US20130224063A1 - Steel plate for pipeline, having excellent hydrogen induced crack resistance, and preparation method thereof - Google Patents

Steel plate for pipeline, having excellent hydrogen induced crack resistance, and preparation method thereof Download PDF

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US20130224063A1
US20130224063A1 US13/853,584 US201313853584A US2013224063A1 US 20130224063 A1 US20130224063 A1 US 20130224063A1 US 201313853584 A US201313853584 A US 201313853584A US 2013224063 A1 US2013224063 A1 US 2013224063A1
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steel plate
less
steel
crack resistance
cooling
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Kyu-Tae Kim
Myung-Jin Lee
Kyu-Heop Park
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Hyundai Steel Co
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Hyundai Steel Co
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    • 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
    • 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
    • C21D8/02—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
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following 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
    • 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
    • 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
    • C22C38/02—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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing 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
    • C22C38/46—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
    • 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
    • C21D2211/005—Ferrite

Definitions

  • the present invention relates to a technology of manufacturing a steel plate for pipelines having excellent hydrogen-induced crack resistance for use as materials for oil pipelines, and more particularly, to a steel plate for pipelines, which does not suffer from significant reduction in impact toughness and has excellent yield ratio and hydrogen-induced crack resistance, and a method for manufacturing the same.
  • Such a steel plate for pipelines is generally produced through a rolling process.
  • Rolling generally includes slab reheating, hot rolling, cooling, and coiling.
  • the reheated slab is subjected to hot rolling at a predetermined reduction rate using rolling rolls.
  • the hot-rolled steel plate is cooled.
  • the steel plate In coiling operation, the steel plate is coiled at a predetermined temperature.
  • An aspect of the present invention is to provide a steel plate for pipelines, which has a low yield ratio and a tensile strength of 450 MPa or more and exhibits excellent hydrogen-induced crack resistance to be applied to materials for oil pipelines and the like.
  • Another aspect of the present invention is to provide a method of manufacturing a steel plate for pipelines having excellent hydrogen-induced crack resistance by controlling process conditions while optimizing a composition ratio of chromium (Cr) and other alloy components excluding copper (Cu).
  • a steel plate for pipelines having excellent hydrogen-induced crack resistance includes: carbon (C): 0.03 ⁇ 0.05 wt %, silicon (Si): 0.2 ⁇ 0.3 wt %, manganese (Mn): 0.5 ⁇ 1.3 wt %, phosphorous (P): 0.010 wt % or less, sulfur (S): 0.005 wt % or less, aluminum (Al): 0.02 ⁇ 0.05 wt %, nickel (Ni): 0.2 ⁇ 0.5 wt %, chromium (Cr): 0.2 ⁇ 0.3 wt %, niobium (Nb): 0.03 ⁇ 0.05 wt %, vanadium (V): 0.02 ⁇ 0.05 wt %, titanium (Ti): 0.01 ⁇ 0.02 wt %, calcium (Ca): 0.001 ⁇ 0.004 wt %, and the balance of iron (Fe) and other un
  • a method of manufacturing a steel plate for pipelines having excellent hydrogen-induced crack resistance includes: (A) reheating a steel slab, the steel slab including carbon (C): 0.03 ⁇ 0.05 wt %, silicon (Si): 0.2 ⁇ 0.3 wt %, manganese (Mn): 0.5 ⁇ 1.3 wt %, phosphorous (P): 0.010 wt % or less, sulfur (S): 0.005 wt % or less, aluminum (Al): 0.02 ⁇ 0.05 wt %, nickel (Ni): 0.2 ⁇ 0.5 wt %, chromium (Cr): 0.2 ⁇ 0.3 wt %, niobium (Nb): 0.03 ⁇ 0.05 wt %, vanadium (V): 0.02 ⁇ 0.05 wt %, titanium (Ti): 0.01 ⁇ 0.02 wt %, calcium (Ca): 0.001 ⁇
  • the steel plate for pipelines contains a suitable amount of chromium and is free from copper (Cu), which is generally used in manufacture of steel plates, thereby providing advantages such as insignificant reduction of impact toughness and excellent hydrogen-induced crack resistance.
  • Cu copper
  • the method of manufacturing a steel plate for pipelines provides a steel plate which exhibits excellent hydrogen-induced crack resistance and allows insignificant reduction in impact toughness even without containing copper (Cu) by controlling rolling and cooling conditions while optimizing a composition ratio of the steel plate.
  • FIG. 1 is a schematic flowchart of a method of manufacturing a steel plate for pipelines in accordance with one embodiment of the present invention.
  • FIG. 2 is a graph depicting yield strength and tensile strength of specimens prepared in inventive examples and comparative examples.
  • FIG. 3 is a graph depicting impact resistance according to temperature of the specimens prepared in inventive examples and comparative examples.
  • FIG. 4 depicts pictures showing occurrence of cracking of specimens prepared in inventive examples and comparative examples upon HIC testing.
  • a steel plate for pipelines having excellent hydrogen-induced crack resistance includes: carbon (C): 0.03 ⁇ 0.05 wt %, silicon (Si): 0.2 ⁇ 0.3 wt %, manganese (Mn): 0.5 ⁇ 1.3 wt %, phosphorous (P): 0.010 wt % or less, sulfur (S): 0.005 wt % or less, aluminum (Al): 0.02 ⁇ 0.05 wt %, nickel (Ni): 0.2 ⁇ 0.5 wt %, chromium (Cr): 0.2 ⁇ 0.3 wt %, niobium (Nb): 0.03 ⁇ 0.05 wt %, vanadium (V): 0.02 ⁇ 0.05 wt %, titanium (Ti): 0.01 ⁇ 0.02 wt %, calcium (Ca): 0.001 ⁇ 0.004 wt %, and the balance of iron (Fe) and other unavoidable impurities.
  • C
  • Carbon (C) is an element for improving strength and hardness of steel.
  • a higher content of carbon can provide higher strength, but can cause deterioration in toughness of steel.
  • processability of the steel increase with increasing content of carbon, causing increase in tensile strength and yield point while decreasing elongation.
  • the steel plate can be deteriorated in hydrogen-induced crack resistance.
  • the carbon content is less than 0.03 wt % in the steel plate, there can be difficulty in securing strength of the steel plate.
  • carbon is present in an amount of 0.03 ⁇ 0.05 wt % in the steel plate according to the present invention.
  • Silicon (Si) acts as an effective deoxidization element and reinforces ferrite structure in steel while improving yield strength.
  • Such effects of silicon can be sufficiently exhibited when the silicon content is 0.2 wt % or more. If the silicon content exceeds 0.3 wt % in the steel, toughness of the steel is deteriorated, reducing formability and causing difficulty in forging and processing.
  • silicon is present in an amount of 0.2 ⁇ 0.3 wt % in the steel plate according to the present invention.
  • Manganese (Mn) serves to improve quenching properties and strength while increasing plasticity at high temperature to improve casting properties.
  • manganese is likely to bind with an unfavorable component, that is, sulfur (S), thereby forming MnS inclusions.
  • manganese is added in an excessive amount exceeding 1.3 wt %, a steel slab can suffer from central segregation, which promotes occurrence of hydrogen induced cracking at a segregated portion of the steel slab. If the manganese content is less than 0.5 wt %, it is difficult to secure strength of the steel.
  • manganese is present in an amount of 0.5 ⁇ 1.3 wt % in the steel plate according to the present invention.
  • Phosphorous (P) is an element that is segregated into a grain boundary, reducing toughness and impact resistance of steel, and causes hydrogen-induced cracking in the steel.
  • the phosphorous content is limited to 0.010 wt % or less in the steel plate according to the present invention.
  • S is an essential element coupled to manganese (Mn) to form MnS inclusions, thereby improving steel machinability.
  • Mn manganese
  • sulfur deteriorates hot processability of the steel, causes fracture, and forms coarse inclusions, causing defects upon surface treatment.
  • sulfur is present in an amount of 0.005 wt % or less in the steel plate according to the present invention.
  • Aluminum (Al) is a strong deoxidization element and is coupled to nitrogen for grain refinement. However, if the aluminum content exceeds 0.05 wt % in the steel, there can be problems of deterioration in impact toughness and hydrogen-induced crack resistance. Further, if the aluminum content is less than 0.02 wt %, insufficient deoxidization can be obtained. Thus, advantageously, aluminum is present in an amount of 0.02 ⁇ 0.05 wt % in the steel plate according to the present invention.
  • the content of nickel (Ni) is suitably adjusted to obtain desired yield strength and a yield ratio of 80% or less even in the absence of copper (Cu). If the nickel content is less than 0.2 wt %, it is difficult for the steel to have a yield strength of 450 MPa or more. If the nickel content exceeds 0.5 wt %, the steel has a yield ratio exceeding 80%. Thus, advantageously, nickel is present in an amount of 0.2 ⁇ 0.5 wt % in the steel plate according to the present invention.
  • the steel plate includes chromium and is free from copper (Cu), which is generally used in manufacture of existing steel plates. Copper can cause deterioration of weldability and surface quality of the steel plate. Thus, the steel plate of the invention does not contain copper and contains an optimal amount of chromium.
  • chromium Through addition of chromium, it is possible to manufacture a steel plate, which does not suffer from significant reduction in impact toughness and has a low yield ratio and excellent hydrogen-induced crack resistance.
  • the chromium content exceeds 0.3 wt %, the steel plate can suffer from deterioration in hydrogen-induced crack resistance. If the chromium content is less than 0.2 wt %, the steel plate cannot obtain desired strength.
  • chromium is present in an amount of 0.2 ⁇ 0.3 wt % in the steel plate according to the present invention.
  • Niobium (Nb) prevents grains of steel from being coarsened at high temperature and promotes refinement of the grains to improve ductility and toughness of the steel.
  • niobium is desirably added in an amount of 0.03 wt % or more. Since secondary phases containing niobium can act as sites for initiation of hydrogen-induced cracking, an upper niobium limit is set to 0.05 wt %.
  • niobium is present in an amount of 0.03 ⁇ 0.05 wt % in the steel plate according to the present invention.
  • Vanadium (V) serves to improve resistance to hydrogen-induced cracking.
  • vanadium is present in an amount of 0.02 ⁇ 0.05 wt % in steel. If the vanadium content is less than 0.02 wt %, the effect of vanadium is not sufficiently exhibited. On the contrary, if the vanadium content exceeds 0.05 wt %, the steel can suffer from deterioration in toughness and hydrogen-induced crack resistance.
  • Titanium is an element which forms carbide or nitride in steel, and serves to improve both strength and low temperature toughness through grain refinement.
  • Titanium precipitates reduces a diffusion coefficient of hydrogen and increases hydrogen-induced crack resistance. If the titanium content exceeds 0.02 wt %, the steel can be deteriorated in hydrogen-induced crack resistance, and if the titanium content is less than 0.01 wt %, it is difficult to obtain desired strength. Thus, advantageously, titanium is present in an amount of 0.01 ⁇ 0.02 wt % in the steel plate according to the present invention.
  • MnS inclusions have a low melting point and are elongated upon rolling to act as starting point of hydrogen-induced cracking. The added calcium reacts with MnS to surround the MnS inclusions, thereby obstructing elongation of the MnS inclusions.
  • calcium is advantageously present in an amount of 0.001 wt % or more.
  • an upper limit of the calcium content is set to 0.004 wt %.
  • the steel plate for pipelines according to the present invention has a yield ratio (YS)/(TS) of 80% or less.
  • the microstructure of the steel plate comprises a composite structure consisting of acicular ferrite and bainite structures.
  • a composite structure consisting of acicular ferrite and bainite structures occupies 30% or more of the entirety of the microstructure in terms of cross-sectional area ratio
  • a composite structure consisting of ferrite and pearlite structures occupies 70% or less of the entirety of the microstructure in terms of cross-sectional area ratio.
  • the composite structure consisting of acicular ferrite and bainite structures occupies 30% or less of the entirety of the microstructure in terms of cross-sectional area ratio, it is difficult to achieved desired strength.
  • FIG. 1 is a schematic flowchart of a method of manufacturing a steel plate for pipelines in accordance with one embodiment of the present invention.
  • the method of manufacturing the steel plate for pipelines includes: (A) reheating a steel slab, the steel slab including carbon (C): 0.03 ⁇ 0.05 wt %, silicon (Si): 0.2 ⁇ 0.3 wt %, manganese (Mn): 0.5 ⁇ 1.3 wt %, phosphorous (P): 0.010 wt % or less, sulfur (S): 0.005 wt % or less, aluminum (Al): 0.02 ⁇ 0.05 wt %, nickel (Ni): 0.2 ⁇ 0.5 wt %, chromium (Cr): 0.2 ⁇ 0.3 wt %, niobium (Nb): 0.03 ⁇ 0.05 wt %, vanadium (V): 0.050 ⁇ 0.095 wt %, titanium (Ti): 0.01 ⁇ 0.02 wt %, calcium (Ca): 0.001 ⁇ 0.004 wt %, and the
  • the method of manufacturing the steel plate for pipelines according to the invention reduces fractions of polygonal ferrite and band structures relatively vulnerable to hydrogen-induced cracking, and includes finish-rolling to be performed at an Ar 3 transformation temperature or less to induce generation of mobile dislocations, which are advantageous for reduction of yield ratio.
  • the steel plate is reduced in yield strength, thereby lowering the yield ratio. That is, the steel plate according to the present invention has a low yield ratio, thereby providing excellent plastic deformation and anti-vibration effects.
  • the cooling rate is controlled to form acicular ferrite and bainite structures in a fraction of 30% or more.
  • reheating is performed at temperatures of 1000° C. or more in order to relieve central segregation.
  • Nb and V can be sufficiently dissolved in the steel during reheating of the steel slab and can be finely precipitated to increase strength of the steel during rolling.
  • the steel slab may be reheated at a temperature from 1100° C. to 1250° C. to achieve sufficient dissolution of Nb and V in the steel slab.
  • finish-rolling is performed at an Ar 3 transformation temperature or less to induce generation of mobile dislocations which are favorable to reduction of the yield ratio.
  • the finish-rolling finishing temperature may be set to 750° C. or more to ensure that the steel plate has excellent hydrogen-induced crack resistance and the acicular ferrite and bainite structures are formed in a fraction of 30% or more.
  • the finish-rolling finishing temperature is set to 850° C. or less to prevent the decrease in strength of the steel plate.
  • the reduction rate of hot rolling is set in the range of 50% to 70% based on a reduction rate of 100 at an Ar 3 transformation temperature or less in order to restrict an average grain size of acicular ferrite microstructure in a final product of the steel plate according to the present invention.
  • the cooling finishing temperature may be restricted in the cooling stage.
  • the cooling finishing temperature may be set to 300° C.
  • the cooling finishing temperature may be sent to 450° C. or less.
  • a cooling rate of less than 15° C./sec makes it difficult for the steel plate to obtain sufficient hardness.
  • a cooling rate exceeding 25° C./sec can cause deterioration in hydrogen-induced crack resistance.
  • the cooling rate is set in the range of 15 ⁇ 25° C./sec.
  • Table 1 shows compositions of steel specimens prepared in examples and comparative examples.
  • steel specimens prepared in Comparative Examples 1 to 3 are conventional steel plates for pipelines, and steel specimens prepared in Examples 1 to 3 are inventive steel plates for pipelines in which chromium and other alloy components are present in a suitable composition ratio without adding copper.
  • the steel specimens prepared in Comparative Examples 1 to 3 are conventional steel plates for pipelines, and the steel specimens prepared in Examples 1 to 3 are inventive steel plates for pipelines in which chromium and other alloy components are present in a suitable composition ratio without adding copper.
  • FIG. 2 is a graph depicting yield strength and tensile strength of each of the specimens prepared in the inventive examples and the comparative examples.
  • left-side bars indicate yield strength (YS) and right-side bars indicate tensile strength (TS).
  • the specimens of Examples 1 to 3 did not contain copper (Cu), which is included in conventional steel plates for pipelines. It can be confirmed that these steel specimens have a tensile strength of 450 MPa or more even without containing Cu.
  • FIG. 3 is a graph depicting results of impact testing with respect to the respective specimens of the inventive examples and the comparative examples.
  • FIG. 4 shows results of hydrogen-induced cracking testing.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Steel (AREA)
US13/853,584 2010-09-29 2013-03-29 Steel plate for pipeline, having excellent hydrogen induced crack resistance, and preparation method thereof Abandoned US20130224063A1 (en)

Applications Claiming Priority (5)

Application Number Priority Date Filing Date Title
KR20100094599 2010-09-29
KR10-2010-0094599 2010-09-29
PCT/KR2011/006373 WO2012043984A2 (ko) 2010-09-29 2011-08-29 수소유기균열 저항성이 우수한 라인 파이프용 강판 및 그 제조 방법
KR10-2011-0086685 2011-08-29
KR1020110086685A KR101344638B1 (ko) 2010-09-29 2011-08-29 수소유기균열 저항성이 우수한 라인 파이프용 강판 및 그 제조 방법

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JP2015178647A (ja) * 2014-03-19 2015-10-08 Ｊｆｅスチール株式会社 耐ｈｉｃ性能に優れた極厚鋼板およびその製造方法
JP2019504210A (ja) * 2015-12-23 2019-02-14 ポスコＰｏｓｃｏ 耐水素誘起割れ（ｈｉｃ）性に優れた圧力容器用鋼材及びその製造方法
CN111936643A (zh) * 2018-03-19 2020-11-13 塔塔钢铁公司 根据x-65级的api 5l psl-2规范的具有增强的氢致开裂(hic)抗性的钢组合物及制造钢组合物的钢的方法
US11155906B2 (en) * 2016-11-11 2021-10-26 Posco Pressure vessel steel having excellent hydrogen induced cracking resistance, and manufacturing method therefor

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JP6344538B1 (ja) * 2017-09-19 2018-06-20 新日鐵住金株式会社 鋼管及び鋼板
KR101988771B1 (ko) * 2017-12-22 2019-09-30 주식회사 포스코 수소유기균열 저항성 및 길이방향 강도 균일성이 우수한 강판 및 그 제조방법
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