform, and the size of the alpha sheet layer is 1-3 mu m. After the final rolling, the alpha phase of the sheet layer is fully crushed to form uniform and fine equiaxial or worm-shaped alpha, the size of the short side is 1-3um, and no large alpha exists in the whole observation range. After double annealing heat treatment, part of alpha is coarsened to form primary alpha with the size of 5-8um, and other parts are dissolved back and then are separated out to form a beta transformation structure. Because no large alpha blocks exist and the primary alpha size is uniform, the tensile strength of the material at room temperature and high temperature of 600 ℃ is obviously improved, and the details are shown in table 1.
Example 2:
a bar of phi 80mm after cogging + forging in the comparative example was used. The bar is polished and then put into an electric furnace, the temperature is 1070 ℃, the temperature is kept for 80 minutes, and then the bar is rolled into a blank with the deformation of 60 percent. After the surface defects of the rolled blank are removed by polishing, the rolled blank is put into an electric furnace, the temperature is 920 ℃, the temperature is kept for 40 minutes, and the rolled blank is rolled into a bar with the deformation of 70 percent. In contrast to example 1, example 2 produced a mill blank using a rolling process, whereas example 1 produced a mill blank using a radial forging process.
FIG. 5 is the microstructure morphology of the bar obtained in example 2 by the preparation process proposed by the present invention. It can be seen that the rolled bar structure, the rolled bar structure and the heat-treated structure of the rolled bar obtained were similar to those of example 1, since the deformation process of the rolled bar was also at or above the transformation point and the deformation, the finishing temperature and the finishing deformation were the same as those of example 1. The tensile strength of the material at room temperature and at a high temperature of 600 ℃ is significantly improved compared to the comparative examples, which are detailed in table 1.
Example 3:
a bar of phi 80mm after cogging + forging in the comparative example was used. The bar is polished and then put into an electric furnace, the temperature is 1050 ℃, the temperature is kept for 80 minutes, and then the bar is radially forged into a blank with 50 percent of deformation. After the surface defects of the rolled blank are removed by grinding, the rolled blank is put into an electric furnace, the temperature is 960 ℃, the temperature is kept for 40 minutes, and the rolled blank is rolled into a bar, and the deformation is 85 percent. The tensile strength of the material at room temperature and at a high temperature of 600 ℃ is significantly improved compared to the comparative examples, which are detailed in table 1.
Example 4:
a bar of 80mm diameter after cogging + forging in the comparative example was used. The bar is polished and then put into an electric furnace, the temperature is 1070 ℃, the temperature is kept for 80 minutes, and then the bar is rolled into a blank with the deformation of 65 percent. After the surface defects of the rolled blank are removed by polishing, the rolled blank is put into an electric furnace, the temperature is 940 ℃, the temperature is kept for 40 minutes, and the rolled blank is rolled into a bar with the deformation of 65 percent. The tensile strength of the material at room temperature and at a high temperature of 600 ℃ is significantly improved compared to the comparative examples, which are detailed in table 1.
TABLE 1 mechanical properties of examples and comparative examples
It will be appreciated by those skilled in the art that the above embodiments are only for illustrating the present invention and are not to be construed as limiting the present invention, and that changes and modifications to the above described embodiments are within the scope of the claims of the present invention as long as they are within the spirit and scope of the present invention.
Claims (1)
1. A hot working method for improving the high-temperature tensile strength of a titanium alloy rolled bar is characterized by comprising the following steps:
1) Heating and deforming a bar material obtained by cogging and intermediate billet forging in a beta single-phase region to obtain a final rolled bar blank, and setting the heating temperature to be 30-50 ℃ above the phase transformation point in the process of heating and deforming the bar material in the beta single-phase region to obtain the final rolled bar blank o C, keeping the temperature for 1min/mm, then performing radial forging or roll forming, wherein the deformation amount is 40-70%, and performing air cooling after deformation;
2) Grinding the bar stock obtained in the step 1) to remove surface defects, then heating and rolling the bar stock in an alpha + beta two-phase region low-temperature section, and setting the heating temperature of the finally rolled bar stock to be 60-100 ℃ below the transformation point in the process of heating and rolling the bar stock in the alpha + beta two-phase region low-temperature section o And C, keeping the temperature for 1min/mm, then rolling and forming, wherein the rolling deformation is 60-90%, and air cooling is carried out after deformation.
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| Application Number | Priority Date | Filing Date | Title |
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| CN202210811072.9A CN115178598A (en) | 2022-07-11 | 2022-07-11 | Hot processing method for improving high-temperature tensile strength of titanium alloy rolled bar |
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| CN202210811072.9A CN115178598A (en) | 2022-07-11 | 2022-07-11 | Hot processing method for improving high-temperature tensile strength of titanium alloy rolled bar |
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN116987992A (en) * | 2023-09-27 | 2023-11-03 | 成都先进金属材料产业技术研究院股份有限公司 | Heating method of large-thickness titanium alloy slab |
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN116987992A (en) * | 2023-09-27 | 2023-11-03 | 成都先进金属材料产业技术研究院股份有限公司 | Heating method of large-thickness titanium alloy slab |
| CN116987992B (en) * | 2023-09-27 | 2024-02-02 | 成都先进金属材料产业技术研究院股份有限公司 | Heating method of large-thickness titanium alloy slab |
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