CN110983105A - High-strength titanium alloy suitable for cold rolling and preparation method thereof, titanium alloy cold-rolled tube and preparation method thereof - Google Patents
High-strength titanium alloy suitable for cold rolling and preparation method thereof, titanium alloy cold-rolled tube and preparation method thereof Download PDFInfo
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- 229910001069 Ti alloy Inorganic materials 0.000 title claims abstract description 249
- 238000005097 cold rolling Methods 0.000 title claims abstract description 70
- 238000002360 preparation method Methods 0.000 title claims abstract description 26
- 238000010438 heat treatment Methods 0.000 claims abstract description 63
- 239000010936 titanium Substances 0.000 claims abstract description 23
- 239000012535 impurity Substances 0.000 claims abstract description 21
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 12
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 5
- 238000000137 annealing Methods 0.000 claims description 26
- 238000005096 rolling process Methods 0.000 claims description 22
- 238000004140 cleaning Methods 0.000 claims description 21
- 238000000034 method Methods 0.000 claims description 20
- 238000005242 forging Methods 0.000 claims description 18
- 239000000203 mixture Substances 0.000 claims description 16
- 239000002994 raw material Substances 0.000 claims description 11
- 238000003825 pressing Methods 0.000 claims description 8
- 230000009466 transformation Effects 0.000 claims description 8
- 238000002156 mixing Methods 0.000 claims description 7
- 238000002844 melting Methods 0.000 claims description 6
- 230000008018 melting Effects 0.000 claims description 6
- 238000004519 manufacturing process Methods 0.000 claims description 5
- 238000004321 preservation Methods 0.000 claims description 5
- 229910045601 alloy Inorganic materials 0.000 abstract description 14
- 239000000956 alloy Substances 0.000 abstract description 14
- 230000008901 benefit Effects 0.000 abstract description 2
- 238000003723 Smelting Methods 0.000 description 23
- 238000001816 cooling Methods 0.000 description 14
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 12
- 239000002245 particle Substances 0.000 description 10
- 230000008569 process Effects 0.000 description 10
- 239000002253 acid Substances 0.000 description 9
- 229910000604 Ferrochrome Inorganic materials 0.000 description 8
- 229910001309 Ferromolybdenum Inorganic materials 0.000 description 8
- 229910001182 Mo alloy Inorganic materials 0.000 description 8
- UNQHSZOIUSRWHT-UHFFFAOYSA-N aluminum molybdenum Chemical compound [Al].[Mo] UNQHSZOIUSRWHT-UHFFFAOYSA-N 0.000 description 8
- 229910052799 carbon Inorganic materials 0.000 description 8
- 235000010627 Phaseolus vulgaris Nutrition 0.000 description 7
- 244000046052 Phaseolus vulgaris Species 0.000 description 7
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 7
- 101100366060 Caenorhabditis elegans snap-29 gene Proteins 0.000 description 4
- 238000005336 cracking Methods 0.000 description 3
- 238000010586 diagram Methods 0.000 description 3
- 238000005034 decoration Methods 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 238000005498 polishing Methods 0.000 description 2
- 239000007858 starting material Substances 0.000 description 2
- 238000005482 strain hardening Methods 0.000 description 2
- 229910052719 titanium Inorganic materials 0.000 description 2
- 230000032683 aging Effects 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000003889 chemical engineering Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
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- 239000000463 material Substances 0.000 description 1
- 239000003208 petroleum Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C14/00—Alloys based on titanium
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B19/00—Tube-rolling by rollers arranged outside the work and having their axes not perpendicular to the axis of the work
- B21B19/02—Tube-rolling by rollers arranged outside the work and having their axes not perpendicular to the axis of the work the axes of the rollers being arranged essentially diagonally to the axis of the work, e.g. "cross" tube-rolling ; Diescher mills, Stiefel disc piercers or Stiefel rotary piercers
- B21B19/04—Rolling basic material of solid, i.e. non-hollow, structure; Piercing, e.g. rotary piercing mills
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B45/00—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
- B21B45/02—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills for lubricating, cooling, or cleaning
- B21B45/0269—Cleaning
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B45/00—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
- B21B45/04—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills for de-scaling, e.g. by brushing
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
- B21J5/002—Hybrid process, e.g. forging following casting
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
- C22F1/18—High-melting or refractory metals or alloys based thereon
- C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon
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Abstract
The invention provides a high-strength titanium alloy suitable for cold rolling and a preparation method thereof, a titanium alloy cold-rolled tube and a preparation method thereof, and belongs to the technical field of titanium alloys. The high-strength titanium alloy suitable for cold rolling provided by the invention comprises the following components in percentage by weight: 3 to 4.5 percent of Al, 2.5 to 3.5 percent of Mo, 1.5 to 2.5 percent of Cr, 1.5 to 2.0 percent of Fe, and the balance of Ti and inevitable impurities. The high-strength titanium alloy provided by the invention has good hot and cold processing properties, and the prepared titanium alloy cold-rolled tube can obtain higher strength and elongation rate and also has good plasticity no matter the titanium alloy cold-rolled tube is subjected to common heat treatment or double heat treatment. In addition, the components of the high-strength titanium alloy provided by the invention do not contain expensive alloy elements, and the high-strength titanium alloy has the advantage of low cost.
Description
Technical Field
The invention relates to the technical field of titanium alloys, in particular to a high-strength titanium alloy suitable for cold rolling and a preparation method thereof, a titanium alloy cold-rolled tube and a preparation method thereof.
Background
At present, the titanium alloys which can be suitable for cold rolling in national standard and American standard include TA9, TA10, TA16, TA18, TA21, TA22, TC1, TC2 and the like, and the cold workability of the alloys is excellent, but the strength of the alloys is only 400-850 MPa. The high-strength titanium alloy seamless pipe has the characteristics of high strength, high density, good corrosion resistance and the like, and is an ideal material for key parts in the fields of aviation, aerospace, petroleum, chemical engineering, ships and the like. However, the existing high-strength titanium alloy has the defects of large room-temperature deformation resistance, remarkable processing hardening and easy cracking due to cold deformation, and a cold rolling process cannot be used, so that the high-strength titanium alloy pipe with a certain length and wall thickness and excellent mechanical property is very difficult to process. For example, the strength of the high-strength titanium alloy TC4 titanium alloy can reach 980MPa, but the pipe of the titanium alloy can not be produced by cold rolling at present, can only be prepared by a hot continuous rolling process, and can not ensure the dimensional precision and the quality of the inner and outer surfaces.
Disclosure of Invention
The invention aims to provide a high-strength titanium alloy suitable for cold rolling and a preparation method thereof, and a titanium alloy cold-rolled tube and a preparation method thereof.
In order to achieve the above object, the present invention provides the following technical solutions:
the invention provides a high-strength titanium alloy suitable for cold rolling, which comprises the following components in percentage by weight: 3 to 4.5 percent of Al, 2.5 to 3.5 percent of Mo, 1.5 to 2.5 percent of Cr, 1.5 to 2.0 percent of Fe, and the balance of Ti and inevitable impurities.
Preferably, the high-strength titanium alloy suitable for cold rolling comprises the following components in percentage by weight: 3.0% of Al, 3.5% of Mo3.5%, Cr2.5%, 1.5% of Fe, and the balance of Ti and inevitable impurities.
Preferably, the high-strength titanium alloy suitable for cold rolling comprises the following components in percentage by weight: 3.5% of Al, 2.65% of Mo2, 2.0% of Cr2, 1.7% of Fe, and the balance of Ti and inevitable impurities.
Preferably, the high-strength titanium alloy suitable for cold rolling comprises the following components in percentage by weight: 4.0% of Al, 3.0% of Mo3, 1.8% of Cr, 1.9% of Fe, and the balance of Ti and inevitable impurities.
Preferably, the high-strength titanium alloy suitable for cold rolling comprises the following components in percentage by weight: 4.5% of Al, 2.3% of Mo2, 1.5% of Cr, 2.0% of Fe, and the balance of Ti and inevitable impurities.
The invention also provides a preparation method of the high-strength titanium alloy suitable for cold rolling, which comprises the following steps:
mixing raw materials of high-strength titanium alloy suitable for cold rolling according to a design proportion, pressing the mixture into an electrode, and carrying out vacuum consumable arc melting to obtain a titanium alloy ingot;
and forging the titanium alloy ingot to obtain the high-strength titanium alloy suitable for cold rolling.
The invention also provides a titanium alloy cold-rolled tube which is prepared from the high-strength titanium alloy suitable for cold rolling in the technical scheme or the high-strength titanium alloy suitable for cold rolling prepared by the preparation method in the technical scheme.
The invention also provides a preparation method of the titanium alloy cold-rolled tube, which comprises the following steps:
the preparation method of the technical scheme is adopted to prepare the rod-shaped high-strength titanium alloy suitable for cold rolling, and the rod-shaped high-strength titanium alloy is marked as a high-strength titanium alloy bar;
carrying out cross piercing on the high-strength titanium alloy bar to obtain a titanium alloy tube blank;
removing oxide skins on the inner surface and the outer surface of the titanium alloy tube blank after the titanium alloy tube blank is subjected to first heat treatment to obtain a titanium alloy pierced billet;
and carrying out multi-pass cold rolling on the titanium alloy pierced billet, and then annealing to obtain the titanium alloy cold-rolled pipe.
Preferably, the temperature of the cross-piercing is 30-50 ℃ below the phase transition point;
the temperature of the first heat treatment is 700-750 ℃, and the time is 90-120 min;
the multi-pass cold rolling comprises 3-4 passes of rolling, and cleaning and second heat treatment are sequentially carried out between two adjacent passes of rolling; the pass deformation is 30-45% independently, the temperature of each second heat treatment is 700-750 ℃ independently, and the time is 3h independently; the second heat treatment is performed under vacuum conditions.
Preferably, the annealing is normal annealing or dual annealing; the common annealing is heat preservation for 1h at 700-800 ℃; and the double annealing is to keep the temperature at 810-850 ℃ for 1h, then air-cool the mixture to room temperature, and then heat the mixture to 480-560 ℃ for 4-8 h.
The invention provides a high-strength titanium alloy suitable for cold rolling, which comprises the following components in percentage by weight: 3 to 4.5 percent of Al, 2.5 to 3.5 percent of Mo, 1.5 to 2.5 percent of Cr, 1.5 to 2.0 percent of Fe, and the balance of Ti and inevitable impurities. According to the invention, Mo element is added into the titanium alloy, and is matched with other components, so that the grain size can be reduced, and the plasticity of the titanium alloy can be improved. In addition, the components of the high-strength titanium alloy provided by the invention do not contain expensive alloy elements (such as V, which needs to be added in the form of AlV55 master alloy, and the alloy is expensive), and the high-strength titanium alloy has the advantage of low cost.
The strength of the titanium alloy cold-rolled tube can reach more than 1000MPa, the elongation is more than 10%, the titanium alloy cold-rolled tube can be prepared by adopting the cross piercing and cold rolling processes, the process is simple, and the preparation efficiency and the yield are high.
Drawings
FIG. 1 is a schematic representation of a titanium alloy tubular blank obtained in example 1;
FIG. 2 is a physical representation of a semi-finished tube obtained in example 1;
FIG. 3 is a real object diagram of the inner and outer surfaces of the cold-rolled titanium alloy finished pipe obtained in example 1;
FIG. 4 is a transverse structural view and a longitudinal structural view of a 1# titanium alloy cold rolled tube obtained in example 1.
Detailed Description
The invention provides a high-strength titanium alloy suitable for cold rolling, which comprises the following components in percentage by weight: 3 to 4.5 percent of Al, 2.5 to 3.5 percent of Mo, 1.5 to 2.5 percent of Cr, 1.5 to 2.0 percent of Fe, and the balance of Ti and inevitable impurities.
In the present invention, the high-strength titanium alloy suitable for cold rolling preferably comprises the following components in percentage by weight: 3.0% of Al, 3.5% of Mo, 2.5% of Cr, 1.5% of Fe, and the balance of Ti and inevitable impurities.
In the present invention, the high-strength titanium alloy suitable for cold rolling preferably comprises the following components in percentage by weight: 3.5% of Al3, 2.65% of Mo, 2.0% of Cr2, 1.7% of Fe, and the balance of Ti and inevitable impurities.
In the present invention, the high-strength titanium alloy suitable for cold rolling preferably comprises the following components in percentage by weight: 4.0% of Al, 3.0% of Mo, 1.8% of Cr, 1.9% of Fe, and the balance of Ti and inevitable impurities.
In the present invention, the high-strength titanium alloy suitable for cold rolling preferably comprises the following components in percentage by weight: 4.5% of Al, 2.3% of Mo, 1.5% of Cr, 2.0% of Fe, and the balance of Ti and inevitable impurities.
The invention also provides a preparation method of the high-strength titanium alloy suitable for cold rolling, which comprises the following steps:
mixing raw materials of high-strength titanium alloy suitable for cold rolling according to a design proportion, pressing the mixture into an electrode, and carrying out vacuum consumable arc melting to obtain a titanium alloy ingot;
and forging the titanium alloy ingot to obtain the high-strength titanium alloy suitable for cold rolling.
The invention mixes the raw materials of the high-strength titanium alloy suitable for cold rolling according to the design proportion, presses the mixture into an electrode, and carries out vacuum consumable arc melting to obtain the titanium alloy ingot.
The invention has no special limitation on the specific types of the raw materials of the high-strength titanium alloy suitable for cold rolling, and the proportion of the high-strength titanium alloy required to be prepared can be obtained. In the embodiment of the invention, the raw materials of the high-strength titanium alloy suitable for cold rolling preferably comprise titanium sponge, aluminum-molybdenum alloy, low-carbon ferrochrome, ferromolybdenum and aluminum beans; the aluminum-molybdenum alloy is preferably AlMo60, the low-carbon ferrochrome is preferably FeCr69C0.06, and the ferromolybdenum alloy is preferably FeMo 60; the titanium sponge is preferably 0-grade or 1-grade titanium sponge; the raw material of the high-strength titanium alloy suitable for cold rolling is preferably a granular raw material, the particle size of the raw material is not particularly limited, and a person skilled in the art can select a proper particle size according to circumstances and can press an electrode, in the embodiment of the invention, the particle size of the aluminum-molybdenum alloy is preferably 0.1-0.8 mm, the particle size of the low-carbon ferrochrome is preferably 60 meshes, the particle size of the ferromolybdenum alloy is preferably 1-5 mm, the particle size of the aluminum beans is preferably 8-13 mm, and the particle size of the titanium sponge is preferably 0.83-25.4 mm.
The invention has no special limitation on the concrete parameters of the pressing, and can obtain the electrode which is suitable for the vacuum consumable electrode arc furnace.
In the present invention, the absolute pressure of the vacuum consumable arc melting is preferably 10-2Pa, the smelting current is preferably 8-24 kA, the smelting voltage is preferably 28-35V, and the number of times of vacuum consumable arc smelting is preferably 2-3 times, and more preferably 3 times. In the invention, vacuum consumable arc melting is adopted for 2-3 times, which is beneficial to obtaining the titanium alloy ingot with uniform components.
After the titanium alloy ingot is obtained, the titanium alloy ingot is forged to obtain the high-strength titanium alloy suitable for cold rolling.
The shape of the high-strength titanium alloy suitable for cold rolling is not particularly limited, and a person skilled in the art can forge the alloy into different shapes according to the needs. In the embodiment of the invention, in order to prepare the titanium alloy cold rolled tube, the titanium alloy ingot is forged into a high-strength titanium alloy in a rod shape suitable for cold rolling.
In the invention, the forging is preferably performed by cogging and forging the titanium alloy ingot at 1050-1180 ℃, and then at 30-50 ℃ below the transformation point (T for short)βUpsetting and drawing forging at the temperature of minus 30 to 50 ℃. The specific forging method of the cogging forging and the upsetting forging is not specially limited, and the required high-strength titanium alloy can be obtained. The specification of the high-strength titanium alloy in a rod shape suitable for cold rolling is not particularly limited, and can be selected by those skilled in the art according to the needs.
The invention also provides a titanium alloy cold-rolled tube which is prepared from the high-strength titanium alloy suitable for cold rolling in the technical scheme or the high-strength titanium alloy suitable for cold rolling prepared by the preparation method in the technical scheme.
The invention also provides a preparation method of the titanium alloy cold-rolled tube, which comprises the following steps:
the preparation method of the technical scheme is adopted to prepare the rod-shaped high-strength titanium alloy suitable for cold rolling, and the rod-shaped high-strength titanium alloy is marked as a high-strength titanium alloy bar;
carrying out cross piercing on the high-strength titanium alloy bar to obtain a titanium alloy tube blank;
removing oxide skins on the inner surface and the outer surface of the titanium alloy tube blank after the titanium alloy tube blank is subjected to first heat treatment to obtain a titanium alloy pierced billet;
and carrying out multi-pass cold rolling on the titanium alloy pierced billet, and then annealing to obtain the titanium alloy cold-rolled pipe.
The preparation method of the titanium alloy cold-rolled tube provided by the invention is simple, and has higher production efficiency and yield. Specifically, the high-strength titanium alloy adopted by the invention has excellent hot and cold processing performances, so that the hot processing can realize single-pass large deformation, and the single-pass large deformation can be realized in the cold processing process, so that the hot processing pass and the cold processing pass are reduced under the condition of equal total deformation, and the preparation efficiency of the titanium alloy cold-rolled tube is improved. In addition, due to the excellent cold and hot processing performance, the surface cracking is light or no crack is generated in the hot processing process, the surface polishing time is shortened, the production efficiency is improved, the polishing amount is small, and the yield is improved.
Firstly, preparing a rod-shaped high-strength titanium alloy suitable for cold rolling by adopting the preparation method of the technical scheme, and marking the rod-shaped high-strength titanium alloy as a high-strength titanium alloy bar; and then carrying out cross roll piercing on the high-strength titanium alloy bar to obtain a titanium alloy tube blank.
In the invention, peeling is preferably carried out before the cross rolling perforation, and the high-strength titanium alloy bar subjected to peeling is subjected to cross rolling perforation; the scalping can remove the surface oxide layer and the small defects of the high-strength titanium alloy bar, and can further improve the size precision; the temperature of the cross-piercing (namely the temperature of the high-strength titanium alloy bar) is preferably 30-50 ℃ below the transformation point (abbreviated as T)β- (30-50) ° c); in order to keep the temperature during cross piercing within the above range, it is preferable to perform cross piercing after holding the titanium alloy rod at 30 to 50 ℃ below the transformation point for 90 to 180 min.
After a titanium alloy tube blank is obtained, carrying out first heat treatment on the titanium alloy tube blank, and then removing oxide skins on the inner surface and the outer surface of the titanium alloy tube blank to obtain a titanium alloy pierced billet;
in the invention, the temperature of the first heat treatment is preferably 700-750 ℃, and the time is preferably 90-120 min. In the present invention, the atmosphere of the first heat treatment is not particularly limited, and may be performed in an atmospheric atmosphere or under a vacuum condition. In the present invention, the first heat treatment can sufficiently eliminate work hardening by cold working, and improve the working plasticity of the titanium alloy.
The method for removing the oxide skin is not particularly limited, and a conventional removing method can be adopted, for example, a lathe is adopted to peel the outer surface of the titanium alloy tube blank after the first heat treatment so as to remove the oxide skin on the outer surface, and a boring machine is adopted to bore the inner surface of the titanium alloy tube blank after the first heat treatment so as to remove the oxide skin on the inner surface.
After the titanium alloy pierced billet is obtained, the titanium alloy pierced billet is subjected to multi-pass cold rolling and then annealing to obtain the titanium alloy cold-rolled tube.
In the invention, the multi-pass cold rolling preferably comprises 3-4 passes of rolling, and cleaning and second heat treatment which are sequentially carried out are preferably carried out between two adjacent passes of rolling; the pass deformation is preferably 30-45% independently, the temperature of each second heat treatment is preferably 700-750 ℃ independently, and the time is preferably 3h independently; the second heat treatment is preferably carried out under vacuum, and the absolute pressure of the second heat treatment is preferably 10-2Pa; the cleaning preferably comprises oil removal and acid cleaning, the oil removal and acid cleaning process is not particularly limited, and the conventional oil removal and acid cleaning steps are adopted, so that the oil removal and acid cleaning can avoid polluting a heat treatment furnace in the vacuum heat treatment process, and can also avoid forming a pollution layer on the surface of the pipe. In the present invention, the rolling equipment is not particularly limited, and a conventional cold pilger mill may be used, and in the embodiment of the present invention, a two-roll cycle cold pilger mill or a three-roll cycle cold pilger mill is preferably used.
After the multi-pass cold rolling is finished, the invention preferably carries out oil removal firstly and then carries out annealing.
In the present invention, the annealing is preferably normal annealing or double annealing; the common annealing is preferably carried out at 700-800 ℃ for 1 h; the double annealing is preferably carried out for 1 hour at 810-850 ℃, then air cooling is carried out to room temperature, and then the temperature is increased to 480-560 ℃ for heat preservation for 4-8 hours. In the double annealing, the heat preservation at 810-850 ℃ for 1h is a solid solution heat treatment, and the heat preservation at 480-560 ℃ for 4-8 h is an aging heat treatment process; after the annealing is completed, air cooling to room temperature is preferred.
The present invention provides a high-strength titanium alloy suitable for cold rolling and a method for manufacturing the same, a titanium alloy cold rolled tube and a method for manufacturing the same, which are described in detail below with reference to the examples, but they should not be construed as limiting the scope of the present invention.
Example 1
The titanium alloy of the present example has nominal composition of Ti-3.0Al-3.5Mo-2.5Cr-1.5Fe, i.e. comprises the following components in weight percent: 3.0% of Al, 3.5% of Mo, 2.5% of Cr, 1.5% of Fe, and the balance of Ti and inevitable impurities;
raw materials: titanium sponge grade 0: the particle size is 0.85-25.4 mm; the aluminum-molybdenum alloy is AlMo60 with the grain diameter of 0.1-0.8 mm; the low-carbon ferrochrome is FeCr69C0.06 with 60 meshes; the ferro-molybdenum alloy is FeMo60 with the grain diameter of 1-5 mm; the particle size of the aluminum beans is 8-13 mm;
(1) mixing 0-grade sponge titanium, aluminum-molybdenum alloy, low-carbon ferrochrome, ferromolybdenum alloy and aluminum beans according to the design proportion, pressing into an electrode, and then carrying out three-time smelting in a vacuum consumable arc furnace to obtain a titanium alloy cast ingot with phi 560 mm; wherein the absolute pressure of the third smelting is 10-2Pa, the current of the first smelting is 8kA, the voltage is 28V, the current of the second smelting is 11kA, the voltage is 30V, the current of the third smelting is 19kA, and the voltage is 32V;
(2) cogging and forging the titanium alloy ingot at 1050 ℃ and TβUpsetting, drawing and forging at-30 ℃ (namely 30 ℃ below the transformation point) to obtain a titanium alloy bar with the diameter of 75 mm;
(3) peeling the titanium alloy bar to obtain a titanium alloy ingot blank with the diameter of phi 70mm, and then performing T treatment on the titanium alloy ingot blankβHeating at-30 ℃ for 60-180 min at TβCarrying out cross piercing at-30 ℃ to obtain a titanium alloy tube blank with phi of 70 multiplied by 10mm (namely, the outer diameter is 70mm, and the wall thickness is 10 mm);
(4) carrying out first heat treatment on the titanium alloy tube blank in a vacuum annealing furnace at 700 ℃ for 90min, then peeling the outer surface of the titanium alloy tube blank subjected to the first heat treatment by using a lathe, and boring the inner surface of the titanium alloy tube blank subjected to the first heat treatment by using a boring machine to obtain a titanium alloy pierced billet with the diameter of 69 x 9.5 mm;
(5) carrying out cold rolling on the titanium alloy pierced billet for 4 times, wherein the rolling process comprises the following steps: phi 69 multiplied by 9.5mm → phi 54 multiplied by 7mm → phi 45 multiplied by 5.5mm → phi 35 multiplied by 4mm → phi 32 multiplied by 3mm (namely the specification of the semi-finished tube obtained by the first pass rolling is phi 54 multiplied by 7mm, the specification of the semi-finished tube obtained by the second pass rolling is phi 45 multiplied by 5.5mm, the specification of the semi-finished tube obtained by the third pass rolling is phi 35 multiplied by 4mm, the specification of the finished tube obtained by the fourth pass rolling is phi 32 multiplied by 3mm), cleaning and second heat treatment are sequentially carried out between the two adjacent passes of rolling, each cleaning comprises oil removal and acid cleaning which are sequentially carried out, and each second heat treatment comprises oil removal and acid cleaning which are sequentially carried outThe temperature of the treatment is 700 deg.C, the time is 3h, and the absolute pressure of each second heat treatment is 10-2Pa; after cold rolling is finished, deoiling to obtain a cold-rolled titanium alloy finished pipe with the diameter of 32 multiplied by 3 mm;
(6) and (3) preserving the heat of the cold-rolled titanium alloy finished pipe for 1h at 700 ℃, and then air-cooling to room temperature to obtain a titanium alloy cold-rolled pipe, which is marked as a No. 1 titanium alloy cold-rolled pipe.
Preparing a cold-rolled titanium alloy finished pipe according to the steps (1) to (5), heating the cold-rolled titanium alloy finished pipe to 810 ℃, preserving heat for 1h, then air-cooling to room temperature, heating to 540 ℃, preserving heat for 6h, and then air-cooling to room temperature to obtain the titanium alloy cold-rolled pipe, which is marked as a 1' # titanium alloy cold-rolled pipe.
The room temperature tensile strength and the elongation of the cold-rolled tube of the titanium alloy No. 1 and the cold-rolled tube of the titanium alloy No. 1' # are tested by the method disclosed in GB228.1-2010, and the results are as follows: the tensile strength of the No. 1 titanium alloy cold-rolled tube at room temperature is 1060MPa, and the elongation is 23%; the 1' # titanium alloy cold-rolled tube has the room-temperature tensile strength of 1210MPa and the elongation of 15%.
Example 2
The titanium alloy of the present example has nominal composition of Ti-3.5Al-2.65Mo-2.0Cr-1.7Fe, i.e. comprises the following components in weight percent: 3.5% of Al, 2.65% of Mo, 2.0% of Cr, 1.7% of Fe, and the balance of Ti and inevitable impurities;
the raw materials are the same as those in example 1 except that the titanium sponge is grade 1 titanium sponge, and the particle size of the grade 1 titanium sponge used in the example is the same as that in example 1;
(1) mixing grade 1 titanium sponge, aluminum-molybdenum alloy, low-carbon ferrochrome, ferromolybdenum alloy and aluminum beans according to the design proportion, pressing into an electrode, and then carrying out three-time smelting in a vacuum consumable arc furnace to obtain a titanium alloy ingot with the diameter of phi 640 mm; wherein the absolute pressure of the third smelting is 10-2Pa, the current for the first smelting is 10kA, the voltage is 30V, the current for the second smelting is 18kA, the voltage is 32V, the current for the third smelting is 24kA, and the voltage is 35V;
(2) cogging and forging the titanium alloy ingot at 1150 ℃ and Tβ-40 ℃ (i.e. 40 ℃ below the transformation point)Part) upsetting, drawing and forging to obtain a titanium alloy bar with the diameter of 113 mm;
(3) peeling the titanium alloy bar to obtain a titanium alloy ingot blank with phi 108, and then performing TβHeating at-40 ℃ for 90-210 min at TβCarrying out cross piercing at-40 ℃ to obtain a titanium alloy tube blank with phi of 108 multiplied by 12 mm;
(4) carrying out first heat treatment on the titanium alloy tube blank in a vacuum annealing furnace at 750 ℃ for 90min, then peeling the outer surface of the titanium alloy tube blank subjected to the first heat treatment by adopting a lathe, and boring the inner surface of the titanium alloy tube blank subjected to the first heat treatment by adopting a boring machine to obtain a titanium alloy pierced billet with the diameter of phi 107 multiplied by 11.5 mm;
(5) carrying out 3 times of cold rolling on the titanium alloy pierced billet, wherein the rolling process comprises the following steps: phi 107 multiplied by 11.5mm → phi 89 multiplied by 7.5mm → phi 69 multiplied by 6mm → phi 55 multiplied by 4.5mm, and comprises cleaning and second heat treatment which are carried out in sequence between two adjacent rolling passes, wherein each cleaning comprises oil removal and acid cleaning which are carried out in sequence, the temperature of each second heat treatment is 750 ℃, the time is 3 hours, and the absolute pressure of each second heat treatment is 10-2Pa; after cold rolling is finished, deoiling to obtain a cold-rolled titanium alloy finished pipe with the diameter of 55 multiplied by 4.5 mm;
(6) and (3) preserving the heat of the cold-rolled titanium alloy finished pipe for 1h at 750 ℃, and then air-cooling to room temperature to obtain a titanium alloy cold-rolled pipe, which is marked as a No. 2 titanium alloy cold-rolled pipe.
Preparing a cold-rolled titanium alloy finished pipe according to the steps (1) to (5), heating the cold-rolled titanium alloy finished pipe to 850 ℃, preserving heat for 1h, then air-cooling to room temperature, heating to 560 ℃, preserving heat for 4h, and then air-cooling to room temperature to obtain a titanium alloy cold-rolled pipe, which is marked as a 2' # titanium alloy cold-rolled pipe.
The room temperature tensile strength and the elongation of the 2# titanium alloy cold-rolled tube and the 2' # titanium alloy cold-rolled tube are tested by a GB228.1-2010 method, and the results are as follows: the room-temperature tensile strength of the No. 2 titanium alloy cold-rolled tube is 1030MPa, and the elongation is 21%; the room-temperature tensile strength of the 2' # titanium alloy cold-rolled tube is 1160MPa, and the elongation is 14%.
Example 3
The titanium alloy of the present example has nominal composition of Ti-4.0Al-3.0Mo-1.8Cr-1.9Fe, i.e. comprises the following components in weight percent: 4.0% of Al, 3.0% of Mo, 1.8% of Cr, 1.9% of Fe, and the balance of Ti and inevitable impurities;
the starting materials were the same as in example 1;
(1) mixing 0-grade sponge titanium, aluminum-molybdenum alloy, low-carbon ferrochrome, ferromolybdenum alloy and aluminum beans according to the design proportion, pressing into an electrode, and then carrying out three-time smelting in a vacuum consumable arc furnace to obtain a titanium alloy ingot with the diameter of phi 640 mm; wherein the absolute pressure of the third smelting is 10-2Pa, the current for the first smelting is 10kA, the voltage is 30V, the current for the second smelting is 18kA, the voltage is 32V, the current for the third smelting is 24kA, and the voltage is 35V;
(2) cogging and forging the titanium alloy ingot at 1180 ℃ at TβUpsetting, drawing and forging at-50 ℃ (namely 50 ℃ below the transformation point, namely 850 ℃) to obtain a titanium alloy bar with the diameter of 60 mm;
(3) peeling the titanium alloy bar to obtain a titanium alloy ingot blank with phi 55, and then carrying out TβHeating at-50 deg.C (850 deg.C) for 60-180 min at TβCarrying out cross piercing at-50 ℃ to obtain a titanium alloy tube blank with phi of 55 x 8 mm;
(4) carrying out first heat treatment on the titanium alloy tube blank in a vacuum annealing furnace at 700 ℃ for 90min, then peeling the outer surface of the titanium alloy tube blank subjected to the first heat treatment by using a lathe, and boring the inner surface of the titanium alloy tube blank subjected to the first heat treatment by using a boring machine to obtain a titanium alloy pierced billet with the diameter of 54 x 7.5 mm;
(5) carrying out cold rolling on the titanium alloy pierced billet for 4 times, wherein the rolling process comprises the following steps: phi 54 multiplied by 7.5mm → phi 45 multiplied by 4.8mm → phi 35 multiplied by 4mm → phi 32 multiplied by 2.8mm → phi 28 multiplied by 2.0mm, and comprises cleaning and second heat treatment which are carried out in sequence between two adjacent rolling passes, wherein each cleaning comprises oil removal and acid cleaning which are carried out in sequence, the temperature of each second heat treatment is 730 ℃, the time is 3 hours, and the absolute pressure of each second heat treatment is 10-2Pa; after cold rolling is finished, removing oil to obtain a cold-rolled titanium alloy finished pipe with the diameter of phi 28 multiplied by 2 mm;
(6) and (3) preserving the heat of the cold-rolled titanium alloy finished pipe for 1h at 800 ℃, and then air-cooling to room temperature to obtain the titanium alloy cold-rolled pipe, which is marked as a No. 3 titanium alloy cold-rolled pipe.
Preparing a cold-rolled titanium alloy finished pipe according to the steps (1) to (5), heating the cold-rolled titanium alloy finished pipe to 830 ℃, preserving heat for 1h, then air-cooling to room temperature, heating to 560 ℃, preserving heat for 6h, and then air-cooling to room temperature to obtain a titanium alloy cold-rolled pipe, which is marked as a 3' # titanium alloy cold-rolled pipe.
The room temperature tensile strength and the elongation of the cold-rolled tube of the 3# titanium alloy and the cold-rolled tube of the 3' # titanium alloy are tested by the method GB228.1-2010, and the results are as follows: the room-temperature tensile strength of the No. 3 titanium alloy cold-rolled tube is 1080MPa, and the elongation is 22%; the room-temperature tensile strength of the 3' # titanium alloy cold-rolled tube is 1180MPa, and the elongation is 13%.
Example 4
The titanium alloy of this example has a nominal composition of Ti-4.5Al-2.5Mo-1.5Cr-2.0Fe, i.e., comprises the following components in weight percent: 4.5% of Al, 2.5% of Mo, 1.5% of Cr, 2.0% of Fe, and the balance of Ti and inevitable impurities;
the starting materials were the same as in example 2;
(1) mixing grade 1 titanium sponge, aluminum-molybdenum alloy, low-carbon ferrochrome, ferromolybdenum alloy and aluminum beans according to the design proportion, pressing into an electrode, and then carrying out three-time smelting in a vacuum consumable arc furnace to obtain a phi 560 titanium alloy cast ingot; wherein the absolute pressure of the third smelting is 10-2Pa, the current for the first smelting is 8kA, the voltage is 28V, the current for the second smelting is 10kA, the voltage is 30V, the current for the third smelting is 18kA, and the voltage is 32V;
(2) cogging and forging the titanium alloy ingot at 1100 ℃, and performing forging at TβUpsetting, drawing and forging at-40 ℃ (namely 40 ℃ below the transformation point, namely 880 ℃) to obtain a titanium alloy bar with the diameter of 135 mm;
(3) peeling the titanium alloy bar to obtain a titanium alloy ingot blank with phi 130, and then performing TβHeating at-40 deg.C (880 deg.C) for 90-120 min at TβCarrying out cross piercing at-40 ℃ to obtain a titanium alloy tube blank with the diameter of 130 x 10 mm;
(4) carrying out first heat treatment on the titanium alloy tube blank in a vacuum annealing furnace at 750 ℃ for 120min, then peeling the outer surface of the titanium alloy tube blank subjected to the first heat treatment by using a lathe, and boring the inner surface of the titanium alloy tube blank subjected to the first heat treatment by using a boring machine to obtain a titanium alloy pierced billet with phi 129 x 9.5 mm;
(5) carrying out cold rolling on the titanium alloy pierced billet for 4 times, wherein the rolling process comprises the following steps: phi 129 multiplied by 9.5mm → phi 45 multiplied by 4.8mm → phi 35 multiplied by 4mm → phi 32 multiplied by 2.8mm → phi 28 multiplied by 2.0mm, wherein cleaning and second heat treatment are carried out in sequence between two adjacent rolling passes, each cleaning comprises oil removal and acid cleaning which are carried out in sequence, the temperature of each second heat treatment is 750 ℃, the time is 3 hours, and the absolute pressure of each second heat treatment is 10-2Pa; after cold rolling is finished, removing oil to obtain a cold-rolled titanium alloy finished pipe with the diameter of phi 28 multiplied by 2.0 mm;
(6) and (3) preserving the heat of the cold-rolled titanium alloy finished pipe for 1h at 780 ℃, and then air-cooling to room temperature to obtain a titanium alloy cold-rolled pipe, which is marked as a No. 4 titanium alloy cold-rolled pipe.
Preparing a cold-rolled titanium alloy finished pipe according to the steps (1) to (5), heating the cold-rolled titanium alloy finished pipe to 850 ℃, preserving heat for 1h, then air-cooling to room temperature, heating to 480 ℃, preserving heat for 8h, and then air-cooling to room temperature to obtain the titanium alloy cold-rolled pipe, which is marked as a 4' # titanium alloy cold-rolled pipe.
The room temperature tensile strength and the elongation of the 4# titanium alloy cold-rolled tube and the 4' # titanium alloy cold-rolled tube are tested by the GB228.1-2010 method, and the results are as follows: the tensile strength at room temperature of the No. 4 titanium alloy cold-rolled tube is 1020MPa, and the elongation is 21%; the room-temperature tensile strength of the 4' # titanium alloy cold-rolled tube is 1130MPa, and the elongation is 12%.
FIG. 1 is a schematic representation of a titanium alloy pipe blank obtained in example 1, FIG. 2 is a schematic representation of a semi-finished pipe (Φ 35X 4mm) obtained in example 1, and FIG. 3 is a schematic representation of the outer surface (a) and the inner surface (b) of the cold rolled titanium alloy finished pipe obtained in example 3. As can be seen from the figures 1 to 3, no cracking phenomenon occurs in the whole processing process, and the inner and outer surfaces of the cold-rolled titanium alloy finished pipe are smooth, so that the quality of the finished pipe is high.
FIG. 4 shows a transverse structural diagram (a) and a longitudinal structural diagram (b) of the cold rolled tube of # 1 titanium alloy obtained in example 1. As can be seen from FIG. 4, the crystal grains of the cold rolled tube of titanium alloy obtained in this example are fine and about 3 to 5 μm.
The foregoing is only a preferred embodiment of the present invention, and it should be noted that, for those skilled in the art, various modifications and decorations can be made without departing from the principle of the present invention, and these modifications and decorations should also be regarded as the protection scope of the present invention.
Claims (10)
1. A high-strength titanium alloy suitable for cold rolling is characterized by comprising the following components in percentage by weight: 3 to 4.5 percent of Al, 2.5 to 3.5 percent of Mo, 1.5 to 2.5 percent of Cr, 1.5 to 2.0 percent of Fe, and the balance of Ti and inevitable impurities.
2. A high strength titanium alloy suitable for cold rolling according to claim 1, comprising the following composition in weight percent: 3.0% of Al, 3.5% of Mo, 2.5% of Cr, 1.5% of Fe, and the balance of Ti and inevitable impurities.
3. A high strength titanium alloy suitable for cold rolling according to claim 1, comprising the following composition in weight percent: 3.5% of Al, 2.65% of Mo, 2.0% of Cr, 1.7% of Fe, and the balance of Ti and inevitable impurities.
4. A high strength titanium alloy suitable for cold rolling according to claim 1, comprising the following composition in weight percent: 4.0% of Al, 3.0% of Mo, 1.8% of Cr, 1.9% of Fe, and the balance of Ti and inevitable impurities.
5. A high strength titanium alloy suitable for cold rolling according to claim 1, comprising the following composition in weight percent: 4.5% of Al, 2.3% of Mo, 1.5% of Cr, 2.0% of Fe, and the balance of Ti and inevitable impurities.
6. A preparation method of the high-strength titanium alloy suitable for cold rolling according to any one of claims 1 to 5, characterized by comprising the following steps:
mixing raw materials of high-strength titanium alloy suitable for cold rolling according to a design proportion, pressing the mixture into an electrode, and carrying out vacuum consumable arc melting to obtain a titanium alloy ingot;
and forging the titanium alloy ingot to obtain the high-strength titanium alloy suitable for cold rolling.
7. A titanium alloy cold rolled tube is characterized by being prepared from the high-strength titanium alloy suitable for cold rolling according to any one of claims 1 to 5 or the high-strength titanium alloy suitable for cold rolling prepared by the preparation method according to claim 6.
8. The method for preparing the titanium alloy cold rolled tube according to claim 7, which is characterized by comprising the following steps:
preparing a rod-shaped high-strength titanium alloy suitable for cold rolling by adopting the preparation method of claim 6, and marking as a high-strength titanium alloy rod;
carrying out cross piercing on the high-strength titanium alloy bar to obtain a titanium alloy tube blank;
removing oxide skins on the inner surface and the outer surface of the titanium alloy tube blank after the titanium alloy tube blank is subjected to first heat treatment to obtain a titanium alloy pierced billet;
and carrying out multi-pass cold rolling on the titanium alloy pierced billet, and then annealing to obtain the titanium alloy cold-rolled pipe.
9. The preparation method according to claim 8, wherein the temperature of the cross piercing is 30 to 50 ℃ below the transformation point;
the temperature of the first heat treatment is 700-750 ℃, and the time is 90-120 min;
the multi-pass cold rolling comprises 3-4 passes of rolling, and cleaning and second heat treatment are sequentially carried out between two adjacent passes of rolling; the pass deformation is 30-45% independently, the temperature of each second heat treatment is 700-750 ℃ independently, and the time is 3h independently; the second heat treatment is performed under vacuum conditions.
10. The production method according to claim 8, wherein the annealing is normal annealing or double annealing; the common annealing is heat preservation for 1h at 700-800 ℃; and the double annealing is to keep the temperature at 810-850 ℃ for 1h, then air-cool the mixture to room temperature, and then heat the mixture to 480-560 ℃ for 4-8 h.
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Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111349816A (en) * | 2020-04-13 | 2020-06-30 | 新疆湘润新材料科技有限公司 | Novel Ti-1300F high-strength high-toughness titanium alloy and preparation method thereof |
| CN112496052A (en) * | 2020-11-11 | 2021-03-16 | 西部金属材料股份有限公司 | Titanium or titanium alloy seamless square and rectangular tube and preparation method thereof |
| CN112605123A (en) * | 2020-11-30 | 2021-04-06 | 西北有色金属研究院 | Preparation method of low-cost high-toughness titanium alloy pipe for ocean engineering |
| CN114657417A (en) * | 2022-05-07 | 2022-06-24 | 北京航空航天大学 | High-strength plastic titanium alloy suitable for cold deformation processing and preparation method thereof |
| CN115821112A (en) * | 2022-12-26 | 2023-03-21 | 西部金属材料股份有限公司 | Titanium alloy suitable for cold machining, preparation method thereof and titanium alloy component |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101333612A (en) * | 2008-08-05 | 2008-12-31 | 北京正安广泰新材料科技有限公司 | Low cost alpha and beta type titan alloy |
| CN101403058A (en) * | 2008-11-21 | 2009-04-08 | 北京正安广泰新材料科技有限公司 | Low cost alpha and beta type titan alloy |
| JP2012041609A (en) * | 2010-08-20 | 2012-03-01 | Nhk Spring Co Ltd | High-strength titanium alloy member and process for production thereof |
| JP6269836B2 (en) * | 2014-07-25 | 2018-01-31 | 新日鐵住金株式会社 | Titanium alloy member having shape change characteristic in the same direction as the machining direction |
| CN107746991A (en) * | 2017-09-29 | 2018-03-02 | 北京金宇顺达科技股份有限公司 | A kind of titanium alloy and preparation method thereof |
| CN108160742A (en) * | 2016-12-07 | 2018-06-15 | 北京有色金属研究总院 | A kind of metastable beta-type titanium alloy TB16 cold rolled tube processing methods |
-
2019
- 2019-12-23 CN CN201911336468.7A patent/CN110983105B/en active Active
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101333612A (en) * | 2008-08-05 | 2008-12-31 | 北京正安广泰新材料科技有限公司 | Low cost alpha and beta type titan alloy |
| CN101403058A (en) * | 2008-11-21 | 2009-04-08 | 北京正安广泰新材料科技有限公司 | Low cost alpha and beta type titan alloy |
| JP2012041609A (en) * | 2010-08-20 | 2012-03-01 | Nhk Spring Co Ltd | High-strength titanium alloy member and process for production thereof |
| JP6269836B2 (en) * | 2014-07-25 | 2018-01-31 | 新日鐵住金株式会社 | Titanium alloy member having shape change characteristic in the same direction as the machining direction |
| CN108160742A (en) * | 2016-12-07 | 2018-06-15 | 北京有色金属研究总院 | A kind of metastable beta-type titanium alloy TB16 cold rolled tube processing methods |
| CN107746991A (en) * | 2017-09-29 | 2018-03-02 | 北京金宇顺达科技股份有限公司 | A kind of titanium alloy and preparation method thereof |
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111349816A (en) * | 2020-04-13 | 2020-06-30 | 新疆湘润新材料科技有限公司 | Novel Ti-1300F high-strength high-toughness titanium alloy and preparation method thereof |
| CN112496052A (en) * | 2020-11-11 | 2021-03-16 | 西部金属材料股份有限公司 | Titanium or titanium alloy seamless square and rectangular tube and preparation method thereof |
| CN112605123A (en) * | 2020-11-30 | 2021-04-06 | 西北有色金属研究院 | Preparation method of low-cost high-toughness titanium alloy pipe for ocean engineering |
| CN112605123B (en) * | 2020-11-30 | 2022-03-15 | 西北有色金属研究院 | Preparation method of low-cost high-toughness titanium alloy pipe for ocean engineering |
| CN114657417A (en) * | 2022-05-07 | 2022-06-24 | 北京航空航天大学 | High-strength plastic titanium alloy suitable for cold deformation processing and preparation method thereof |
| CN114657417B (en) * | 2022-05-07 | 2022-12-23 | 北京航空航天大学 | High-strength plastic titanium alloy suitable for cold deformation processing and preparation method thereof |
| CN115821112A (en) * | 2022-12-26 | 2023-03-21 | 西部金属材料股份有限公司 | Titanium alloy suitable for cold machining, preparation method thereof and titanium alloy component |
| CN115821112B (en) * | 2022-12-26 | 2024-03-15 | 西部金属材料股份有限公司 | Titanium alloy suitable for cold working, preparation method thereof and titanium alloy component |
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