WO2013094647A1 - 溶接管用α+β型チタン合金板とその製造方法およびα+β型チタン合金溶接管製品 - Google Patents
溶接管用α+β型チタン合金板とその製造方法およびα+β型チタン合金溶接管製品 Download PDFInfo
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- WO2013094647A1 WO2013094647A1 PCT/JP2012/082954 JP2012082954W WO2013094647A1 WO 2013094647 A1 WO2013094647 A1 WO 2013094647A1 JP 2012082954 W JP2012082954 W JP 2012082954W WO 2013094647 A1 WO2013094647 A1 WO 2013094647A1
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- type titanium
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- 229910001069 Ti alloy Inorganic materials 0.000 title claims abstract description 81
- 238000004519 manufacturing process Methods 0.000 title claims description 27
- 239000013078 crystal Substances 0.000 claims abstract description 56
- 239000010936 titanium Substances 0.000 claims abstract description 27
- 238000005096 rolling process Methods 0.000 claims abstract description 25
- 239000000203 mixture Substances 0.000 claims abstract description 9
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 238000005098 hot rolling Methods 0.000 claims description 74
- 230000009466 transformation Effects 0.000 claims description 35
- 238000010438 heat treatment Methods 0.000 claims description 24
- 230000009467 reduction Effects 0.000 claims description 24
- 238000003466 welding Methods 0.000 claims description 6
- 229910052719 titanium Inorganic materials 0.000 abstract description 22
- 229910052757 nitrogen Inorganic materials 0.000 abstract description 4
- 238000005452 bending Methods 0.000 description 33
- 239000000463 material Substances 0.000 description 32
- 238000000034 method Methods 0.000 description 25
- 238000012360 testing method Methods 0.000 description 23
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 21
- 229910045601 alloy Inorganic materials 0.000 description 10
- 239000000956 alloy Substances 0.000 description 10
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- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
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- 238000005275 alloying Methods 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
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Images
Classifications
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- 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
- F16L9/17—Rigid pipes obtained by bending a sheet longitudinally and connecting the edges
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C14/00—Alloys based on titanium
-
- 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
Definitions
- the present invention relates to an ⁇ + ⁇ -type titanium alloy for welded pipes excellent in pipe forming property, strength and rigidity in the longitudinal direction of the pipe, and a manufacturing method thereof, and further relates to an ⁇ + ⁇ -type titanium alloy welded pipe product.
- ⁇ + ⁇ type titanium alloys have been used for a long time as components of aircraft by utilizing high specific strength. In recent years, the weight ratio of titanium alloys used in aircraft is increasing and its importance is increasing. Also in the field of consumer products, ⁇ + ⁇ type titanium alloys characterized by high Young's modulus and light specific gravity are increasingly used for golf club face applications. Furthermore, high-strength ⁇ + ⁇ -type titanium alloys are also used in parts for automobiles where weight reduction is important, or in geothermal well casings and riser pipes for subsea oil wells that require corrosion resistance and specific strength. Further expansion of application is expected.
- ⁇ + ⁇ type titanium alloy tube products have excellent corrosion resistance and high strength, and are therefore used for energy applications such as the above-mentioned geothermal well casing and oil well tube. Further, heat-resistant alloy tube products having high specific strength and excellent high-temperature strength are used for automobile exhaust pipes and the like. Furthermore, ⁇ + ⁇ type titanium alloy tube products are expected to be applied to strength members such as frames and reinforcing parts of high-grade cars and motorcycles by utilizing high specific strength. For this application, it is necessary that the strength and rigidity in the longitudinal direction of the pipe be high, and in particular, a tensile strength of 1050 MPa or more and a Young's modulus of 130 GPa or more are desirable. Furthermore, the manufacturing cost is required to be lower than other applications.
- Patent Document 1 and Patent Document 2 disclose a method of manufacturing a seamless tube using a tilt rolling method.
- hot-rolling conditions are prescribed
- annealed above the ⁇ transformation point it becomes a complete acicular structure, and the strength and elastic modulus in the longitudinal direction and the circumferential direction are the same at a level that is not so high, and the high strength in the longitudinal direction that the present invention aims at It is difficult to achieve high rigidity and high rigidity.
- Patent Document 2 since a large shear strain is introduced into the surface of the material, in the inclined rolling process in which severe hot working is performed on the material to be hot-rolled, the aim is to ensure the hot workability of the material. Specifies the hot working temperature in the process. Also in this case, it is impossible to obtain a hot-rolled texture in which the longitudinal direction of the tube has high strength, and it is difficult to achieve high strength and high rigidity in the longitudinal direction of the tube aimed by the present invention.
- Patent Document 3 As a method of obtaining an ⁇ + ⁇ type titanium alloy tube, bending is performed on a plate-like material obtained by hot rolling or further cold rolling, and the butt portion is welded by TIG, MIG, EB, plasma arc welding or the like.
- the manufacturing method is shown in Patent Document 3 and Patent Document 4. Both are more productive than inclined rolling or hot extrusion processes, and also eliminate the need for cutting to correct the uneven thickness often seen in seamless pipes, resulting in higher yields and lower manufacturing costs. Can be planned.
- Patent Document 3 discloses that the thickness tolerance of a welded pipe is specified to be small in Ti-3% Al-2.5% V and Ti-6% Al-4% V (% is mass%, hereinafter omitted). Uneven thickness is suppressed and a large amount of cutting is not required. Furthermore, as in Patent Document 1, the object is to increase fracture toughness by utilizing a ⁇ -annealed structure. Accordingly, in this case as well, the strength is the same in the tube longitudinal direction and the circumferential direction, and since large material in-plane material anisotropy is not manifested, the strength and rigidity of the tube longitudinal direction targeted by the present invention are increased. It is difficult to get.
- Patent Document 5 Patent Document 6 and Patent Document 7 disclose heat resistant titanium alloys for use in exhaust pipes of automobiles and motorcycles. These alloys are characterized by excellent high-temperature strength and oxidation resistance, and excellent cold workability. However, the tensile strength at room temperature of these alloys is about 400 to 600 MPa, and the room temperature tensile strength in the longitudinal direction of the pipe of 1050 MPa or more required for high-grade motorcycles and bicycle frames, automobile strength members, etc. Can not get.
- Non-Patent Document 1 describes an example of the relationship between the strength anisotropy in the plate surface and the texture of pure titanium.
- Basal-texture HCP bottom surface is oriented in the normal direction of the plate or in a direction close thereto.
- B-texture texture
- the trans-texture c-axis orientation which is the normal direction of the (0001) plane which is the bottom surface of the HCP of the titanium ⁇ phase is stronger in the plate width direction (the direction perpendicular to the rolling direction). It is said that the anisotropy of the yield stress is large in the oriented texture (hereinafter referred to as T-texture).
- FIG. 1 shows how to express the c-axis orientation that is the normal direction of the (0001) plane that is the bottom surface of the hexagonal HCP structure of the titanium ⁇ phase.
- An angle formed by the ND axis (in the normal direction of the plate surface) and the c axis is defined as ⁇ .
- An angle formed by a line obtained by projecting the c-axis onto the plate surface and the TD axis (plate width direction) is ⁇ .
- the B-texture is an orientation in which the c-axis is close to the ND axis, and there is no particular deviation in the plane of the plate. Therefore, the angle ⁇ is small and the angle ⁇ is around ⁇ 180 degrees to 180 degrees. It can be expressed as being distributed.
- Non-Patent Document 1 describes that a texture similar to T-texture is formed by heating pure titanium to the ⁇ temperature range and performing unidirectional rolling in the ⁇ temperature range. However, Non-Patent Document 1 does not describe an ⁇ + ⁇ type titanium alloy plate. Further, Non-Patent Document 1 does not investigate effects such as improvement of pipe forming property.
- Patent Document 8 discloses a technique for starting hot rolling in a ⁇ temperature range in pure titanium. This is to prevent the generation of wrinkles by making the crystal grains finer. However, Patent Document 8 does not describe the ⁇ + ⁇ type titanium alloy plate.
- Patent Document 9 discloses a titanium alloy containing Fe—Al.
- Patent Document 10 discloses a titanium alloy for golf club heads containing Fe and Al, and describes that Young's modulus is controlled by final finishing heat treatment.
- Patent Document 9 does not investigate texture evaluation or material anisotropy in the plate surface.
- Patent Document 10 does not investigate the effect of controlling the material anisotropy in the plate surface of the hot-rolled sheet by forming a texture based on hot-rolling condition control.
- ⁇ + ⁇ type titanium alloy plates that can be processed with good pipe forming properties, such as when a high strength ⁇ + ⁇ type titanium alloy tube having an axial strength of 1050 MPa or more is conventionally produced by rolling a thin plate material, and the use thereof
- the technology relating to the high-strength ⁇ + ⁇ -type titanium alloy tube product has not been disclosed.
- Patent Document 11 discloses a technique for improving bending workability by developing T-texture in an ⁇ + ⁇ type alloy.
- Patent Document 12 describes that an ⁇ + ⁇ type alloy hot-rolled sheet with a developed T-texture has an axial direction in the sheet width direction by utilizing the fact that tensile strength and Young's modulus increase in the sheet width direction.
- a manufacturing method of these parts having high axial rigidity is disclosed by processing automotive parts such as a connecting rod and an engine valve so as to have the above.
- automotive parts such as a connecting rod and an engine valve
- the present invention has been made against the background described above.
- the present invention uses a plate-like material whose material anisotropy in the plate surface is enhanced by developing a texture, bending the plate-like material, and butt-welding both ends to produce a welded pipe.
- the plate material is formed and welded so that the plate width direction is the longitudinal direction of the tube and the longitudinal direction is the circumferential direction of the tube.
- An object of the present invention is to provide a high-strength ⁇ + ⁇ -type titanium alloy plate with improved pipe forming properties and a method for producing the same.
- Another object of the present invention is to provide an ⁇ + ⁇ type titanium alloy tube product manufactured by the method and having high strength and rigidity in the tube longitudinal direction.
- the present inventors have made extensive studies focusing on the texture of the ⁇ + ⁇ type titanium alloy plate, and developed and stabilized the T-texture of the texture in the plate surface direction. It has been found that the ductility in the longitudinal direction of the plate is improved. Furthermore, the present inventors conducted extensive studies to evaluate the stability of T-texture. In an ⁇ + ⁇ type titanium alloy plate having a sufficiently developed and stable T-texture with good ductility in the longitudinal direction of the plate, the texture in the plate surface direction is the (0002) pole of the ⁇ phase having a hexagonal crystal structure.
- the ratio of the strongest value of the X-ray relative intensity from the bottom of the ⁇ phase in the first crystal grain group and the second crystal grain group (second crystal grain group / first crystal grain group) is 5.
- the present invention has been conceived by finding that it is 0 or more.
- the present inventors have conducted earnest research and repeated investigations on the manufacturing method of the ⁇ + ⁇ type titanium alloy plate in consideration of the formation process of the texture.
- the titanium alloy when the titanium alloy is hot-rolled in one direction, it exhibits T-texture, and the strength in the plate width direction becomes extremely high.
- the longitudinal direction of the tube By making this direction the longitudinal direction of the tube, the strength and rigidity in the tube axis direction are significantly increased.
- the ⁇ phase transforms into the ⁇ phase, the Burgers relationship is satisfied and the crystal orientation relationship is maintained, but the ⁇ phase is transformed by hot rolling in one direction to enhance the orientation of the ⁇ phase.
- the present inventors have found that, when forming by making the longitudinal direction of the plate on which the texture has been developed into the circumferential direction of the tube, the deformation resistance is low and the tube forming property is improved. It was. This is because the development of T-texture reduces the strength in the longitudinal direction of the plate and improves the ductility, as shown below. By making the direction the circumferential direction of the pipe, the bending workability in the circumferential direction is improved. It is because it becomes favorable.
- the yield stress in the plate width direction differs greatly between B-texture and T-texture, but the yield stress in the plate longitudinal direction is almost unchanged.
- the strength in the longitudinal direction is actually lowered when the T-texture is stabilized. This is because, when cold-working titanium near room temperature as in cold rolling, the main slip surface is limited to the bottom surface, and pure titanium has a direction close to the c-axis of HCP in addition to slip deformation. Because twin deformation occurs in the twin direction, the plastic anisotropy is smaller than that of the titanium alloy.
- the ⁇ + ⁇ -type titanium alloy which has a higher O content than pure titanium and contains Al, etc., suppresses twinning deformation and dominates slip deformation. By orientation, material anisotropy in the plate surface is further promoted. In this way, in the ⁇ + ⁇ type titanium alloy, by stabilizing the T-texture, the strength in the longitudinal direction of the plate is lowered and ductility is improved. By setting this direction as the circumferential direction of the tube, forming into the tube The deformation resistance at the time is lowered and the tube forming property is improved.
- the present inventors have found that in the ⁇ + ⁇ type titanium alloy, the hot rolling heating temperature at which strong T-texture is obtained is an appropriate temperature range in the ⁇ single phase region, and hot rolling starts in the ⁇ single phase region, and ⁇ + ⁇ 2 It has been found that it is more effective to increase the total reduction ratio by applying a large reduction in the phase region. As described above, the crystal orientation relationship that satisfies the Burgers relationship is maintained during the ⁇ ⁇ ⁇ phase transformation, but the orientation of the ⁇ phase is increased during hot rolling, and T-texture is further developed.
- the inventors have further developed T-texture by optimizing the combination and addition amount of alloy elements and selecting appropriate hot rolling conditions, and can enhance the above-mentioned effects. It was found that a tensile strength of 1050 MPa or more and a Young's modulus of 130 GPa or more can be obtained.
- the present invention is as follows. [1] ⁇ + ⁇ -type titanium alloy plate used for welded pipes with the rolling direction as the circumferential direction, 0.8% to 1.5% Fe, 4.8% to 5.5% Al, 0.020% by mass
- the angle ⁇ is 80 to 100 °
- the angle ⁇ which is the angle formed by the projection line on the c-axis plate surface in the (0002) pole figure of ⁇ phase and the plate width direction, is ⁇ 10 to 10
- a second crystal grain group oriented in a region that is at a temperature of the ⁇ -phase bottom surface in the first crystal grain group and the
- a total slab thickness is reduced after heating a slab containing O in the range of 0.38 and having the balance Ti and impurities to a hot rolling heating temperature not lower than the ⁇ transformation point and not higher than the ⁇ transformation point + 150 ° C.
- One-way hot rolling is performed at a rate of 90% or more, of which the thickness reduction rate in the ⁇ + ⁇ region is 80% or more, and the hot rolling finishing temperature is from the ⁇ transformation point ⁇ 50 ° C. or lower to the ⁇ transformation point ⁇ 250 ° C. or higher.
- the pipe is formed with the plate width direction as the longitudinal direction of the tube and the plate longitudinal direction as the circumferential direction of the tube, and the tensile strength in the longitudinal direction of the tube ⁇ + ⁇ -type titanium alloy welded pipe product having a Young's modulus exceeding 130 GPa.
- an ⁇ + ⁇ -type titanium alloy plate for a welded pipe that is optimal for manufacturing a welded pipe that has excellent pipe forming properties, strength in the longitudinal direction of the pipe, and excellent rigidity.
- the present inventors have investigated in detail the influence of the texture in the plate surface on the tube forming property of the ⁇ + ⁇ type titanium alloy plate for welded pipe.
- the deformation resistance in the plate longitudinal direction is lowered and the ductility is improved, so that the plate longitudinal direction becomes the circumferential direction of the tube when manufacturing a welded pipe.
- bending work improves the bending workability of the blank.
- the plate width direction has high strength and high Young's modulus
- the longitudinal direction of the tube exhibits characteristics of high strength and high rigidity. The present invention has been made based on this finding.
- the texture of the titanium ⁇ phase is limited in the present invention.
- the orientation of the c-axis which is the normal line of the (0001) plane, which is the six-fold symmetric crystal plane, of the titanium ⁇ phase, ie, the phase having a hexagonal crystal (HCP) crystal structure.
- HCP hexagonal crystal
- the angle between the c-axis and the plate normal (ND) direction is the angle ⁇
- the angle between the projection line of the c-axis on the plate surface and the plate width (TD) direction is the angle.
- FIG. 2 shows an example of a (0002) pole figure representing the integration direction of the bottom surface of the ⁇ phase (HCP). This (0002) pole figure is a typical example of T-texture, and the c-axis is strongly oriented in the plate width direction.
- Such a texture is obtained by taking a ratio between the accumulation degree of the first crystal grains whose c-axis is mainly oriented in the ND direction and the accumulation degree of the second crystal grains whose c-axis is mainly oriented in the TD direction.
- the angle ⁇ which is the angle formed between the c-axis and the plate normal (ND) direction in the (0002) pole figure of the ⁇ phase, is 0 degree to 30 degrees as shown in the hatched portion of FIG.
- the angle ⁇ which is the angle formed between the projection line to the c-axis plate surface and the plate width (TD) direction
- XND which is the strongest intensity (the strongest value of X-ray relative intensity) among the X-ray (0002) reflections from the bottom surface of the ⁇ phase is obtained.
- the angle ⁇ formed by the c-axis and the plate normal (ND) direction in the (0002) pole figure of the ⁇ phase is 80 ° to 100 ° as shown in the hatched portion of FIG. 1 (c).
- XTD which is the strongest intensity (the strongest value of the X-ray relative intensity) among the X-ray (0002) reflections from the second crystal grains oriented in the region where the angle ⁇ is ⁇ 10 to 10 ° is obtained.
- FIG. 3 schematically shows measurement positions of XTD and XND.
- the X-ray anisotropy index was associated with the ease of bending in the longitudinal direction of the plate.
- FIG. 4 shows the 0.2% proof stress in the longitudinal direction of the plate obtained by a tensile test with respect to the X-ray anisotropy index by processing a JIS 13B plate tensile test piece from this material. As shown in FIG. 4, the 0.2% yield strength in the longitudinal direction of the plate decreases as the X-ray anisotropy index increases.
- the tensile strength in the longitudinal direction of the tube increases as the X-ray anisotropy index increases.
- a tensile strength of 1050 MPa or more required for use as a frame of a high-grade motorcycle or a strength member of an automobile can be obtained when the X-ray anisotropy index is 5.0 or more.
- the plate width direction of the ⁇ + ⁇ type titanium alloy has a high Young's modulus exceeding 130 GPa.
- the ratio of the strongest value of the X-ray relative intensity (peak) from the bottom of the ⁇ phase in the first crystal grains and the second crystal grains (second crystal grains / first crystal grains) was limited to 5.0 or more.
- the X-ray anisotropy index is preferably 7.5 or more in order to obtain further excellent bending workability, tensile strength and Young's modulus.
- the X-ray intensity from the first crystal grains is very small, that is, the crystal grains belonging to the first crystal grains may be very small. In this case, the X-ray anisotropy index is very low. Sometimes it grows and diverges. Therefore, there is no upper limit for the X-ray anisotropy index.
- the composition of the ⁇ + ⁇ type titanium alloy plate for welded pipes of the present invention will be described. Since the ⁇ + ⁇ -type titanium alloy plate for welded pipes of the present invention has the chemical components shown below, it has a high pipe forming property, mainly bending workability when producing a welded pipe by bending the plate into a tubular shape. In addition, the longitudinal direction of the tube has high strength and rigidity.
- the reasons for selecting the component elements of the ⁇ + ⁇ -type titanium alloy plate for welded pipes of the present invention and the reasons for limiting the component ranges are shown below.
- Fe is an inexpensive additive element among the ⁇ -phase stabilizing elements and has a function of strengthening the ⁇ -phase by solid solution.
- Fe has a characteristic that ⁇ -stabilizing ability is higher than other ⁇ -stabilizing elements. Fe can be added in a smaller amount than other ⁇ -stabilizing elements, and solid solution strengthening at room temperature with Fe is not so high, and high ductility can be maintained, so that bending workability can be ensured.
- Al is a stabilizing element of the titanium ⁇ phase, has high solid solution strengthening ability, and is an inexpensive additive element.
- the lower limit of the addition amount is 4. 8%.
- Al is added exceeding 5.5%, the deformation resistance becomes too high and the ductility is lowered, the tube forming property by bending is lowered, and the hot workability is lowered by increasing the hot deformation resistance. Bring. Therefore, the amount of Al needs to be 5.5% or less.
- a more preferable range of the Al content is 4.9 to 5.3%.
- N is an interstitial solid solution in the ⁇ phase and has a solid solution strengthening action.
- N is added in an amount exceeding 0.020% by a normal method such as using a sponge titanium containing a high concentration of N, undissolved inclusions called LDI are likely to be generated, resulting in a low product yield. Become. Therefore, 0.020% was made the upper limit.
- a more preferable range of the N content is 0.010% or less.
- O like N, has an action of interstitial solid solution in the ⁇ phase to strengthen the solid solution.
- Q [O] + 2.77 ⁇ [N]
- [O] is the O content [% by mass]
- [N] is the N content [% by mass].
- the welded pipe product of the present invention is produced by using the ⁇ + ⁇ type titanium alloy plate for welded pipe of the present invention, with the plate width direction being the longitudinal direction of the tube and the plate longitudinal direction being the circumferential direction of the tube. Therefore, the welded pipe product of the present invention has excellent strength and rigidity in the longitudinal direction of the pipe, in which the tensile strength in the longitudinal direction of the pipe exceeds 1050 MPa and the Young's modulus exceeds 130 GPa.
- the manufacturing method of the present invention particularly relates to a method for developing T-texture, improving bending workability, and increasing strength and rigidity in the plate width direction.
- the production method of the present invention is a method for producing an ⁇ + ⁇ -type titanium alloy plate having a texture in the plate surface direction, an X-ray anisotropy index, and a titanium alloy component.
- the total thickness reduction rate is 90% or more, of which the thickness reduction rate in the ⁇ + ⁇ region is 80% or more.
- the hot rolling finishing temperature is set to a ⁇ transformation point of ⁇ 50 ° C. or less to a ⁇ transformation point of ⁇ 250 ° C. or more, and a hot rolling process for performing unidirectional hot rolling is provided.
- a slab with a predetermined composition is in the ⁇ single-phase region.
- a hot rolling heating temperature By heating to the hot rolling heating temperature and holding for 30 minutes or longer, for example, a ⁇ single-phase state is once obtained.
- the hot rolling finishing temperature which is the high temperature region of the ⁇ + ⁇ 2 phase, a one-way heat is applied to reduce the total plate thickness reduction rate of 90% or more, of which the plate thickness reduction rate is 80% or more in the ⁇ + ⁇ region. It is necessary to perform hot rolling.
- the temperature of the ⁇ transformation point can be measured by differential thermal analysis. 10 or more kinds of materials whose constituent compositions of Fe, Al, N, and O are changed in advance within the planned production range, laboratory-level small volume vacuum-melted and forged test pieces, each at a 1150 ° C ⁇ single phase region
- the ⁇ ⁇ ⁇ transformation start temperature and transformation end temperature are investigated by differential thermal analysis with slow cooling. At the time of actual production, it is possible to determine whether it is in the ⁇ single-phase region or the ⁇ + ⁇ region on the spot by sequential chemical measurement of the manufactured material and sequential temperature measurement using a radiation thermometer.
- the temperature of the slab and the ⁇ + ⁇ type titanium alloy plate is measured by a radiation thermometer installed between each stand of the hot rolling mill.
- the temperature of the hot rolled material (slab and ⁇ + ⁇ type titanium alloy plate) on the entrance side of each stand is in the ⁇ + ⁇ 2 phase region, it is determined that the stand is hot rolled in the ⁇ + ⁇ 2 phase region.
- the thickness reduction rate at the stand is measured as the thickness reduction rate in the ⁇ + ⁇ region.
- the hot rolling heating temperature is less than the ⁇ transformation point, that is, in the ⁇ + ⁇ 2 phase region, or when the hot rolling finishing temperature is less than the ⁇ transformation point of ⁇ 250 ° C.
- the hot rolling finishing temperature is less than the ⁇ transformation point of ⁇ 250 ° C.
- the hot deformation resistance is suddenly increased and the hot workability is lowered, so that there is a problem that ear cracks occur frequently and the yield is lowered. Therefore, it is necessary that the lower limit of the hot rolling heating temperature is the ⁇ transformation point and the lower limit of the hot rolling finishing temperature is the ⁇ transformation point of ⁇ 250 ° C. or more.
- the sheet thickness reduction rate from the ⁇ single phase region to the ⁇ + ⁇ 2 phase region (from the hot rolling heating temperature to the hot rolling finishing temperature) at this time is less than 90%, the processing strain to be introduced is not sufficient and the strain is It is difficult to introduce uniformly over the entire thickness. Therefore, the ⁇ -phase orientation cannot be obtained over the entire plate thickness, and the T-texture may not be sufficiently developed.
- the plate thickness reduction rate in the ⁇ + ⁇ region is less than 80%, the orientation of the ⁇ phase cannot be sufficiently obtained, and the crystal orientation of the ⁇ phase generated by transformation is partially randomized.
- the sheet thickness reduction rate in the hot rolling process needs to be 90% or more, of which 80% or more is necessary in the ⁇ + ⁇ region.
- the hot rolling heating temperature region should have the ⁇ transformation point + 150 ° C. as the upper limit and the ⁇ transformation point as the lower limit.
- the hot rolling finishing temperature at the time of hot rolling exceeds the ⁇ transformation point ⁇ 50 ° C.
- most of the hot rolling is performed in the ⁇ single phase region, and the initial structure becomes coarse ⁇ grains.
- the strain due to the inter-working is introduced non-uniformly depending on the crystal orientation of ⁇ grains.
- the ⁇ -phase orientation after the ⁇ ⁇ ⁇ transformation is not sufficient, and an ⁇ -phase having a partially random crystal orientation is generated. Therefore, there is a problem that the T-texture is not sufficiently developed.
- the upper limit of the hot rolling finishing temperature needs to be set at the ⁇ transformation point ⁇ 50 ° C. Therefore, the hot rolling finishing temperature needs to be in a temperature range from ⁇ transformation point ⁇ 50 ° C. or lower to ⁇ transformation point ⁇ 250 ° C. or higher.
- the temperature drop at both ends of the plate can be kept low.
- good hot workability is maintained at both ends of the plate, and there is an advantage that the occurrence of ear cracks is suppressed.
- unidirectional hot rolling is performed in which rolling is performed only in one direction.
- the present invention aims to improve the bending workability by reducing the deformation resistance during bending. This is because a T-texture having a high strength and a high Young's modulus in the longitudinal direction of the tube can be efficiently obtained. In this way, it is possible to obtain an ⁇ + ⁇ -type titanium alloy plate for a welded pipe having a low strength in the longitudinal direction of the plate, easy to form into a tube by bending, excellent in tube forming properties, and high strength and Young's modulus in the longitudinal direction of the plate. .
- light annealing equivalent to recovery heat treatment may be performed after the hot rolling step. If a decrease in the yield strength in the longitudinal direction is obtained by performing light annealing, the bending formability at the time of pipe forming is increased, and a better pipe forming property can be obtained. However, when annealing at a high temperature for a long time, the hot-rolled texture is broken and the strength in the plate width direction is lowered. Therefore, when annealing is performed, it is preferable that the temperature is maintained within a range of 700 to 900 ° C. for 30 minutes or less.
- an ⁇ + ⁇ type titanium alloy plate manufactured by the method for manufacturing an ⁇ + ⁇ type titanium alloy plate for welded pipes of the present invention is bent into a tubular shape with the plate width direction being the longitudinal direction of the tube and the plate longitudinal direction being the circumferential direction of the tube.
- Example 1 A titanium material having the composition shown in Table 1 was melted by a vacuum arc melting method, and this was hot rolled into a slab, heated to 1070 ° C. at a hot rolling heating temperature, and then subjected to a sheet thickness reduction rate of 97.5. % Hot rolled into 3.5 mm hot rolled sheet.
- the hot rolling finishing temperature was 840 ° C., and the sheet thickness reduction rate in the ⁇ + ⁇ region was 85%.
- unidirectional hot rolling was performed in the hot rolling process.
- rolling was performed not only in the plate longitudinal direction but also in the plate width direction in the hot rolling step.
- the hot-rolled sheet was pickled to remove the oxide scale, and a tensile test piece was collected to examine the tensile properties. Further, it is oriented in a region where the angle ⁇ between the c-axis and the plate normal direction in the (0002) pole figure of the ⁇ phase having a hexagonal crystal structure in the texture in the plate direction is 0 to 30 °.
- the angle between the first crystal grain group and the angle ⁇ between the angle ⁇ of 80 to 100 ° and the projection line to the c-axis plate surface in the (0002) pole figure of the ⁇ phase and the plate width direction With respect to the second crystal grain group oriented in the region where ⁇ is ⁇ 10 to 10 °, the strongest value of the X-ray relative intensity from the bottom surface of the ⁇ phase was measured by the X-ray diffraction method. Then, an X-ray anisotropy index which is the ratio (second crystal grain group (XTD) / first crystal grain group (XND)) was calculated to evaluate the degree of texture development in the plate surface direction.
- Pipe-forming property was evaluated using 0.2% proof stress in the longitudinal direction of the plate.
- the longitudinal direction of the plate is bent into a tubular shape and welded portions are welded to form a welded tube
- the 0.2% proof stress in the longitudinal direction of the plate is 820 MPa or less
- the longitudinal direction of the plate Since the plastic working is easy, the tube forming property is good.
- the longitudinal direction of the plate is bent into a tubular shape by press bending, and the attached portion is TIG welded to produce a welded tube having an outer diameter of 88.9 mm and a wall thickness of 3.5 mm. Tubed.
- An actual pipe tensile test piece was collected from the welded pipe, and the Young's modulus and tensile strength (JISZ2201) in the longitudinal direction of the pipe product were evaluated.
- JISZ2201 Young's modulus and tensile strength
- Test Nos. 1 and 2 are results for an ⁇ + ⁇ type titanium alloy manufactured by a process including hot rolling and rolling in the sheet width direction, and the X-ray anisotropy index is less than 5.0.
- the 0.2% proof stress in the longitudinal direction of the plate exceeds 820 MPa, the deformation resistance at the time of pipe making with the longitudinal direction of the plate as the bending direction is high, and the productivity of pipe making is low.
- the tensile strength in the longitudinal direction of the manufactured tube is less than 1050 MPa, and the Young's modulus does not reach 130 GPa, which is not preferable for applications that require strength and rigidity in the longitudinal direction of the tube.
- the 0.2% proof stress in the plate longitudinal direction is less than 820 MPa.
- the deformation resistance when bending in the longitudinal direction of the plate is sufficiently low, and the tube forming property is excellent when making the tube with the longitudinal direction of the plate being the circumferential direction of the tube.
- the tensile strength in the longitudinal direction of the manufactured tube is 1050 MPa or more and the Young's modulus exceeds 130 GPa, the material properties preferable for applications requiring strength and rigidity in the longitudinal direction of the tube are shown.
- test numbers 3, 7, and 11 the tensile strength in the longitudinal direction of the pipe after pipe making does not reach 1050 MPa.
- test numbers 3 and 7 each had a lower tensile strength in the longitudinal direction of the pipe because the amount of Al or Fe added was below the lower limit of the present invention.
- the nitrogen and oxygen contents were particularly low, and the Q value shown in Table 1 was below the lower limit of the specified amount.
- the tensile strength in the tube longitudinal direction reached a sufficiently high level. Not.
- test numbers 6, 10, and 14 the X-ray anisotropy index exceeds 5.0, but the 0.2% proof stress in the longitudinal direction of the plate exceeds 820 MPa, and it is difficult to make a pipe.
- the Fe addition amount, the Al addition amount, and the Q value were added in excess of the upper limit values of the present invention, so that the strength of this component system alloy was too high.
- Test No. 15 since many defects occurred in many portions of the hot-rolled sheet and the product yield was low, the characteristics could not be evaluated. This is because LDI occurred frequently because N was added exceeding the upper limit of the present invention.
- the titanium alloy plate having the element content and XTD / XND defined in the present invention has strong material anisotropy, the yield strength in the longitudinal direction of the plate is low, and the tube is bent in the longitudinal direction of the plate. Since the deformation resistance was low when producing the tube product, it was confirmed that the tube product was excellent in manufacturability and excellent in tensile strength and Young's modulus in the tube longitudinal direction of the tube product.
- the amount of alloying elements specified in the present invention and XTD / XND are deviated, strong material anisotropy, accompanied by low deformation resistance in the longitudinal direction of the plate and high strength and Young's modulus in the longitudinal direction of the pipe product. I can't get it.
- Example 2 Titanium materials having the compositions of test numbers 4, 8, and 13 in Table 1 were melted and hot-forged into slabs, which were unidirectionally hot-rolled under various conditions shown in Tables 2 to 4 at 800 ° C. After annealing for 120 seconds, pickling and removing the oxide scale, the tensile properties were examined and the X-ray anisotropy index was calculated in the same manner as in Example 1 to collect the plate surface direction. The degree of tissue development, the 0.2% proof stress in the longitudinal direction of the plate, the Young's modulus in the longitudinal direction of the pipe product and the tensile strength were evaluated. The results of evaluating these characteristics are also shown in Tables 2 to 4. Tables 2, 3, and 4 show the results for the hot-rolled annealed plates having the compositions of test numbers 4, 8, and 13, respectively.
- test numbers 18, 19, 26, 27, 34, and 35 which are examples of the present invention manufactured by the manufacturing method of the present invention, show a 0.2% proof stress of 820 MPa or less in the longitudinal direction of the plate and are good.
- in the longitudinal direction of the manufactured pipe product it has a tensile strength exceeding 1050 MPa and a Young's modulus exceeding 130 GPa, and is excellent in strength and rigidity in the longitudinal direction of the pipe.
- the 0.2% proof stress in the longitudinal direction of the plate exceeds 820 MPa
- the pipe forming property is inferior
- the tensile strength in the longitudinal direction of the tube is less than 1050 MPa.
- the Young's modulus in the longitudinal direction of the pipe is less than 130 GPa and does not have sufficient strength and rigidity characteristics as a strength member for high-grade motorcycle frames and automobiles.
- the total sheet thickness reduction rate during hot rolling was lower than the lower limit of the present invention, so that T-texture could not be sufficiently developed, and 0.2% proof stress in the plate longitudinal direction. This is because the tensile strength and Young's modulus in the longitudinal direction of the pipe after pipe making were not sufficiently increased.
- the plate thickness reduction rate in the ⁇ + ⁇ region was lower than the lower limit of the present invention, so that sufficient development of T-texture was not observed, and the 0.2% proof stress in the plate longitudinal direction decreased. This is because the tensile strength and Young's modulus in the longitudinal direction of the pipe after pipe making were not sufficiently high.
- the heating temperature before hot rolling was less than or equal to the lower limit temperature of the present invention, so the processing rate in the ⁇ single phase region was zero, and T-texture could not be sufficiently developed.
- the hot rolling finishing temperature was not more than the lower limit temperature of the present invention, and thus a large amount of ear cracks occurred.
- the heating temperature before hot rolling exceeds the upper limit temperature of the present invention
- the hot rolling finishing temperature exceeds the upper limit temperature of the present invention. Because most of the processing was performed in the ⁇ single-phase region, the T-texture was underdeveloped and destabilized due to the hot rolling of coarse ⁇ grains, and the formation of coarse final microstructures. This is because the 0.2% yield strength in the longitudinal direction of the plate was not sufficiently lowered, and the tensile strength and Young's modulus in the longitudinal direction of the tube were not sufficiently increased.
- a welded tube is manufactured by forming a plate into a tubular shape and butt-welding both ends, the deformation resistance is low, the tube forming property is excellent, and the tensile strength in the longitudinal direction of the formed welded tube
- a titanium alloy having the texture shown in the present invention and an additive element in the component range is used for the sheet thickness reduction rate, hot rolling heating temperature and It has been confirmed that it may be produced by hot-rolling in the finishing temperature range and producing the pipe by making the longitudinal direction of the plate the circumferential direction of the pipe.
- an ⁇ + ⁇ -type titanium alloy plate capable of producing a high-strength titanium alloy welded tube having good bending workability when bending a plate material into a tubular shape and having a high strength and Young's modulus in the longitudinal direction of the tube, and its A high-strength titanium alloy welded tube using an ⁇ + ⁇ type titanium alloy plate can be manufactured.
- This can be widely used for automotive parts such as high-grade motorcycles and bicycle frames and automobile strength members, and consumer products that require strength and rigidity in the longitudinal direction of the pipe.
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Abstract
Description
[1]
圧延方向を周方向とする溶接管に用いられるα+β型チタン合金板であり、質量%で、0.8~1.5%のFe、4.8~5.5%のAl、0.020%以下のNを含有し、下記式(1)に示すQ=0.14~0.38を満足する範囲のOを含有し、残部Tiおよび不純物からなる組成を有し、板面方向の集合組織が、六方晶結晶構造を有するα相の(0002)極点図におけるc軸と板法線方向とのなす角度である角度θが0~30°である領域に配向している第1結晶粒群と、前記角度θが80~100°であって、かつα相の(0002)極点図におけるc軸の板面への射影線と板幅方向とのなす角度である角Φが-10~10°である領域に配向している第2結晶粒群とを有し、前記第1結晶粒群と前記第2結晶粒群とにおけるα相の底面からのX線相対強度の最強値の比(第2結晶粒群/第1結晶粒群)が5.0以上である、溶接管用α+β型チタン合金板。
Q=[O]+2.77×[N] ・・・ (1)
上記式(1)において、[O]はOの含有量[質量%]であり、[N]はNの含有量[質量%]である。
質量%で、0.8~1.5%のFe、4.8~5.5%のAl、0.020%以下のNを含有し、下記式(1)に示すQ=0.14~0.38を満足する範囲のOを含有し、残部Tiおよび不純物からなる組成を有するスラブを、β変態点以上からβ変態点+150℃以下の熱延加熱温度に加熱した後、トータル板厚減少率を90%以上、うち、α+β域での板厚減少率を80%以上とし、熱延仕上温度をβ変態点-50℃以下からβ変態点-250℃以上として、一方向熱間圧延を行う熱間圧延工程を備える、溶接管用α+β型チタン合金板の製造方法。
Q=[O]+2.77×[N] ・・・ (1)
上記式(1)において、[O]はOの含有量[質量%]であり、[N]はNの含有量[質量%]である。
[1]に記載の溶接管用α+β型チタン合金板を使用して、板幅方向を管の長手方向、板長手方向を管の周方向にして造管してなり、管長手方向の引張強さが1050MPaを超え、ヤング率が130GPaを超える、α+β型チタン合金溶接管製品。
まず、集合組織の発達程度を、X線回折法により得られる、α相底面からのX線相対強度の最強値の比を用いて評価した。図2にα相(HCP)底面の集積方位を表す(0002)極点図の例を示す。この(0002)極点図は、T-textureの典型的な例であり、c軸が強く板幅方向に配向している。
Q=[O]+2.77×[N]
上記式(1)において、[O]はOの含有量[質量%]であり、[N]はNの含有量[質量%]である。
真空アーク溶解法により表1に示す組成を有するチタン材を溶解し、これを熱間で分塊圧延してスラブとし、1070℃に熱延加熱温度に加熱した後、板厚減少率97.5%の熱間圧延により3.5mmの熱延板とした。熱延仕上温度は840℃であり、α+β域での板厚減少率は85%であった。なお、表1に示す試験番号3~14については、熱間圧延工程において一方向熱間圧延を行った。試験番号1、2については、熱間圧延工程において板長手方向だけでなく板幅方向への圧延も行った。
表1の試験番号4、8、13の組成を有するチタン材を溶解し、これを熱間で鍛造してスラブとし、表2~4に示す種々の条件で一方向熱延して、800℃、120秒保持による焼鈍を行い、酸洗して酸化スケールを除去した後、実施例1と同様にして、引張特性を調べるとともに、X線異方性指数を算出して、板面方向の集合組織の発達程度、板長手方向の0.2%耐力、管製品の長手方向のヤング率および引張強度を評価した。これらの特性を評価した結果も合せて表2~4に示す。なお、表2、3、4は、それぞれ、試験番号4、8、13の組成の熱延焼鈍板における結果である。
Claims (3)
- 圧延方向を周方向とする溶接管に用いられるα+β型チタン合金板であり、
質量%で、0.8~1.5%のFe、4.8~5.5%のAl、0.020%以下のNを含有し、下記式(1)に示すQ=0.14~0.38を満足する範囲のOを含有し、残部Tiおよび不純物からなる組成を有し、
板面方向の集合組織が、六方晶結晶構造を有するα相の(0002)極点図におけるc軸と板法線方向とのなす角度である角度θが0~30°である領域に配向している第1結晶粒群と、前記角度θが80~100°であって、かつα相の(0002)極点図におけるc軸の板面への射影線と板幅方向とのなす角度である角Φが-10~10°である領域に配向している第2結晶粒群とを有し、前記第1結晶粒群と前記第2結晶粒群とにおけるα相の底面からのX線相対強度の最強値の比(第2結晶粒群/第1結晶粒群)が5.0以上である、溶接管用α+β型チタン合金板。
Q=[O]+2.77×[N] ・・・ (1)
上記式(1)において、[O]はOの含有量[質量%]であり、[N]はNの含有量[質量%]である。 - 質量%で、0.8~1.5%のFe、4.8~5.5%のAl、0.020%以下のNを含有し、下記式(1)に示すQ=0.14~0.38を満足する範囲のOを含有し、残部Tiおよび不純物からなる組成を有するスラブを、β変態点以上からβ変態点+150℃以下の熱延加熱温度に加熱した後、トータル板厚減少率を90%以上、うち、α+β域での板厚減少率を80%以上とし、熱延仕上温度をβ変態点-50℃以下からβ変態点-250℃以上として、一方向熱間圧延を行う熱間圧延工程を備える、溶接管用α+β型チタン合金板の製造方法。
Q=[O]+2.77×[N] ・・・ (1)
上記式(1)において、[O]はOの含有量[質量%]であり、[N]はNの含有量[質量%]である。 - 請求項1に記載の溶接管用α+β型チタン合金板を使用して、板幅方向を管の長手方向、板長手方向を管の周方向にして造管してなり、管長手方向の引張強さが1050MPaを超え、ヤング率が130GPaを超える、α+β型チタン合金溶接管製品。
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EP12860967.4A EP2801631B1 (en) | 2011-12-20 | 2012-12-19 | Alpha+beta-type titanium alloy plate for welded pipe, method for producing same, and alpha+beta-type titanium-alloy welded pipe product |
JP2013515621A JP5354136B1 (ja) | 2011-12-20 | 2012-12-19 | 溶接管用α+β型チタン合金板とその製造方法およびα+β型チタン合金溶接管製品 |
US14/366,239 US9587770B2 (en) | 2011-12-20 | 2012-12-19 | α + β type titanium alloy sheet for welded pipe, manufacturing method thereof, and α + β type titanium alloy welded pipe product |
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WO2016084243A1 (ja) * | 2014-11-28 | 2016-06-02 | 新日鐵住金株式会社 | 高強度、高ヤング率を有し疲労特性、衝撃靭性に優れるチタン合金 |
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KR101963428B1 (ko) * | 2017-10-13 | 2019-03-28 | 한국기계연구원 | 타이타늄 합금 및 타이타늄 합금의 제조방법 |
CN109706344A (zh) * | 2018-12-26 | 2019-05-03 | 中国石油天然气集团公司管材研究所 | 用于油气开发的高强度高韧性钛合金管材及其制备方法 |
CN109706344B (zh) * | 2018-12-26 | 2021-11-23 | 中国石油天然气集团公司管材研究所 | 用于油气开发的高强度高韧性钛合金管材及其制备方法 |
RU2808020C1 (ru) * | 2022-12-12 | 2023-11-22 | Публичное Акционерное Общество "Корпорация Всмпо-Ависма" | Холоднокатаная полоса для изготовления коррозионно-стойких компонентов оборудования и способ ее получения |
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JP5354136B1 (ja) | 2013-11-27 |
US9587770B2 (en) | 2017-03-07 |
EP2801631B1 (en) | 2018-02-07 |
EP2801631A4 (en) | 2016-03-02 |
US20150292650A1 (en) | 2015-10-15 |
EP2801631A1 (en) | 2014-11-12 |
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