EP1546417B1 - High strength seamless steel pipe excellent in hydrogen-induced cracking resistance and its production method - Google Patents

High strength seamless steel pipe excellent in hydrogen-induced cracking resistance and its production method Download PDF

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Publication number
EP1546417B1
EP1546417B1 EP03799144A EP03799144A EP1546417B1 EP 1546417 B1 EP1546417 B1 EP 1546417B1 EP 03799144 A EP03799144 A EP 03799144A EP 03799144 A EP03799144 A EP 03799144A EP 1546417 B1 EP1546417 B1 EP 1546417B1
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Prior art keywords
steel
steel pipe
less
seamless steel
high strength
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German (de)
English (en)
French (fr)
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EP1546417A1 (en
Inventor
Nobutoshi Sumitomo Metal Industries Ltd. Murao
Nobuyuki Sumitomo Metal Industries Ltd. HISAMUNE
Hajime Sumitomo Metal Industries Ltd. OSAKO
Kunio Sumitomo Metal Industries Ltd. Kondo
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Nippon Steel Corp
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Sumitomo Metal Industries Ltd
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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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C22C38/04—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C22C38/44—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
    • 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
    • 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

  • the present invention relates to a seamless steel pipe excellent in hydrogen-induced cracking resistance (hereinafter referred to as "HIC resistance”), which is used as a line pipe having 5L-X70 grade or higher of American Petroleum Institute (API) Standard in strength level.
  • HIC resistance hydrogen-induced cracking resistance
  • oil well and the like In recent years, well conditions of an oil well for crude oil and a gas well for natural gas (hereinafter referred to as only "oil well and the like" generally) become severe and the transportation of the crude oil and natural gas has been performed under a severe environment. As the depth of water is increased, the well condition of the oil well and the like tends to contain CO 2 , H 2 S, Cl - , and the like in the ambient, and H 2 S is often contained in the crude oil and natural gas.
  • HIC hydrogen-induced cracking or hydrogen-induced blistering or the like
  • the above-mentioned HIC is a steel material fracture phenomenon that inclusions such as MnS, Al 2 O 3 , CaO, CaS and the like existing in steel are changed, during the rolling of a steel material, to elongated ones in the rolling direction or crushed cluster-like ones, hydrogen absorbed into the interfaces between these inclusions and matrix steel is accumulated and gasified, cracks are generated by the gas pressure of the accumulated hydrogen, and these cracks propagate in steel.
  • Japanese Patent Application Laid-open No. S50-97515 proposes steel for a line pipe in which Cu: 0.2 - 0.8 % is added to steel having strength of X42 - X80 grade in the API standard to form an anticorrosive film thereby preventing hydrogen from absorbing into the matrix steel.
  • Japanese Patent Application Laid-open No. S53-106318 proposes a steel material for a line pipe in which Ca: excess 0.005 % - 0.020 or less %, which is comparatively a large amount, is added to steel and inclusion (MnS) in steel is spheroidized by a shape control by Ca treatment thereby reducing cracking sensitivity Even at present HIC resistant steel has been produced based on these proposed technologies.
  • the HIC resistant steel since the principal use of the HIC resistant steel is a transporting pipeline for crude oil and natural gas, weldability is important. Thus a low-carbon steel is applied to the HIC resistant steel, but high strength steel is difficult to obtain due to the low C content of the steel. On the other hand, as mentioned above, consumers require for high strength materials. Thus, to satisfy the requirement, the following steps are often performed: after finish rolling a steel pipe by hot rolling, the steel pipe is heated and quenched, and subsequently tempered.
  • Such quenching and tempering treatment of a rolled steel pipe is effective for avoiding a ferrite and pearlite band-shaped microstructure in which HIC is liable to occur.
  • a seamless steel pipe of a high strength material was produced by quenching and tempering after soaking without cooling the rolled steel pipe to Ar3 point after hot rolling by the use of a previously proposed steel in which inclusions (MnS) are shape-controlled by Ca treatment.
  • MnS inclusions
  • the occurrence of HIC exhibiting a form of an intergranular fracture was observed.
  • the HIC resistant steel proposed in the above-described Japanese Patent Application Laid-open No. S53-106318 and the like was applied to a high strength steel, the HIC resistance is not necessarily improved.
  • JP 57-5819 discloses a seamless pipe formed with the steel containing 0.05 ⁇ 0.20% C, 0.1 ⁇ 1.0% Si, 0.5 ⁇ 2.0% Mn, 0.03% or less P, 0.006% or less S, 0.005% or less O, 0.01 ⁇ 0.07% sol.Al, 0.05 ⁇ 0.1% one or more elements ofNb and V and, if necessary, further one or more elements of 0.10 ⁇ 0.40% Cu, 0.05 ⁇ 0.20% Ni, 0.05 ⁇ 0.8% one or more elements of Cr and Mo and 0.0005 ⁇ 0.005% B.
  • the pipe is quenched through its both inner and outer surfaces from a temperature of 900°C or higher with the cooling water having a temperature of 100° ⁇ 50°C. Subsequently, it is tempered at a temperature within the range of 550°C ⁇ AC 1 .
  • the present invention was made in consideration to the production of a seamless steel pipe having high strength and HIC resistance, and an object of the present invention is to provide a high strength seamless steel pipe, which can exhibit excellent HIC resistance and its production method.
  • the present inventors have collated the knowledge about behaviors of HIC, which occurs in a line pipe, to solve the above-mentioned problem.
  • HIC is a breakage of steel by hydrogen-induced cracking or hydrogen-induced blistering, which is generated by the facts that hydrogen generated by corrosion absorbs into the steel and accumulates at the interface between the inclusions in the steel and the matrix steel and gasifies, and that the gas pressure is increased more than the yield strength of the steel to generate cracks, which propagate in the steel.
  • an inclusion shape control and the like were performed so that the absorbed hydrogen hardly gasificates.
  • all of starting point of HIC is not at inclusions, and an HIC fracture exhibits a fracture like sulfide stress-corrosion cracking and can exhibit a form of intergranular fracture.
  • the present invention has been completed based on the above-mentioned knowledge and the gist of the present invention is the following high strength seamless steel pipe and the following production method of the high strength seamless steel pipe.
  • the present invention provides a high strength seamless steel pipe excellent in hydrogen-induced cracking resistance, the steel pipe consisting of, by mass %, C: 0.03 - 0.11 %, Si: 0.05 - 0.5 %, Mn: 0.8 - 1.6 %, P: 0.025 % or less, S: 0.003 % or less, Ti; 0.002 - 0.017 %, Al: 0.001 - 0.10 %, Cr: 0.05 - 0.5 %, Mo: 0.02 - 0.3 %, V: 0.02 - 0.20 %, Ca: 0.0005 - 0.005 %, N: 0.008 % or less and O (Oxygen): 0.004 % or less, optionally Cu: 0.05-0.5% and Ni: 0.05-0.5% and Nb: 0.1% or less, and the balance Fe and impurities, wherein the microstructure of the steel is bainite and martensite, ferrite is precipitated at grain boundaries and yield stress is 483 MPa or more
  • the present invention further provides a production method of a high strength seamless steel pipe excellent in hydrogen-induced cracking resistance, wherein after rolling a billet having a composition according to claim 1 or claim 2 to a seamless steel pipe by hot rolling, said seamless steel pipe is immediately soaked and then cooled at a starting temperature of quenching of (Ar 3 point + 50°C) to 1100°C and at a cooling rate of 5°C/sec or more, and then said seamless steel pipe is tempered at 550°C to Ac 1 points, whereby a seamless steel pipe in which the microstructure of steel is bainite and martensite, ferrite is precipitated at grain boundaries and yield stress is 483 MPa or more is produced.
  • C Carbon is an element necessary to enhance hardenability and to increase the strength of the steel.
  • the content of C is less than 0.03 %, the hardenability are lowered, and high strength is difficult to ensure.
  • the content of C exceeds 0.11 %, in a case where QT is applied, the steel tends to have a fully quenched microstructure such as bainite and/or martensite or the like, whereby the HIC resistance of the steel is not only lowered but also weldability is lowered.
  • Si Silicon
  • Si is added to steel for the purpose of deoxidation of steel, and contributes to an increase in strength and enhancing a softening resistance during tempering the steel.
  • the addition of 0.05 % or more Si is needed.
  • the Si content was set to 0.5 % or less.
  • Mn Manganese
  • Mn is an effective element for increasing hardenability of the steel to increase strength thereof and for enhancing hot workability of the steel. Particularly, to enhance the hot workability of steel 0.8 % or more Mn is needed. However, since the excess addition of Mn decreases toughness and weldability of steel, the Mn content was set to 1.6 % or less.
  • P P (Phosphorus) exists in the steel as impurities. Since the segregation of P in grain boundaries deteriorates toughness of steel, the P content was set to 0.025 % or less. The P content is preferably 0.015 % or less, and more preferably 0.009 % or less.
  • S sulfur
  • MnS manganese
  • HIC resistance HIC resistance
  • Ti is an element effective to prevent cracking of the billet. To exhibit the effect the Ti content of 0.002 % or more is needed. On the other hand, since excessive addition of Ti deteriorates toughness of the steel, the Ti content was set to 0.017 % or less, and preferably 0.010 % or less.
  • Al is an indispensable element for deoxidation of the steel.
  • the Al content was set to 0.001 % or more.
  • the Al content was set to 0.10 % or less, and preferably 0.040 % or less.
  • Cr Chromium is an element for enhancing the strength of the steel.
  • the significant effect can be obtained by addition of 0.05 % or more Cr.
  • the Cr content was set to 0.5 % or less.
  • Mo Mo is an element for enhancing the strength of the steel.
  • the significant effect can be obtained by addition of 0.02 % or more Mo.
  • the Mo content was set to 0.3 % or less.
  • V (Vanadium) is an element for enhancing the strength of the steel. The significant effect can be obtained by addition of 0.02 % or more V. However, since even excessive addition of V saturates the effect, the V content was set to 0.20 % or less and preferably 0.09 % or less.
  • Ca (Calcium) is used for the shape controlling of inclusion. To enhance the HIC resistance by sphering the MnS inclusions, the Ca content of 0.0005 % or more is needed. On the other hand, when the Ca content exceeds 0.005 %, the effect is saturated and further effects cannot be exhibited. Additionally, Ca inclusions tend to be clusters so that the HIC resistance is lowered. Accordingly, the upper limit of Ca content was set to 0.005%.
  • N (Nitrogen) exists in the steel as impurities. When the N content is increased, cracks are generated in the billet so that the steel property deteriorates. Thus the N content was set to 0.008 % or less. Preferably, the N content is 0.006 % or less.
  • the O content means a total content of soluble oxygen in the steel and oxygen in oxide inclusions. This O content is substantially the same as the O content in oxide inclusions in the sufficiently deoxidized steel. Therefore, as the O content is increased, there exist increased oxide inclusions in the steel thereby decreasing HIC resistance. Accordingly, smaller O content is better and the O content was set to 0.004 % or less.
  • Nb The Nb (Niobium) content does not influence on the HIC resistance and strength of the steel.
  • the Nb element can be cared as an impurity element and its content is not be defined in the present invention.
  • the Nb content exceeds 0.1 %, undesirable effects such as deterioration of the toughness of the steel become significant.
  • the Nb content range is preferably 0.1 % or-less.
  • a steel pipe microstructure In the seamless steel pipe of the present invention, a steel pipe microstructure must be a quenched microstructure such as bainite and/or martensite to ensure the strength of 5L - X70 grade or more by use of a comparatively low C steel as shown by the above-mentioned chemical compositions.
  • the inline QT is preferably applied.
  • the precipitation of ferrite on the bainite and/or martensite grain boundary has an effect to prevent the generation of HIC, which exhibits a form of a intergranular fracture such as sulfide stress-corrosion cracking, while ensuring the strength of 5L - X70 grade or more.
  • FIG. 1 is a view showing a microstructure photograph of a seamless steel pipe inferior in HIC resistance.
  • the microstructure in FIG. 1 is a structure etched by a nital and exhibits a bainite and/or martensite fully quenched microstructure in which prior austenite grain boundaries can be clearly recognized.
  • an HIC which exhibits a form of intergranular fracture such as sulfide stress-corrosion cracking, tends to generate.
  • FIG. 2 is a view showing a microstructure photograph of a seamless steel pipe excellent in HIC resistance relating to the present invention.
  • FIG. 2 shows a microstructure etched by a nital as in FIG. 1 . Because a ferrite phase is generated in the grain boundary, the prior austenitic grain boundaries are not clear in the microstructure. In a case of such a microstructure, the HIC, which shows a form of intergranular fracture, is not occurred.
  • a seamless steel pipe excellent in an aimed performance i.e. HIC resistance can be obtained.
  • a preferable production method for obtaining a seamless steel pipe, which satisfies the microstructure and the high strength simultaneously, is shown as follows.
  • the obtained steel pipe is soaked immediately to a temperature of (Ar 3 point + 50 °C) or more by use of soaking furnace without cooling it to the Ar 3 point and is quenched.
  • the starting temperature of quenching is less than (Ar 3 point + 50 °C)
  • variation is generated in strength.
  • the starting temperature of quenching is increased, toughness of the steel pipe is significantly lowered.
  • the starting temperature of quenching must be 1100 °C or less. Therefore, the starting temperature of quenching is set to (Ar 3 point + 50 °C) to 1100 °C.
  • the quenching of the finish rolled steel pipe is performed by cooling it to room temperature, for example, while keeping the cooling rate of 5 °C/sec.
  • the cooling rate during this quenching is less than 5 °C/sec, a microstructure including martensite and bainite required for obtaining necessary strength cannot be ensured.
  • the cooling rate of 5 °C/sec or more should be kept.
  • a tempering temperature of 550 °C or more is needed.
  • the tempering temperature exceeds Ac 1 point, the strength of the steel pipe is decreased. Accordingly, the tempering must be performed under a temperature condition of 550 °C to Ac 1 point.
  • the present invention does not limit production steps until finish rolling a steel pipe from a billet, which is a starting material.
  • a Mannesmann-mandrel mill process a billet cast by a continuous casting machine or a billet obtained by rolling in a blooming mill after casting is heated and a hollow shell is obtained by a piercer such as a inclined rolling mill. After that a mandrel bar is inserted into the pipe to roll it, a finish rolling is performed by use of a sizer or reducer.
  • a seamless steel pipe having the chemical compositions and microstructure defined in said (1) or (2) of the present invention can obtain the HIC resistance of the present invention.
  • Some kinds of steels having chemical compositions shown in Table 1, were melted by a converter. Billets produced by continuous casting were heated to 1100 °C or more and hollow shells were obtained by use of a tilting roller piercer. These hollow shells were finish rolled to steel pipes by a mandrel mill and a sizer. After that without cooling the steel pipes to Ar 3 point or less, they were soaked at 950 °C and subjected to quenching and tempering treatment to produce seamless steel pipes.
  • the steel pipe sizes and heat treatment conditions are shown in Table 2. In this case the cooling rate was set to 30 °C/sec.
  • Tensile test specimens of JIS 12 were taken from the obtained steel pipes as tensile tests and tensile strength (TS) and yield strength (YS) were measured. It is noted that the tensile tests were performed in accordance with JIS Z 2241.
  • specimens having thickness of 12 to 20 mm, width of 20 mm and length of 100 mm were taken for HIC resistance tests.
  • CAR crack area ratios
  • the steel of No. 3 in Table 1 was melted by converter, and an billet produced by continuous casting was heated to 1100 °C or more and a hollow shell was obtained by use of a inclined rolling mill.
  • the hollow shell was finish rolled to a steel pipe by a mandrel mill and a sizer. After that the steel pipe was cooled in a range of 920 °C to 20 °C, and seamless steel pipes were produced by changing the cooling starting temperature, cooling rate and tempering temperature.
  • the sizes of the produced steel pipes and heat treatment conditions are shown in Table 3.
  • the Ar 3 point of the tested steel of No. 3 was 768 °C
  • the Ac 1 point thereof was 745 °C.
  • Example 1 tensile test specimens of JIS 12 were taken and as tensile tests, tensile strength (TS) and yield strength (YS) were measured. Further, HIC resistance tests were performed under the same conditions as in Example 1, and crack area ratios (CAR (%)) were measured. Further, after HIC resistance testing, cross-sections of HIC test specimens were cut off and microstructure observation was performed by an optical microscope. These results are shown in Table 3. Table 3 Steel No. Test No.
  • the steel of test No. 30 adopts a tempering temperature, which is outside the specified values of the present invention, and the strength could not satisfy 5L - X70 grade.
  • the steel of test No. 31 adopts a cooling rate outside the specified values of the present invention and the microstructure of the steel is a ferrite-pearlite microstructure whereby the strength of the steel could not satisfy 5L - X70 grade.
  • the steel of test No. 33 could not ensure a tempering temperature of 550 °C or more, an additional welding test was performed and it was found that the strength was decreased in a welding heat affected zone.
  • the chemical compositions of the steels, the microstructure of the steel, and the precipitation of ferrite at grain boundaries in the steels are specified. Accordingly, the steel can obtain high strength and stable, excellent HIC resistance. Further, by specifying the conditions in a case where an inhne QT is applied a pipeline having excellent HIC resistance and high yield stress of 483 MPa or more can be provided without inhibiting the cost down or cost saving of heat treatment process and the improvement of productivity. Therefore, the seamless steel pipe and its production method of the present invention can be utilized widely in technical fields requiring for a high strength seamless steel pipe excellent in HIC resistance.
EP03799144A 2002-10-01 2003-09-26 High strength seamless steel pipe excellent in hydrogen-induced cracking resistance and its production method Expired - Lifetime EP1546417B1 (en)

Applications Claiming Priority (5)

Application Number Priority Date Filing Date Title
JP2002288661 2002-10-01
JP2002288661 2002-10-01
JP2003051427A JP2004176172A (ja) 2002-10-01 2003-02-27 耐水素誘起割れ性に優れた高強度継目無鋼管およびその製造方法
JP2003051427 2003-02-27
PCT/JP2003/012373 WO2004031420A1 (en) 2002-10-01 2003-09-26 High strength seamless steel pipe excellent in hydrogen-induced cracking resistance and its production method

Publications (2)

Publication Number Publication Date
EP1546417A1 EP1546417A1 (en) 2005-06-29
EP1546417B1 true EP1546417B1 (en) 2012-04-25

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EP03799144A Expired - Lifetime EP1546417B1 (en) 2002-10-01 2003-09-26 High strength seamless steel pipe excellent in hydrogen-induced cracking resistance and its production method

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EP (1) EP1546417B1 (ja)
JP (1) JP2004176172A (ja)
AR (1) AR041434A1 (ja)
AT (1) ATE555220T1 (ja)
AU (1) AU2003264947B2 (ja)
BR (1) BR0314819B1 (ja)
CA (1) CA2500518C (ja)
MX (1) MXPA05003412A (ja)
NO (1) NO339589B1 (ja)
WO (1) WO2004031420A1 (ja)

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EP3351650A4 (en) * 2015-09-17 2018-08-29 JFE Steel Corporation Steel structure for hydrogen which exhibits excellent hydrogen embrittlement resistance properties in high-pressure hydrogen gas, and method for producing same

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JP2004176172A (ja) 2004-06-24
NO20051405L (no) 2005-06-21
BR0314819B1 (pt) 2011-07-12
EP1546417A1 (en) 2005-06-29
AU2003264947B2 (en) 2006-08-31
ATE555220T1 (de) 2012-05-15
CA2500518C (en) 2010-08-03
MXPA05003412A (es) 2005-10-05
AR041434A1 (es) 2005-05-18
NO339589B1 (no) 2017-01-09
AU2003264947A1 (en) 2004-04-23
WO2004031420A1 (en) 2004-04-15
BR0314819A (pt) 2005-08-02

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