WO2009119570A1 - Tube d'acier uoe pour tubes de canalisation et son procédé de fabrication - Google Patents

Tube d'acier uoe pour tubes de canalisation et son procédé de fabrication Download PDF

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Publication number
WO2009119570A1
WO2009119570A1 PCT/JP2009/055803 JP2009055803W WO2009119570A1 WO 2009119570 A1 WO2009119570 A1 WO 2009119570A1 JP 2009055803 W JP2009055803 W JP 2009055803W WO 2009119570 A1 WO2009119570 A1 WO 2009119570A1
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uoe steel
steel pipe
uoe
stress
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PCT/JP2009/055803
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English (en)
Japanese (ja)
Inventor
出 湊
伸彰 高橋
昭夫 山本
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住友金属工業株式会社
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Publication of WO2009119570A1 publication Critical patent/WO2009119570A1/fr

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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C37/00—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
    • B21C37/06—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of tubes or metal hoses; Combined procedures for making tubes, e.g. for making multi-wall tubes
    • B21C37/08—Making tubes with welded or soldered seams
    • B21C37/0815—Making tubes with welded or soldered seams without continuous longitudinal movement of the sheet during the bending operation
    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/02—Modifying the physical properties of iron or steel by deformation by cold working
    • C21D7/10—Modifying the physical properties of iron or steel by deformation by cold working of the whole cross-section, e.g. of concrete reinforcing bars
    • C21D7/12—Modifying the physical properties of iron or steel by deformation by cold working of the whole cross-section, e.g. of concrete reinforcing bars by expanding tubular bodies
    • 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
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
    • 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
    • C22C38/02—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
    • C22C38/18—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
    • C21D2211/004—Dispersions; Precipitations
    • 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

Definitions

  • This invention relates to the UOE steel pipe for line pipes, and its manufacturing method.
  • the present invention is a line pipe of X70 grade or more (pipe axis direction strength of 485 MPa or more) excellent in earthquake resistance, which is designed by a strain-based design and is used in cold regions such as Canada.
  • the present invention relates to a UOE steel pipe for use and a manufacturing method thereof.
  • UOE steel pipes composing line pipes laid in cold regions such as Canada are deformed by tensile stress acting in the axial direction as frozen soil (ground) repeatedly expands and contracts due to seasonal temperature fluctuations. There is concern. In particular, it is absolutely necessary to prevent major accidents from occurring due to the destruction of long-distance pipelines that transport natural gas and oil. For this reason, in order to apply a high-strength UOE steel pipe to a pipeline, the high-strength UOE steel pipe needs to have higher fracture safety than a conventional strength UOE steel pipe.
  • the high-strength UOE steel pipe that constitutes a line pipe used particularly in cold regions is excellent not only in strength but also in earthquake resistance evaluated by deformability (for example, yield ratio and uniform elongation) against fracture deformation. Is required.
  • a high-strength UOE steel pipe for a line pipe used in a cold region is designed based on stress design that emphasizes not only strength but also yield ratio and uniform elongation, for example.
  • Patent Document 1 and Patent Document 2 as a steel pipe excellent in earthquake resistance
  • Patent Document 3 as a method of manufacturing a line pipe having high strength, high toughness and excellent earthquake resistance
  • both UOE steel pipes are used. It is disclosed that having a round-shaped stress-strain curve with no yield point improves seismic resistance.
  • Patent Document 4 discloses that a steel pipe excellent in earthquake resistance is manufactured on a trial basis by cooling after rolling. JP-A-9-196243 Japanese Patent Laid-Open No. 11-80900 Japanese Patent Laid-Open No. 9-202922 JP 2004-131810 A
  • all pipeline UOE steel pipes are typically 150 ° C or higher and 250 ° C or lower by high-frequency heating, for example, at the site where they are laid, in order to prevent damage during construction and external corrosion during operation.
  • An external coating is applied with a heat treatment that is held at temperature for about 5 minutes (referred to herein as “pre-coating heat-treatment”).
  • the shape of the stress-strain curve of a UOE steel pipe after pipe making is always Round House type because many cold strains are imparted to the UOE steel pipe. Therefore, in order to improve the earthquake resistance of the UOE steel pipe, the stress-strain curve after the pre-coating heat treatment can maintain the Round House type stress-strain curve without changing to the Yield Point type having the upper yield point. At the same time, a low yield ratio can be achieved.
  • the inventors of the present invention among various factors that affect the earthquake resistance of high-strength UOE steel pipes (UOE steel pipe dimensions, yield ratio, uniform elongation, and stress-strain curve shape, etc.)
  • the present inventors have intensively studied means for maintaining the Round House type in which the shape of the stress-strain curve after the heat treatment does not have an upper yield point.
  • the inventors have (A) Controlling the content ratio (Ti / N) of each of Ti and N in the UOE steel pipe to an appropriate value, and (b) accelerating after rolling is completed in the production stage of the rolled steel sheet as the base material By reducing the free N that fixes dislocations by cooling, and manufacturing the UOE steel pipe by the UOE pipe manufacturing method using this rolled steel sheet as a raw material, the stress of the Round House type shape even after the pre-coating heat treatment is performed. -The inventors have found that high strength UOE steel pipes with strain curves can be produced and have completed the present invention.
  • C 0.03% or more and 0.10% or less (unless otherwise specified, “%” in terms of composition means “mass%”), Si: 0.05% or more and 0 50% or less, Mn: 1.50% or more and 2.2% or less, P: 0.025% or less, S: 0.002% or less, Cu: 1.0% or less, Cr: 1.0% or less, Ni: 2.0% or less, Mo: 1.0% or less, Nb: 0.1% or less, V: 0.1% or less, Ti: 0.025% or less, Al: 0.06% or less, N: 0.0050% or less, Ca: 0.0050% or less, and ratio of Ti and N content (Ti / N): 4.0 or more, having a steel composition composed of the balance Fe and impurities. More desirably, the circumferential strength is 550 MPa or more, X70 grade or more (pipe axis direction strength 485MPa or more) UOE steel pipe for line pipe.
  • the present invention provides C: 0.03% to 0.10%, Si: 0.05% to 0.50%, Mn: 1.50% to 2.2%, P : 0.025% or less, S: 0.002% or less, Cu: 1.0% or less, Cr: 1.0% or less, Ni: 2.0% or less, Mo: 1.0% or less, Nb: 0 0.1% or less, V: 0.1% or less, Ti: 0.025% or less, Al: 0.06% or less, N: 0.0050% or less, Ca: 0.0050% or less, and Ti The ratio of Ti and N content (Ti / N): 4.0 or more, and immediately after rolling at a finishing temperature of 700 ° C. or higher and 850 ° C.
  • the content ratio (Ti / N) of each of Ti and N in the UOE steel pipe is set to an appropriate range, and accelerated cooling is performed after the hot rolling of the rolled steel sheet that is the material of the UOE steel pipe is finished.
  • free N for fixing dislocations can be reduced, and a metal structure composed of ferrite and bainite or a metal structure composed of ferrite, bainite, and martensite can be desirably formed.
  • the stress-strain curve of the Round House type shape can be maintained even after the pre-coating heat treatment while reducing the yield ratio of the UOE steel pipe. It is possible to provide a high-strength UOE steel pipe for line pipe.
  • C 0.03% to 0.10%
  • C is an element effective for increasing the strength, and is contained in an amount of 0.03% or more in order to have strength of X70 grade or higher, particularly X100 grade.
  • C content if the C content exceeds 0.10%, the toughness is significantly lowered, which adversely affects the mechanical properties of the base material and promotes the occurrence of surface scratches on the slab. For this reason, C content shall be 0.03% or more and 0.10% or less.
  • Si 0.05% to 0.50%
  • Si acts as a deoxidizer and as a component for strengthening steel.
  • the Si content is limited to 0.05% or more and 0.50% or less.
  • the Si content is preferably determined in consideration of the balance with the plate thickness. (Mn: 1.50% or more and 2.2% or less) By containing 1.50% or more, Mn strengthens and strengthens steel. However, if the Mn content exceeds 2.2%, the toughness of the welded portion deteriorates. Therefore, the Mn content is 1.50% or more and 2.2% or less.
  • P 0.025% or less
  • P is an impurity contained in steel, and its content is preferably low. However, extreme reduction is accompanied by a corresponding increase in manufacturing costs. Therefore, the P content is 0.025% or less.
  • S 0.002% or less
  • S exceeds 0.002%, the target toughness of the base material cannot be secured. Therefore, the S content is set to 0.002% or less.
  • Cu 1.0% or less
  • Cu is desirably contained in an amount of 0.01% or more, it exerts an effect of strengthening without greatly impairing toughness due to solid solution strengthening and structural change due to the effect of increasing hardenability.
  • the Cu content exceeds 1.0%, Cu checking that is harmful to the surface defects of the slab occurs, which necessitates low-temperature heating of the slab, and increases the restrictions on the manufacturing conditions. Therefore, the Cu content is 1.0% or less.
  • Cr 1.0% or less
  • Cr like Cu and Ni, desirably contains 0.01% or more, thereby exerting an effect of strengthening without greatly impairing toughness due to solid solution strengthening and structural change due to the effect of increasing hardenability.
  • the Cr content exceeds 1.0%, the toughness of the heat-affected zone is lowered. Therefore, the Cr content is 1.0% or less.
  • Ni like Cu, desirably contains 0.01% or more, thereby exerting an effect of strengthening without greatly impairing toughness due to solid solution strengthening and structural change due to the effect of increasing hardenability. At the same time, it exerts an effect of suppressing deterioration of the toughness of the base material and the heat-affected zone after hot bending.
  • the Ni content is set to 2.0% or less.
  • Mo 1.0% or less
  • Mo is desirably contained in an amount of 0.01% or more, it is effective for increasing the strength of the base material and the welded portion.
  • the Mo content exceeds 1.0%, the circumferential weldability at the construction site and the toughness of the heat affected zone are deteriorated. Therefore, the Mo content is 1.0% or less.
  • Nb and Ti both have a great effect on the increase in strength due to precipitation strengthening and hardenability increasing effects, or on the improvement of toughness accompanying crystal grain refinement.
  • the Nb content exceeds 0.1% or the V content exceeds 0.1%, the toughness of the welded portion decreases. Therefore, the Nb content is 0.1% or less, and the V content is 0.1% or less.
  • Ti 0.025% or less
  • Al 0.06% or less
  • Al has an effect as a deoxidizing material, but is preferably contained in an amount of 0.010% or more for complete grain sizing.
  • Al content is set to 0.06% or less.
  • N 0.0050% or less
  • N forms nitrides with V, Ti, etc., and brings about an effect of improving high temperature strength.
  • N content exceeds 0.0050%, Nb, V, Ti and carbonitride are formed, and the toughness of the base material and the heat-affected zone is lowered.
  • the N content is 0.0050% or less.
  • the N content is preferably 0.0035% or less.
  • Ca is effective in controlling the form of inclusions, specifically in spheroidization, and prevents hydrogen-induced cracking and lamellar tear.
  • the Ca content is set to 0.0050% or less.
  • the Ca content is closely related to the S content, and when the S content is 0.0010% or more, it is 0.0005% or more due to the spheroidization of MnS inclusions. Is desirable.
  • the lower limit of the Ca content is not particularly required to be set. For these reasons, the Ca content is set to 0.0050% or less.
  • FIG. 1 is a graph showing changes in the stress-strain curve before and after the pre-coating heat treatment. Case 1 in FIG.
  • Case 1 is based on the conditions that the finishing temperature is 800 ° C. and the cooling rate after rolling is 20 ° C./sec.
  • 2 shows a stress-strain curve after heat treatment before coating at 200 ° C. for a UOE steel pipe made of the produced rolled steel sheet.
  • Case 2 is a rolled product manufactured under the conditions of a finishing temperature of 800 ° C. and a cooling rate of 20 ° C./sec after rolling. 2 shows a stress-strain curve of a UOE steel pipe made of a steel plate after heat treatment before coating at 270 ° C.
  • both cases 1 and 2 have Round House type stress-strain curves.
  • heat treatment before coating is performed.
  • the shape of the stress-strain curve after the heat treatment before coating in the case 2 that satisfies the conditions specified in the present invention is maintained in the Round House type while the shape of the stress-strain curve after that changes to the Yield Point type.
  • the stress after the pre-coating heat treatment is performed with particular attention to the shape of the stress-strain curve.
  • C or N which is an element that fixes dislocations, and among these, attention was focused on the ratio of Ti and N content (Ti / N).
  • FIG. 2 is a graph showing the influence of (Ti / N) on the relationship between stress and strain in a tensile test in the L direction of a test piece.
  • the slab having the steel composition described above is rolled at a cooling rate of 3 ° C./sec to 30 ° C./sec immediately after rolling at a finishing temperature of 700 ° C. or more and 850 ° C. or less according to a conventional method.
  • a rolled steel sheet is obtained.
  • the rolled steel sheet has a metal structure composed of ferrite and bainite or a metal structure composed of ferrite, bainite and martensite.
  • a UOE steel pipe is manufactured using the rolled steel plate manufactured in this way as a raw material using the well-known UOE pipe manufacturing method.
  • a rolled steel sheet which is a material, is U-pressed and formed into a U shape, further O-pressed into an O shape and formed into a cylindrical shape, and then a seam at the end. Butt and weld.
  • this is the surrounding pipe making method, and further explanation regarding the UOE pipe making method is omitted.
  • C 0.03% to 0.10%
  • Si 0.05% to 0.50%
  • Mn 1.50% to 2.2%
  • P 0.025% or less
  • S 0.002% or less
  • Cu 1.0% or less
  • Cr 1.0% or less
  • Ni 2.0% or less
  • Mo 1.0% or less
  • Nb 0.0.
  • Ti 0.025% or less
  • Al 0.06% or less
  • N 0.0050% or less
  • Ca 0.0050% or less
  • the ratio (Ti / N) is limited to an appropriate range, and accelerated cooling is performed after hot rolling of the rolled steel sheet that is the material of the UOE steel pipe, thereby reducing free N and desirably
  • a metal structure consisting of ferrite and bainite or a metal structure consisting of ferrite, bainite and martensite the shape of the stress-strain curve of the UOE steel pipe can be maintained in the Round House type even after heat treatment before coating.
  • the yield ratio YR of the UOE steel pipe can be suppressed to 90% or less, desirably 85% or less. In this way, it is possible to provide a UOE steel pipe for line pipes of X70 grade or higher that is excellent in earthquake resistance.
  • the UOE steel pipe constituting the laid line pipe may be deformed by the tensile stress acting in the axial direction due to repeated expansion and contraction of frozen soil (ground) due to seasonal temperature fluctuations.
  • the earthquake resistance which is a deformability against fracture deformation, is extremely desirable.
  • the tensile test pieces 1 to 7 cut out from these UOE steel pipes were subjected to a heat treatment simulating a pre-coating heat treatment held at 250 ° C. for 5 minutes, and then subjected to a tensile test.
  • the chemical compositions and metal structures of the tensile test pieces 1 to 7 are shown in Table 1, and the rolling finishing temperature and cooling rate of the rolled steel sheet as the material, the mechanical properties of the tensile test pieces 1 to 7 (tensile strength TS, yield strength YS). , Yield ratio YR) and toughness (Charpy impact test absorbed energy vE-10 (° C.)) are shown in Table 2.
  • the shape of the stress-strain curve in the tensile test is shown in graphs in FIGS. 3 (a) to 3 (g).
  • the shape of the stress-strain curve is classified into two types (I) and (II) as shown below, and is important for evaluating the quality of earthquake resistance.
  • (I) Round House type This is the shape of the stress-strain curve that appears in normal UOE steel pipes that are not heat-treated before coating, and shows excellent earthquake resistance.
  • (II) Yield Point type The shape of the stress-strain curve often appears in the UOE steel pipe after the pre-coating heat treatment, which is inferior to the round type in buckling resistance and unsuitable for use in the strain based design.
  • the ratio of Ti and N in the UOE steel pipe (Ti / N) is within an appropriate range, and rolling is the material of the UOE steel pipe. Accelerated cooling is performed after hot rolling of the steel sheet is completed.
  • it can be set as the metal structure which consists of a ferrite and a bainite, or the metal structure which consists of a ferrite, a bainite, and a martensite, and low yield ratio reduction of a UOE steel pipe
  • it has a Round House type stress-strain curve. For this reason, it turns out that the UOE steel pipe for line pipes excellent in earthquake resistance can be provided.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Organic Chemistry (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Steel (AREA)
  • Metal Rolling (AREA)
  • Heat Treatment Of Articles (AREA)

Abstract

L'invention porte sur un tube d'acier UOE à haute résistance présentant une excellente performance sismique. L'invention porte sur un tube d'acier UOE pour tubes de canalisation, qui est doté d’une haute résistance et a une composition d'acier contenant C : 0,03 à 0,10 %, Si : 0,05 à 0,50 %, Mn : 1,50 à 2,2 %, P : 0,025 % ou moins, S : 0,002 % ou moins, Cu : 1,0 % ou moins, Cr : 1,0 % ou moins, Ni : 2,0 % ou moins, Mo : 1,0 % ou moins, Nb : 0,1 % ou moins, V : 0,1 % ou moins, Ti : 0,025 % ou moins, Al : 0,06 % ou moins, N : 0,0050 % ou moins et Ca : 0,0050 % ou moins à un rapport Ti/N supérieur ou égal à 4,0, le reste étant Fe et des impuretés, et qui a soit une structure métallique constituée de ferrite et de bainite soit une structure métallique constituée de ferrite, de bainite et de martensite.
PCT/JP2009/055803 2008-03-25 2009-03-24 Tube d'acier uoe pour tubes de canalisation et son procédé de fabrication WO2009119570A1 (fr)

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JP2008-077985 2008-03-25
JP2008077985A JP2009228099A (ja) 2008-03-25 2008-03-25 ラインパイプ用ｕｏｅ鋼管及びその製造方法

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Cited By (3)

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CN102220547A (zh) * 2011-06-10 2011-10-19 马鞍山钢铁股份有限公司 Ct80级连续油管用钢带及其制备方法
EP3026140A4 (fr) * 2013-07-25 2017-03-08 Nippon Steel & Sumitomo Metal Corporation Tôle d'acier pour tube de canalisation et tube de canalisation
CN107130173A (zh) * 2017-05-27 2017-09-05 内蒙古包钢钢联股份有限公司 钢结构用q235kz抗震热轧h型钢及其制备方法

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WO2012029945A1 (fr) * 2010-09-03 2012-03-08 住友金属工業株式会社 Tôle d'acier à haute résistance présentant d'excellents résultats de résistance à la rupture et de résistance à la fissuration induite par hydrogène
JP5835625B2 (ja) * 2012-08-28 2015-12-24 新日鐵住金株式会社 ポリオレフィン被覆ｕｏｅ鋼管及びその製造方法

Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2003201535A (ja) * 2001-10-22 2003-07-18 Jfe Steel Kk 電子ビーム溶接用鋼板、鋼管および溶接金属部の低温靱性に優れたパイプライン
JP2003293089A (ja) * 2002-04-09 2003-10-15 Nippon Steel Corp 変形性能に優れた高強度鋼板、高強度鋼管および製造方法
JP2005015823A (ja) * 2003-06-24 2005-01-20 Nippon Steel Corp 変形性能に優れたパイプライン用高強度鋼管及びその製造方法
JP2006283147A (ja) * 2005-04-01 2006-10-19 Nippon Steel Corp 時効後の変形特性に優れたパイプライン用高強度鋼管およびその製造方法
JP2006299398A (ja) * 2005-03-22 2006-11-02 Nippon Steel Corp 歪み時効特性に優れた引張強さ７６０ＭＰａ級以上の高強度鋼板の製造方法およびそれを用いた高強度鋼管の製造方法
JP2007146230A (ja) * 2005-11-28 2007-06-14 Nippon Steel Corp 耐水素誘起割れ性および延性破壊特性に優れた引張強さ７６０ＭＰａ級以上の高強度鋼板の製造方法およびその鋼板を用いた高強度鋼管の製造方法
JP2008101242A (ja) * 2006-10-19 2008-05-01 Jfe Steel Kk 耐ｈｉｃ特性に優れたラインパイプ用高強度鋼板およびその製造方法

Family Cites Families (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP4280222B2 (ja) * 2004-10-28 2009-06-17 新日本製鐵株式会社 パイプライン変形特性および低温靭性に優れた超高強度鋼板及び超高強度鋼管並びにそれらの製造方法

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2003201535A (ja) * 2001-10-22 2003-07-18 Jfe Steel Kk 電子ビーム溶接用鋼板、鋼管および溶接金属部の低温靱性に優れたパイプライン
JP2003293089A (ja) * 2002-04-09 2003-10-15 Nippon Steel Corp 変形性能に優れた高強度鋼板、高強度鋼管および製造方法
JP2005015823A (ja) * 2003-06-24 2005-01-20 Nippon Steel Corp 変形性能に優れたパイプライン用高強度鋼管及びその製造方法
JP2006299398A (ja) * 2005-03-22 2006-11-02 Nippon Steel Corp 歪み時効特性に優れた引張強さ７６０ＭＰａ級以上の高強度鋼板の製造方法およびそれを用いた高強度鋼管の製造方法
JP2006283147A (ja) * 2005-04-01 2006-10-19 Nippon Steel Corp 時効後の変形特性に優れたパイプライン用高強度鋼管およびその製造方法
JP2007146230A (ja) * 2005-11-28 2007-06-14 Nippon Steel Corp 耐水素誘起割れ性および延性破壊特性に優れた引張強さ７６０ＭＰａ級以上の高強度鋼板の製造方法およびその鋼板を用いた高強度鋼管の製造方法
JP2008101242A (ja) * 2006-10-19 2008-05-01 Jfe Steel Kk 耐ｈｉｃ特性に優れたラインパイプ用高強度鋼板およびその製造方法

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN102220547A (zh) * 2011-06-10 2011-10-19 马鞍山钢铁股份有限公司 Ct80级连续油管用钢带及其制备方法
EP3026140A4 (fr) * 2013-07-25 2017-03-08 Nippon Steel & Sumitomo Metal Corporation Tôle d'acier pour tube de canalisation et tube de canalisation
CN107130173A (zh) * 2017-05-27 2017-09-05 内蒙古包钢钢联股份有限公司 钢结构用q235kz抗震热轧h型钢及其制备方法

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