CN114700387B - Preparation method of high-strength titanium alloy cold-rolled pipe - Google Patents
Preparation method of high-strength titanium alloy cold-rolled pipe Download PDFInfo
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- CN114700387B CN114700387B CN202210309957.9A CN202210309957A CN114700387B CN 114700387 B CN114700387 B CN 114700387B CN 202210309957 A CN202210309957 A CN 202210309957A CN 114700387 B CN114700387 B CN 114700387B
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- 229910001069 Ti alloy Inorganic materials 0.000 title claims abstract description 253
- 238000002360 preparation method Methods 0.000 title claims abstract description 20
- 238000010438 heat treatment Methods 0.000 claims abstract description 115
- 238000005097 cold rolling Methods 0.000 claims abstract description 35
- 238000001816 cooling Methods 0.000 claims abstract description 32
- 238000005242 forging Methods 0.000 claims abstract description 29
- 238000005096 rolling process Methods 0.000 claims abstract description 28
- 238000001125 extrusion Methods 0.000 claims abstract description 27
- 238000000034 method Methods 0.000 claims abstract description 17
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims abstract description 17
- 238000005098 hot rolling Methods 0.000 claims abstract description 15
- 238000004381 surface treatment Methods 0.000 claims abstract description 9
- 238000004321 preservation Methods 0.000 claims description 16
- 239000002253 acid Substances 0.000 claims description 10
- 238000010304 firing Methods 0.000 claims description 9
- 238000005406 washing Methods 0.000 claims description 8
- 238000005238 degreasing Methods 0.000 claims description 6
- 230000009466 transformation Effects 0.000 claims description 3
- 230000007423 decrease Effects 0.000 claims 1
- 238000004519 manufacturing process Methods 0.000 claims 1
- 229910052751 metal Inorganic materials 0.000 abstract description 3
- 239000002184 metal Substances 0.000 abstract description 3
- 238000010586 diagram Methods 0.000 description 33
- 239000000314 lubricant Substances 0.000 description 29
- 239000011521 glass Substances 0.000 description 23
- 239000000843 powder Substances 0.000 description 21
- 230000003287 optical effect Effects 0.000 description 19
- 239000011248 coating agent Substances 0.000 description 12
- 238000000576 coating method Methods 0.000 description 12
- 239000000956 alloy Substances 0.000 description 10
- 229910045601 alloy Inorganic materials 0.000 description 9
- 229910001040 Beta-titanium Inorganic materials 0.000 description 8
- 238000007599 discharging Methods 0.000 description 8
- 239000000463 material Substances 0.000 description 8
- 230000008569 process Effects 0.000 description 7
- 238000005266 casting Methods 0.000 description 4
- 238000005336 cracking Methods 0.000 description 4
- 238000005482 strain hardening Methods 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 2
- 230000003247 decreasing effect Effects 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 230000002349 favourable effect Effects 0.000 description 2
- 229910002804 graphite Inorganic materials 0.000 description 2
- 239000010439 graphite Substances 0.000 description 2
- 238000005554 pickling Methods 0.000 description 2
- 230000007704 transition Effects 0.000 description 2
- 230000006978 adaptation Effects 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 230000008030 elimination Effects 0.000 description 1
- 238000003379 elimination reaction Methods 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
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- 239000007769 metal material Substances 0.000 description 1
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- 238000012986 modification Methods 0.000 description 1
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Classifications
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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
- B21C37/06—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of tubes or metal hoses; Combined procedures for making tubes, e.g. for making multi-wall tubes
Abstract
The invention relates to the technical field of metal processing, and provides a preparation method of a high-strength titanium alloy cold-rolled pipe. The method provided by the invention comprises the steps of carrying out finish forging or extrusion on a titanium alloy cast ingot in a beta phase region, wherein the room temperature tensile strength of titanium alloy forming the titanium alloy cast ingot is more than or equal to 700MPa, obtaining a bar blank, carrying out oblique rolling perforation and online water cooling on the bar blank in the beta phase region to obtain a tube blank 1, then carrying out extrusion or hot rolling on the tube blank 1 in a two-phase region to obtain a tube blank 2, and carrying out cold rolling, surface treatment and heat treatment on the tube blank 2 to obtain the high-strength titanium alloy tube. According to the invention, the titanium alloy is treated in the beta phase region and the two phase region, so that the cold processing performance of the titanium alloy is improved, the titanium alloy can be prepared into a pipe through cold rolling, and the problem of poor dimensional accuracy caused by a hot continuous rolling method is solved.
Description
Technical Field
The invention relates to the technical field of metal processing, in particular to a preparation method of a high-strength titanium alloy cold-rolled pipe.
Background
At present, titanium alloy materials suitable for cold rolling in national standards and American standards comprise TA9, TA10, TA16, TA18, TA21, TA22, TC1, TC2 and the like, and the alloys have good cold processing performance, so that the prepared cold-rolled part has high dimensional accuracy and good surface quality, but the strength of the cold-rolled seamless pipe cannot meet the requirements of the existing market because the tensile strength of the materials is between 400 and 700MPa.
To meet the demands of the existing market, high-strength titanium alloy seamless tubes begin to enter the field of vision of people. The high-strength titanium alloy seamless pipe is a seamless pipe prepared from titanium alloy with tensile strength of more than 700Mpa, has the characteristics of high strength, high density, corrosion resistance and the like, and is an ideal material for key parts in the fields of aviation, aerospace, petroleum, chemical industry, ships, armored vehicles and the like. However, the existing high-strength titanium alloy has the problems of high room temperature deformation resistance, remarkable work hardening, easy cracking during cold deformation and the like. Therefore, the high-strength titanium alloy pipe cannot be produced by using a cold rolling process in the preparation process, and can only be produced by using a hot continuous rolling process, and the pipe prepared by using the hot continuous rolling process has low dimensional accuracy.
Disclosure of Invention
In view of the above, the invention provides a preparation method of a high-strength titanium alloy cold-rolled pipe. The high-strength titanium alloy cold-rolled tube prepared by the method provided by the invention has high dimensional accuracy.
In order to achieve the above object, the present invention provides the following technical solutions: a preparation method of a high-strength titanium alloy cold-rolled pipe comprises the following steps:
heating a titanium alloy ingot in a beta phase region, and forging or extruding to obtain a titanium alloy rod blank; the firing number of the forging or extrusion is independently equal to or more than 1 firing number;
heating the titanium alloy rod blank in a beta phase region, and then sequentially performing oblique rolling perforation, water cooling, first heat treatment and straightening to obtain a titanium alloy tube blank 1;
heating the titanium alloy tube blank 1 in a two-phase region, extruding or hot rolling, and performing second heat treatment and straightening to obtain a titanium alloy tube blank 2;
performing inner and outer surface treatment on the titanium alloy tube blank 2 to obtain a titanium alloy tube blank 3;
performing cold rolling for more than or equal to 1 pass on the titanium alloy tube blank 3, and performing aftertreatment after each cold rolling to obtain a high-strength titanium alloy cold-rolled tube;
the post-treatment comprises degreasing, acid washing, third heat treatment and straightening;
the room temperature tensile strength of the titanium alloy forming the titanium alloy cast ingot is more than or equal to 700MPa.
Preferably, the heating temperature of the titanium alloy ingot in the beta phase region is 1170 ℃ to (T) β +30)℃。
Preferably, the temperature at which the titanium alloy rod blank is heated in the beta phase region is (T) β +30)℃～1050℃，T β For the beta phase transition temperature of the titanium alloy, the heat preservation time of the titanium alloy rod blank in a beta phase region meets the following relationship: t is t 1 ＝0.8D 1 min～(0.8D 1 +120) min, where t 1 The heat preservation time D of heating the titanium alloy rod blank in the beta phase region 1 The diameter of the titanium alloy rod blank is in mm, and the deformation of the titanium alloy rod blank after the oblique rolling perforation is 15-55%.
Preferably, the tube blank 1 is heated in the two-phase zone at a temperature (T β -50)℃～(T β -30)℃，T β For the titanium alloy beta transformation temperature, the deformation of the titanium alloy tube blank 1 after heating in a two-phase region for extrusion is 65-86%; the deformation amount of the hot rolling is 70-85%.
Preferably, the temperature of the first heat treatment is 750 ℃ to 900 ℃, and the temperature of the second heat treatment is 700 ℃ to 800 ℃.
Preferably, the heat-preserving time of heating the tube blank 1 in the two-phase zone, the heat-preserving time of the first heat treatment, the second heat treatment and the third heat treatment are independently 60 to 180 minutes.
Preferably, the single pass rolling deformation amount of the cold rolling is 30 to 46%.
Preferably, the titanium alloy ingot comprises TA15, TA17, TA18CF, TA23, TA24, TC3, TC4ELI, ti32 or TC16.
Preferably, the wall thickness of the high-strength titanium alloy cold-rolled pipe is less than or equal to 6mm.
The invention provides a preparation method of a high-strength titanium alloy cold-rolled pipe, which comprises the following steps: heating a titanium alloy ingot in a beta phase region, and forging or extruding to obtain a titanium alloy rod blank; the firing number of the forging or extrusion is independently equal to or more than 1 firing number; heating the titanium alloy rod blank in a beta phase region, and then sequentially performing oblique rolling perforation, water cooling, first heat treatment and straightening to obtain a titanium alloy tube blank 1; heating the titanium alloy tube blank 1 in a two-phase region, extruding or hot rolling, and performing second heat treatment and straightening to obtain a titanium alloy tube blank 2; performing inner and outer surface treatment on the titanium alloy tube blank 2 to obtain a titanium alloy tube blank 3; performing cold rolling for more than or equal to 1 pass on the titanium alloy tube blank 3, and performing aftertreatment after each cold rolling to obtain a high-strength titanium alloy cold-rolled tube; the post-treatment comprises degreasing, acid washing, third heat treatment and straightening; the room temperature tensile strength of the titanium alloy forming the titanium alloy cast ingot is more than or equal to 700MPa. The invention forges or extrudes the titanium alloy cast ingot in the beta phase region to obtain a titanium alloy rod blank with fine and uniform beta grains, heats the titanium alloy rod blank in the beta phase region, performs oblique rolling perforation and water cooling to obtain a tube blank 1 with a beta phase structure with fine alpha sheet layers, and extrudes or hot-rolls the titanium alloy cast ingot after heating the two phase regions, so that the beta grains in the titanium alloy can be further crushed, and the cold processing performance of the high-strength titanium alloy is improved. Meanwhile, the strong texture formed in the axial direction of the tube blank can be eliminated through forging or extrusion in the beta phase region, oblique rolling perforation in the beta phase region, water cooling and heat treatment after water cooling, so that the high-strength titanium alloy tube blank 3 is more beneficial to cold rolling treatment, and when the forging or extrusion firing time of the beta phase region is more than 1 time, the elimination effect on the strong texture formed in the axial direction is more obvious. The preparation method provided by the invention effectively solves the problems of large room temperature deformation resistance, remarkable work hardening, easy cracking during cold deformation and the like in the cold working process of the high-strength titanium alloy, and the obtained high-strength titanium alloy cold-rolled pipe has the dimensional accuracy.
Furthermore, the high-precision high-strength titanium alloy pipe with the wall thickness below 6mm is difficult to prepare by the existing hot continuous rolling technology, and the method provided by the invention is superior to the existing hot continuous rolling technology, and the high-precision high-strength titanium alloy pipe with the wall thickness less than or equal to 6mm can be prepared.
Drawings
FIG. 1 is a process flow diagram of the present invention for preparing a high strength titanium alloy tubing;
FIG. 2 is an internal structure diagram of a TA18CF titanium alloy tube blank 1 in example 2;
FIG. 3 is an internal structure diagram of the TA18CF titanium alloy finished tube in example 2;
FIG. 4 is an internal structure diagram of a Ti32 titanium alloy tube blank 1 in example 3;
FIG. 5 is an internal structure diagram of the TC4 titanium alloy finished tubing of example 3;
FIG. 6 is an internal structure diagram of a TC4 titanium alloy pipe blank 1 in example 4;
FIG. 7 is an internal structure diagram of the TC4 titanium alloy finished tubing of example 4;
FIG. 8 is an internal structure diagram of a TC16 titanium alloy pipe blank 1 in example 6;
FIG. 9 is an internal structure diagram of the TC16 titanium alloy finished tubing of example 6.
Detailed Description
The invention provides a preparation method of a high-strength titanium alloy cold-rolled pipe, which comprises the following steps:
heating a titanium alloy ingot in a beta phase region, and then forging or extruding the ingot in sequence to obtain a titanium alloy rod blank; the firing times of forging or extrusion are independently not less than 1 firing time;
heating the titanium alloy rod blank in a beta phase region, and then sequentially performing oblique rolling perforation, water cooling, first heat treatment and straightening to obtain a titanium alloy tube blank 1;
heating the titanium alloy tube blank 1 in a two-phase region, extruding or hot rolling, and performing second heat treatment and straightening to obtain a titanium alloy tube blank 2;
performing inner and outer surface treatment on the titanium alloy tube blank 2 to obtain a titanium alloy tube blank 3;
performing cold rolling for more than or equal to 1 pass on the titanium alloy tube blank 3, and performing aftertreatment after each cold rolling to obtain a high-strength titanium alloy cold-rolled tube;
the post-treatment comprises degreasing, acid washing, third heat treatment and straightening;
the room temperature tensile strength of the titanium alloy forming the titanium alloy cast ingot is more than or equal to 700MPa.
The preparation raw materials used in the invention are all commercially available unless otherwise specified.
In the invention, a titanium alloy ingot is heated in a beta phase region, and then is forged or extruded in sequence to obtain a titanium alloy rod blank; the number of fires of forging or extrusion is independently not less than 1 fire. In the present invention, the room temperature tensile strength of the titanium alloy constituting the titanium alloy ingot is not less than 700MPa, preferably 700 to 1050MPa, more preferably 800 to 1000MPa. In the invention, the material of the titanium alloy cast ingot is preferably near alpha or alpha+beta titanium alloy, and the material of the titanium alloy cast ingot preferably comprises TA15, TA17, TA18CF, TA23, TA24, TC3, TC4ELI, ti32 or TC16, wherein TA18CF and Ti32 are products commonly developed by northwest nonferrous metal research institute and western metal materials, inc., and the composition of TA18CF is as follows: ti-3Al-2V-1Cr-0.8Fe, the Ti32 comprises the following components: ti-3.5Al-2.5Mo-1.5Cr-1.7Fe. In an embodiment of the present invention, the material of the titanium alloy ingot is preferably TA15, T18CF, ti32, TC4, TA24 or TC16. In the invention, the near alpha or alpha+beta titanium alloy has higher tensile strength and proper processability, and is beneficial to preparing the high-strength titanium alloy cold-rolled tube.
In the invention, the heating temperature of the titanium alloy cast ingot in the beta phase region is preferably 1170 ℃ to (T) β +30) DEG C, the number of fires of the forging or extrusion is preferably not less than 1 fire independently, more preferably 2 to 4 times, still more preferably 2 to 3 times. When the number of fires for forging or extrusion is greater than 1, the heating temperature of the titanium alloy ingot at the 1 st time in the beta phase region is preferably 1100 to 1170 ℃, the heating temperature at the 2 nd time is preferably 1050 to 1100 ℃, and the heating temperature at the 3 rd time or after the 3 rd time is preferably (T) β +30) DEG C-1100 ℃ and the heating temperature at or after the 3 rd time is not more than the heating temperature at the 2 nd time, in the present invention, the heating temperature of the titanium alloy ingot in the beta phase region is more preferably decreased with the number of fires of forging or extrusion. In a specific embodiment of the present invention, when the number of fires for forging or extrusion is 2, the temperature at which the titanium alloy ingot is heated in the β -phase region is preferably 1150 ℃ and 1070 ℃, or 1170 ℃ and 1100 ℃, and when the number of fires for forging or extrusion is 3, the temperature at which the titanium alloy ingot is heated in the β -phase region is preferably 1170 ℃, 1100 ℃ and 1050 ℃. According to the invention, the beta phase region of the titanium alloy ingot is heated and forged or extruded, so that a high-strength titanium alloy rod blank with uniform and fine beta grains is obtained, when the forging or extrusion times are more than 1 time, a heating mode with temperature decreasing is adopted during forging or extrusion, heating and forging are firstly carried out in the beta phase region, an original cast structure with coarse crystalline state is crushed, then cooling is carried out, heating and forging are carried out in the two phase region, and alpha sheets are crushed, so that more uniform and finer beta grains are obtained, the required structure and performance are achieved, and meanwhile, energy sources can be saved.
After the titanium alloy rod blank is obtained, the titanium alloy rod blank is heated in a beta phase region, and then the cross rolling perforation, water cooling, first heat treatment and straightening are sequentially carried out to obtain a titanium alloy tube blank 1. In the invention, before the titanium alloy rod blank is heated in the beta phase region, the titanium alloy rod blank is preferably peeled and the surface of the titanium alloy rod blank is coated with a lubricant, and in the invention, the lubricant can play a role in lubrication when the titanium alloy rod blank is subjected to oblique rolling perforation, so that the defects such as pits and the like on the surface of the obtained tube blank are prevented from being adhered between the rod blank and a die. In the present invention, the lubricant is preferably a glass frit lubricant or a graphite-based lubricant, and more preferably a glass frit lubricant. The glass powder lubricant is more favorable for reducing the preparation cost and is more environment-friendly. In the present invention, the temperature at which the titanium alloy rod blank is heated in the beta phase region is preferably (T) β +30) DEG C to 1050 ℃, more preferably (T) β +50)℃～1050℃。T β Is the beta transus temperature of the titanium alloy. The heating temperature is preferably kept to be not lower than the phase change point of the material in the processing process, so that the rheological stress of the material is not reduced, the processing resistance of the material is increased, and the heating at the temperature is also favorable for obtaining more uniform and finer beta grains. The heat preservation time of the titanium alloy rod blank heated in the beta phase region preferably meets the following relationship: t is t 1 ＝0.8D 1 min～(0.8D 1 +120) min, where t 1 The heat preservation time D of heating the titanium alloy rod blank in the beta phase region 1 Is the diameter of the rod blank, and is expressed in mm. In the present invention, the deformation amount of the titanium alloy rod blank after the piercing by skew rolling is preferably 15 to 55%, more preferably 20 to 55%, further preferably 25 to 50%, and most preferably 30 to 50%. In the invention, the water cooling can obtain finer lamellar tissues, and the plasticity and toughness of the tube blank are improved. In the present invention, the first heat treatment is preferably performed in a resistance furnace, and the temperature of the first heat treatment is preferably 750 ℃ to 900 ℃, more preferably 800 ℃ to 900 ℃. The present invention has no special requirements for said straightening, in a manner known to the person skilled in the art. The invention has the advantages thatThe strong texture formed in the axial direction of the titanium alloy tube blank 1 can be eliminated by selecting the titanium alloy tube blank 1 prepared under the conditions, so that the tube blank is easier to cold-roll.
After the titanium alloy tube blank 1 is obtained, the titanium alloy tube blank 1 is heated in a two-phase region, extruded or hot rolled, and subjected to second heat treatment and straightening to obtain a titanium alloy tube blank 2. Before the titanium alloy tube blank 1 is heated in the two-phase region, the inner and outer surfaces of the titanium alloy tube blank 1 are preferably coated with a lubricant, preferably a glass powder lubricant or a graphite lubricant, and more preferably a glass powder lubricant. In the present invention, the temperature at which the titanium alloy tube blank 1 is heated in the two-phase region is preferably (T) β -50)℃～(T β -30) DEG C, more preferably (T) β -40)℃～(T β -30)℃，T β For the titanium alloy beta transformation temperature, in the present invention, when the titanium alloy tube blank 1 is heated to the temperature in a two-phase region, it is preferable to keep the temperature for 60 to 180 minutes and then to extrude or hot-roll the titanium alloy tube blank. The invention preferably heats the titanium alloy tube blank 1 in the two phase regions in the temperature range, and can prevent the temperature rise generated in the processing process from rising the temperature of the central part of the titanium alloy tube blank 1 to be above the phase transition point. In addition, heating in this range is advantageous in preventing the deformation resistance of the titanium alloy tube blank 1 from being increased due to the excessively low temperature in the extrusion process, and thus preventing the occurrence of such phenomena as extrusion immobility and cracking. In the present invention, the deformation amount of the titanium alloy tube blank 1 after the two-phase zone heating to the extrusion is preferably 65 to 86%, more preferably 65 to 80%, and the deformation amount of the hot rolling is preferably 70 to 85%, more preferably 70 to 80%. The deformation is preferably controlled in the range, so that on one hand, the tube blank can be effectively deformed in the preparation process, the surface cracking condition is reduced, and the surface quality is improved; on the other hand, a suitable amount of deformation can bring the internal structure and properties of the final product to the desired requirements. In the present invention, the second heat treatment is preferably performed in a resistance furnace, and the temperature of the second heat treatment is preferably 700 to 800 ℃, more preferably 750 to 800 ℃. The present invention has no special requirements for said straightening, in a manner known to the person skilled in the art.
After the titanium alloy tube blank 2 is obtained, the invention carries out inner and outer surface treatment on the titanium alloy tube blank 2 to obtain a titanium alloy tube blank 3. In the present invention, the inner surface treatment is preferably an inner bore and the outer surface treatment is preferably an outer skin. In the present invention, the means for treating the inner and outer surfaces are well known to those skilled in the art.
After the titanium alloy tube blank 3 is obtained, the invention carries out cold rolling for more than or equal to 1 pass on the titanium alloy tube blank 3, and carries out post treatment after each cold rolling to obtain the high-strength titanium alloy cold-rolled tube. According to the invention, the titanium alloy tube blank 3 is subjected to more than or equal to 1 cold rolling, preferably 2-4 cold rolling, and more preferably 2-3 cold rolling. In the present invention, the single pass rolling deformation amount of the cold rolling is preferably 30 to 46%, more preferably 30 to 40%. The cold rolling mode is not particularly limited in the present invention, and is a mode well known to those skilled in the art. In the present invention, the post-treatment includes degreasing, pickling, a third heat treatment, and straightening. The present invention is not particularly limited to the described means of degreasing, pickling, third heat treatment and straightening, and is well known to the person skilled in the art.
In the present invention, the holding time for heating the tube blank 1 in the two-phase zone, the holding time for the first heat treatment, the second heat treatment and the third heat treatment are independently 60 to 180 minutes, more preferably 80 to 140 minutes, still more preferably 100 to 120 minutes.
In the invention, the wall thickness of the high-strength titanium alloy cold-rolled pipe is preferably not more than 6mm, more preferably not more than 5mm, and further preferably 2 to 5mm. The method provided by the invention can be used for preparing the high-strength titanium alloy cold-rolled thin-wall pipe with the wall thickness less than or equal to 6mm, and can effectively solve the defect of preparing the high-strength titanium alloy cold-rolled thin-wall pipe by hot continuous rolling.
Fig. 1 is a process flow chart of the invention for preparing a high-strength titanium alloy pipe, wherein an ingot is subjected to precision forging or extrusion in a beta phase region to obtain a bar blank, then the bar blank is subjected to oblique rolling perforation in the beta phase region and is subjected to online water cooling to obtain a pipe blank 1, then the pipe blank 1 is subjected to extrusion or hot rolling in a two phase region to obtain a pipe blank 2, and the pipe blank 2 is subjected to cold rolling, surface treatment and heat treatment to obtain the high-strength titanium alloy pipe.
The technical solutions of the present invention will be clearly and completely described in the following in connection with the embodiments of the present invention.
Example 1:
preparation of TA15 titanium alloy tubing (specification: Φ60.3 (outer diameter). Times.6 mm (wall thickness)):
TA15 (T) β Titanium alloy ingot casting was heated in the beta phase region and forged 3 times on a free forging machine at 1170 ℃, 1100 ℃ and 1050 ℃ each time to obtain Φ170mm rod billet. Peeling a titanium alloy rod blank to obtain a titanium alloy optical rod with the diameter of 160mm, coating a glass powder lubricant on the surface of the titanium alloy optical rod, heating at 1050 ℃, maintaining the temperature for 130-250 min, performing oblique rolling perforation to the diameter of 180 multiplied by 18mm, performing online water cooling, and performing first heat treatment on the water-cooled pipe blank, namely: heating to 900 ℃ in an atmospheric environment in a resistance furnace, preserving heat for 120min, cooling in air after the heat preservation is finished, and straightening to obtain the titanium alloy tube blank 1. And then, coating glass powder lubricant on the inner and outer surfaces of the titanium alloy tube blank 1, heating the titanium alloy tube blank to 965 ℃ in an atmospheric environment, preserving heat for 60-180 min, discharging, and hot-rolling to obtain the TA15 titanium alloy tube blank with phi 84 multiplied by 12mm. And carrying out second heat treatment on the TA15 titanium alloy tube blank obtained after hot rolling, namely: heating to 800 ℃ in an atmospheric environment in a resistance furnace, preserving heat for 120min, and straightening to obtain a tube blank 2. And (3) carrying out internal boring and external skinning on the tube blank 2 to obtain a tube blank 3 with phi 82 multiplied by 10 mm. And (3) carrying out 2-pass cold rolling on the machined tube blank 3, wherein phi is 82 multiplied by 10mm, phi is 70 multiplied by 8mm, phi is 60.3 multiplied by 6mm, and sequentially carrying out oil removal, acid washing, vacuum heat treatment at 800 ℃ for 180min and straightening on the tube blank after each-pass cold rolling, so as to finally obtain the TA15 titanium alloy tube with the diameter of phi of 60.3 multiplied by 6mm.
The dimensional accuracy of the TA15 titanium alloy pipe is as follows: the outer diameter is 60.30-60.34 mm, and the wall thickness is 5.94-6.07 mm.
The TA15 titanium alloy pipe has the following room temperature mechanical properties: tensile strength R m :1080MPa, yield strength Rp 0.2 :940MPa, elongation A:11%.
Example 2
Preparation of TA18CF titanium alloy tubing (specification: Φ73 (outer diameter). Times.6 mm (wall thickness)):
TA18CF (T) β Titanium alloy ingot was heated in the β phase region at temperatures of 1150 ℃ and 1070 ℃ each time to obtain Φ210mm bar, and forged 2 times on a free forging machine. Peeling a titanium alloy rod blank to obtain a titanium alloy optical rod with the diameter of 200mm, coating a glass powder lubricant on the surface of the titanium alloy optical rod, heating at 920 ℃, maintaining the temperature for 160-280 min, performing oblique rolling perforation to the diameter of 200X 40mm, performing online water cooling, and performing first heat treatment on the water-cooled pipe blank, namely: heating to 750 ℃ in an atmospheric environment in a resistance furnace, preserving heat for 120min, performing air cooling after heat preservation is finished, and straightening to obtain the titanium alloy tube blank 1. And then, coating glass powder lubricant on the inner and outer surfaces of the titanium alloy tube blank 1, heating the titanium alloy tube blank to 840 ℃ in a resistance furnace under the atmospheric environment, preserving heat for 60-180 min, discharging, and carrying out hot rolling to obtain the TA18CF titanium alloy tube blank with the diameter of phi 110 multiplied by 16 mm. And carrying out second heat treatment on the TA18CF titanium alloy tube blank obtained after hot rolling, namely: heating to 700 ℃ in an atmospheric environment in a resistance furnace, preserving heat for 120min, cooling in air after the heat preservation is finished, and straightening to obtain a tube blank 2. And (3) carrying out internal boring and external skinning on the tube blank 2 to obtain a tube blank 3 with phi 108 multiplied by 14mm. And (3) performing 2-pass cold rolling on the machined tube blank 3, wherein phi 108 multiplied by 14mm, phi 89 multiplied by 9mm and phi 73 multiplied by 6mm, sequentially removing oil and acid from the tube blank after each pass of cold rolling, performing vacuum heat treatment at 700 ℃ for 180min, and straightening to finally obtain the TA18CF titanium alloy tube with the diameter phi 73 multiplied by 6mm.
The dimensional accuracy of the TA18CF titanium alloy pipe is as follows: the outer diameter is 73.02-73.05 mm, and the wall thickness is 5.95-6.14 mm.
The mechanical properties of the TA18CF titanium alloy pipe at room temperature are as follows: tensile strength R m :760MPa, yield strength Rp 0.2 :650MPa, elongation A:15%.
The internal structures of the TA18CF titanium alloy tube blank 1 and the finished tube prepared in example 2 are characterized by adopting an optical microscope, and the obtained results are shown in figures 2-3. Fig. 2 is an internal structure diagram of the TA18CF titanium alloy tube blank 1, and fig. 2 is a left diagram of a structure of a transverse section and fig. 2 is a right diagram of a structure of a longitudinal section. As can be seen from fig. 2, the fine-layered weissels in the tube blank 1 are sufficiently crushed and spheroidized. Fig. 3 is an internal structure diagram of the TA18CF titanium alloy finished tube, the left diagram of fig. 3 is a structure of a transverse section, and the right diagram is a structure of a longitudinal section. As can be seen from fig. 3, the interior of the finished tube is an equiaxed structure with fine and uniform grains.
Example 3
Preparation of Ti32 titanium alloy tubing (specification: Φ70 (outer diameter). Times.3 mm (wall thickness)):
ti32 (T) β Titanium alloy ingot was heated in the β phase region at temperatures of 1150 ℃ and 1070 ℃ each time to obtain Φ210mm bar, and forged 2 times on a free forging machine. Peeling a titanium alloy rod blank to obtain a titanium alloy optical rod with the diameter of 200mm, coating a glass powder lubricant on the surface of the titanium alloy optical rod, heating at 940 ℃, maintaining the temperature for 160-280 min, performing oblique rolling perforation to the diameter of 200 multiplied by 50mm, performing online water cooling, and performing first heat treatment on the water-cooled pipe blank, namely: heating to 850 ℃ in an atmospheric environment in a resistance furnace, preserving heat for 120min, performing air cooling after heat preservation is finished, and straightening to obtain the titanium alloy tube blank 1. And then, coating glass powder lubricant on the inner and outer surfaces of the titanium alloy tube blank 1, heating the glass powder lubricant to 850 ℃ in a resistance furnace under the atmospheric environment, preserving heat for 60-180 min, discharging the glass powder lubricant, and extruding the glass powder lubricant to obtain the Ti32 titanium alloy tube blank with phi 110 multiplied by 11mm. And carrying out second heat treatment on the Ti32 titanium alloy tube blank obtained after extrusion, namely: heating to 800 ℃ in an atmospheric environment in a resistance furnace, preserving heat for 120min, cooling in air after the heat preservation is finished, and straightening to obtain a tube blank 2. And (3) carrying out internal boring and external skinning on the tube blank 2 to obtain a tube blank 3 with phi 108 multiplied by 9 mm. And (3) carrying out 2-pass cold rolling on the machined tube blank 3, wherein phi 108 multiplied by 9mm, phi 89 multiplied by 6mm, phi 73 multiplied by 4.2mm and phi 70 multiplied by 3mm, sequentially carrying out oil removal, acid washing, vacuum heat treatment at 750 ℃ for 120min and straightening on the tube blank after each-pass cold rolling, and finally obtaining the Ti32 titanium alloy tube with the diameter phi 70 multiplied by 3mm.
The dimensional accuracy of the Ti32 titanium alloy pipe is as follows: the outer diameter is 70.0-70.02 mm, and the wall thickness is 2.97-3.11 mm.
The room temperature mechanical properties of the Ti32 titanium alloy pipe are as follows: tensile strength R m :970MPa, yield strength Rp 0.2 :825MPa, elongation A:16%。
The internal structures of the Ti32 titanium alloy tube blank 1 and the finished tube prepared in example 3 were characterized by an optical microscope, and the obtained results are shown in FIGS. 4 to 5. Fig. 4 is an internal structure diagram of the Ti32 titanium alloy tube blank 1, and fig. 4 is a left diagram showing a structure of a transverse section and fig. 4 is a right diagram showing a structure of a longitudinal section. As can be seen from fig. 4, the fine-layered weissels in the tube blank 1 are sufficiently crushed and spheroidized. Fig. 5 is an internal structure diagram of the Ti32 titanium alloy finished tube, wherein the left diagram of fig. 5 is a structure of a transverse section, and the right diagram is a structure of a longitudinal section. As can be seen from fig. 5, the interior of the finished tubing is a fine and uniform grain equiaxed structure.
Example 4
Preparation of TC4 titanium alloy tubing (specification: Φ114.3 (outer diameter). Times.6 mm (wall thickness)):
TC4 (T) β Titanium alloy ingot casting was heated in the beta phase region and forged 2 times on a free forging machine at 1170 ℃ and 1100 ℃ each time to obtain Φ180mm bar billet. Peeling a titanium alloy rod blank to obtain a titanium alloy optical rod with the diameter of phi 170mm, coating a glass powder lubricant on the surface of the titanium alloy optical rod, heating at 1050 ℃, maintaining the temperature for 140-260 min, performing oblique rolling perforation until the diameter of the titanium alloy optical rod blank is phi 180 multiplied by 45mm, performing online water cooling, and performing first heat treatment on the water-cooled pipe blank, namely: heating to 850 ℃ in an atmospheric environment in a resistance furnace, preserving heat for 120min, performing air cooling after heat preservation is finished, and straightening to obtain the titanium alloy tube blank 1. And then, coating glass powder lubricant on the inner and outer surfaces of the titanium alloy tube blank 1, heating the glass powder lubricant to 945 ℃ in a resistance furnace under the atmospheric environment, preserving heat for 60-180 min, discharging the titanium alloy tube blank, and extruding to obtain the TC4 titanium alloy tube blank with the diameter of 134 multiplied by 14mm. And carrying out second heat treatment on the TC4 titanium alloy tube blank obtained after extrusion, namely: heating to 750 ℃ in an atmospheric environment in a resistance furnace, preserving heat for 120min, cooling in air after the heat preservation is finished, and straightening to obtain a tube blank 2. The tube blank 2 is internally bored and externally peeled to obtain a tube blank 3 with phi 132 multiplied by 12mm. 2-pass cold rolling is carried out on the machined tube blank 3, phi 132 multiplied by 12mm, phi 120 multiplied by 9mm, phi 114.3 multiplied by 6mm, oil removal and acid washing are sequentially carried out on the tube blank after each-pass cold rolling is finished, and vacuum heat treatment is carried out on the tube blank at 750 ℃ for 120mAnd (5) in and straightening to finally obtain the TC4 titanium alloy pipe with the diameter of phi 114.3 multiplied by 6mm.
The dimensional accuracy of the TC4 titanium alloy pipe is as follows: the outer diameter is 114.32-114.35 mm, and the wall thickness is 5.97-6.12 mm.
The room temperature mechanical properties of the TC4 titanium alloy pipe are as follows: tensile strength R m :960MPa, yield strength Rp 0.2 :870MPa, elongation A:13%.
The internal structures of the TC4 titanium alloy pipe blank 1 and the finished pipe prepared in example 4 were characterized by using an optical microscope, and the obtained results are shown in FIGS. 6 to 7. Fig. 6 is an internal structure diagram of the TC4 titanium alloy tube blank 1, and fig. 6 is a left diagram of a structure of a transverse section and fig. 6 is a right diagram of a structure of a longitudinal section. As can be seen from fig. 6, the fine-layered weissels in the tube blank 1 are sufficiently crushed and spheroidized. Fig. 7 is an internal structure diagram of the TC4 titanium alloy finished tube, wherein the left diagram of fig. 7 is a structure of a transverse section, and the right diagram of fig. 7 is a structure of a longitudinal section. As can be seen from fig. 7, the interior of the finished tubing is a fine and uniform grain equiaxed structure.
Example 5
Preparation of TA24 titanium alloy tubing (specification: Φ89 (outer diameter). Times.5 mm (wall thickness)):
TA24 (T) β Titanium alloy ingot casting was heated in the beta phase region and forged 3 times on a free forging machine at 1170 ℃, 1100 ℃ and 1050 ℃ each time to obtain Φ240mm rod billet. Peeling a titanium alloy rod blank to obtain a titanium alloy optical rod with the diameter of 230mm, coating a glass powder lubricant on the surface of the titanium alloy optical rod, heating the titanium alloy optical rod at 1030 ℃ for 180-300 min, performing oblique rolling perforation until the diameter of the titanium alloy optical rod is 240X 45mm, performing online water cooling, and performing first heat treatment on the water-cooled pipe blank, namely: heating to 850 ℃ in an atmospheric environment in a resistance furnace, preserving heat for 120min, performing air cooling after heat preservation is finished, and straightening to obtain the titanium alloy tube blank 1. And then, coating glass powder lubricant on the inner and outer surfaces of the titanium alloy tube blank 1, heating the glass powder lubricant to 880 ℃ in a resistance furnace in the atmospheric environment, preserving heat for 120min, discharging the titanium alloy tube blank, and extruding to obtain the TA24 titanium alloy tube blank with the diameter of phi 116 multiplied by 12.5 mm. And carrying out second heat treatment on the TA24 titanium alloy tube blank obtained after extrusion, namely: in a resistance furnaceHeating to 800 ℃ in the middle atmosphere environment, preserving heat for 120min, cooling in air after heat preservation is finished, and straightening to obtain a tube blank 2. And (3) carrying out internal boring and external skinning on the tube blank 2 to obtain a tube blank 3 with phi 114 multiplied by 10 mm. And (3) performing 2-pass cold rolling on the machined tube blank 3, wherein phi 114×10mm, phi 100×7mm and phi 89×5mm, sequentially removing oil and acid from the tube blank after each pass of cold rolling, performing vacuum heat treatment at 800 ℃ for 180min, and straightening to finally obtain the TA24 titanium alloy tube with the diameter phi 89×5mm.
The dimensional accuracy of the TA24 titanium alloy pipe is as follows: the outer diameter is 89.98-90.01 mm, and the wall thickness is 5.20-4.93 mm.
The mechanical properties of the TA24 titanium alloy pipe at room temperature are as follows: tensile strength R m :780MPa, yield strength Rp 0.2 :710MPa, elongation A:15%.
Example 6
Preparation of TC16 titanium alloy tubing (specification: Φ89 (outer diameter). Times.6 mm (wall thickness)):
TC16 (T) β Titanium alloy ingot casting was heated in the β phase region and forged 2 times on a free forging machine at 1170 ℃ and 1050 ℃ each time to obtain Φ210mm rod billet. Peeling a titanium alloy rod blank to obtain a titanium alloy optical rod with the diameter of 200mm, coating a glass powder lubricant on the surface of the titanium alloy optical rod, heating at 930 ℃ for 160-280 min, performing oblique rolling perforation until the diameter of 200mm is 40mm, performing online water cooling, and performing first heat treatment on the water-cooled pipe blank, namely: heating to 800 ℃ in an atmospheric environment in a resistance furnace, preserving heat for 120min, cooling to 500 ℃ after the heat preservation is finished, discharging, cooling by air, and straightening to obtain the titanium alloy tube blank 1. And then, coating glass powder lubricant on the inner and outer surfaces of the titanium alloy tube blank 1, heating the glass powder lubricant to 800 ℃ in a resistance furnace under the atmospheric environment, preserving heat for 120min, discharging, and carrying out hot rolling to obtain the TC16 titanium alloy tube blank with the diameter of phi 100 multiplied by 11mm. Performing second heat treatment on the TC16 titanium alloy tube blank obtained after hot rolling, namely: heating to 800 ℃ in an atmospheric environment in a resistance furnace, preserving heat for 120min, cooling to 500 ℃ after the heat preservation is finished, discharging, air cooling, and straightening to obtain a tube blank 2. And (3) carrying out internal boring and external skinning on the tube blank 2 to obtain a tube blank 3 with phi 98 multiplied by 9 mm. Feeding the machined tube blank 3And (3) carrying out 1-pass cold rolling, wherein phi is 98 multiplied by 9mm and phi is 89 multiplied by 6mm, sequentially carrying out oil removal, acid washing and vacuum heat treatment at 800 ℃ on the pipe after the cold rolling is finished for 120min, carrying out air cooling and straightening, and finally obtaining the TC16 titanium alloy pipe with the diameter phi of 89 multiplied by 6mm.
The dimensional accuracy of the TC16 titanium alloy pipe is as follows: the outer diameter is 89.02-89.05 mm, and the wall thickness is 5.95-6.14 mm.
The room temperature mechanical properties of the TC16 titanium alloy pipe are as follows: tensile strength R m :1030MPa, yield strength Rp 0.2 :860MPa, elongation a:14.5%.
The internal structures of the TC16 titanium alloy pipe blank 1 and the finished pipe prepared in example 6 were characterized by using an optical microscope, and the obtained results are shown in FIGS. 8 to 9. Fig. 8 is an internal structure diagram of the TC16 titanium alloy tube blank 1, and fig. 8 is a left diagram of a structure of a transverse section and fig. 8 is a right diagram of a structure of a longitudinal section. As can be seen from fig. 8, the fine-layered weissels in the tube blank 1 are sufficiently crushed and spheroidized. Fig. 9 is an internal structure diagram of the TC16 titanium alloy finished tube, wherein the left diagram of fig. 9 is a structure of a transverse section, and the right diagram of fig. 9 is a structure of a longitudinal section. As can be seen from fig. 9, the interior of the finished tubing is a fine and uniform grain equiaxed structure.
The foregoing is merely a preferred embodiment of the present invention and it should be noted that modifications and adaptations to those skilled in the art may be made without departing from the principles of the present invention, which are intended to be comprehended within the scope of the present invention.
Claims (7)
1. The preparation method of the high-strength titanium alloy cold-rolled pipe is characterized by comprising the following steps of:
heating a titanium alloy ingot in a beta phase region, and forging or extruding to obtain a titanium alloy rod blank; the firing number of the forging or extrusion is independently 2-3 firing numbers;
heating the titanium alloy rod blank in a beta phase region, and then sequentially performing oblique rolling perforation, water cooling, first heat treatment and straightening to obtain a titanium alloy tube blank 1;
heating the titanium alloy tube blank 1 in a two-phase region, extruding or hot rolling, and performing second heat treatment and straightening to obtain a titanium alloy tube blank 2;
performing inner and outer surface treatment on the titanium alloy tube blank 2 to obtain a titanium alloy tube blank 3;
performing cold rolling for more than or equal to 1 pass on the titanium alloy tube blank 3, and performing aftertreatment after each cold rolling to obtain a high-strength titanium alloy cold-rolled tube;
the post-treatment comprises degreasing, acid washing, third heat treatment and straightening;
the heating temperature of the titanium alloy cast ingot in a beta phase region is 1170 ℃ to (T) β +30) DEG C, the heating temperature of the titanium alloy ingot in the beta phase zone decreases with the number of fires of forging or extrusion;
the temperature at which the titanium alloy rod blank is heated in the beta phase region is (T) β +30)℃～1050℃；
The T is β Is the beta transus temperature of the titanium alloy;
the deformation of the hot rolling is 80-85%;
the room temperature tensile strength of the titanium alloy forming the titanium alloy cast ingot is more than or equal to 700MPa;
the wall thickness of the high-strength titanium alloy cold-rolled pipe is less than or equal to 5mm.
2. The method of claim 1, wherein the heat retention time of the titanium alloy rod blank in the beta phase region satisfies the following relationship: t is t 1 ＝0.8D 1 min～(0.8D 1 +120) min, where t 1 The heat preservation time D of heating the titanium alloy rod blank in the beta phase region 1 The diameter of the titanium alloy rod blank is in mm, and the deformation of the titanium alloy rod blank after the oblique rolling perforation is 15-55%.
3. The method according to claim 1, wherein the tube blank 1 is heated in the two-phase zone at a temperature (T β -50)℃～(T β -30)℃，T β For the titanium alloy beta transformation temperature, the deformation amount of the titanium alloy tube blank 1 after heating in a two-phase region and performing extrusion is 65-86%.
4. The method according to claim 1, wherein the temperature of the first heat treatment is 750 ℃ to 900 ℃ and the temperature of the second heat treatment is 700 ℃ to 800 ℃.
5. The production method according to claim 3 or 4, wherein the holding time of the heating of the tube blank 1 in the two-phase region, the holding time of the first heat treatment, the second heat treatment and the third heat treatment are independently 60 to 180 minutes.
6. The method according to claim 1, wherein the single pass rolling deformation of the cold rolling is 30 to 46%.
7. The method of claim 1, wherein the titanium alloy ingot comprises TA15, TA17, TA18CF, TA23, TA24, TC3, TC4ELI, ti32, or TC16.
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| 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 |
| CN109280787A (en) * | 2018-11-30 | 2019-01-29 | 西北有色金属研究院 | A kind of preparation method of petroleum gas industrial titanium alloy seamless tubular goods |
| WO2019144584A1 (en) * | 2018-01-23 | 2019-08-01 | 苏州钢特威钢管有限公司 | Method for preparing 1cr25ti high-chromium ferrite stainless steel seamless tube |
| CN112453104A (en) * | 2021-02-03 | 2021-03-09 | 西安稀有金属材料研究院有限公司 | Large-caliber thin-wall Ti35 titanium alloy seamless pipe 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 |
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| 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 |
| WO2019144584A1 (en) * | 2018-01-23 | 2019-08-01 | 苏州钢特威钢管有限公司 | Method for preparing 1cr25ti high-chromium ferrite stainless steel seamless tube |
| CN109280787A (en) * | 2018-11-30 | 2019-01-29 | 西北有色金属研究院 | A kind of preparation method of petroleum gas industrial titanium alloy seamless tubular goods |
| 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 |
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