CN117102273A - Titanium alloy seamless pipe and method for improving rotation bending fatigue performance thereof - Google Patents
Titanium alloy seamless pipe and method for improving rotation bending fatigue performance thereof Download PDFInfo
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- CN117102273A CN117102273A CN202311379314.2A CN202311379314A CN117102273A CN 117102273 A CN117102273 A CN 117102273A CN 202311379314 A CN202311379314 A CN 202311379314A CN 117102273 A CN117102273 A CN 117102273A
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- 229910001069 Ti alloy Inorganic materials 0.000 title claims abstract description 250
- 238000000034 method Methods 0.000 title claims abstract description 47
- 238000005452 bending Methods 0.000 title claims abstract description 41
- 238000005097 cold rolling Methods 0.000 claims abstract description 97
- 238000005498 polishing Methods 0.000 claims abstract description 36
- 238000000137 annealing Methods 0.000 claims abstract description 30
- 238000005242 forging Methods 0.000 claims abstract description 20
- 238000005098 hot rolling Methods 0.000 claims abstract description 11
- 238000003723 Smelting Methods 0.000 claims abstract description 9
- 238000005554 pickling Methods 0.000 claims abstract description 7
- 238000004519 manufacturing process Methods 0.000 claims abstract description 4
- 238000001514 detection method Methods 0.000 claims description 23
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 22
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 11
- 229910052742 iron Inorganic materials 0.000 claims description 11
- 229910052760 oxygen Inorganic materials 0.000 claims description 11
- 239000001301 oxygen Substances 0.000 claims description 11
- 238000005096 rolling process Methods 0.000 claims description 10
- 238000009661 fatigue test Methods 0.000 claims description 7
- 229910000831 Steel Inorganic materials 0.000 claims description 5
- 238000002441 X-ray diffraction Methods 0.000 claims description 5
- 238000005553 drilling Methods 0.000 claims description 5
- 238000000227 grinding Methods 0.000 claims description 5
- 239000002245 particle Substances 0.000 claims description 5
- 238000004321 preservation Methods 0.000 claims description 5
- 230000001105 regulatory effect Effects 0.000 claims description 5
- HBMJWWWQQXIZIP-UHFFFAOYSA-N silicon carbide Chemical compound [Si+]#[C-] HBMJWWWQQXIZIP-UHFFFAOYSA-N 0.000 claims description 5
- 229910010271 silicon carbide Inorganic materials 0.000 claims description 5
- 239000010935 stainless steel Substances 0.000 claims description 5
- 229910001220 stainless steel Inorganic materials 0.000 claims description 5
- 239000010959 steel Substances 0.000 claims description 5
- 230000009466 transformation Effects 0.000 claims description 5
- 239000000463 material Substances 0.000 claims description 3
- 229910052751 metal Inorganic materials 0.000 abstract description 3
- 239000002184 metal Substances 0.000 abstract description 3
- 230000008569 process Effects 0.000 description 20
- 230000007547 defect Effects 0.000 description 11
- 238000010304 firing Methods 0.000 description 5
- 239000002253 acid Substances 0.000 description 4
- 230000001276 controlling effect Effects 0.000 description 4
- 238000005336 cracking Methods 0.000 description 4
- 238000005070 sampling Methods 0.000 description 4
- 238000005406 washing Methods 0.000 description 4
- 230000009471 action Effects 0.000 description 3
- 238000009826 distribution Methods 0.000 description 2
- 230000014509 gene expression Effects 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000003754 machining Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 238000002360 preparation method Methods 0.000 description 2
- 239000004576 sand Substances 0.000 description 2
- 230000007704 transition Effects 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000000265 homogenisation Methods 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 230000003746 surface roughness Effects 0.000 description 1
- 238000004381 surface treatment Methods 0.000 description 1
- 238000000844 transformation Methods 0.000 description 1
Classifications
-
- 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
-
- 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
- B21B19/06—Rolling hollow basic material, e.g. Assel mills
-
- 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
- B21C37/30—Finishing tubes, e.g. sizing, burnishing
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
-
- C—CHEMISTRY; METALLURGY
- 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
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
- C23G3/00—Apparatus for cleaning or pickling metallic material
- C23G3/04—Apparatus for cleaning or pickling metallic material for cleaning pipes
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16L—PIPES; JOINTS OR FITTINGS FOR PIPES; SUPPORTS FOR PIPES, CABLES OR PROTECTIVE TUBING; MEANS FOR THERMAL INSULATION IN GENERAL
- F16L9/00—Rigid pipes
- F16L9/02—Rigid pipes of metal
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- Engineering & Computer Science (AREA)
- Chemical & Material Sciences (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Organic Chemistry (AREA)
- Metallurgy (AREA)
- Physics & Mathematics (AREA)
- Crystallography & Structural Chemistry (AREA)
- Thermal Sciences (AREA)
- General Engineering & Computer Science (AREA)
- Chemical Kinetics & Catalysis (AREA)
- General Chemical & Material Sciences (AREA)
- Forging (AREA)
Abstract
The invention belongs to the technical field of metal seamless tubes, and particularly relates to a titanium alloy seamless tube and a method for improving the rotating bending fatigue property of the titanium alloy seamless tube. The invention discloses a method for improving the rotation bending fatigue property of a titanium alloy seamless pipe, which comprises the following steps: s1, smelting by adopting a three-time vacuum consumable arc furnace to obtain a titanium alloy cast ingot; s2, performing three-upsetting three-drawing free forging on the titanium alloy cast ingot for 3-5 times to obtain a square billet, and performing hot rolling and radial forging on the square billet to obtain a titanium alloy round bar; s3, manufacturing a titanium alloy round bar into a hollow tube blank; s4, cold rolling the hollow tube blank for 3-4 times to prepare a titanium alloy tube, and carrying out vacuum annealing on the titanium alloy tube subjected to each time of cold rolling; s5, pickling the titanium alloy tube obtained in the step S4, and polishing the inner surface and the outer surface of the pickled titanium alloy tube respectively; and S6, performing magnetic polishing treatment on the titanium alloy tube obtained in the step S5. The method disclosed by the invention greatly improves the rotation bending fatigue performance of the titanium alloy pipe.
Description
Technical Field
The invention belongs to the technical field of metal seamless tubes, and particularly relates to a titanium alloy seamless tube and a method for improving the rotating bending fatigue property of the titanium alloy seamless tube.
Background
The high cycle bending fatigue performance of tens of millions of times is an important index for measuring the performance of titanium alloy pipe products. The existing cold rolling, heat treatment and inner surface treatment processes of the titanium alloy pipe are not optimized for the high-cycle bending fatigue performance, so that the high-cycle bending fatigue performance of the titanium alloy pipe is unqualified.
There are several reasons for the failure of high cycle cornering fatigue performance, for example: firstly, because the grain orientation distribution of the titanium alloy pipe is unreasonable, the evolution process of the grain orientation distribution of the pipe is the whole process from the forging start of the titanium alloy ingot to the hot rolling, the multipass cold rolling and the heat treatment; secondly, the fatigue and the early failure of the high-cycle turning curve are caused by the defects of the inner surface and the outer surface of the titanium alloy tube and the surface roughness; thirdly, the residual tensile stress of the inner surface and the outer surface of the titanium alloy pipe caused by cold rolling deformation reduces the high-cycle bending fatigue performance of the titanium alloy pipe.
Based on this, a method for improving the rotational bending fatigue performance is required.
Disclosure of Invention
In order to solve the technical problems, the invention provides a titanium alloy seamless pipe and a method for improving the rotating bending fatigue performance of the titanium alloy seamless pipe, which can solve the technical problem that the high-cycle rotating bending fatigue performance of the conventional titanium alloy pipe is unqualified.
On one hand, the embodiment of the invention discloses a method for improving the rotation bending fatigue property of a titanium alloy seamless pipe, which comprises the following steps:
s1, smelting by adopting a three-time vacuum consumable arc furnace to obtain a titanium alloy cast ingot, wherein the oxygen content in the titanium alloy cast ingot is controlled to be less than or equal to 0.075% and the iron content is controlled to be less than or equal to 0.12% according to mass percentage;
s2, performing three-drawing free forging on the titanium alloy cast ingot for 3-5 times by three piers to obtain a preset number of square billets with the same volume, and performing hot rolling for 1-2 times and diameter forging for 2-3 times on each square billet to obtain a titanium alloy round bar;
s3, manufacturing the titanium alloy round bar into a hollow tube blank;
s4, cold rolling the hollow tube blank for 3-4 times to obtain a titanium alloy tube, and carrying out vacuum annealing on the titanium alloy tube subjected to each time cold rolling, wherein the feeding amount of each time cold rolling to a rolling mill is determined according to the cold rolling deformation rate epsilon of each time, the vacuum annealing temperature of the titanium alloy tube obtained by each time cold rolling is determined according to the transformation point temperature T of the titanium alloy and the cold rolling deformation rate epsilon of each time, and the annealing heat preservation time is determined according to the wall thickness S of the titanium alloy tube obtained by each time cold rolling;
s5, pickling the titanium alloy tube obtained in the step S4, and polishing the inner surface and the outer surface of the pickled titanium alloy tube respectively until the roughness Ra of the inner surface and the outer surface of the titanium alloy tube is less than or equal to 0.1 micrometer;
and S6, performing magnetic polishing treatment on the titanium alloy tube obtained in the step S5.
According to one embodiment of the present invention, in the step S2, the titanium alloy ingot is freely forged and cut into billets by three drawing at the time of 4 firings, wherein the titanium alloy ingot is freely forged and cut into 2 billets with the same volume by three drawing at the time of 1 st firings, the 2 billets with the same volume are freely forged and cut into 4 billets with the same volume by three drawing at the time of 2 nd firings, the 4 billets with the same volume are freely forged and cut into 8 billets with the same volume by three drawing at the time of 3 rd firings, and the 8 billets with the same volume are freely forged and cut into 16 billets with the same volume by three drawing at the time of 4 th firings.
According to one embodiment of the invention, the flaw detection of the titanium alloy round bar obtained in the step S2 reaches the AA grade of GB/T5193 standard.
According to one embodiment of the invention, the titanium alloy round bar is machined into a hollow tube blank by deep hole drilling, internal boring and external turning, and the grain orientation type of the hollow tube blank is alpha phase <0001>// tube radial direction and <10-10>// tube axial direction.
According to one embodiment of the present invention, in the step S4, the hollow shell is cold rolled into a titanium alloy tube through 3 to 4 passes in a two-roll cold pilger mill, and the deformation rate epsilon is calculated according to the following formula:
ε=｛（D n －S n ）×S n －（D n+1 －S n+1 ）×S n+1 ｝/｛（D n －S n ）×S n ｝
wherein D is n The outer diameter of the hollow tube blank or the titanium alloy tube before each pass of cold rolling is in mm; s is S n The wall thickness of the hollow tube blank or the titanium alloy tube before each pass of cold rolling is measured in mm; d (D) n+1 The unit is mm for the outer diameter of the titanium alloy tube after each pass of cold rolling; s is S n+1 The wall thickness of the titanium alloy tube after each pass of cold rolling is expressed in mm.
According to one embodiment of the present invention, in the step S4, the feeding amount of the cold rolling to the rolling mill is (24×ε) mm, and the outer diameter obtained by cold rolling with a cold rolling deformation rate ε is D n+1 The wall thickness is S n+1 The vacuum annealing temperature of the titanium alloy tube is (T-350 xepsilon) DEG C, and the annealing heat-preserving time is (65 xS) n+1 ) And (3) minutes.
According to one embodiment of the present invention, in the step S5, the outer surface of the pickled titanium alloy tube is polished with a green silicon carbide abrasive belt having a granularity of not less than 1000 mesh, and the inner surface of the pickled titanium alloy tube is polished with a abrasive flow.
According to one embodiment of the invention, in the step S6 of magnetic polishing treatment, a stainless steel round needle with the length of 3mm and the diameter of 0.4mm is adopted as a magnetic polishing grinding steel needle, a pipe section sample of the titanium alloy pipe is taken after the treatment, the residual compressive stress is detected by an X-ray diffraction stress analyzer, and the magnetic polishing treatment is regulated until the residual compressive stress of the inner surface and the outer surface of the titanium alloy pipe is more than or equal to 300MPa.
According to one embodiment of the present invention, further comprising: and (3) performing ultrasonic flaw detection on the titanium alloy tube subjected to the magnetic polishing treatment in the step (S6), and taking the flaw detection sample tube with the carving depth of 0.03mm, the width of 0.10mm and the length of 1.4mm as detection standards, wherein the flaw detection sample tube is a titanium alloy sample tube which has no flaw and has the same material and the same specification as the titanium alloy tube subjected to the magnetic polishing treatment.
On the other hand, the embodiment of the invention also discloses a titanium alloy seamless pipe, the rotating bending fatigue performance of which is improved by adopting the method of any one of the embodiments, wherein the titanium alloy seamless pipe is a TA18 titanium alloy seamless pipe, and the TA18 titanium alloy seamless pipe can pass 1500-1600 ten thousand rotating bending fatigue tests.
By adopting the technical scheme, the invention has at least the following beneficial effects:
according to the method for improving the rotating bending fatigue performance of the titanium alloy seamless pipe, disclosed by the invention, the oxygen and iron content in the titanium alloy components is controlled through three times of vacuum consumable arc furnace smelting, so that the bending fatigue performance of a titanium alloy finished pipe is prevented from being damaged due to overhigh iron and oxygen content; the thermal deformation process combination of hot rolling and radial forging ensures that the structure and the performance of the round titanium alloy rod are uniform, and the grain orientation type of the titanium alloy tube blank is adjusted; the feeding quantity of each pass of cold rolling to the rolling mill is determined according to the cold rolling deformation rate epsilon of each pass, so that cracks on the inner surface and the outer surface of the titanium alloy tube in the cold rolling deformation process are avoided; the titanium alloy tube can be guaranteed to be fully recovered and recrystallized by controlling reasonable annealing process parameters, the plasticity is improved, and the cracking defect of the titanium alloy tube in the subsequent cold rolling deformation process is reduced; the roughness of the inner and outer surfaces of the titanium alloy tube is reduced by polishing the inner and outer surfaces of the titanium alloy tube respectively; the residual compressive stress on the surface of the titanium alloy tube is strengthened by acid washing and then magnetic polishing, so that the acid washing is avoided and the residual compressive stress on the surface of the titanium alloy tube is reduced. Therefore, the method provided by the invention greatly improves the rotating bending fatigue performance of the titanium alloy tube through the combined action of regulating and controlling the grain orientation, eliminating the cold rolling defect of the titanium alloy tube, reducing the roughness of the inner surface and the outer surface of the titanium alloy finished tube and increasing the residual compressive stress of the surface of the titanium alloy finished tube.
Drawings
In order to more clearly illustrate the embodiments of the invention or the technical solutions in the prior art, the drawings that are required in the embodiments or the description of the prior art will be briefly described, it being obvious that the drawings in the following description are only some embodiments of the invention, and that other drawings may be obtained according to these drawings without inventive effort for a person skilled in the art.
FIG. 1 is a flow chart of a method for improving the rotational bending fatigue performance of a titanium alloy seamless tube according to an embodiment of the invention.
Detailed Description
In order to make the objects, technical solutions and advantages of the present invention more apparent, the following embodiments of the present invention will be described in further detail with reference to the accompanying drawings.
It should be noted that, in the embodiments of the present invention, all the expressions "first" and "second" are used to distinguish two entities with the same name but different entities or different parameters, and it is noted that the "first" and "second" are only used for convenience of expression, and should not be construed as limiting the embodiments of the present invention, and the following embodiments are not described one by one.
According to a first aspect of the present invention, as shown in fig. 1, an embodiment of the present invention discloses a method for improving the rotational bending fatigue performance of a titanium alloy seamless pipe, comprising the steps of:
s1, smelting by adopting a three-time vacuum consumable arc furnace to obtain a titanium alloy cast ingot, wherein the oxygen content in the titanium alloy cast ingot is controlled to be less than or equal to 0.075% and the iron content is controlled to be less than or equal to 0.12% in percentage by mass;
s2, performing three-drawing free forging on the titanium alloy cast ingot for 3-5 times, namely three-pier three-drawing free forging to obtain a preset number of square billets with the same volume, and performing hot rolling for 1-2 times and diameter forging for 2-3 times on each square billet to obtain a titanium alloy round bar;
s3, manufacturing a titanium alloy round bar into a hollow tube blank;
s4, cold rolling the hollow tube blank for 3-4 times to obtain a titanium alloy tube, and carrying out vacuum annealing on the titanium alloy tube subjected to each time cold rolling, wherein the feeding quantity of each time cold rolling to a rolling mill is determined according to the deformation rate epsilon of each time cold rolling, the vacuum annealing temperature of the titanium alloy tube obtained by each time cold rolling is determined according to the transformation point temperature T of the titanium alloy and the deformation rate epsilon of each time cold rolling, and the annealing heat preservation time is determined according to the wall thickness S of the titanium alloy tube obtained by each time cold rolling;
s5, pickling the titanium alloy tube obtained in the step S4, and polishing the inner surface and the outer surface of the pickled titanium alloy tube respectively until the roughness Ra of the inner surface and the outer surface of the titanium alloy tube is less than or equal to 0.1 micrometer;
and S6, performing magnetic polishing treatment on the titanium alloy tube obtained in the step S5.
In the embodiment of the invention, the titanium alloy cast ingot is obtained by adopting three times of vacuum consumable arc furnace smelting, so that the uniform components of the titanium alloy are ensured, the oxygen content in the titanium alloy components is controlled to be less than or equal to 0.075 percent, the iron content is controlled to be less than or equal to 0.12 percent, and the bending fatigue performance of a titanium alloy finished product pipe is prevented from being damaged due to overhigh iron and oxygen contents.
In the embodiment of the invention, the thermal deformation process combination of hot rolling and radial forging ensures that the round bar structure and the performance of the titanium alloy are uniform, the grain orientation type of the tube blank is adjusted through hot rolling and radial forging, and the bending fatigue performance of the titanium alloy finished tube is improved through the proper grain orientation type.
In the embodiment of the invention, the optimized combination of the cold rolling deformation rate epsilon and the feeding technological parameters avoids cracks on the inner and outer surfaces of the titanium alloy tube in the two-roller cold rolling deformation technological process.
In the embodiment of the invention, the vacuum annealing temperature is determined according to the transformation point temperature and the cold rolling deformation rate of the titanium alloy, and the annealing heat preservation time is determined according to the wall thickness of the titanium alloy tube, so that reasonable annealing process parameters are obtained, thereby ensuring that the titanium alloy tube is fully recovered and recrystallized, improving the plasticity, reducing the cracking defect of the titanium alloy tube in the subsequent cold rolling deformation process, and preventing the early failure of the titanium alloy finished tube caused by the inner and outer surface cracks in the bending fatigue test.
According to the embodiment of the invention, the inner surface and the outer surface of the titanium alloy pipe are respectively polished, so that the roughness of the inner surface and the outer surface of the titanium alloy pipe is reduced, and the bending fatigue performance of the titanium alloy pipe is improved.
In the embodiment of the invention, the titanium alloy finished tube is firstly pickled, and then the residual compressive stress on the surface is strengthened by adopting magnetic polishing, so that the pickling is avoided, the residual compressive stress on the surface of the titanium alloy tube is reduced, and the rotating bending fatigue performance of the titanium alloy finished tube is improved.
In some embodiments, in step S2, the titanium alloy ingot is free-forged by three-drawing at 4 times, wherein the titanium alloy ingot is free-forged by three-drawing at 1 st time and then cut into 2 billets of the same volume, the 2 billets of the same volume are free-forged by three-drawing at 2 times, the 4 billets of the same volume are free-forged by three-drawing at 3 times and then cut into 8 billets of the same volume, and the 8 billets of the same volume are free-forged by three-drawing at 4 times and then cut into 16 billets of the same volume. In the embodiment, after three-pier three-drawing free forging, one square billet is cut into 2 square billets with the same volume, and the three-pier three-drawing free forging is performed on the square billets with the volume being continuously halved, so that the center structure of the square billet is better forged, and the homogenization of the forged structure is promoted.
In some embodiments, the round bar flaw detection of titanium alloy obtained in step S2 reaches the AA level of GB/T5193 standard. The structure and the uniform performance of the titanium alloy round bar are ensured.
In some embodiments, in step S3, a round bar of titanium alloy is machined by deep hole drilling, internal boring, external turning to produce a hollow shell, the grain orientation type of which is α -phase <0001>// tube radial, <10-10>// tube axial. The proper grain orientation type improves the bending fatigue properties of the finished titanium alloy tube.
In some embodiments, in step S4, the hollow shell is cold rolled in 3 to 4 passes in a two-roll cold pilger mill to form a titanium alloy tube, and the deformation rate epsilon is calculated according to the following formula:
ε=｛（D n －S n ）×S n －（D n+1 －S n+1 ）×S n+1 ｝/｛（D n －S n ）×S n ｝
wherein D is n The outer diameter of the hollow tube blank or the titanium alloy tube before each pass of cold rolling is in mm; s is S n The wall thickness of the hollow tube blank or the titanium alloy tube before each pass of cold rolling is measured in mm; d (D) n+1 The unit is mm for the outer diameter of the titanium alloy tube after each pass of cold rolling; s is S n+1 The wall thickness of the titanium alloy tube after each pass of cold rolling is expressed in mm.
In some embodiments, in step S4, the cold rolling of each pass is performed with a feed rate of (24 ∈) mm to the rolling mill, and the cold rolling with a cold rolling deformation rate of ε gives an outer diameter of D n+1 The wall thickness is S n+1 The vacuum annealing temperature of the titanium alloy tube is (T-350 xepsilon) DEG C, and the annealing heat-preserving time is (65 xS) n+1 ) And (3) minutes. The feeding amount of each cold rolling pass to the rolling mill is (24 xepsilon) mm, so that the larger feeding amount of each cold rolling pass is ensured, the weight of the metal participating in the cold rolling deformation of each pilger is ensured to be large enough, and the optimized combination of the cold rolling deformation rate epsilon and the feeding amount technological parameters avoids cracks on the inner surface and the outer surface of the titanium alloy tube in the two-roller cold rolling deformation technological process. The reasonable annealing temperature and annealing heat preservation time ensure that the titanium alloy tube fully recovers and recrystals, improves plasticity, reduces cracking defects of the titanium alloy tube in the subsequent cold rolling deformation process, and prevents early failure of the titanium alloy finished tube caused by inner and outer surface cracks in bending fatigue test.
In some embodiments, in step S5, the outer surface of the pickled titanium alloy tube is polished with a green silicon carbide abrasive belt having a particle size of at least 1000 mesh, and the inner surface of the pickled titanium alloy tube is polished with a stream of abrasive particles. Greatly reduces the roughness of the inner surface and the outer surface of the titanium alloy tube and greatly improves the bending fatigue property of the titanium alloy tube.
In some embodiments, in the step S6 of magnetic polishing treatment, a stainless steel round needle with the length of 3mm and the diameter of 0.4mm is adopted as the magnetic polishing grinding steel needle, a pipe section sample of the titanium alloy pipe is taken after the treatment, the residual compressive stress is detected by an X-ray diffraction stress analyzer, and the magnetic polishing treatment is regulated until the residual compressive stress of the inner surface and the outer surface of the titanium alloy pipe is more than or equal to 300MPa. Greatly improves the rotation bending fatigue performance of the titanium alloy finished pipe.
In some embodiments, ultrasonic flaw detection is performed on the titanium alloy tube subjected to the magnetic polishing treatment in the step S6, and the flaw detection sample tube is a titanium alloy tube which is free of defects and has the same material and the same specification as the titanium alloy tube subjected to the magnetic polishing treatment, and the flaw detection sample tube has a flaw detection depth of 0.03mm, a width of 0.10mm and a length of 1.4 mm. In this example, the depth of the cut was the shallowest cut that can be cut currently, and the ultrasonic flaw detection was performed on the entire length of each finished tube of titanium alloy to confirm that the inner and outer surfaces of the finished tube of titanium alloy were free of defects. The defect problem of the titanium alloy pipe can be strictly controlled through flaw detection, and the influence of the defect problem of the titanium alloy pipe on the rotation bending fatigue performance of the titanium alloy pipe is prevented.
According to a second aspect of the present invention, there is provided a titanium alloy seamless tube, wherein the titanium alloy seamless tube is a TA18 titanium alloy seamless tube, and the TA18 titanium alloy seamless tube can pass 1500-1600 ten thousand rotational bending fatigue tests by adopting the method as described in any of the above embodiments.
The invention will now be described with reference to specific examples, which are intended to be illustrative only and not limiting in any way.
Example 1
This example produced TA18 titanium alloy seamless tubes of gauge Φ14X0.8 mm (i.e., 14mm outside diameter, 0.8mm wall thickness).
The preparation process adopted in this example is as follows:
1. smelting by adopting a three-time vacuum consumable arc furnace to obtain a round TA18 titanium alloy cast ingot with the diameter of phi 490mm (the diameter of 490 mm), wherein the oxygen content (mass fraction) of the cast ingot is 0.059-0.065%, and the iron content (mass fraction) is 0.11%;
2. freely forging a titanium alloy cast ingot with the diameter of 490mm into a square billet with the length, width and height of 220mm by a hydraulic press with three piers and three drawing steps for 4 times;
3. performing hot rolling on a square billet with 220mm by 1 fire to prepare a black skin round bar with phi of 100mm (the diameter is 100 mm);
4. forging a black skin round bar with the diameter of phi 100mm into a black skin round bar with the diameter of phi 70mm (with the diameter of 70 mm) by 2 fire times, wherein the flaw detection of the obtained black skin round bar reaches the AA level of GB/T5193 standard;
5. machining a black skin round bar with the diameter of 70mm into a hollow tube blank with the diameter of phi 54 multiplied by 5 (the outer diameter is 54mm, the wall thickness is 5 mm) by deep hole drilling, inner boring and outer turning, sampling and measuring the phase transition point temperature T of TA18 titanium alloy to be 926 ℃, and sampling and measuring the grain orientation type of the hollow tube blank to be alpha phase <0001>// radial of the tube and <10-10>// axial of the tube;
6. cold rolling the phi 54 multiplied by 5 hollow tube blank into a phi 33 multiplied by 3 (the outer diameter is 33mm, the wall thickness is 3 mm) titanium alloy tube in a two-roll cold-rolling tube mill, calculating according to a calculation formula (1) to obtain a cold-rolling deformation rate epsilon of 63.3%, feeding the cold-rolling mill with a feeding amount of 15.192mm (the calculation formula is 24 multiplied by 0.633), vacuum annealing the titanium alloy tube obtained by the cold-rolling process at 704 ℃ (the calculation formula is 926-350 multiplied by 0.633), and keeping the temperature for 195 minutes (the calculation formula is 65 multiplied by 3);
ε=｛（D n －S n ）×S n －（D n+1 －S n+1 ）×S n+1 ｝/｛（D n －S n ）×S n ｝（1）
wherein D is n The outer diameter of the hollow tube blank or the titanium alloy tube before each pass of cold rolling is in mm; s is S n The wall thickness of the hollow tube blank or the titanium alloy tube before each pass of cold rolling is measured in mm; d (D) n+1 The unit is mm for the outer diameter of the titanium alloy tube after each pass of cold rolling; s is S n+1 The wall thickness of the titanium alloy tube after each pass of cold rolling is in mm;
7. cold rolling a phi 33 multiplied by 3 titanium alloy pipe into a phi 21 multiplied by 1.7 (with an outer diameter of 21mm and a wall thickness of 1.7 mm) titanium alloy pipe in a two-roll cold pilger mill, calculating to obtain a cold rolling deformation rate epsilon of 63.5% of the pass according to a calculation formula (1) in the process 6, feeding the cold rolling pass into the mill by 15.24mm (a calculation formula: 24 multiplied by 0.635), vacuum annealing the titanium alloy pipe obtained by the cold rolling pass by 704 ℃ (a calculation formula: 926-350 multiplied by 0.635), and keeping the cold time of 110.5 minutes (a calculation formula: 65 multiplied by 1.7);
8. cold rolling a phi 21 multiplied by 1.7 titanium alloy tube into a phi 14 multiplied by 0.8 (with an outer diameter of 14mm and a wall thickness of 0.8 mm) titanium alloy tube in a two-roll cold pilger mill, calculating to obtain a cold rolling deformation rate epsilon of 67.8% of the pass according to a calculation formula (1) in the process 6, feeding the cold rolling mill with a feeding amount of 16.272mm (with a calculation formula of 24 multiplied by 0.678), and carrying out vacuum annealing at 688.7 ℃ (926-350 multiplied by 0.678) for the titanium alloy tube obtained by the cold rolling of the pass, wherein the time for holding the cold rolling of the pass is 52 minutes (with a calculation formula of 65 multiplied by 0.8);
9. straightening and pickling a phi 14 multiplied by 0.8 titanium alloy pipe, removing the wall thickness by 0.02mm, polishing the outer surface of the phi 14 multiplied by 0.8 titanium alloy pipe by using a 1000-mesh green silicon carbide sand belt, and measuring the roughness Ra of the outer surface of the titanium alloy pipe to be 0.07 micrometers; polishing abrasive particle flow on the inner surface of a phi 14 multiplied by 0.8 titanium alloy pipe, and measuring the roughness Ra of the inner surface of the titanium alloy pipe to be 0.08 micrometers;
10. performing magnetic polishing treatment on a phi 14 multiplied by 0.8 titanium alloy pipe, wherein a stainless steel round needle with the length of 3mm and the diameter of 0.4mm is adopted as a magnetic polishing grinding steel needle, a pipe section sample of the titanium alloy pipe is taken after the treatment, the residual compressive stress is detected by an X-ray diffraction stress analyzer, and the residual compressive stress on the inner surface of the titanium alloy pipe is 318MPa and the residual compressive stress on the outer surface of the titanium alloy pipe is 326MPa;
11. the phi 14 multiplied by 0.8 titanium alloy tube is subjected to full-length ultrasonic flaw detection (flaw detection tube length of 0.03mm, width of 0.10mm and length of 1.4 mm) one by one, and the tensile and bending fatigue properties are sampled and checked.
The TA18 titanium alloy seamless tube with the specification of phi 14 x 0.8mm prepared in this example had a yield strength of 465MPa, a tensile strength of 595MPa and an elongation of 24%, and passed 1500 ten thousand times of rotational bending fatigue test.
Example 2
This example produced TA18 titanium alloy seamless tubes of a gauge of Φ15X1 mm (i.e., 15mm outside diameter, 1mm wall thickness).
The preparation process adopted in this example is as follows:
1. smelting by adopting a three-time vacuum consumable arc furnace to obtain a round TA18 titanium alloy cast ingot with the diameter of phi 490mm (the diameter of 490 mm), wherein the oxygen content (mass fraction) of the cast ingot is 0.059-0.065%, and the iron content (mass fraction) is 0.11%;
2. freely forging a titanium alloy cast ingot with the diameter of 490mm into a square billet with the length, width and height of 220mm by a hydraulic press with three piers and three drawing steps for 4 times;
3. performing hot rolling on a square billet with 220mm by 1 fire to prepare a black skin round bar with phi of 100mm (the diameter is 100 mm);
4. forging a black skin round bar with the diameter of phi 100mm into a black skin round bar with the diameter of phi 70mm (with the diameter of 70 mm) by 2 fire times, wherein the flaw detection of the obtained black skin round bar reaches the AA level of GB/T5193 standard;
5. machining a black skin round bar with the diameter of 70mm into a hollow tube blank with the diameter of 50 multiplied by 5.5 (the outer diameter is 50mm, the wall thickness is 5.5 mm) by deep hole drilling, inner boring and outer turning, sampling and measuring the phase transition point temperature T of TA18 titanium alloy to be 926 ℃, and sampling and measuring the grain orientation type of the hollow tube blank to be alpha phase <0001>// radial of the tube and <10-10>// axial of the tube;
6. cold rolling a phi 50×5.5 hollow shell into a phi 32×3.4 (outer diameter 32mm, wall thickness 3.4 mm) titanium alloy tube by a two-roll cold pilger mill, calculating according to a calculation formula (1) in example 1 to obtain a cold rolling deformation rate epsilon of 60.3% in the pass, feeding the cold rolling in the pass to a rolling mill to be 14.472mm (calculation formula: 24×0.603), vacuum annealing the titanium alloy tube obtained in the cold rolling in the pass to be 715 ℃ (calculation formula: 926-350×0.603), and keeping the temperature for 221 minutes in the pass (calculation formula: 65×3.4);
7. cold rolling a phi 32 multiplied by 3.4 titanium alloy tube into a phi 21 multiplied by 2 (the outer diameter is 21mm, the wall thickness is 2 mm) titanium alloy tube in a two-roll cold pilger mill, calculating to obtain a cold rolling deformation rate epsilon of 60.9% of the pass according to a calculation formula (1) in the embodiment 1, feeding the cold rolling mill with a feeding amount of 14.616mm (the calculation formula is 24 multiplied by 0.609), performing vacuum annealing at 713 ℃ (the calculation formula is 926-350 multiplied by 0.609) for 130 minutes (the calculation formula is 65 multiplied by 2);
8. cold rolling the phi 21 multiplied by 2 titanium alloy tube into a phi 15 multiplied by 1 (with an outer diameter of 15mm and a wall thickness of 1 mm) titanium alloy tube in a two-roll cold-rolling mill, calculating to obtain a cold-rolling deformation rate epsilon of 63.2% in the pass according to a calculation formula (1) in the example 1, feeding the cold-rolling mill with a feeding amount of 15.168mm (a calculation formula: 24 multiplied by 0.632), and carrying out vacuum annealing at 705 ℃ (926-350 multiplied by 0.632) for the titanium alloy tube obtained by the cold-rolling in the pass, wherein the annealing temperature is 65 minutes (the calculation formula: 65 multiplied by 1);
9. straightening and pickling a phi 15 multiplied by 1 titanium alloy pipe, removing the wall thickness of 0.02mm, polishing the outer surface of the phi 15 multiplied by 1 titanium alloy pipe by using a 1000-mesh green silicon carbide sand belt, and measuring the roughness Ra of the outer surface of the titanium alloy pipe to be 0.07 micrometers; polishing abrasive particle flow on the inner surface of a phi 15 multiplied by 1 titanium alloy pipe, and measuring the roughness Ra of the inner surface of the titanium alloy pipe to be 0.08 micrometers;
10. performing magnetic polishing treatment on a phi 15 multiplied by 1 titanium alloy tube, wherein a stainless steel round needle with the length of 3mm and the diameter of 0.4mm is adopted as a magnetic polishing grinding steel needle, a tube section sample of the titanium alloy tube is taken after the treatment, the residual compressive stress is detected by an X-ray diffraction stress analyzer, and the residual compressive stress on the inner surface of the titanium alloy tube is 309MPa and the residual compressive stress on the outer surface of the titanium alloy tube is 314MPa;
11. the phi 15 multiplied by 1 titanium alloy tube is subjected to full-length ultrasonic flaw detection (flaw detection tube length of 0.03mm, width of 0.10mm and length of 1.4 mm) one by one, and the tensile and bending fatigue properties are sampled and checked.
The TA18 titanium alloy seamless tube with the specification of phi 15 multiplied by 1mm prepared in the embodiment has the yield strength of 510MPa, the tensile strength of 650MPa and the elongation of 27 percent, and passes 1600-ten-thousand times rotational bending fatigue test.
In conclusion, the embodiment of the invention controls the oxygen and iron content in the titanium alloy component through three times of vacuum consumable arc furnace smelting, and avoids damaging the bending fatigue performance of the titanium alloy finished product pipe due to overhigh iron and oxygen content; the thermal deformation process combination of hot rolling and radial forging ensures that the structure and the performance of the round titanium alloy rod are uniform, and the grain orientation type of the titanium alloy tube blank is adjusted; the feeding quantity of each pass of cold rolling to the rolling mill is determined according to the cold rolling deformation rate epsilon of each pass, so that cracks on the inner surface and the outer surface of the titanium alloy tube in the cold rolling deformation process are avoided; the titanium alloy tube can be guaranteed to be fully recovered and recrystallized by controlling reasonable annealing process parameters, the plasticity is improved, and the cracking defect of the titanium alloy tube in the subsequent cold rolling deformation process is reduced; the roughness of the inner and outer surfaces of the titanium alloy tube is reduced by polishing the inner and outer surfaces of the titanium alloy tube respectively; the residual compressive stress on the surface of the titanium alloy tube is strengthened by acid washing and then magnetic polishing, so that the acid washing is avoided and the residual compressive stress on the surface of the titanium alloy tube is reduced. Therefore, the method provided by the invention greatly improves the rotating bending fatigue performance of the titanium alloy tube through the combined action of regulating and controlling the grain orientation, eliminating the cold rolling defect of the titanium alloy tube, reducing the roughness of the inner surface and the outer surface of the titanium alloy finished tube and increasing the residual compressive stress of the surface of the titanium alloy finished tube.
It should be noted that, each component or step in each embodiment may be intersected, replaced, added, and deleted, and therefore, the combination formed by these reasonable permutation and combination transformations shall also belong to the protection scope of the present invention, and shall not limit the protection scope of the present invention to the embodiments.
The foregoing is an exemplary embodiment of the present disclosure, and the order in which the embodiments of the present disclosure are disclosed is merely for the purpose of description and does not represent the advantages or disadvantages of the embodiments. It should be noted that the above discussion of any of the embodiments is merely exemplary and is not intended to suggest that the scope of the disclosure of embodiments of the invention (including the claims) is limited to these examples and that various changes and modifications may be made without departing from the scope of the invention as defined in the claims. The functions, steps and/or actions of the method claims in accordance with the disclosed embodiments described herein need not be performed in any particular order. Furthermore, although elements of the disclosed embodiments may be described or claimed in the singular, the plural is contemplated unless limitation to the singular is explicitly stated.
Those of ordinary skill in the art will appreciate that: the above discussion of any embodiment is merely exemplary and is not intended to imply that the scope of the disclosure of embodiments of the invention, including the claims, is limited to such examples; combinations of features of the above embodiments or in different embodiments are also possible within the idea of an embodiment of the invention, and there are many other variations of the different aspects of the embodiments of the invention as described above, which are not provided in detail for the sake of brevity. Therefore, any omissions, modifications, equivalent substitutions, improvements, and the like, which are made within the spirit and principles of the embodiments of the invention, are included within the scope of the embodiments of the invention.
Claims (10)
1. A method for improving the rotational bending fatigue property of a titanium alloy seamless pipe, which is characterized by comprising the following steps:
s1, smelting by adopting a three-time vacuum consumable arc furnace to obtain a titanium alloy cast ingot, wherein the oxygen content in the titanium alloy cast ingot is controlled to be less than or equal to 0.075% and the iron content is controlled to be less than or equal to 0.12% according to mass percentage;
s2, performing three-drawing free forging on the titanium alloy cast ingot for 3-5 times by three piers to obtain a preset number of square billets with the same volume, and performing hot rolling for 1-2 times and diameter forging for 2-3 times on each square billet to obtain a titanium alloy round bar;
s3, manufacturing the titanium alloy round bar into a hollow tube blank;
s4, cold rolling the hollow tube blank for 3-4 times to obtain a titanium alloy tube, and carrying out vacuum annealing on the titanium alloy tube subjected to each time cold rolling, wherein the feeding amount of each time cold rolling to a rolling mill is determined according to the cold rolling deformation rate epsilon of each time, the vacuum annealing temperature of the titanium alloy tube obtained by each time cold rolling is determined according to the transformation point temperature T of the titanium alloy and the cold rolling deformation rate epsilon of each time, and the annealing heat preservation time is determined according to the wall thickness S of the titanium alloy tube obtained by each time cold rolling;
s5, pickling the titanium alloy tube obtained in the step S4, and polishing the inner surface and the outer surface of the pickled titanium alloy tube respectively until the roughness Ra of the inner surface and the outer surface of the titanium alloy tube is less than or equal to 0.1 micrometer;
and S6, performing magnetic polishing treatment on the titanium alloy tube obtained in the step S5.
2. The method according to claim 1, wherein in the step S2, the titanium alloy ingot is free-forged by three upsets of 4 times to form billets, wherein the titanium alloy ingot is free-forged by three upsets of 1 st times to form billets of 2 times, the billets of 2 times are free-forged by three upsets of 2 times to form billets of 4 volumes, the billets of 4 volumes are free-forged by three upsets of 3 times to form billets of 8 volumes, and the billets of 8 volumes are free-forged by three upsets of 4 times to form billets of 16 volumes.
3. The method according to claim 1, wherein the round bar flaw detection of titanium alloy obtained in the step S2 reaches the AA level of GB/T5193 standard.
4. The method according to claim 1, wherein in the step S3, the round titanium alloy rod is machined by deep hole drilling, internal boring, external turning to produce a hollow shell having a grain orientation type of α -phase <0001>// tube radial, <10-10>// tube axial.
5. The method according to claim 1, wherein in the step S4, the hollow shell is cold rolled into a titanium alloy tube in 3 to 4 passes in a two-roll cold pilger mill, and the deformation rate ε is calculated according to the following formula:
ε=｛（D n －S n ）×S n －（D n+1 －S n+1 ）×S n+1 ｝/｛（D n －S n ）×S n ｝
wherein D is n The outer diameter of the hollow tube blank or the titanium alloy tube before each pass of cold rolling is in mm; s is S n The wall thickness of the hollow tube blank or the titanium alloy tube before each pass of cold rolling is measured in mm; d (D) n+1 The unit is mm for the outer diameter of the titanium alloy tube after each pass of cold rolling; s is S n+1 The wall thickness of the titanium alloy tube after each pass of cold rolling is expressed in mm.
6. The method according to claim 5, wherein in the step S4, the feeding amount of the cold rolling to the rolling mill is (24 xε) mm, and the outer diameter obtained by cold rolling with a cold rolling deformation rate ε is D n+1 The wall thickness is S n+1 The vacuum annealing temperature of the titanium alloy tube is (T-350 xepsilon) DEG C, and the annealing temperature is keptThe interval is (65X S) n+1 ) And (3) minutes.
7. The method according to claim 1, wherein in the step S5, the outer surface of the pickled titanium alloy tube is polished with a green silicon carbide abrasive belt having a granularity of not less than 1000 mesh, and the inner surface of the pickled titanium alloy tube is polished with a stream of abrasive particles.
8. The method according to claim 1, wherein in the step S6 of magnetic polishing treatment, a stainless steel round needle with the length of 3mm and the diameter of 0.4mm is adopted as the magnetic polishing grinding steel needle, a tube section sample of the titanium alloy tube is taken after the treatment, the residual compressive stress is detected by an X-ray diffraction stress analyzer, and the magnetic polishing treatment is regulated until the residual compressive stress of the inner surface and the outer surface of the titanium alloy tube is more than or equal to 300MPa.
9. The method as recited in claim 1, further comprising: and (3) performing ultrasonic flaw detection on the titanium alloy tube subjected to the magnetic polishing treatment in the step (S6), and taking the flaw detection sample tube with the carving depth of 0.03mm, the width of 0.10mm and the length of 1.4mm as detection standards, wherein the flaw detection sample tube is a titanium alloy sample tube which has no flaw and has the same material and the same specification as the titanium alloy tube subjected to the magnetic polishing treatment.
10. A titanium alloy seamless pipe, characterized in that the rotary bending fatigue performance of the titanium alloy seamless pipe is improved by adopting the method of any one of claims 1-9, the titanium alloy seamless pipe is a TA18 titanium alloy seamless pipe, and the TA18 titanium alloy seamless pipe can pass 1500-1600 ten thousand rotary bending fatigue tests.
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN117358778A (en) * | 2023-12-08 | 2024-01-09 | 成都先进金属材料产业技术研究院股份有限公司 | Titanium alloy seamless tube and preparation method thereof |
| CN117358778B (en) * | 2023-12-08 | 2024-03-08 | 成都先进金属材料产业技术研究院股份有限公司 | Titanium alloy seamless tube and preparation method thereof |
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