WO2013099192A1 - Feuille d'acier laminée à chaud à haute résistance et son procédé de fabrication - Google Patents

Feuille d'acier laminée à chaud à haute résistance et son procédé de fabrication Download PDF

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WO2013099192A1
WO2013099192A1 PCT/JP2012/008211 JP2012008211W WO2013099192A1 WO 2013099192 A1 WO2013099192 A1 WO 2013099192A1 JP 2012008211 W JP2012008211 W JP 2012008211W WO 2013099192 A1 WO2013099192 A1 WO 2013099192A1
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steel sheet
hot
composition
phase
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WO2013099192A8 (fr
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博士 中田
友彰 柴田
力 上
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Ｊｆｅスチール株式会社
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Priority to KR1020147018457A priority Critical patent/KR101664635B1/ko
Priority to EP12863451.6A priority patent/EP2799575B1/fr
Priority to CN201280065034.8A priority patent/CN104011245B/zh
Priority to JP2013551228A priority patent/JP5812115B2/ja
Priority to IN1252KON2014 priority patent/IN2014KN01252A/en
Priority to US14/368,857 priority patent/US20140352852A1/en
Publication of WO2013099192A1 publication Critical patent/WO2013099192A1/fr
Publication of WO2013099192A8 publication Critical patent/WO2013099192A8/fr

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • C—CHEMISTRY; METALLURGY
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
    • C21D8/105—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies of ferrous alloys
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/003—Cementite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite

Definitions

  • the present invention is for welded steel pipes that require high strength and high toughness, especially for transport pipes (line pipes) for transporting crude oil, natural gas, etc., and for oil well pipes, especially for high strength ERW steel pipes and high strength spiral steel pipes.
  • the present invention relates to a high-strength hot-rolled steel sheet suitable as a material and a method for producing the same, and particularly relates to a steel sheet having improved deformation characteristics after being pipe-formed (tube-formed).
  • “high-tensile hot-rolled steel sheet” refers to a hot-rolled steel sheet having a high strength of API5L-X65 grade or more and X80 grade or less.
  • high-strength steel pipes are required to have excellent low-temperature toughness as well as high strength from the viewpoint of preventing line pipe breakage.
  • Strengthening by precipitation strengthening using precipitates and toughness by microstructure refinement using controlled rolling have been attempted.
  • Patent Document 1 contains appropriate amounts of C, Si, Mn, and N, further contains Si and Mn in a range where Mn / Si satisfies 5 to 8, and further contains Nb: 0.01 to 0.1%.
  • Patent Document 2 includes C: 0.02 to 0.09%, Si: 0.001 to 0.8%, Mn: 0.5 to 2.5%, and Ti: 0.005 to 0.03%, Nb: 0.005. Including 0.3%, Al: 0.001-0.1%, N: 0.001-0.008%, Ni: 0.1-1.0%, Cu: 0.1-1.0, Mo: 0.05-0.6%, (Ni + Cu)- Aging that is formed by welding a steel sheet having a mixed structure of ferrite with a grain size of 15 ⁇ m or less on average and a balance of martensite and / or bainite, including Mo> 0.5 so as to satisfy Mo> 0.5.
  • a high-strength steel pipe for pipelines having excellent later deformation characteristics is described.
  • This steel pipe is said to be an X-70 to X-100 grade high-strength steel pipe with a uniform elongation after heating at 200 to 300 ° C. of 5% or more and excellent deformation characteristics after aging.
  • Patent Document 2 it is necessary to contain a relatively large amount of alloy elements such as Cu and expensive Ni that cause liquid phase embrittlement during hot rolling, leaving a problem in weldability. It was.
  • the reel barge method has been frequently used for laying submarine line pipes.
  • circumferential welding, inspection, painting, etc. are performed in advance on land, and the resulting long pipe is wound on the reel of a barge ship at sea, and laid on the seabed while rewinding at the target sea. Is the method.
  • tensile and compressive stress due to bending-bending back acts on a part of the pipe when winding the pipe and laying the pipe. For this reason, local buckling arises in a pipe, and there exists a problem that destruction of a pipe arises from it.
  • Patent Document 3 includes C: 0.03 to 0.20%, Si: 0.05 to 0.50%, Mn: 0.50 to 1.5%, Al: 0.005 to 0.060%, and Nb + V + Ti to 0.04% or less.
  • ESR with excellent reel barge laying property with a yield ratio of 85% or less and less weld softening, with a limited composition, carbon equivalent Ceq of 0.20 to 0.35% and weld crack sensitivity index Pcm of 0.25% or less Steel pipes are described. According to the technique described in Patent Document 3, local buckling that occurs in a pipe when a pipeline is laid using a reel barge method can be prevented.
  • Patent Document 4 discloses that a strain having a composition containing C: 0.1% or less and Mn: 2.3% or less is given a strain of 15% or less on the average in the thickness direction before the pipe forming step. A method for producing an electric resistance welded steel pipe, which is subjected to an applying step, is described. Thereby, local buckling at the time of pipe laying can be prevented.
  • the present invention solves the above-mentioned problems of the prior art, has a high strength of API5L-X65 or higher and X80 or lower, and has a high toughness with a fracture surface transition temperature vTrs of ⁇ 80 ° C. or lower in the Charpy impact test.
  • Another object of the present invention is to provide a high-tensile hot-rolled steel sheet having excellent deformation characteristics such that the uniform elongation at the center in the sheet thickness direction is 10% or more and excellent deformation characteristics after tube forming.
  • excellent deformation characteristics after tube forming as used herein means that the surface layer portion has a uniform elongation of 10 in a tensile test using a JIS No.
  • the paint bake-hardening amount ⁇ YS after coating bake-hardening treatment heated at 250 ° C x 60 min is 40MPa or less. Further, it means that the occurrence of yield elongation is suppressed after the tube forming-paint baking process, and when the tube is subjected to bending deformation, it has a deformation characteristic capable of suppressing the occurrence of local buckling.
  • the present inventors diligently studied various factors that affect the deformation characteristics, particularly the occurrence of yield elongation, after being subjected to paint baking as a pipe.
  • Cr and Nb, Ti, V are essential, the total amount of Nb, Ti, V is adjusted to an appropriate range, and the structure of the surface layer part is bainite as the main phase and a small amount as the second phase.
  • the surface layer has a uniform deformation at a high elongation of 10% or more, and after applying 2% pre-strain, heat treatment (paint baking treatment) is performed at 250 ° C x 60 min.
  • the gist of the present invention is as follows. (1) By mass%, C: 0.04 to 0.08%, Si: 0.50% or less, Mn: 0.8 to 2.2%, P: 0.02% or less, S: 0.006% or less, Al: 0.1% or less, N: 0.008% or less Cr: 0.05 to 0.8%, Nb: 0.01 to 0.08%, V: 0.001 to 0.12%, Ti: 0.005 to 0.04%, the following formula (1): 0.05 ⁇ Nb + V + Ti ⁇ 0.20 (1) (Here, Nb, V, and Ti indicate the content (mass%) in the steel.) And the balance is composed of Fe and inevitable impurities, the surface layer is bainite as the main phase, and the volume ratio of 0.5 to 4% martensite as the second phase, and A high-tensile hot-rolled steel sheet having a structure containing, as a third phase, one or more selected from ferrite phase, pearlite, and cement
  • the central portion of the steel sheet has bainite as the main phase, martensite at a volume ratio of 0.5 to 4% as the second phase, and a total volume ratio of 20% or less.
  • a high-tensile hot-rolled steel sheet having a structure containing one or more selected from a ferrite phase, pearlite, and cementite as a third phase and having a uniform elongation of 10% or more.
  • the composition further contains one or two kinds selected from Zr: 0.04% or less and Ta: 0.07% or less in mass%.
  • Zr 0.04% or less
  • Ta 0.07% or less in mass%.
  • the composition further contains one or two kinds selected from Ca: 0.005% or less and REM: 0.005% or less by mass%.
  • the steel material is heated and then hot-rolled to form a hot-rolled sheet. Immediately after the hot-rolling, the hot-rolled sheet is subjected to accelerated cooling and then coiled at a coiling temperature.
  • a method for producing a rolled steel sheet wherein the steel material is, in mass%, C: 0.04 to 0.08%, Si: 0.50% or less, Mn: 0.8 to 2.2%, P: 0.02% or less, S: 0.006% or less, Al: 0.1% or less, N: 0.008% or less, Cr: 0.05 to 0.8%, Nb: 0.01 to 0.08%, V: 0.001 to 0.12%, Ti: 0.005 to 0.04%, the following formula (1): 0.05 ⁇ Nb + V + Ti ⁇ 0.20 (1) (Here, Nb, V, and Ti indicate the content (mass%) in the steel.) And the balance is composed of Fe and inevitable impurities, the heating of the steel material is set to a temperature in the range of 1100 to 1250 ° C., and the
  • the composition further comprises one or two selected from the group consisting of Zr: 0.04% or less and Ta: 0.07% or less in mass%.
  • Zr 0.04% or less
  • Ta 0.07% or less in mass%.
  • the composition further contains one or two kinds selected from Ca: 0.005% or less and REM: 0.005% or less by mass%.
  • a high-tensile hot-rolled steel sheet that does not cause local buckling when subjected to bending deformation as a steel pipe, has excellent deformation characteristics after pipe forming, and is suitable for line pipes and oil well pipes. Can be manufactured at a low cost, and has a remarkable industrial effect.
  • the high-tensile hot-rolled steel sheet of the present invention has a high strength of API5L-X65 grade or more and X80 grade or less, and is suitable for line pipes and oil well pipes, and has excellent deformation characteristics after pipe forming (piping). Is a hot-rolled steel sheet that can be manufactured.
  • C 0.04-0.08% C is an element having an effect of increasing the strength of steel, and in the present invention, it is necessary to contain 0.04% or more in order to ensure a desired strength. On the other hand, when it contains more than 0.08%, the toughness of the base metal and the weld heat affected zone toughness are lowered. For this reason, C is limited to the range of 0.04 to 0.08%. Note that the content is preferably 0.05 to 0.07%.
  • Si 0.50% or less
  • Si is an element that acts as a deoxidizer, and such an effect is recognized when the content is 0.01% or more. Moreover, Si forms an oxide containing Si during ERW welding, lowers the weld zone quality, and lowers the weld heat affected zone toughness. From this point of view, it is desirable to reduce Si as much as possible, but it is acceptable up to 0.50%. For these reasons, Si is limited to 0.50% or less. In addition, Preferably it is 0.40% or less.
  • Mn 0.8-2.2%
  • Mn is an element that improves the hardenability and contributes to an increase in the strength of the steel sheet through the improvement of the hardenability. Further, Mn forms MnS and fixes S, thereby preventing S grain boundary segregation and suppressing slab cracking. In order to obtain such an effect, the content of 0.8% or more is required. On the other hand, an excessive content exceeding 2.2% promotes segregation during solidification, leaves Mn-concentrated portions in the steel sheet, and increases the occurrence of separation. For this reason, Mn was limited to the range of 0.8 to 2.2%. Note that the content is preferably 0.9 to 2.1%.
  • P 0.02% or less
  • P has an effect of increasing the strength of steel, but has a strong segregation tendency and lowers toughness. Therefore, in the present invention, it is desirable to reduce P as much as possible, but it is acceptable up to 0.02%. Therefore, P is limited to 0.02% or less. In addition, Preferably it is 0.016% or less.
  • S 0.006% or less S is present as an inclusion (sulfide) in steel, and has an adverse effect on reducing ductility and toughness. For this reason, it is desirable to reduce S as much as possible, but it is acceptable up to 0.006%. For these reasons, S is limited to 0.006% or less. In addition, Preferably it is 0.004% or less.
  • Al 0.1% or less Al is an element that acts as a deoxidizer, and in order to obtain such an effect, 0.001% or more is desirable. On the other hand, a content exceeding 0.1% significantly impairs the cleanliness of the welded part during ERW welding. For this reason, Al was limited to 0.1% or less.
  • N 0.008% or less N is an element inevitably contained, but excessive inclusion frequently causes cracks during slab casting.
  • solute N causes aging and increases yield strength (paint bake hardening) during paint baking, so it is desirable to reduce it as much as possible. For these reasons, N is limited to 0.008% or less.
  • Cr 0.05-0.8% Cr is an element that has the effect of improving the hardenability and increasing the strength of the steel sheet, and Cr has the effect of suppressing the occurrence of yield elongation after the coating baking process. In order to acquire such an effect, 0.05% or more of content is required. On the other hand, if it exceeds 0.8%, the strength becomes too high and the ductility and toughness are lowered. Therefore, Cr is limited to the range of 0.05 to 0.8%. Preferably, the content is 0.3 to 0.5%.
  • Nb 0.01-0.08%
  • Nb is an element that has the action of suppressing the austenite grain boundary movement and suppressing the austenite grain coarsening and recrystallization. Moreover, Nb has the effect
  • V 0.001 to 0.12%
  • Ti 0.005-0.04%
  • Ti has the effect of increasing the strength of the steel sheet by fine precipitation as carbonitride. Ti also fixes C and N, suppresses the occurrence of yield elongation after paint baking, and improves the deformation characteristics after tube forming. In order to acquire such an effect, 0.005% or more of content is required. On the other hand, if the content exceeds 0.04%, weldability decreases. For this reason, Ti is limited to the range of 0.005 to 0.04%.
  • Nb, V, and Ti are contained within the above-described range and adjusted to satisfy the following formula (1).
  • 0.05 ⁇ Nb + V + Ti ⁇ 0.20 (1) (Nb, V, Ti: content (mass%)) If the total content of Nb, V, and Ti is less than 0.05%, the desired high strength cannot be ensured, and the occurrence of yield elongation after paint baking cannot be suppressed. On the other hand, when the content exceeds 0.20%, the ductility and toughness deteriorate significantly. For these reasons, Nb, V, and Ti are adjusted and contained so as to satisfy the expression (1).
  • the above components are the basic components, and in addition to these basic compositions, the elements selected from Mo: 0.3% or less, Cu: 0.5% or less, Ni: 0.5% or less, B: 0.001% or less are selected.
  • One or two or more selected from Zr: 0.04% or less, Ta: 0.07% or less, and / or Ca: 0.005% or less, REM: 0.005% or less 1 type or 2 types chosen from can be selected and contained as needed.
  • Mo 0.3% or less
  • Cu 0.5% or less
  • Ni 0.5% or less
  • B One or more selected from 0.001% or less Mo, Cu, Ni, and B all increase the strength of the steel sheet.
  • it can select from Mo, Cu, Ni, and B, and can select and contain 1 type, or 2 or more types as needed.
  • Mo has an effect of increasing the strength of the steel sheet through the improvement of hardenability, and contributes to an increase in the strength of the steel sheet by being finely precipitated as carbonitride.
  • Mo has the effect
  • the content exceeding 0.3% lowers the weldability. For this reason, when it contains, it is preferable to limit Mo to 0.3% or less. Further, Cu dissolves or precipitates to increase the steel sheet strength. In order to acquire such an effect, it is desirable to contain 0.05% or more. On the other hand, if the content exceeds 0.5%, the surface quality of the steel sheet may be deteriorated. For this reason, when it contains, it is preferable to limit Cu to 0.5% or less. Ni also dissolves to increase the strength of the steel sheet and contributes to improving the toughness of the steel sheet. In order to acquire such an effect, it is desirable to contain 0.05% or more. On the other hand, if the content exceeds 0.5%, the production cost increases.
  • Ni when contained, Ni is preferably limited to 0.5% or less.
  • B when contained in a small amount, significantly improves the hardenability and contributes to an increase in steel sheet strength. Such an effect becomes remarkable when the content is 0.0003% or more, but even if the content exceeds 0.001%, the effect is saturated. For these reasons, when it is contained, it is preferably limited to 0.001% or less.
  • Zr 0.04% or less
  • Ta 0.07% or less Zr
  • Ta is an element that has the effect of increasing the steel sheet by fine precipitation as carbonitrides. Can be selected and contained. In order to obtain such an effect, it is desirable to contain Zr: 0.005% or more and Ta: 0.01% or more, but if it contains more than Zr: 0.04%, Ta: 0.07%, the weldability is lowered. For this reason, when it contains, it is preferable to limit to Zr: 0.04% or less and Ta: 0.07% or less.
  • Ca 0.005% or less
  • REM 0.005% or less
  • Both Ca and REM contribute to the control of the morphology of the sulfide with the expanded coarse sulfide as a spherical sulfide. It is an element that can be selected and contained as necessary. In order to obtain such an effect, it is desirable to contain Ca: 0.001% or more, REM: 0.001% or more, but if it contains a large amount exceeding Ca: 0.005% and REM: 0.005%, respectively, the cleanliness of the steel sheet Reduce. For this reason, it is preferable to limit Ca to 0.005% or less and REM to 0.005% or less.
  • the balance other than the above-described composition components is composed of Fe and inevitable impurities.
  • the high-tensile hot-rolled steel sheet of the present invention includes a surface layer of the steel sheet containing bainite as a main phase and martensite at a volume ratio of 0.5 to 4% as a second phase.
  • a three-phase it has a structure containing at least one of ferrite, pearlite, and cementite in a total volume ratio of 10% or less.
  • the “main phase” means a phase occupying 50% or more, preferably 80% or more by volume ratio.
  • the “surface layer” here refers to a region from the steel plate surface to 2 mm in the plate thickness direction.
  • the structure of the surface layer of the steel sheet By making the structure of the surface layer of the steel sheet a structure containing bainite as the main phase and martensite at a volume ratio of 0.5 to 4% as the second phase, excellent deformation characteristics with a uniform elongation of preferably 10% or more are preferable. You will be able to have Furthermore, even if paint baking is performed after pipe forming, the amount of curing is small, and after paint baking, yield elongation can be suppressed, and buckling does not occur even if the pipe is bent. It becomes a steel pipe with excellent properties.
  • the “bainite” here includes bainite and bainitic ferrite.
  • the yield ratio is reduced, the deformation characteristics after pipe forming are improved, and the amount of hardening during the coating baking process can be reduced.
  • the occurrence of yield elongation can be suppressed.
  • the third phase other than bainite and martensite may include one or more selected from ferrite phase, pearlite, and cementite. These are preferably as small as possible in order to reduce the uniform elongation, but are acceptable if the total volume ratio is 10% or less.
  • the central portion of the steel sheet preferably has bainite as the main phase, martensite at a volume ratio of 0.5 to 4% as the second phase, and a ferrite phase or pearlite with a total volume ratio of 20% or less. And having a structure containing at least one selected from cementite as the third phase.
  • the structure of the steel plate thickness central part of the steel sheet into a structure containing bainite as the main phase and martensite as the second phase in the volume ratio of 0.5 to 4%, it has both high strength and high toughness. Can be made. Specifically, a uniform elongation of 10% or more can be realized while having high strength.
  • the “plate thickness central portion” refers to a portion other than the surface layer.
  • the third phase other than bainite and martensite may include one or more selected from ferrite phase, pearlite, and cementite. These are preferably as small as possible in order to reduce the strength and toughness, but are preferably 20% or less in terms of the total volume ratio.
  • a steel material having the above-described composition is used as a starting material.
  • the method for producing the steel material is not particularly limited, and any generally known melting method such as a converter can be applied.
  • the melted steel can be applied to any generally known casting method such as a continuous casting method, and can be cast on a steel material such as a slab.
  • the obtained steel material is then reheated.
  • the steel material is reheated at a temperature in the range of 1100 to 1250 ° C.
  • the reheating temperature is less than 1100 ° C.
  • the amount of increase in strength due to the solid solution of Nb and precipitation after rolling is reduced, and it becomes difficult to secure a desired high strength.
  • the heating temperature of the steel material is preferably limited to the range of 1100 to 1250 ° C.
  • the steel raw material has the heat which can ensure the temperature of the above-mentioned range, you may perform hot rolling, without reheating or through a short time heating furnace holding
  • finish rolling is rolling in which the cumulative rolling reduction in a temperature range of 930 ° C. or lower is 50% or higher and the finish rolling finish temperature is 760 ° C. or higher. If the cumulative rolling reduction in a temperature range of 930 ° C. or lower (non-recrystallization temperature range) is less than 50%, crystal grain refinement cannot be achieved, and desired high toughness cannot be ensured. In addition, Preferably it is 85% or less.
  • the cumulative rolling reduction in the non-recrystallization temperature range is 50% or more, preferably 85% or less.
  • the finish rolling finish temperature is less than 760 ° C.
  • the austenite ⁇ ferrite transformation proceeds particularly in the surface layer, and the surface layer structure cannot be made a structure having a desired bainite phase as the main phase, and the desired high toughness is achieved. It cannot be secured.
  • it is 870 degrees C or less.
  • the finish rolling finish temperature exceeds 870 ° C., the structure cannot be refined and the toughness is lowered. Therefore, the finish rolling finish temperature is limited to 760 ° C. or higher, preferably 870 ° C. or lower.
  • accelerated cooling is preferably started within 15 s, more preferably within 10 s.
  • Accelerated cooling is performed at an average cooling rate of 7 to 50 ° C / s to the cooling stop temperature, and the cooling is stopped. Thereby, the generation of ferrite phase and pearlite is suppressed, and coarsening of crystal grains can be prevented.
  • the cooling rate is less than 7 ° C./s on average, the ferrite phase is excessively generated, and it becomes difficult to secure desired high strength and high toughness.
  • a large amount of ferrite formed at high temperature is formed, it becomes difficult to form a fine bainite phase.
  • a martensite phase is easily formed, and a desired structure having a bainite phase as a main phase is hardly formed. For this reason, the cooling rate of accelerated cooling was limited to the range of 7 to 50 ° C./s on average. In addition, Preferably it is 20 degrees C / s or less.
  • the cooling stop temperature for accelerated cooling shall be in the range of 550 ° C or higher (SCT + 30 ° C) or lower.
  • SCT + 30 ° C The cooling stop temperature for accelerated cooling shall be in the range of 550 ° C or higher (SCT + 30 ° C) or lower.
  • a cooling treatment or a slow cooling treatment in which the residence time in the temperature range of (SCT ⁇ 20 ° C.) to (SCT + 30 ° C.) is 10 to 60 seconds.
  • the residence time in the above temperature range is less than 10 s, recuperation is insufficient and the surface martensite amount is insufficient.
  • bainite grows and the toughness decreases, and the productivity of the steel sheet decreases.
  • the period from the accelerated cooling stop to the winding is set as a cooling treatment or a slow cooling treatment in which the residence time in the temperature range of (SCT ⁇ 20 ° C.) to (SCT + 30 ° C.) is 10 to 60 s.
  • the coiling temperature should be 430 ° C or higher (SCT-50 ° C) or lower.
  • SCT-50 ° C the diffusion of C is suppressed, and the martensite phase is not generated in the bainite that is the main phase.
  • the temperature exceeds (SCT-50 ° C)
  • pearlite is generated and a desired structure cannot be generated.
  • Molten steel having the composition shown in Table 1 was melted in a converter and made into a slab (wall thickness: 220 mm) by a continuous casting method. These slabs are heated to 1200 ° C., subjected to hot rolling consisting of rough rolling and finish rolling under the conditions shown in Table 2, and then subjected to accelerated cooling and cooling treatment under the cooling conditions shown in Table 2 after finishing rolling. These were wound into a coil shape under the conditions shown in Table 2 and allowed to cool to obtain a hot rolled steel sheet (hot rolled steel strip) having a thickness of 12 to 16 mm.
  • Samples are taken from the obtained hot-rolled steel sheet (hot-rolled steel strip) and subjected to structure observation, tensile test, impact test, and tensile test after paint baking treatment, and the structure, tensile properties, toughness, paint baking treatment Later tensile properties were evaluated.
  • the evaluation method is as follows.
  • Microstructure observation A specimen for microstructural observation is collected from the obtained hot-rolled steel sheet, the cross section in the rolling direction is polished and corroded, and an optical microscope (magnification: 1000 times) or a scanning electron microscope (magnification: 1000 times). Then, at least 5 fields of view were observed at the surface layer (position 1 mm from the surface) and the center position of the plate thickness and imaged. About the obtained structure
  • the tensile test piece in the surface layer (region from the surface to 2 mm in the plate thickness direction) was sampled so that the position of 1 mm from the surface was the central position in the thickness direction, and the thickness of the test piece was set to 1.6 mm. .
  • the tensile test piece at the center position of the plate thickness was prepared by removing the surface layer (region from the surface to 2 mm in the plate thickness direction) by cutting so that the center position of the plate thickness becomes the center position in the thickness direction. Table 4 shows the obtained results.
  • each of the inventive examples has a structure having a bainite phase as a main phase, a yield strength YS: high strength of X65 class of 450 MPa or more, and vTrs of ⁇ 80 ° C. or less. It has high toughness, exhibits excellent deformation characteristics with a uniform elongation of 10% or more at the surface layer and in the center in the plate thickness direction, and yield elongation has been observed even after paint baking.
  • the paint bake hardening amount was 40MPa or less, and the steel was also low in paint bake hardenability.
  • the comparative example out of the scope of the present invention is insufficient in strength, has reduced toughness, has deteriorated elongation characteristics, or has yield elongation, as a high-strength hot-rolled steel sheet for line pipes. Desired characteristics are not secured.
  • the hot-rolled steel sheet of the present invention example was made into an electric-welded steel pipe by cold forming using a roll, and further subjected to reduction rolling to obtain a steel pipe having an outer diameter of 406 mm ⁇ .
  • a tensile strain tube making strain
  • the obtained ERW steel pipe was further subjected to heat treatment at 250 ° C. for 60 minutes.
  • an arc-shaped tensile test piece with the pipe axis direction as the tensile direction was collected, and a tensile test was carried out according to the API-5L standard.
  • These steel pipes are steel pipes in which the occurrence of buckling is suppressed even when subjected to bending.

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Abstract

La présente invention a pour but de proposer une feuille d'acier laminée à chaud à haute résistance qui ne présente pas de voilage local lorsqu'elle est façonnée en un tuyau d'acier et est déformée par pliage, présente d'excellentes caractéristiques de déformation après avoir été façonnée en un tuyau, et est utilisable de manière appropriée comme tuyaux de canalisation et tuyaux pour puits de pétrole. La constitution de la présente invention est une composition comprenant, en % en masse, 0,04 - 0,08 % de C, pas plus de 0,50 % de Si, 0,8 - 2,2 % de Mn, pas plus de 0,02 % de P, pas plus de 0,006 % de S, pas plus de 0,1 % d'Al, pas plus de 0,008 % de N, 0,05 - 0,8 % de Cr, 0,01 - 0,08 % de Nb, 0,001 - 0,12 % de V, et 0,005 - 0,04 % de Ti, les teneurs de Nb, V et Ti étant réglées de façon à satisfaire un besoin défini, le reste étant composé de Fe et des impuretés inévitables, caractérisée en ce qu'une couche de surface a une structure comprenant de la bainite comme phase primaire, 0,5 - 4 % en volume de martensite comme phase secondaire, et pas plus de 10 % en volume au total d'un ou plusieurs éléments choisis parmi une phase de ferrite, de la perlite et de la cémentite comme phase tertiaire.
PCT/JP2012/008211 2011-12-27 2012-12-21 Feuille d'acier laminée à chaud à haute résistance et son procédé de fabrication WO2013099192A1 (fr)

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EP12863451.6A EP2799575B1 (fr) 2011-12-27 2012-12-21 Feuille d'acier laminée à chaud à haute résistance et son procédé de fabrication
CN201280065034.8A CN104011245B (zh) 2011-12-27 2012-12-21 高张力热轧钢板及其制造方法
JP2013551228A JP5812115B2 (ja) 2011-12-27 2012-12-21 高張力熱延鋼板及びその製造方法
IN1252KON2014 IN2014KN01252A (fr) 2011-12-27 2012-12-21
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JPWO2021200402A1 (fr) * 2020-04-02 2021-10-07
CN115362273B (zh) * 2020-04-02 2023-12-08 杰富意钢铁株式会社 电阻焊钢管及其制造方法
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US20140352852A1 (en) 2014-12-04
KR20140099321A (ko) 2014-08-11
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EP2799575A1 (fr) 2014-11-05
KR101664635B1 (ko) 2016-10-10
JPWO2013099192A1 (ja) 2015-04-30
EP2799575A4 (fr) 2015-10-28
CN104011245B (zh) 2017-03-01
IN2014KN01252A (fr) 2015-10-16
JP5812115B2 (ja) 2015-11-11
EP2799575B1 (fr) 2016-12-21

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