WO2016143270A1 - 高強度電縫鋼管およびその製造方法 - Google Patents
高強度電縫鋼管およびその製造方法 Download PDFInfo
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- WO2016143270A1 WO2016143270A1 PCT/JP2016/000847 JP2016000847W WO2016143270A1 WO 2016143270 A1 WO2016143270 A1 WO 2016143270A1 JP 2016000847 W JP2016000847 W JP 2016000847W WO 2016143270 A1 WO2016143270 A1 WO 2016143270A1
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- steel pipe
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 132
- 239000010959 steel Substances 0.000 title claims abstract description 132
- 238000004519 manufacturing process Methods 0.000 title claims description 26
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 43
- 230000000717 retained effect Effects 0.000 claims abstract description 26
- 229910001568 polygonal ferrite Inorganic materials 0.000 claims abstract description 25
- 239000000203 mixture Substances 0.000 claims abstract description 24
- 229910001563 bainite Inorganic materials 0.000 claims abstract description 18
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 13
- 229910001562 pearlite Inorganic materials 0.000 claims abstract description 11
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 5
- 239000002245 particle Substances 0.000 claims abstract description 5
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 5
- 238000010438 heat treatment Methods 0.000 claims description 58
- 238000001816 cooling Methods 0.000 claims description 43
- 238000000034 method Methods 0.000 claims description 39
- 238000005098 hot rolling Methods 0.000 claims description 33
- 239000000463 material Substances 0.000 claims description 25
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- 229910052802 copper Inorganic materials 0.000 claims description 9
- 229910052759 nickel Inorganic materials 0.000 claims description 9
- 238000002844 melting Methods 0.000 claims description 7
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- 229910052748 manganese Inorganic materials 0.000 abstract description 5
- 229910052799 carbon Inorganic materials 0.000 abstract description 4
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- 230000000694 effects Effects 0.000 description 15
- 229910000859 α-Fe Inorganic materials 0.000 description 12
- 230000009466 transformation Effects 0.000 description 11
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- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 6
- 229910052720 vanadium Inorganic materials 0.000 description 5
- 229910001567 cementite Inorganic materials 0.000 description 4
- 238000001887 electron backscatter diffraction Methods 0.000 description 4
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
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- 229910052750 molybdenum Inorganic materials 0.000 description 3
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- -1 Mo: 0.5% or less Substances 0.000 description 2
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 2
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- VNWKTOKETHGBQD-UHFFFAOYSA-N methane Chemical compound C VNWKTOKETHGBQD-UHFFFAOYSA-N 0.000 description 2
- 229910052758 niobium Inorganic materials 0.000 description 2
- 230000003287 optical effect Effects 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 238000009751 slip forming Methods 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 238000002441 X-ray diffraction Methods 0.000 description 1
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- 238000004458 analytical method Methods 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 239000010953 base metal Substances 0.000 description 1
- 230000033228 biological regulation Effects 0.000 description 1
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- 239000003795 chemical substances by application Substances 0.000 description 1
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- 150000001247 metal acetylides Chemical class 0.000 description 1
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- 229910052757 nitrogen Inorganic materials 0.000 description 1
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- 235000019362 perlite Nutrition 0.000 description 1
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- 238000001953 recrystallisation Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 230000007017 scission Effects 0.000 description 1
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- 230000006641 stabilisation Effects 0.000 description 1
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- 238000005728 strengthening Methods 0.000 description 1
- 238000010998 test method Methods 0.000 description 1
- 150000003568 thioethers Chemical class 0.000 description 1
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Classifications
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
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- B23K11/002—Resistance welding; Severing by resistance heating specially adapted for particular articles or work
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- B23K11/16—Resistance welding; Severing by resistance heating taking account of the properties of the material to be welded
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- B23K13/02—Seam welding
- B23K13/025—Seam welding for tubes
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- B23K31/02—Processes relevant to this subclass, specially adapted for particular articles or purposes, but not covered by only one of the preceding main groups relating to soldering or welding
- B23K31/027—Making tubes with soldering or welding
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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- C—CHEMISTRY; METALLURGY
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- C—CHEMISTRY; METALLURGY
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- C22C—ALLOYS
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
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- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
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- F16L—PIPES; JOINTS OR FITTINGS FOR PIPES; SUPPORTS FOR PIPES, CABLES OR PROTECTIVE TUBING; MEANS FOR THERMAL INSULATION IN GENERAL
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
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- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
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Definitions
- the present invention relates to an electric-welded steel pipe for line pipes that transports oil and natural gas. Particularly, it is suitable for laying a reel barge and has a high strength of X60 (yield strength YS: 415 MPa or more) grade and excellent bending.
- the present invention relates to a high-strength ERW steel pipe having characteristics and a method for producing the same.
- the reel barge method has been widely used as a method for laying submarine pipelines.
- the reel barge method performs circumferential welding, inspection, coating, etc. of pipes on land in advance, winds up the resulting long pipe onto the reel of a barge ship, and rewinds the pipe from the reel at the target sea.
- This reel barge method can perform the submarine pipeline laying operation very efficiently.
- tensile and compressive stress due to bending-bending back acts on a part of the pipe when winding and laying the pipe. For this reason, local breakage and buckling occur in the used pipe, and the pipe may be broken starting from this.
- a steel pipe for pipelines laid by the reel barge method needs to be a steel pipe having excellent bending characteristics, that is, excellent buckling resistance on the compression side and bending resistance on the tensile side during bending deformation.
- the buckling resistance is largely governed by the uniformity of the shape of the tube, and the fracture resistance is important in that uniform elongation is large and ductile fracture can be prevented.
- ERW steel pipes have been applied for line pipes from an economic point of view.
- ERW steel pipes have better wall thickness deviation and roundness than seamless steel pipes, and are superior to seamless steel pipes in buckling resistance, which is strongly influenced by the shape factor.
- ERW steel pipes are formed into a substantially cylindrical shape by continuous roll forming of hot-rolled steel sheets, a considerable amount of plastic strain is introduced in the pipe axis direction, and uniform elongation in the pipe axis direction is achieved. descend. For this reason, the uniform elongation of the ERW steel pipe is usually lower than that of the seamless steel pipe, and breakage is likely to occur even with a small strain, and the fracture resistance is reduced as compared with the seamless steel pipe.
- Patent Document 1 proposes a method for manufacturing a high-strength steel pipe excellent in buckling resistance.
- C 0.02 to 0.15%
- Si 0.1 to 2.0%
- Mn 0.5 to 2.0%
- Al 0.01 to 0.1%
- N 0.01% or less
- P 0.02% or less
- S 0.005% or less
- Nb 0.1% or less
- V 0.1% or less
- Ti 0.1% or less
- Mo Mo
- Cu Recrystallization after heating a slab containing one or more of 2.0% or less
- Ni: 2.0% or less, Cr: 1.0% or less and having a composition with a relatively low Si content to 1050 ° C or higher performs rough rolling at a temperature above, then, Ar 3 transformation point [°C] above 900 ° C.
- Patent Document 1 requires isothermal holding during cooling, and the hot rolling line that cools while continuously transporting a cooling zone arranged in one direction has a very long equipment length. Need to be long. Further, the technique described in Patent Document 1 has a problem that the cooling stop temperature is 350 to 450 ° C., the deformation resistance is increased, and it is difficult to wind the steel sheet into a coil shape. Moreover, Patent Document 1 does not include any mention to improve the uniform elongation of the steel pipe.
- the present invention solves such problems of the prior art, and provides a high-strength electric-resistance-welded steel pipe having improved bending characteristics and excellent bending characteristics without subjecting the entire pipe to heat treatment, and a method for producing the same. For the purpose.
- high strength here refers to the case where the yield strength YS in the tube axis direction is 415 MPa or more.
- excellent bending property here refers to a case where the uniform elongation Elu in the tube axis direction is 8% or more, particularly with respect to fracture resistance.
- the present inventors diligently studied various factors that affect the uniform elongation of a hot-rolled steel sheet, which is a pipe material for an electric resistance steel pipe.
- Cr which is a ferrite former.
- the composition that positively contains the proper amount of Cr, which is a ferrite former, and adjusting the cooling after hot rolling to an appropriate range it is transformed at a high temperature and has a small aspect ratio.
- the present invention has been completed based on such findings and further studies. That is, the gist of the present invention is as follows. (1) By mass, C: 0.04 to 0.15%, Si: 0.10 to 0.50%, Mn: 1.0 to 2.2%, P: 0.050% or less, S: 0.005% or less, Cr: 0.2 to 1.0%, Ti: 0.005 -0.030%, Al: 0.010-0.050%, the composition consisting of the balance Fe and inevitable impurities, and the retained austenite of 3-20% by volume with polygonal ferrite having a volume fraction of 70% or more, The balance is composed of one or more selected from martensite, bainite, and pearlite, and the polygonal ferrite has a structure having an average particle diameter of 5 ⁇ m or more and an aspect ratio of 1.40 or less.
- ERW steel pipe (2) In (1), in addition to the above-mentioned composition, by mass%, Mo: 0.5% or less, Cu: 0.5% or less, Ni: 1.0% or less, Co: 1.0% or less Or a high-strength ERW steel pipe containing two or more types. (3) In (1) or (2), in addition to the above composition, in addition to mass, high strength containing one or two selected from Nb: 0.10% or less and V: 0.10% or less ERW steel pipe. (4) A high-strength electric resistance welded steel pipe according to any one of (1) to (3), further containing Ca: 0.0005 to 0.0050% by mass% in addition to the above composition.
- a method for producing a high-strength electric resistance welded steel pipe according to any one of (1) to (4), wherein the steel material is subjected to heating, hot rolling, and cooling after hot rolling.
- a tube material manufacturing process in which a hot rolled steel strip is wound in a coil shape, and the hot rolled steel strip is formed into an open tube having a substantially circular cross section, and then the widthwise end faces of the open tube are brought into contact with each other.
- the method for producing an ERW steel pipe includes: a pipe forming step of heating to a melting point or higher and pressure welding to form an ERW steel pipe; and an in-line heat treatment step in which an ERW weld portion of the ERW steel pipe is heat treated in-line.
- the heating in the tube material manufacturing process is heating to a heating temperature of 1100 to 1250 ° C., and cooling after the hot rolling in the tube material manufacturing process is performed at a temperature at the center position in the thickness direction of the steel strip. More than 650 ° C. at a temperature T 20 after 20 s starting from the time t 0 after leaving the final hot rolling pass and less than 650 ° C.
- the present invention such as a submarine pipeline laid by a reel barge method, an S-Lay method, or a J-Lay method, a pipeline laid in a crustal movement zone such as an earthquake zone, etc.
- High-strength ERW steel pipe with high strength of X60 grade or better, suitable for line pipes, and superior bending properties can be manufactured at a lower cost than seamless steel pipe without heat treatment of the entire pipe.
- the present invention has an effect of being able to effectively contribute to the use in which high deformability is required, for example, for civil engineering.
- the ERW steel pipe of the present invention is in mass%, C: 0.04 to 0.15%, Si: 0.10 to 0.50%, Mn: 1.0 to 2.2%, P: 0.050% or less, S: 0.005% or less, Cr: 0.2 to 1.0 , Ti: 0.005 to 0.030%, Al: 0.010 to 0.050%, the composition consisting of the balance Fe and unavoidable impurities, and polygonal ferrite with a volume fraction of 70% or more, and a volume fraction of 3 to 20 % Of retained austenite, the balance is one or more selected from martensite, bainite and pearlite, and the polygonal ferrite has an average grain size of 5 ⁇ m or more and an aspect ratio of 1.40 or less.
- the yield strength YS in the tube axis direction is 415 MPa or more, and the uniform elongation Elu in the tube axis direction is 8% or more.
- C 0.04-0.15%
- C is an element that contributes to stabilization of the austenite phase, and is an important element in the present invention in order to ensure a desired amount of retained austenite. In order to obtain such an effect, it is necessary to contain 0.04% or more of C. On the other hand, the content of C exceeding 0.15% decreases weldability. For this reason, C is limited to the range of 0.04 to 0.15%.
- C is 0.06% or more.
- C is 0.12% or less. More preferably, C is 0.08 to 0.12%.
- Si 0.10 to 0.50%
- Si is an element that acts as a deoxidizer, suppresses precipitation of cementite, and greatly contributes to the formation of retained austenite.
- Si has the effect
- it is necessary to contain 0.10% or more of Si.
- the content of Si exceeding 0.50% lowers the ERW weldability. For these reasons, Si was limited to the range of 0.10 to 0.50%.
- Si is 0.10 to 0.30%.
- Mn 1.0-2.2%
- Mn is an element that increases the stability of the austenite phase and suppresses decomposition into pearlite or bainite. In order to obtain such an effect, it is necessary to contain 1.0% or more of Mn. On the other hand, when Mn is contained excessively exceeding 2.2%, the formation of high-temperature transformed ferrite is suppressed, and the discharge / concentration of C into untransformed austenite is hindered. For this reason, Mn was limited to a range of 1.0 to 2.2%. Preferably, Mn is 1.2% or more. Preferably, Mn is 1.6% or less.
- P 0.050% or less
- P is an element that has an adverse effect of segregating at grain boundaries and lowering toughness.
- P is preferably reduced as much as possible, but 0.050% is acceptable. For this reason, P was limited to 0.050% or less.
- Preferably it is 0.030% or less.
- P is preferably 0.002% or more.
- S 0.005% or less S is present as sulfide inclusions (MnS) in steel.
- MnS sulfide inclusions
- S it is desirable to reduce S as much as possible, but it is acceptable up to 0.005%. For this reason, S was limited to 0.005% or less.
- S is preferably 0.003% or less.
- S is preferably 0.0002% or more.
- Cr 0.2-1.0% Cr is an important element in the present invention that suppresses precipitation of cementite in untransformed austenite and contributes to the formation of retained austenite. In order to obtain such an effect, it is necessary to contain 0.2% or more of Cr. On the other hand, an excessive content exceeding 1.0% lowers the ERW weldability. Therefore, Cr is limited to the range of 0.2 to 1.0%. Note that Cr is preferably 0.2 to 0.8%, more preferably 0.2 to 0.5%.
- Ti is an element having an action of fixing N as TiN and suppressing a decrease in steel toughness due to N. Such an effect is recognized when the Ti content is 0.005% or more. On the other hand, if the Ti content exceeds 0.030%, the amount of Ti carbonitride that precipitates along the cleavage plane of Fe increases, and the toughness of the steel decreases. For this reason, Ti is limited to the range of 0.005 to 0.030%. Preferably, Ti is 0.005 to 0.025%.
- Al 0.010 to 0.050%
- Al is an element that acts as a strong deoxidizing agent and suppresses cementite precipitation and greatly contributes to the formation of retained austenite. In order to obtain such an effect, a content of 0.010% or more is required. On the other hand, if the content exceeds 0.050%, Al-based oxides tend to remain in the steel, and the cleanliness of the steel is lowered. For this reason, Al is limited to the range of 0.010 to 0.050%. Note that the content is preferably 0.010 to 0.045%.
- the balance other than the above components is composed of Fe and inevitable impurities.
- Inevitable impurities include N: 0.005% or less and O (oxygen): 0.005% or less.
- Mo 0.5% or less
- Cu 0.5% or less
- Ni 1.0% or less
- Co 1.0% or less
- One or two or more, and / or Nb: 0.10% or less, V: 0.10% or less, and / or Ca: 0.0005 to 0.0050% can be contained.
- Mo: 0.5% or less, Cu: 0.5% or less, Ni: 1.0% or less, Co: 1.0% or less Mo, Cu, Ni, and Co are all stable in the austenite phase. It is an element that improves the properties and contributes to the formation of retained austenite. In order to obtain such an effect, it is desirable to contain Mo: 0.05% or more, Cu: 0.05% or more, Ni: 0.05% or more, Co: 0.05% or more. On the other hand, if the content exceeds Mo: 0.5%, Cu: 0.5%, Ni: 1.0%, and Co: 1.0%, the above effects are saturated and weldability is reduced.
- Mo 0.5% or less
- Cu 0.5% or less
- Ni 1.0% or less
- Co 1.0% or less
- Mo 0.4% or less
- Cu 0.4% or less
- Co 0.4% or less
- Nb 0.10% or less
- V One or two of 0.10% or less Nb and V both form carbonitrides or carbides and contribute to increasing the strength of the hot-rolled steel strip through precipitation strengthening It is.
- Nb 0.01% or more
- V 0.01% or more
- the content exceeds Nb: 0.10% and V: 0.10%, coarse precipitates are formed, leading to a decrease in base metal toughness or weldability. For this reason, when it contains, it is preferable to limit to Nb: 0.10% or less and V: 0.10% or less.
- Ca 0.0005 to 0.0050%
- Ca is an element that contributes effectively to the control of the morphology of sulfide inclusions, detoxifies sulfides such as MnS, and contributes to improving the toughness of the hot-rolled steel strip.
- it is necessary to contain 0.0005% or more of Ca.
- Ca is preferably limited to a range of 0.0005 to 0.0050%. More preferably, Ca is 0.0010% or more. More preferably, Ca is 0.0040% or less.
- the electric resistance welded steel pipe of the present invention has the above-described composition, mainly composed of polygonal ferrite (volume fraction of 70% or more), 3 to 20% residual austenite by volume, and the balance being martensite, bainite and pearlite.
- the polygonal ferrite has a structure having an average particle diameter of 5 ⁇ m or more and an aspect ratio of 1.40 or less.
- Polygonal ferrite 70% or more in volume fraction
- “Polygonal ferrite” as used herein means high-temperature transformation ferrite that transforms with diffusion.
- the high temperature transformation ferrite discharges C to untransformed austenite with the progress of transformation, stabilizes the untransformed austenite, and facilitates the formation of a desired amount of retained austenite.
- polygonal ferrite is mainly used.
- the “subject” as used in the present invention refers to a tissue occupying 70% or more of the volume fraction.
- the main structure is bainitic ferrite or bainite
- C concentration to untransformed austenite becomes insufficient
- untransformed austenite is not stable
- pearlite after cooling And transformed into bainite and a retained austenite phase of 3 to 20% in volume fraction cannot be secured. Therefore, the main structure is polygonal ferrite.
- polygonal ferrite is an aspect ratio obtained by (crystal grain diameter in the rolling direction) / (crystal grain diameter in the plate thickness direction): 1.40 or less And an average particle size of 5 ⁇ m or more.
- Residual austenite 3-20% in volume fraction
- the retained austenite contributes to the improvement of the uniform elongation of the ERW steel pipe through the process-induced transformation (TRIP phenomenon). In order to obtain such an effect, a residual austenite phase of 3% or more in volume fraction is required.
- the content exceeds 20%, the carbon concentration contained in the retained austenite decreases, the retained austenite becomes unstable with respect to deformation, and the uniform elongation decreases. For this reason, the retained austenite was limited to the range of 3 to 20% by volume. It is preferably 3 to 15%. More preferably, it is 5 to 15%.
- the balance other than the polygonal ferrite and retained austenite, which are the main structures described above, is preferably 10% or less (0% by volume) 1 type or two or more types selected from martensite, bainite, and perlite. If one or more selected from the remaining martensite, bainite, and pearlite exceeds 10% by volume in total, the strength increases excessively and the uniform elongation decreases. Ferrites other than polygonal ferrite are classified as bainite.
- the above-mentioned polygonal ferrite has a volume fraction of 70% or more, a retained austenite with a volume fraction of 3 to 20%, and the balance is one or two selected from martensite, bainite and pearlite.
- a structure observation specimen is collected from the electric resistance welded pipe so that the observation surface has a cross section in the rolling direction (L cross section). Then, the collected specimen for structure observation is polished, corroded (corrosive solution: nital), and the thickness of the specimen is measured using an optical microscope (magnification: 400 times) and a scanning electron microscope SEM (magnification: 2000 times).
- the tissue at the 1 / 2t position is observed, and images are taken for each of two or more visual fields.
- For the obtained structure photograph use an image analysis device to determine the type of structure, the area ratio of each phase, and the aspect ratio of the crystal grains of polygonal ferrite, and cut the polygonal ferrite according to JIS G 0551 by a cutting method.
- the average crystal grain size can be determined.
- arithmetic average is used for calculation of a value by measurement of said structure
- the area ratio is obtained by SEM / EBSD (Electron Back Scatter Diffraction) method. Further, assuming that the microstructure is three-dimensionally homogeneous, the obtained area ratio is defined as a volume fraction.
- the steel material having the above composition is subjected to heating, hot rolling, and cooling after hot rolling to form a hot rolled steel strip, and a tube material manufacturing process for winding the hot rolled steel strip into a coil shape. Apply.
- the steel material having the above composition is heated to a heating temperature of 1100 to 1250 ° C. and then hot-rolled to form a hot-rolled steel strip.
- Heating temperature of steel material 1100 ⁇ 1250 °C If the heating temperature of the steel material is less than 1100 ° C., the coarse carbonitride and segregation zone generated in the casting process cannot be lost, and the ductility and toughness of the hot-rolled steel sheet are reduced, and further the strength is reduced. On the other hand, heating above 1250 ° C. increases the tendency of crystal grains to become coarse, which may lead to a decrease in the ductility and toughness of the hot-rolled steel sheet, and increases the energy intensity, which is economically disadvantageous. In addition, let the above-mentioned heating temperature be in-furnace preset temperature of a heating furnace.
- the heated steel material is hot-rolled to form a hot-rolled steel strip having a predetermined size and shape.
- the conditions for hot rolling are not particularly limited as long as a predetermined dimension and shape can be ensured, but considering the subsequent cooling, the temperature when the final pass of hot rolling is finished, that is, the finish rolling finish temperature, Is preferably 750 ° C. or higher.
- the temperature at the center position in the thickness direction of the steel strip in the hot-rolled steel strip exceeds 650 ° C. at a temperature T 20 after 20 seconds from the time t 0 when the final pass of the hot rolling is taken.
- the temperature T 80 after 80 s is adjusted to be less than 650 ° C. with the time t 0 from the final pass of the hot rolling as a base point, and the cooling stop temperature is continuously from 600 to 450 ° C. Cooling is performed.
- “Cooling” as used in the present invention is preferably cooling performed by injecting cooling water onto the upper and lower surfaces of the hot-rolled steel strip from a water-cooling zone continuously arranged on a run-out table installed on the exit side of the finishing mill. .
- interval of a water cooling zone, water quantity density, etc. are not specifically limited.
- required by the heat transfer analysis based on the temperature measured with the surface thermometer shall be used for the temperature of the hot rolled steel strip thickness direction center position.
- Cooling after hot rolling The temperature at the center position in the thickness direction of the steel strip exceeds 650 ° C. at the temperature T 20 after 20 s from the time t 0 when the final hot rolling pass is passed, and the final hot rolling pass
- the temperature T 80 after 80 s is adjusted to be less than 650 ° C. with the time t 0 from the base point as long as it is within the composition range of the hot-rolled steel strip of the present invention. Adjusted to exceed 650 ° C. at temperature T 20 after 20 seconds from time t 0 after exiting the final pass of hot rolling, and below 650 ° C. at temperature T 80 after 80 seconds from time t 0 Then, by cooling, polygonal ferrite transformation occurs, and the steel strip structure can be made a structure mainly composed of polygonal ferrite.
- the temperature at the center position in the thickness direction of the steel strip is between 750 and less than 80 seconds with the time from the final hot rolling pass (finishing finish) t 0 as the base point and between 20 seconds and less than 80 seconds. If it becomes 650 ° C., polygonal ferrite transformation occurs, and the steel strip structure can be made a structure mainly composed of polygonal ferrite.
- the cooling after hot rolling is performed at a temperature T 20 after 20 seconds from the time t 0 when the temperature at the center position in the thickness direction of the steel strip leaves the hot rolling final pass.
- the temperature T was adjusted to be less than 650 ° C. at a temperature T 80 after 80 s , with the time t 0 exceeding the temperature of 650 ° C. and leaving the final hot rolling pass as the base point.
- Cooling stop temperature 600 °C ⁇ 450 °C
- the cooling stop temperature is higher than 600 ° C.
- untransformed austenite is transformed into pearlite or bainite after winding, and a desired amount of retained austenite cannot be secured.
- the cooling stop temperature for cooling after hot rolling is limited to a temperature in the range of 600 ° C to 450 ° C.
- the cooling after hot rolling is performed at a temperature T 20 after 20 seconds from the time t 0 when the temperature at the center position in the thickness direction of the steel strip leaves the hot rolling final pass. Adjusted so that the temperature T after 80 s is less than 650 ° C, with the temperature t exceeding 80 ° C and taking the time t 0 after the final pass of hot rolling as the base point, and cooling stop temperature: 600 to 450 ° C
- the cooling process is limited to cooling continuously.
- a pipe making process is performed.
- the hot rolled steel strip wound in a coil shape which is a pipe material
- the end faces in the width direction of the open pipes are brought into contact with each other, the end faces in the width direction of the open pipes are heated to a melting point or higher by high-frequency induction heating or high-frequency resistance heating, and pressure welded with a squeeze roll to obtain an ERW steel pipe.
- the pipe making process in the present invention is not particularly limited as long as it is a process capable of producing an ERW steel pipe having a desired size and shape. Any conventional pipe making process using ordinary ERW steel pipe manufacturing equipment can be applied.
- the ERW steel pipe manufactured in the pipe making process is then subjected to an in-line heat treatment process in which the ERW weld is heat treated in-line.
- the electro-welded zone When hot-rolled steel strip having a composition within the scope of the present invention is electro-welded, the electro-welded zone has a structure mainly composed of martensite and / or upper bainite by rapid heating and rapid cooling during welding. These structures are structures having low toughness, and in the present invention, an in-line heat treatment step is performed to modify the structure to be rich in toughness.
- the term “rich in toughness” as used herein means a case where the Charpy impact test absorbed energy vE 0 (J) at a test temperature of 0 ° C. in the circumferential direction is 150 J or more.
- one or a plurality of induction heating devices and a cooling device such as water cooling that can heat and cool the ERW welded portion in the downstream of the squeeze roll in the ERW steel pipe manufacturing facility, It is preferable to use a conventional apparatus row arranged sequentially.
- In-line heat treatment is performed so that the minimum temperature portion in the thickness direction of the ERW weld is 800 ° C or higher and the maximum heating temperature is 1150 ° C or lower. Cooling to 500 ° C or less at the maximum temperature in the thickness direction.
- in-line refers to linear alignment
- in-line heat treatment refers to, for example, heat treatment using a heating device linearly aligned with the weld.
- the heating device can be directly energized and is not particularly limited.
- Heating temperature for in-line heat treatment 800-1150 ° C
- the structure of the electro-welded welded part cannot be bainitic ferrite and / or bainite rich in toughness over the entire plate thickness direction.
- the heating temperature in the in-line heat treatment of the ERW weld was limited to a temperature in the range of 800 to 1150 ° C. from the lowest temperature part to the highest temperature part.
- the temperature is preferably 850 to 1100 ° C.
- in-line tempering treatment may be performed at a heating temperature (tempering temperature) of 400 ° C. to 700 ° C.
- the in-line tempering treatment is preferably performed using an apparatus row provided with an induction heating apparatus or the like on the downstream side of the in-line heat treatment apparatus.
- the in-line heat treatment time is preferably 800 ° C. or more and 5 seconds or more.
- Molten steel having the composition shown in Table 1 was melted in a converter and made into a slab (steel material: thickness 220 mm) by a continuous casting method. These slabs (steel materials) were made into hot-rolled steel strips having the thicknesses shown in Table 2 in the tube material manufacturing process under the conditions shown in Table 2, and wound into a coil shape to obtain tube materials. Next, the hot rolled steel strip wound in a coil shape, which is a tube material, is rewound and continuously formed by a plurality of rolls in a cold state to form an open tube having a substantially circular cross section.
- the opposite end surfaces in the width direction are brought into contact with each other, the end surfaces in the width direction of the open pipe are heated to a melting point or higher using a high-frequency induction heating device, and pressed with a squeeze roll (thickness / outer diameter).
- ERW steel pipe Next, the induction welded part of the obtained ERW steel pipe is heated to 1050 ° C. at the surface temperature using an induction heating device arranged in-line on the downstream side of the squeeze roll of the ERW steel pipe manufacturing equipment, In-line heat treatment was performed to cool to 500 ° C or less at the maximum temperature in the thickness direction. It has been confirmed that the minimum temperature is 850 ° C or higher. At this time, the average cooling rate on the pipe outer surface of the ERW weld was about 2 ° C./s.
- Test pieces were collected from the obtained electric resistance welded steel pipe and subjected to structure observation, tensile test, and impact test.
- the test method is as follows.
- (1) Microstructure observation A specimen for microstructural observation was collected from the obtained ERW steel tube so that the observation surface was a cross section in the rolling direction (L cross section).
- the collected specimens for structure observation are polished, corroded (corrosive solution: nital), and the thickness is 1 / mm using an optical microscope (magnification: 400 times) and a scanning electron microscope SEM (magnification: 2000 times).
- the tissue at the 2t position was observed and imaged for two or more fields of view.
- the obtained structure photograph, using an image analysis device, the type of structure and the area ratio of each phase, the aspect ratio of the main phase crystal grains and the cutting method in accordance with JIS G 0551, the average crystal grains of the main phase The diameter was determined.
- the obtained value was arithmetically averaged to obtain the value of the steel pipe. Since retained austenite is difficult to distinguish visually, the area ratio was determined by the SEM / EBSD (Electron Back Scatter Diffraction) method. Assuming that the microstructure is three-dimensionally homogeneous, the obtained area ratio was defined as the volume fraction.
- the Charpy impact test was conducted in accordance with the above, and the Charpy impact test absorbed energy vE 0 (J) at 0 ° C. was determined. In addition, the test was done 3 each and the arithmetic average value of the obtained value was made into the absorbed energy of the said steel pipe.
- the base material portion having a high strength with a yield strength YS in the tube axis direction of 415 MPa or more, and an “excellent bending property” with a uniform elongation Elu in the tube axis direction of 8% or more, and Charpy impact test absorption energy at 0 ° C. vE 0 : 150 J or more and high strength ERW steel pipe having excellent ERW weld toughness.
- the uniform elongation Elu in the tube axis direction is less than 8%, and the bending characteristics are degraded.
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Abstract
Description
Ts[℃]=780-270×C-90×Mn-37×Ni-70×Cr-83×Mo ・・・ (1)
(1)質量%で、C:0.04~0.15%、Si:0.10~0.50%、Mn:1.0~2.2%、P:0.050%以下、S:0.005%以下、Cr:0.2~1.0%、Ti:0.005~0.030%、Al:0.010~0.050%を含有し、残部Fe及び不可避的不純物からなる組成と、ポリゴナルフェライトを体積分率で70%以上とし、体積率で3~20%の残留オーステナイトと、残部がマルテンサイト、ベイナイトおよびパーライトのうちから選ばれた1種又は2種以上からなり、前記ポリゴナルフェライトが、平均粒径:5μm以上、アスペクト比が1.40以下である組織と、を有する高強度電縫鋼管。
(2)(1)において、前記組成に加えてさらに、質量%で、Mo:0.5%以下、Cu:0.5%以下、Ni:1.0%以下、Co:1.0%以下のうちから選ばれた1種または2種以上を含む高強度電縫鋼管。
(3)(1)または(2)において、前記組成に加えてさらに、質量%で、Nb:0.10%以下、V:0.10%以下のうちから選ばれた1種または2種を含有する高強度電縫鋼管。
(4)(1)ないし(3)のいずれかにおいて、前記組成に加えてさらに、質量%で、Ca:0.0005~0.0050%を含有する組成とする高強度電縫鋼管。
(5)(1)~(4)のいずれかに記載の高強度電縫鋼管の製造方法であり、鋼素材に、加熱と、熱間圧延と、熱間圧延後の冷却とを施して熱延鋼帯とし、該熱延鋼帯をコイル状に巻取る管素材製造工程と、前記熱延鋼帯を、略円形断面のオープン管に成形したのち、該オープン管の幅方向端面同士を突き合わせて融点以上に加熱し、圧接して電縫鋼管となす造管工程と、該電縫鋼管の電縫溶接部をインラインで熱処理を施すインライン熱処理工程と、を含む電縫鋼管の製造方法において、
前記管素材製造工程における前記加熱が、加熱温度:1100~1250℃とする加熱であり、前記管素材製造工程における前記熱間圧延後の冷却を、鋼帯板厚方向中心位置の温度が、熱間圧延最終パスを出た時間t0を基点として20s後の温度T20で650℃超えで、かつ熱間圧延最終パスを出た時間t0を基点として80s後の温度T80で650℃未満になるように調整し、冷却停止温度:600~450℃の温度域の温度まで連続的に冷却する冷却とし、前記インライン熱処理工程における前記熱処理を、前記電縫溶接部の肉厚方向における最低温度部が800℃以上、最高加熱温度が1150℃以下となるように加熱した後、水冷または放冷して、前記電縫溶接部の肉厚方向における最高温度で500℃以下まで冷却する処理とする高強度電縫鋼管の製造方法。
(6)(5)において、前記造管工程が、前記熱延鋼帯を、巻き戻し、複数のロールで連続的に成形し、略円形断面のオープン管としたのち、該オープン管の幅方向端面同士を突き合わせて、前記オープン管の幅方向端面を融点以上に加熱し、圧接して電縫鋼管となす造管工程である高強度電縫鋼管の製造方法。
Cは、オーステナイト相の安定化に寄与する元素であり、本発明では所望の残留オーステナイト量を確保するために重要な元素である。このような効果を得るためには、0.04%以上のCの含有を必要とする。一方、0.15%を超えるCの含有は、溶接性を低下させる。このため、Cは0.04~0.15%の範囲に限定した。なお、好ましくは、Cは0.06%以上である。好ましくは、Cは0.12%以下である。より好ましくは、Cは0.08~0.12%である。
Siは、脱酸剤として作用し、また、セメンタイトの析出を抑制し、残留オーステナイトの生成に大きく寄与する元素である。また、Siは、熱間圧延時のスケールオフ量を小さくする作用を有する。このような効果を得るためには、0.10%以上のSiの含有を必要とする。一方、0.50%を超えるSiの含有は、電縫溶接性を低下させる。このようなことから、Siは0.10~0.50%の範囲に限定した。なお、好ましくは、Siは0.10~0.30%である。
Mnは、オーステナイト相の安定性を高め、パーライトやベイナイトへの分解を抑制する元素である。このような効果を得るためには、1.0%以上のMnの含有を必要とする。一方、2.2%を超えて過度にMnを含有すると、高温変態フェライトの生成が抑制され、Cの未変態オーステナイトへの排出・濃縮を妨げる。このため、Mnは1.0~2.2%の範囲に限定した。なお、好ましくは、Mnは1.2%以上である。好ましくは、Mnは1.6%以下である。
Pは、粒界に偏析して靭性を低下させる悪影響を及ぼす元素であり、本発明では、不純物としてできるだけ低減することが望ましいが、0.050%までは許容できる。このため、Pは0.050%以下に限定した。なお、好ましくは0.030%以下である。また、過度の低減は、精錬コストの高騰を招くため、Pは0.002%以上とすることが好ましい。
Sは、鋼中で硫化物系介在物(MnS)として存在する。とくに、MnSは、熱間圧延工程で薄く延伸され、延性、靭性に悪影響を及ぼす。このため、本発明では、Sは、できるだけ低減することが望ましいが、0.005%までは許容できる。このため、Sは0.005%以下に限定した。なお、好ましくはSは0.003%以下である。なお、過度の低減は、精錬コストの高騰を招くためSは0.0002%以上とすることが好ましい。
Crは、未変態オーステナイト中でのセメンタイトの析出を抑制し、残留オーステナイトの生成に寄与する、本発明では重要な元素である。このような効果を得るためには、0.2%以上のCrの含有を必要とする。一方、1.0%を超える過度の含有は、電縫溶接性を低下させる。このため、Crは0.2~1.0%の範囲に限定した。なお、Crは、好ましくは、0.2~0.8%、より好ましくは0.2~0.5%である。
Tiは、NをTiNとして固定し、Nによる鋼の靭性低下を抑制する作用を有する元素である。このような効果は0.005%以上のTiの含有で認められる。一方、0.030%を超えてTiを含有すると、Feのへき開面に沿って析出するTi炭窒化物の量が増加し、鋼の靭性が低下する。このため、Tiは0.005~0.030%の範囲に限定した。なお、好ましくは、Tiは0.005~0.025%である。
Alは、強力な脱酸剤として作用するとともに、セメンタイト析出を抑制し残留オーステナイトの生成に大きく寄与する元素である。このような効果を得るためには、0.010%以上の含有を必要とする。一方、0.050%を超えて含有すると、鋼中にAl系酸化物が残存しやすく、鋼の清浄度を低下させる。このため、Alは0.010~0.050%の範囲に限定した。なお、好ましくは0.010~0.045%である。
Mo、Cu、Ni、Coはいずれも、オーステナイト相の安定性を高め、残留オーステナイトの生成に寄与する元素である。このような効果を得るためには、Mo:0.05%以上、Cu:0.05%以上、Ni:0.05%以上、Co:0.05%以上を含有することが望ましい。一方、Mo:0.5%、Cu:0.5%、Ni:1.0%、Co:1.0%をそれぞれ超えて含有すると、上記した効果が飽和するうえ、溶接性が低下する。このため、含有する場合には、Mo:0.5%以下、Cu:0.5%以下、Ni:1.0%以下、Co:1.0%以下の範囲に、それぞれ、限定することが好ましい。なお、より好ましくはMo:0.4%以下、Cu:0.4%以下、Ni:0.4%以下、Co:0.4%以下である。
Nb、Vはいずれも、炭窒化物あるいは炭化物を形成し析出強化を介して熱延鋼帯の強度増加に寄与する元素である。このような効果を得るためには、Nb:0.01%以上、V:0.01%以上含有することが望ましい。一方、Nb:0.10%、V:0.10%をそれぞれ超えて含有すると、粗大な析出物が形成され、母材靭性の低下、あるいは溶接性の低下を招く。このため、含有する場合には、Nb:0.10%以下、V:0.10%以下に限定することが好ましい。
Caは、硫化物系介在物の形態制御に有効に寄与する元素であり、MnS等の硫化物を無害化し熱延鋼帯の靭性向上に寄与する。このような効果を得るためには、0.0005%以上Caを含有する必要がある。一方、0.0050%を超えてCaを含有すると、Ca系酸化物クラスターが形成され、熱延鋼帯の靭性が低下する。このため、含有する場合には、Caは0.0005~0.0050%の範囲に限定することが好ましい。なお、より好ましくは、Caは0.0010%以上である。より好ましくは、Caは0.0040%以下である。
ここでいう「ポリゴナルフェライト」は、拡散を伴いながら変態する高温変態フェライトを意味する。高温変態フェライトは、変態の進行とともに、Cを未変態オーステナイトへ排出し、未変態オーステナイトを安定化させて、所望量の残留オーステナイトの生成を容易にする。このようなことから、残留オーステナイトによるTRIP現象を利用して、均一伸びに優れた高強度熱延鋼帯とする本発明では、ポリゴナルフェライトを主体とする。なお、本発明でいう「主体」とは、体積分率で70%以上を占める組織をいうものとする。
残留オーステナイトは、加工誘起変態(TRIP現象)を介して、電縫鋼管の均一伸びの向上に寄与する。このような効果を得るためには、体積分率で3%以上の残留オーステナイト相を必要とする。一方、20%を超える過剰の含有は、残留オーステナイトに含まれる炭素濃度が減少し、残留オーステナイトが変形に対して不安定になり均一伸びが低下する。このため、残留オーステナイトは体積率で3~20%の範囲に限定した。なお、好ましくは3~15%である。より好ましくは、5~15%である。
上記した主体となる組織であるポリゴナルフェライトおよび残留オーステナイト以外の残部は、好ましくは体積率で10%以下(0%を含む)の、マルテンサイト、ベイナイトおよびパーライトのうちから選ばれた1種又は2種以上とする。残部である、マルテンサイト、ベイナイトおよびパーライトのうちから選ばれた1種又は2種以上が、合計で体積率で10%を超えると、強度が増加しすぎて、均一伸びが低下する。なお、ポリゴナルフェライト以外のフェライトは、ベイナイトとして分類する。
鋼素材の加熱温度が1100℃未満では、鋳造工程で生成した粗大炭窒化物や偏析帯を消失させることができず、熱延鋼板の延性や靭性の低下、さらには強度の低下を招く。一方、1250℃を超えて加熱すると、結晶粒が粗大する傾向が強くなり、熱延鋼板の延性や靭性の低下を招く恐れがあるうえ、エネルギー原単位を上昇させ経済的に不利となる。なお、上記した加熱温度は、加熱炉の炉内設定温度とする。
本発明の熱延鋼帯の組成範囲内であれば、鋼帯板厚方向中心位置の温度が、熱間圧延の最終パスを出た時間t0から20s後の温度T20で、650℃超えとなるように、かつ時間t0から80s後の温度T80で、650℃未満になるように調整して、冷却することで、ポリゴナルフェライト変態が生じ、鋼帯組織をポリゴナルフェライトを主体とする組織とすることができる。
このようなことから、本発明では、熱間圧延後の冷却を、鋼帯板厚方向中心位置の温度が、熱間圧延最終パスを出た時間t0を基点として20s後の温度T20で650℃超えで、かつ熱間圧延最終パスを出た時間t0を基点として80s後の温度T80で650℃未満になるように調整することとした。
冷却停止温度が、600℃より高いと、巻き取り後に未変態オーステナイトがパーライトやベイナイトに変態し、所望量の残留オーステナイトを確保することができなくなる。一方、450℃より低いと、未変態オーステナイトの一部がマルテンサイトに変態し、所望量の残留オーステナイトを確保できなくなる。このため、熱間圧延後の冷却の冷却停止温度は600℃~450℃の範囲の温度に限定した。
加熱温度が、最低温度部で800℃未満では、電縫溶接部の組織を、板厚方向全域にわたり、靭性に富むベイニティックフェライトおよび/またはベイナイトとすることができない。一方、加熱温度が、最高加熱部で1150℃を超えて高温となると、オーステナイト粒が顕著に粗大化して、焼入性が増大し、冷却後、マルテンサイトを形成する。このため、電縫溶接部のインライン熱処理における加熱温度は最低温度部から最高温度部で800~1150℃の範囲の温度に限定した。なお、好ましくは850~1100℃である。なお、加熱後の冷却は、要求される強度や靭性に応じて、放冷あるいは水冷とすることができるが、強度と靭性を両立させるためには、水冷とすることが好ましい。なお、水冷後、必要に応じて、加熱温度(焼戻温度):400℃~700℃の範囲でインライン焼戻処理を施しても良い。インライン焼戻処理は、インライン熱処理装置の下流側に誘導加熱装置等を設けた装置列を利用して行うことが好ましい。インライン熱処理の時間は、800℃以上で5秒以上とすることが好ましい。
(1)組織観察
得られた電縫鋼管から、観察面が圧延方向断面(L断面)となるように、組織観察用試験片を採取した。採取した組織観察用試験片を、研磨し、腐食(腐食液:ナイタール)して、光学顕微鏡(倍率:400倍)と走査型電子顕微鏡SEM(倍率:2000倍)を用いて、板厚1/2t位置における組織を観察し、各2視野以上について撮像した。得られた組織写真について、画像解析装置を用い、組織の種類および各相の面積率、さらに主相の結晶粒のアスペクト比およびJIS G 0551に準拠して切断法で、主相の平均結晶粒径を求めた。得られた値を算術平均して当該鋼管の値とした。なお、残留オーステナイトについては、目視での判別が難しいため、SEM/EBSD(Electron Back Scatter Diffraction)法により、面積率を求めた。ミクロ組織は3次元的に均質であるとして、求めた面積率を体積分率とした。
(2)引張試験
得られた電縫鋼管から、管先端側から見て、電縫溶接部から円周方向に時計回りに90°位置で、ASTM A 370の規定に準拠して、引張方向が管軸方向なるように引張試験片を採取し、引張試験を実施し、引張特性(降伏強さYS、引張強さTSおよび均一伸びElu)を求めた。
(3)衝撃試験
得られた電縫鋼管の電縫溶接部の肉厚1/2位置から、円周方向が試験片長手方向となるように、Vノッチ試験片を採取し、ASTM A370の規定に準拠してシャルピー衝撃試験を実施し、試験温度:0℃でのシャルピー衝撃試験吸収エネルギーvE0(J)を求めた。なお、試験は、各3本ずつ行い、得られた値の算術平均値を当該鋼管の吸収エネルギーとした。
Claims (6)
- 質量%で、
C :0.04~0.15%、 Si:0.10~0.50%、
Mn:1.0~2.2%、 P :0.050%以下、
S :0.005%以下、 Cr:0.2~1.0%、
Ti:0.005~0.030%、 Al:0.010~0.050%
を含有し、残部Fe及び不可避的不純物からなる組成と、
ポリゴナルフェライトを体積分率で70%以上とし、体積分率で3~20%の残留オーステナイトと、残部がマルテンサイト、ベイナイトおよびパーライトのうちから選ばれた1種または2種以上からなり、前記ポリゴナルフェライトが、平均粒径:5μm以上、アスペクト比が1.40以下である組織と、
を有する高強度電縫鋼管。 - 前記組成に加えてさらに、質量%で、Mo:0.5%以下、Cu:0.5%以下、Ni:1.0%以下、Co:1.0%以下のうちから選ばれた1種または2種以上を含む請求項1に記載の高強度電縫鋼管。
- 前記組成に加えてさらに、質量%で、Nb:0.10%以下、V:0.10%以下のうちから選ばれた1種または2種を含有する請求項1または2に記載の高強度電縫鋼管。
- 前記組成に加えてさらに、質量%で、Ca:0.0005~0.0050%を含有する組成とする請求項1ないし3のいずれかに記載の高強度電縫鋼管。
- 請求項1~4のいずれかに記載の高強度電縫鋼管の製造方法であり、鋼素材に、加熱と、熱間圧延と、熱間圧延後の冷却とを施し熱延鋼帯となし、該熱延鋼帯をコイル状に巻取る管素材製造工程と、前記熱延鋼帯を、略円形断面のオープン管に成形したのち、該オープン管の幅方向端面同士を突き合わせて融点以上に加熱し、圧接して電縫鋼管となす造管工程と、該電縫鋼管の電縫溶接部をインラインで熱処理を施すインライン熱処理工程と、を含む電縫鋼管の製造方法において、
前記管素材製造工程における前記加熱が、加熱温度:1100~1250℃とする加熱であり、
前記管素材製造工程における前記熱間圧延後の冷却を、鋼帯板厚方向中心位置の温度が、熱間圧延最終パスを出た時間t0を基点として20s後の温度T20で650℃超えで、かつ熱間圧延最終パスを出た時間t0を基点として80s後の温度T80で650℃未満になるように調整し、冷却停止温度:600~450℃の温度域の温度まで連続的に冷却する冷却とし、
前記インライン熱処理工程における前記熱処理を、電縫溶接部の肉厚方向における最低温度部が800℃以上、最高加熱温度が1150℃以下となるように加熱した後、水冷または放冷して、電縫溶接部の肉厚方向における最高温度で500℃以下まで冷却する処理とする高強度電縫鋼管の製造方法。 - 前記造管工程が、前記熱延鋼帯を、巻き戻し、複数のロールで連続的に成形し、略円形断面のオープン管としたのち、該オープン管の幅方向端面同士を突き合わせて、前記オープン管の幅方向端面を融点以上に加熱し、圧接して電縫鋼管となす造管工程である請求項5に記載の高強度電縫鋼管の製造方法。
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US15/554,937 US20180030557A1 (en) | 2015-03-06 | 2016-02-18 | High-strength electric resistance welded steel pipe and method for producing the same |
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EP3246427B1 (en) | 2018-12-12 |
KR20170113626A (ko) | 2017-10-12 |
JP6004144B1 (ja) | 2016-10-05 |
KR101993542B1 (ko) | 2019-09-30 |
EP3246427A4 (en) | 2017-11-22 |
CA2975366C (en) | 2019-06-04 |
JPWO2016143270A1 (ja) | 2017-04-27 |
US20180030557A1 (en) | 2018-02-01 |
CN107406940A (zh) | 2017-11-28 |
CA2975366A1 (en) | 2016-09-15 |
EP3246427A1 (en) | 2017-11-22 |
RU2667943C1 (ru) | 2018-09-25 |
CN107406940B (zh) | 2019-05-07 |
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