EP2832879B1 - Hochfestes stahlrohr für leitungsrohr mit hervorragender beständigkeit gegen wasserstoffinduzierte rissbildung, hochfestes stahlblech für ein leitungsrohr damit und verfahren zur herstellung davon - Google Patents

Hochfestes stahlrohr für leitungsrohr mit hervorragender beständigkeit gegen wasserstoffinduzierte rissbildung, hochfestes stahlblech für ein leitungsrohr damit und verfahren zur herstellung davon Download PDF

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EP2832879B1
EP2832879B1 EP13768001.3A EP13768001A EP2832879B1 EP 2832879 B1 EP2832879 B1 EP 2832879B1 EP 13768001 A EP13768001 A EP 13768001A EP 2832879 B1 EP2832879 B1 EP 2832879B1
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steel
less
steel plate
line pipe
pipe
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French (fr)
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EP2832879A1 (de
EP2832879A4 (de
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Takuya Hara
Taishi Fujishiro
Taro Muraki
Go Suzuki
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Nippon Steel Corp
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Nippon Steel Corp
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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
    • C22C38/001—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
    • 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
    • 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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing 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
    • 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium 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

Definitions

  • HIC resistance hydrogen induced crack resistance
  • H 2 S wet hydrogen sulfide
  • a sour environment An environment in which wet hydrogen sulfide (H 2 S) gas is present (below, referred to as a "sour environment") is formed in the drilling, production, and transportation of oil and natural gas.
  • the steel pipe which is used there is exposed to the sour environment. If the line pipe for transportation of oil, natural gas, etc. is exposed to a sour environment, hydrogen induced cracking (below, referred to as "HIC”) may occur. This is because in a sour environment, hydrogen easily penetrates the steel from its surface.
  • HIC hydrogen induced cracking
  • HIC is due to the hydrogen which accumulates around the elongated MnS which is present at the centerline segregation of steel, accumulated carbonitrides of Ti or Nb or oxide-based inclusions in the oxide accumulation zone, and other defects in the steel.
  • PLTs 1 to 3 disclose methods of improving the HIC resistance by suppressing the segregation of Mn at the center of the steel plate.
  • PLT 1 proposes steel plate which suppresses the ratio of Mn content of the segregated part to the average Mn content in the steel.
  • PLTs 2 and 3 disclose limiting not only the size of Mn segregated spots but also the concentration of P of the segregated part and, furthermore, high strength line pipe using Ca.
  • PLT 4 discloses hot rolled steel plate excellent in HIC resistance which focuses on not only segregation of Mn, but also segregation of Nb.
  • PLTs 5 and 6 a method of suppressing inclusions of carbides, nitrides, etc. of Ti and Nb to improve the HIC resistance is disclosed.
  • PLTs 7 and 8 disclose steel pipes which suppress the segregation of Mn, Nb, and Ti and, furthermore, make the maximum hardness of the centerline segregation 300Hv or less to thereby prevent the occurrence of HIC.
  • High-strength steel pipes are disclosed in WO 2010/093057 and WO 2010/052928 .
  • the present invention was made in consideration of the above actual situation and has as its object the provision of steel pipe for line pipe use which is extremely high in t/D, has excellent HIC resistance as steel pipe as a whole, and prevents HIC at the surface layer of the steel plate and therefore is optimal for steel pipe which is used for line pipe laid across deep ocean floors etc. and line pipe steel plate which is used for the same.
  • the inventors engaged in intensive studies on the conditions for obtaining steel pipe for high strength line pipe use excellent in hydrogen induced crack resistance which has excellent HIC resistance near the inside and outside surfaces of the steel pipe and can prevent HIC at the surface layer even if the t/D is high and the steel plate used for the same.
  • the surface layer region is fast in cooling rate and easily hardens.
  • the inventors discovered that by optimizing the cooling conditions after rolling steel plate, it becomes possible to make the hardness of the surface layer region of steel plate, which in the past was about 350Hv, 300Hv or less and, as a result, suppress the occurrence of HIC from inclusions near the inside and outside surfaces even with high t/D steel pipe and obtain steel pipe which has excellent HIC resistance near the inside and outside surfaces of steel pipe.
  • the present invention was made based on this discovery and has as its gist the following:
  • the steel pipe for high strength line pipe use and steel plate for high strength line pipe use of the present invention have little segregation of Mn, Nb, and Ti, are suppressed in length of non-pressed bonded parts of the centerline segregation and maximum hardness, and further are suppressed in hardness of surface layer region.
  • the HIC resistance is reliable and sufficiently excellent and is extremely excellent as a material of line pipe which is used in a sour environment.
  • the steel pipe for line pipe use of the present invention has a thickness "t" of steel plate [mm] and outside diameter D of steel pipe after pipemaking [mm] satisfying t ⁇ 25 and t/D ⁇ 0.035.
  • the segregation ratios of Mn, Nb, and Ti, the length and maximum hardness of the non-press-bonded part at the centerline segregation and the maximum hardness and structure of the surface layer region from the two front and back surfaces down to a depth of 5 mm are suitably prescribed.
  • C is an element which improves the strength of steel. 0.02% or more has to be added. If the amount of C exceeds 0.08%, the formation of carbides is promoted and the HIC resistance deteriorates. To secure a more superior HIC resistance and suppress the drop in weldability and toughness, the amount of C is preferably made 0.06% or less.
  • Si is a deoxidizing element. 0.01% or more has to be added. If the amount of Si exceeds 0.5%, the toughness of the heat affected zone (HAZ) deteriorates.
  • Mn is an element which improves the strength and toughness. 0.8% or more has to be added. If the amount of Mn exceeds 1.8%, the HIC resistance deteriorates. To further suppress HIC, the amount of Mn is preferably made 1.6% or less.
  • Nb is an element which forms carbides and nitrides, promotes finer grains of the steel plate as rolled, and contributes to the improvement of strength. To obtain this effect, 0.0001% or more of Nb has to be added. If excessively adding Nb, the maximum Nb segregation ratio increases, the accumulation of carbonitrides of Nb is invited, and the HIC resistance deteriorates, so the upper limit of the amount of Nb is made 0.10%. If improving the HIC resistance more, the amount of Nb is preferably made 0.05% or less.
  • Ca is an element which forms the sulfide CaS, suppresses the formation of MnS which flattens in the rolling direction, and remarkably contributes to improvement of the HIC resistance. If the amount of addition of Ca is less than 0.0005%, the effect is not obtained. If the amount of addition of Ca exceeds 0.0050%, the oxides accumulate and the HIC resistance deteriorates.
  • N is an element which forms TiN, NbN, and other nitrides.
  • the amount of addition of N has to be made 0.0010% or more. If the content of N exceeds 0.0060%, carbonitrides of Ti and Nb easily accumulate and the HIC resistance deteriorates.
  • the amount of N is preferably made 0.0035% or less.
  • O is an impurity. To suppress the accumulation of oxides and improve the HIC resistance, it is restricted to 0.0035% or less. To suppress the formation of oxides and improve the base material and HAZ toughness, the amount of O is preferably made 0.0035% or less, more preferably 0.0020% or less. The smaller the amount of O the better, but to make it less than 0.0001%, the refining time becomes long and the cost rises, so the lower limit is made 0.0001%.
  • P is an impurity. If the content exceeds 0.01%, the HIC resistance deteriorates. Further, the HAZ toughness deteriorates. Therefore, the content of P is restricted to 0.01% or less.
  • the amount of S is an element which forms MnS which is elongated in the rolling direction at the time of hot rolling and thereby lowers the HIC resistance.
  • the amount of S has to be reduced to 0.0020% or less.
  • the amount of S is preferably made 0.0010% or less. The smaller the amount of S, the better, but making it less than 0.0001% is difficult. From the viewpoint of the manufacturing cost, the lower limit is preferably made 0.0001% or more.
  • Al is a deoxidizing element, but if the amount of addition exceeds 0.030%, accumulated clusters of Al oxides are formed.
  • the amount of Al is preferably made 0.017% or less.
  • the lower limit value of the amount of Al is not particularly set, but to reduce the amount of oxygen in the molten steel, Al is preferably added in an amount of 0.0005% or more.
  • Ti is an element which is usually utilized as a deoxidizing agent or for refinement of the crystal grains as a nitride-forming element, but is an element which lowers the HIC resistance and toughness due to formation of carbonitrides. Therefore, the content of Ti is restricted to 0.030% or less.
  • FIG. 1 shows the relationship between the CLR (length ratio of HIC) and S/Ca in an HIC test of 0.04%C-1.25%Mn steel. As shown in FIG. 1 , if the ratio of S/Ca becomes 0.5 or more, HIC is formed. If the ratio of S/Ca becomes 0.5 or more, MnS is formed and MnS which is elongated at the time of rolling is formed. As a result, the HIC resistance deteriorates. Therefore, the ratio of S/Ca has to be made less than 0.5.
  • the steel pipe for line pipe use and the steel plate for line pipe use of the present invention may, in accordance with need, have one type or two types or more of elements selected from Ni, Cu, Cr, Mo, W, V, Zr, Ta, and B added to them as elements which improve the strength and toughness.
  • elements selected from Ni, Cu, Cr, Mo, W, V, Zr, Ta, and B added to them as elements which improve the strength and toughness.
  • the reasons for limitation of the amounts of addition of these optional added elements are as follows:
  • Ni is an element which is effective for improvement of toughness and strength. To obtain this effect, 0.01% or more has to be added. If the amount of addition of Ni exceeds 2.0%, the HIC resistance and weldability deteriorate.
  • Cu is an element which is effective for improvement of the strength without causing a drop in toughness. To obtain this effect, 0.01% or more has to be added. If the amount of addition of Cu exceeds 1.0%, cracking easily occurs at the time of heating a steel slab or at the time of welding.
  • Cr is an element which improves the strength of steel by precipitation strengthening. To obtain this effect, 0.01% or more has to be added. If the amount of addition of Cr exceeds 1.0%, the hardenability rises, a bainite structure is formed, and as a result the HIC resistance and toughness fall.
  • Mo is an element which improves the hardenability and simultaneously forms carbonitrides and improves the strength. To obtain this effect, 0.01% or more has to be added. If the amount of addition of Mo exceeds 0.60%, the cost rises. If the steel excessively rises in strength, the HIC resistance and toughness sometimes deteriorate, so the amount of addition of Mo is 0.20% or less.
  • W is an element which is effective for improvement of strength. To obtain this effect, 0.01% or more has to be added. If the amount of addition of W exceeds 1.0%, the toughness sometimes deteriorates.
  • Zr like V, is an element which forms carbides and nitrides and contributes to improvement of the strength. To obtain this effect, 0.0001% or more has to be added. If the amount of addition of Zr exceeds 0.050%, the toughness sometimes deteriorates.
  • Ta 0.0001 to 0.050%
  • Ta also, like V, is an element which forms carbides and nitrides and contributes to improvement of the strength. To obtain this effect, 0.0001% or more has to be added. If the amount of addition of Ta exceeds 0.050%, the toughness sometimes deteriorates.
  • B is an element which segregates at the grain boundaries of the steel and remarkably contributes to improvement of the hardenability. To obtain this effect, 0.0001% or more of B has to be added. B is an element which forms BN, causes solid solution N to fall, and contributes to improvement of the toughness of the heat affected zone, so 0.0005% or more is preferably added. If the amount of addition of B exceeds 0.0020%, segregation at the grain boundaries is suppressed and the toughness sometimes deteriorates.
  • the steel pipe for line pipe use and steel plate for line pipe use of the present invention may in accordance with need have one type or two types or more of a REM (rare earth metal), Mg, Y, Hf, and Re added to them so as to control the oxides, sulfides, and other inclusions.
  • REM rare earth metal
  • Mg, Y, Hf, and Re added to them so as to control the oxides, sulfides, and other inclusions.
  • REM Rotary Earth Metal: 0.0001 to 0.01%
  • An REM is an element which is added as a deoxidizing agent and a desulfurizing agent. To obtain this effect, 0.0001% or more has to be added. If the amount of addition of REM exceeds 0.010%, coarse oxides are formed and the HIC resistance and the toughness of the base material and HAZ sometimes fall.
  • Mg is an element which is added as a deoxidizing agent and a desulfurizing agent. In particular, it forms fine oxides which contributes to improvement of the HAZ toughness. To obtain this effect, adding 0.0001% or more of Mg is necessary. If the amount of addition of Mg exceeds 0.010%, oxides easily accumulate and coarsen and the HIC resistance and base material and HAZ toughness sometimes fall.
  • Y like Ca, is an element which forms sulfides, suppresses the formation of MnS elongated in the rolling direction, and contributes to improvement of the HIC resistance. To obtain such an effect, it is necessary to add Y in an amount of 0.0001% or more. If the amount of addition of Y exceeds 0.005%, oxides increase, accumulate, and coarsen and the HIC resistance deteriorates.
  • Hf like Ca
  • Hf is an element which forms sulfides, suppresses the formation of MnS elongated in the rolling direction, and contributes to improvement of the HIC resistance.
  • the amount of addition of Hf exceeds 0.005%, oxides increase, accumulate, and coarsen and the HIC resistance deteriorates.
  • Re like Ca, is an element which forms sulfides, suppresses the formation of MnS elongated in the rolling direction, and contributes to improvement of the HIC resistance. To obtain such an effect, it is necessary to add Re in an amount of 0.0001% or more. If the amount of addition of Re exceeds 0.005%, oxides increase, accumulate, and coarsen and the HIC resistance deteriorates.
  • the balance other than the above elements is Fe and unavoidable impurities.
  • the above-mentioned Ni, Cu, Cr, Mo, W, V, Zr, Ta, and B may all be contained in fine amounts of less than the above lower limit values as impurities.
  • REM, Mg, Y, Hf, and Re may also be contained in extremely fine amounts of less than the lower limit values as impurities.
  • Mn Segregation Ratio 2.0 or less, Nb Segregation Ratio: 4.0 or less, Ti Segregation Ratio: 4.0 or less HIC is due to the hydrogen which accumulates around the elongated MnS present at the centerline segregation of the steel, the accumulated carbonitrides of Ti and NB, etc.
  • the maximum Mn segregation ratio of the steel plate and steel pipe has to be made 2.0 or less. Furthermore, by suppressing segregated carbonitrides of Ti and Nb, it is possible to remarkably prevent the occurrence of HIC of the steel pipe for line pipe use and steel plate for line pipe use.
  • N 0.0050% or less the amount of C 0.06% or less, and the maximum segregation ratio of Nb and Ti 4.0 or less.
  • the “maximum Mn segregation ratio” is the maximum amount of Mn at the centerline segregation compared with the average amount of Mn in the distribution of concentration of Mn in the plate thickness direction of steel plate and in the distribution of concentration of Mn in the thickness direction of the pipe wall of steel pipe.
  • the Nb segregation ratio and the Ti segregation ratio are the averaged maximum amount of Nb (amount of Ti) at the centerline segregation compared with the average amount of Nb (amount of Ti) in the distributions of concentration of Nb and Ti in the plate thickness direction of steel plate and in the distributions of concentration of Nb and Ti in the thickness direction of the pipe wall of steel pipe.
  • the maximum Mn segregation ratio is found by measuring the distribution of concentration of Mn of steel plate and steel pipe by an EPMA (electron probe micro analyzer) or CMA (computer aided micro analyzer) able to perform image processing on the measurement results of the EPMA.
  • the measured object is an HIC test piece (20 mm width ⁇ 20mm thickness machined from both surface of full thickness ⁇ 100 mm length), while a region of the HIC test piece of 20 mm width (test piece width) ⁇ 20mm thickness machined from both surface of full thickness (HIC) test piece thickness was made the measurement region.
  • the same region may be measured by EPMA or CMA to measure the distribution of concentration of Nb and the distribution of concentration of Ti.
  • the probe diameter of the EPMA (or CMA) is made 2 ⁇ m.
  • the maximum Mn segregation ratio is found by measuring the concentration of Mn using an EPMA by a 50 ⁇ m beam diameter in a measurement region of a 20 mm width (HIC test piece width) ⁇ 20mm thickness machined from both surface of full thickness (HIC test piece thickness) at equal intervals in the plate thickness direction and plate width direction to measure the distribution of concentration of Mn and make the average value at the measured distribution of concentration of Mn the average Mn concentration.
  • a region of 1 mm (width) ⁇ 1 mm (thickness) including the location of the greatest concentration of the amount of Mn was measured for 50 points ⁇ 50 points of Mn concentration at equal intervals in the plate thickness direction and plate width direction while changing the beam diameter to 2 ⁇ m.
  • the maximum Mn concentration was found from the distribution. Further, the ratio of the maximum Mn concentration which is obtained by a 2 ⁇ m beam diameter and the average Mn concentration which is obtained by a 50 ⁇ m beam diameter is defined as the "maximum Mn segregation ratio".
  • the Nb segregation ratio and the Ti segregation ratio are similarly found by measuring the distributions of concentration of Nb and Ti using an EPMA by a 50 ⁇ m beam diameter in a measurement region of a 20 mm width (HIC test piece width) ⁇ 20mm thickness machined from both surface of full thickness (HIC test piece thickness), then measuring the concentrations of Nb and Ti by a 2 ⁇ m beam diameter in the region of 1 mm (width) ⁇ 1 mm (thickness) of the locations where the amounts of Nb and Ti are most concentrated.
  • the segregation ratio sometimes becomes larger in appearance, but if there are inclusions, it is possible to judge these as regions where the peaks sharply rise in the distributions of concentration of Nb and Ti, so the segregation ratios are found after subtracting the measurement values of these regions.
  • soft reduction at the time of the final solidification at continuous casting is optimum.
  • the soft reduction at the time of final solidification is performed for eliminating the mixture of solidified parts and nonsolidified parts due to uneven cooling during casting. Due to this, it is possible to eliminate the spaces accompanying shrinkage upon solidification to keep down the flow of molten steel at the unsolidified parts to cause uniform solidification of the steel slab.
  • centerline segregation of the steel plate has a center-porosity of a length of 0.1 mm or more, it becomes a starting point of HIC and the HIC resistance deteriorates.
  • a "center-porosity" is a space which is formed in a steel slab at the time of solidification which is not press-bonded due to hot rolling, but remains in the steel plate. The length of a center-porosity can be measured by an ultrasonic or other nondestructive test.
  • the cause of center-porosities remaining at the centerline segregation is mainly the hydrogen which is contained in the steel slab before hot rolling.
  • the steel solidifies and shrinks upon cooling, so spaces are easily formed in particular at the center part of the steel slab. If the spaces are negative in pressure, if the amount of hydrogen which is contained in the steel slab is large, the hydrogen gas will penetrate into the spaces.
  • the hydrogen which is contained in the steel when produced by secondary refining remains almost as is in the spaces in the steel slab after continuous casting.
  • the structure of the steel slab is austenite with a large amount of hydrogen which can form a solid solution in a face-centered cubic structure, so the hydrogen is not dispersed to the outside of the steel slab. If heating the steel slab and reducing it by hot rolling, the spaces inside the steel slab become smaller, but the pressure of the hydrogen gas which is contained in the spaces becomes higher in reverse proportion to the size of the spaces. Therefore, it is not possible to press bond the spaces due to the hot rolling. Center-porosities remain inside the steel plate, in particular, the centerline segregation.
  • the amount of hydrogen in the steel which is referred to here was found by measuring the molten steel which was sampled after secondary refining by the combustion method.
  • the amount of hydrogen which remains in the steel plate after hot rolling decreases compared with the amount of hydrogen after the secondary refining since the hydrogen is dispersed to the outside if the steel plate is cooled and the metal structure transforms from austenite to ferrite, bainite, martensite, pearlite, etc.
  • the HIC resistance it is effective to make the maximum hardness of the centerline segregation 300Hv or less.
  • the maximum hardness of the centerline segregation is measured by a Vicker's hardness test at a 25 g load based on JIS Z 2244 after corrosion by a Nital solution which consists of 3% nitric acid and 97% ethanol.
  • the "centerline segregation" is a portion where the concentration of Mn which is measured by EPMA or CMA becomes maximum.
  • the HIC resistance can be reliably raised. That is, by making the upper limit of the maximum hardness of the surface layer region from the topmost surface down to 5 mm 300Hv or less, even in steel pipe for line pipe use with a high t/D of 0.035 or more, it is possible to reliably prevent the occurrence of HIC due inclusions, blisters, etc. at the surface layer.
  • the maximum hardness of the surface layer region is found by conducting a Vicker's hardness test at predetermined intervals in the depth direction (for example, 0.1 mm intervals) from the topmost surface to a position of a depth of 5 mm and using the highest value among the values as the maximum hardness. Specifically, this is investigated by corroding the surface by a Nital solution which consists of 0.13% nitric acid and 97% ethanol, then conducting a Vicker's hardness test based on JIS Z 2244 by a 25 g load at 50 points x 50 points at 0.1 mm intervals from the topmost surface to a position at a depth of 5 mm.
  • the steel structure of the base material is preferably a uniform and fine acicular ferrite or bainite structure. Therefore, the structure of the steel base material for high strength line pipe of the present invention considering the HIC resistance is basically preferably bainite or acicular ferrite.
  • heavy wall pipe for line pipe use often is required to have properties able to withstand a drop weight test such as DWTT.
  • FIG. 2 shows a relationship between a total area rate of polygonal ferrite and deformed ferrite at the surface layer of steel pipe and an area rate of HIC.
  • 3 o'clock, 6 o'clock, and 9 o'clock are positions in the circumferential direction of the steel pipe from which the test piece is taken. The weld zone was made 0 o'clock. Test pieces were taken from positions of 3 o'clock (90°), 6 o'clock (180°), and 9 o'clock (270°) as seen from the bottom part of the steel pipe and observed for structure.
  • the HIC area ratio greatly exceeds 3%. Therefore, even when the surface layer region contains polygonal ferrite and deformed ferrite, to reliably improve the HIC resistance, it is preferable to suppress the total fraction of the polygonal ferrite and the deformed ferrite to an area ratio of 20% or less. From the viewpoint of the HIC resistance, the smaller the deformed ferrite the better.
  • the fraction of the deformed ferrite is preferably an area ratio of 10% or less. Absence is more preferable.
  • the method of measurement of the fractions of the polygonal ferrite and deformed ferrite is to take five 200X optical micrographs, extract the polygonal ferrite and deformed ferrite, and find the values by image analysis.
  • the white regions are polygonal ferrite or deformed ferrite. Regions with an aspect ratio (ratio of horizontal length and vertical length) of less than 3 are defined as polygonal ferrite, while regions with an aspect ratio of 3 or more are defined as deformed ferrite.
  • the later explained method of production may be used. That is, if making the rolling end temperature and/or water cooling start temperature 750°C or more, it is possible to make the fraction of the polygonal ferrite and deformed ferrite at the surface layer region 20% or less. However, if the rolling end temperature and/or the water cooling start temperature decreases below 750°C, the polygonal ferrite and deformed ferrite of the surface layer region increase exceeding 20% as a general trend, so the rolling end temperature and/or the water cooling start temperature preferably is made 750°C or more. Further, to make the fraction of the polygonal ferrite and deformed ferrite 10% or less, it is more preferable to make the rolling end temperature or the water cooling start temperature 770°C or more.
  • the above “fraction” means the area rate when observing the L cross-section (surfaces in plate thickness direction and rolling direction). Further, the structure other than the above polygonal ferrite and deformed ferrite, that is, the structure accounting for 80% or more of the area of the surface layer region, should be bainite and/or acicular ferrite.
  • the structure at the inside from the above surface layer region is not particularly limited, but to secure properties for steel plate and steel pipe for high strength line pipe use with a tensile strength of 500 MPa or more such as base material high strength, base material toughness, HAZ toughness, weldability, etc., it is sufficient to make the structure mainly acicular ferrite or bainite.
  • steel which has the above-mentioned chemical composition is produced by an ordinary method so that the amount of hydrogen in the molten steel after secondary refining becomes 2.5 ppm or less, then is continuously cast to obtain a steel slab, then the steel slab is reheated and rolled by heavy plate rolling to obtain steel plate.
  • the steel plate After finishing rolling, the steel plate is water cooled by a start temperature of 750°C or more and a stop temperature of 400 to 600°C.
  • the "stop temperature" of water cooling referred to here means the highest temperature of the temperature of the steel plate which rises due to reheating after the cooling water is stopped.
  • the recrystallization temperature region is the temperature region where recrystallization occurs after rolling. With the components of the steel of the present invention, it is generally over 900°C.
  • the non-recrystallization temperature region is a temperature region where no recrystallization or ferrite transformation occurs after rolling and is generally 750 to 900°C with the components of the steel of the present invention.
  • the rolling in the recrystallization temperature region is called “recrystallization rolling" or "rough rolling”
  • the rolling in the non-recrystallization temperature region is called the “non-recrystallization rolling" or "final rolling".
  • the maximum hardness of the centerline segregation can be suppressed to 300Hv or less. If making the water cooling start temperature less than 750°C, a large amount of ferrite is formed before the start of cooling, C (carbon) is discharged from the ferrite to the austenite, and C is concentrated at the austenite phase. As a result, the austenite phase where C concentrates transforms to hard martensite which contains a large amount of C in the cooling process.
  • the water cooling start temperature 750°C or more it is possible to suppress the formation of hard martensite, so it is possible to suppress the maximum hardness of the centerline segregation to 300Hv or less. Further, if making the water cooling stop temperature 400°C or more, after the transformation, the hard martensite partially breaks down, so the maximum hardness of the centerline segregation can be suppressed to 300Hv or less. If the water cooling stop temperature is too high, the steel pipe deteriorates in strength, so the water cooling stop temperature is made 600°C or less.
  • the maximum hardness of the surface layer region from the topmost surface down 5 mm to 300Hv or less, in addition to making the water cooling stop temperature 400°C to 600°C or less, it is necessary to optimize the cooling pattern of the surface layer. Specifically, when cooling the surface layer, by performing reheating treatment at least two times, it is possible to make the maximum hardness from the topmost layer down to 5 mm 300Hv or less. This is because by performing reheating, a tempering effect is exhibited and the surface layer region can be lowered in hardness.
  • the lower limit of the reheating temperature is preferably made 300°C, while the upper limit temperature is preferably 750°C.
  • the reheating temperature becomes less than 300°C, 50% or more of martensite is formed and hardens and the surface layer no longer deteriorates in hardness. If the reheating temperature exceeds 750°C, the surface layer region deteriorates too much in hardness.
  • FIG. 3A and FIG. 3B show examples of cooling patterns of the cooling step in the present invention.
  • 1 is the change in temperature due to self-reheating treatment
  • the temperature of 2 is the reheating start temperature
  • the temperature of 3 is the reheating end temperature.
  • the temperature of 4 is the water cooling stop temperature.
  • Such a cooling pattern can be controlled by switching the nozzle for spraying cooling water on and off and adjusting the amount of water.
  • FIG. 3C shows the cooling pattern by the conventional method of production. After stopping the cooling water, the steel plate rises in temperature, so a single reheating is included.
  • the structure of the surface layer region from the topmost surface down to 5 mm can be suppressed to a total fraction of polygonal ferrite and deformed ferrite of 20% or less. If the water cooling start temperature becomes lower than 750°C, it becomes lower than the ⁇ / ⁇ -transformation temperature of 500 MPa or more steel, so polygonal ferrite or deformed ferrite is easily formed and the total fraction of polygonal ferrite and deformed ferrite exceeds 20%.
  • the base material steel plate need only be shaped into a tube, then arc welded at both plate edge beveled to obtain a welded steel pipe.
  • a UOE step of shaping steel plate by a C-press, U-press, and O-press is preferable.
  • arc welding from the viewpoint of the toughness of the weld metal and productivity, it is preferable to employ submerged arc welding.
  • the input heat at the time of arc welding is not particularly limited, but is usually preferably 2.0 to 15.0kJ/mm.
  • the Steels 1 to 35 which have the chemical compositions which are shown in Table 1A to Table 1C were produced and continuously cast to thickness 240 mm or 300 mm steel slabs. Further, Table 1A to Table 1C show analysis values of the amounts of hydrogen of the molten steel.
  • the first reheating start and end temperatures and the second reheating start temperature are shown in Table 2A.
  • the second reheating end temperature (when there is a single reheating treatment, the first reheating end temperature) is the cooling end temperature.
  • Each obtained steel plate was shaped into a tube by a C press, U press, or O press, the end faces were tack welded, main welding was performed from the inside and outside surfaces, then the tube was expanded to obtain steel pipe for line pipe use. Note that, for the main welding, submerged arc welding was applied.
  • Tensile test pieces, HIC test pieces, and macro test pieces were taken from the obtained steel plates and steel pipes and used for the respective tests.
  • the HIC test was performed based on NACETM0284.
  • the macro test pieces were measured for segregation ratios of Mn, Nb, and Ti by EPMA.
  • the segregation ratio was measured by EPMA by probe diameters of 50 ⁇ m and 2 ⁇ m.
  • Vicker's hardness of the centerline segregation and the Vicker's hardness at the surface layer region from the topmost surface of the steel plate and steel pipe down to a depth of 5 mm were measured based on JIS Z 2244.
  • the Vicker's hardness was measured using a 25 g load at the portion of the highest Mn concentration in the distribution of concentration of Mn in the thickness direction measured by EPMA.
  • Table 2A to Table 2C show the thickness of the steel plate, maximum Mn segregation ratio, Nb segregation ratio, Ti segregation ratio, length of center-porosities, maximum hardness of centerline segregation, maximum hardness of surface region, tensile strength and length ratio of HIC (CLR) found by HIC test, and total fraction of polygonal ferrite and deformed ferrite in surface layer region.
  • CLR HIC
  • Table 3 shows the thickness of steel pipe, heat input of main welding, and length ratio of HIC (CLR) found from an HIC test. Note that, the maximum Mn segregation ratio in the steel pipe, Nb segregation ratio, Ti segregation ratio, length of center-porosities, and maximum hardness of centerline segregation are all the same as the steel plate. Further, the tensile strength of steel pipe becomes 10 to 20 MPa or more larger than steel plate.
  • Table 1A Components (mass%) C Si Mn P S Al Ti Nb N Ca 1 0.040 0.10 1.32 0.005 0.0005 0.004 0.012 0.030 0.0025 0.0015 2 0.052 0.13 1.35 0.008 0.0006 0.013 0.003 0.040 0.0030 0.0017 3 0.046 0.08 1.45 0.003 0.0008 0.008 0.012 0.030 0.0021 0.0021 4 0.060 0.07 1.48 0.004 0.0003 0.010 0.016 0.060 0.0018 0.0011 5 0.052 0.25 1.47 0.009 0.0006 0.007 0.012 0.054 0.0015 0.0017 6 0.046 0.10 1.25 0.008 0.0004 0.016 0.012 0.026 0.0023 0.0013 7 0.042 0.02 1.36 0.006 0.0006 0.005 0.013 0.030 0.0031 0.0017 8 0.035 0.15 1.38 0.007 0.0005 0.013 0.008 0.050 0.0035 0.0015
  • Steel Plates 1 to 23 are invention examples. As shown in Table 2A to Table 2C, these steel plates had a maximum Mn segregation ratio of 1.6 or less, Nb segregation ratio of 4.0 or less, and Ti segregation ratio of 4.0 or less. Further, the maximum hardness from the topmost layers of the top and bottom surfaces of the steel plate and the inside and outside surfaces of the steel pipe down to 5 mm are 300Hv or less, while the maximum hardness of the centerline segregation was 300Hv or less. Furthermore, the total fraction of the polygonal ferrite and the deformed ferrite was 20% or less. Therefore, no HIC occurred due to the HIC test. The steel pipes made using these Steel Plates 1 to 23 as materials also gave similar results as shown in Table 3.
  • Steel Plates 24 to 43 are comparative examples outside the scope of the present invention.
  • Steel Plates 24 to 35 have one of the elements among the basic components or optional added elements outside the scope of the present invention.
  • Steel Plates 36 to 43 do not satisfy the production conditions of the present invention.
  • HIC occurred in HIC tests, the CLR exceeded 3%, or the ductile fracture rate of DWTT at 0°C was less than 85%.
  • FIG. 4A shows the hardness distribution from the topmost layer down to 5 mm of the Steel 11 produced by the method of production of the present invention
  • FIG. 4B shows a photo of the structure of the surface layer of the Steel 11.
  • FIG. 5A shows the hardness distribution from the topmost layer down to 5 mm of the Steel 40 produced by the conventional method of production of the present invention
  • FIG. 5B shows a photo of the structure of the surface layer of the Steel 40.
  • the hardness distribution of the steel plate of the present invention which is shown in FIG. 4A has a maximum hardness of a low 245Hv, but the hardness distribution of the steel plate which was produced by the conventional method which is shown in FIG. 5A has a part where the hardness locally exceeds 300Hv. This can become the starting point of HIC.
  • the steel plate which was produced by the conventional method which is shown in FIG. 5B was treated for reheating one time, so the base material was not sufficiently tempered and a hard structure was formed.

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Claims (7)

  1. Ein Stahlrohr zur Verwendung als hochfestes Leitungsrohr mit hervorragender Beständigkeit gegen wasserstoffinduzierte Rissbildung,
    wobei
    das Stahlrohr aus einem Stahlblech hergestellt ist, bestehend aus, in Massen-%,
    C: 0,02 bis 0,08%,
    Si: 0,01 bis 0,5%,
    Mn: 1,2 bis 1,8%,
    Nb: 0,001 bis 0,10%,
    Ca: 0,0005 bis 0,0050%,
    N: 0,0010 bis 0,0060%,
    O: 0,0001 bis 0,0035 %, und
    gegebenenfalls ferner enthaltend, in Massen-%, eines oder mehrere von
    Ni: 0,01 bis 2,0%,
    Cu: 0,01 bis 1,0%,
    Cr: 0,01 bis 1,0%,
    Mo: 0,01 bis 0,60%,
    W: 0,01 bis 1,0%,
    V: 0,01 bis 0,10%,
    Zr: 0,0001 bis 0,050%,
    Ta: 0,0001 bis 0,050%,
    B: 0,0001 bis 0,0020%,
    Seltenerdmetalle: 0,0001 bis 0,01%,
    Mg: 0,0001 bis 0,01%,
    Y: 0,0001 bis 0,005%,
    Hf: 0,0001 bis 0,005% und
    Re: 0,0001 bis 0,005% und
    einem Rest bestehend aus Fe und unvermeidbaren Verunreinigungen, wobei Gehalte beschränkt sind auf
    P: 0,01% oder weniger,
    S: 0,0020% oder weniger,
    Al: 0,030% oder weniger, und
    Ti: 0,030% oder weniger, und
    Gehalte von S und Ca
    S/Ca<0,5
    erfüllen;
    das Stahlblech erfüllt:
    maximales Mn-Seigerungsverhältnis: 2,0 oder weniger,
    Nb-Seigerungsverhältnis: 4,0 oder weniger,
    Ti-Seigerungsverhältnis: 4,0 oder weniger,
    Länge der Zentrums-Porositäten an der Mittellinienseigerung: 0,1 mm oder weniger,
    maximale Härte der Mittellinienseigerung: 300 HV oder weniger,
    maximale Härte des Oberflächenschichtbereichs von der obersten Oberfläche von zwei Vorder- und Rückblechoberflächen bis zu einer Tiefe von 5 mm: 300 HV oder weniger, und
    einen Gesamtanteil an polygonalem Ferrit und verformtem Ferrit mit einem Seitenverhältnis von 3 oder mehr im Oberflächenschichtbereich von der obersten Oberfläche von zwei Vorder- und Rückblechoberflächen bis zu einer Tiefe von 5 mm: 0,1 bis 20%, wobei die von polygonalem Ferrit und verformtem Ferrit verschiedene Struktur Bainit- und/oder nadelförmiger Ferrit ist;
    wobei der Gesamtanteil von polygonalem Ferrit und verformtem Ferrit mit einem Seitenverhältnis von 3 oder mehr im Oberflächenschichtbereich von der obersten Oberfläche von zwei Vorder- und Rückblechoberflächen bis zu einer Tiefe von 5 mm gemessen wird, indem fünf 200X optische Mikroskopieaufnahmen in Oberflächen in Blechdickenrichtung und Walzrichtung aufgenommen werden, die Flächenanteile des polygonalen Ferrits und verformten Ferrits gemessen werden und ihr Gesamtanteil berechnet wird, und
    Dicke "t"[mm] des Stahlblechs und Außendurchmesser D [mm] des Stahlrohres nach der Rohrherstellung
    t≥25 und
    t/D≥0,035 entspricht.
  2. Das Stahlrohr zur Verwendung als hochfestes Leitungsrohr mit hervorragender Beständigkeit gegen wasserstoffinduzierte Rissbildung nach Anspruch 1, wobei das Stahlblech in Massen-% einen oder mehrere enthält:
    Ni: 0,01 bis 2,0%,
    Cu: 0,01 bis 1,0%,
    Cr: 0,01 bis 1,0%,
    Mo: 0,01 bis 0,60%,
    W: 0,01 bis 1,0%,
    V: 0,01 bis 0,10%,
    Zr: 0,0001 bis 0,050%,
    Ta: 0,0001 bis 0,050%,
    B: 0,0001 bis 0,0020%,
    Seltenerdmetalle: 0,0001 bis 0,01%,
    Mg: 0,0001 bis 0,01%,
    Y: 0,0001 bis 0,005%,
    Hf: 0,0001 bis 0,005% und
    Re: 0,0001 bis 0,005%.
  3. Das Stahlrohr zur Verwendung als hochfestes Leitungsrohr mit hervorragender Beständigkeit gegen wasserstoffinduzierte Rissbildung nach Anspruch 1 oder 2, wobei es kein verformtes Ferrit mit einem Seitenverhältnis von 3 oder mehr im Oberflächenschichtbereich von der obersten Oberfläche von zwei Vorder- und Rückblechoberflächen bis zu einer Tiefe von 5 mm gibt.
  4. Ein Stahlblech zur Verwendung für ein hochfestes Leitungsrohr mit hervorragender Beständigkeit gegen wasserstoffinduzierte Rissbildung, wobei das Stahlblech, verwendet für das Stahlrohr zur Verwendung als hochfestes Leitungsrohr mit hervorragender Beständigkeit gegen wasserstoffinduzierte Rissbildung, nach einem der Ansprüche 1 bis 3 ist.
  5. Ein Verfahren zur Herstellung eines Stahlblechs zur Verwendung für ein hochfestes Leitungsrohr mit hervorragender Beständigkeit gegen wasserstoffinduzierte Rissbildung nach Anspruch 4, wobei das Verfahren die Schritte umfasst:
    einen Schritt des Herstellens von geschmolzenem Stahl, bestehend aus, in Massen-%,
    C: 0,02 bis 0,08%,
    Si: 0,01 bis 0,5%,
    Mn: 1,2 bis 1,8%,
    Nb: 0,001 bis 0,10%,
    Ca: 0,0005 bis 0,0050%,
    N: 0,0010 bis 0,0060%,
    O: 0,0001 bis 0,0035 %, und
    gegebenenfalls ferner enthaltend, in Massen-%, eines oder mehrere von
    Ni: 0,01 bis 2,0%,
    Cu: 0,01 bis 1,0%,
    Cr: 0,01 bis 1,0%,
    Mo: 0,01 bis 0,60%,
    W: 0,01 bis 1,0%,
    V: 0,01 bis 0,10%,
    Zr: 0,0001 bis 0,050%,
    Ta: 0,0001 bis 0,050%,
    Seltenerdmetalle: 0,0001 bis 0,01%,
    B: 0,0001 bis 0,0020%,
    Mg: 0,0001 bis 0,01%,
    Y: 0,0001 bis 0,005%,
    Hf: 0,0001 bis 0,005% und
    Re: 0,0001 bis 0,005% und
    einem Rest bestehend aus Fe und unvermeidbaren Verunreinigungen, wobei
    Gehalte beschränkt sind auf
    P: 0,01% oder weniger,
    S: 0,0020% oder weniger,
    Al: 0,030% oder weniger, und
    Ti: 0,030% oder weniger,
    Gehalte von S und Ca
    S/Ca<0,5
    erfüllen, und
    ein Gehalt an Wasserstoff nach dem Sekundärfrischen 2,5 ppm oder weniger beträgt;
    einen Schritt des Herstellens einer Stahlbramme aus dem geschmolzenen Stahl durch Stranggießen;
    einen Schritt des Erwärmens der Stahlbramme auf 1000°C oder mehr;
    einen Schritt des Warmwalzens der erwärmten Stahlbramme bei einer Reduktionsrate in einem Rekristallisationstemperaturbereich von 2 oder mehr und einer Reduktionsrate in dem Nicht-Rekristallisationstemperaturbereich von 3 oder mehr, um ein Stahlblech zu erhalten; und
    einen Abkühlschritt des Wasserkühlens des Stahlblechs von 750°C oder mehr auf 400 bis 600°C, wobei der Abkühlschritt mindestens zwei Selbstwiedererwärmungsbehandlungen beinhaltet, welche die Temperatur des Stahlblechs erhöhen, und
    bei der Selbstwiedererwärmungsbehandlung eine Anfangstemperatur einer ersten Selbstwiedererwärmungsbehandlung 300°C oder mehr beträgt und eine Endtemperatur aller Selbstwiedererwärmungsbehandlungen weniger als 750°C beträgt.
  6. Ein Verfahren zur Herstellung eines Stahlblechs zur Verwendung für ein hochfestes Leitungsrohr mit hervorragender Beständigkeit gegen wasserstoffinduzierte Rissbildung, nach Anspruch 5, wobei der geschmolzene Stahl in Massen-% einen oder mehrere von
    Ni: 0,01 bis 2,0%,
    Cu: 0,01 bis 1,0%,
    Cr: 0,01 bis 1,0%,
    Mo: 0,01 bis 0,60%,
    W: 0,01 bis 1,0%,
    V: 0,01 bis 0,10%,
    Zr: 0,0001 bis 0,050%,
    Ta: 0,0001 bis 0,050%,
    B: 0,0001 bis 0,0020%,
    Seltenerdmetalle: 0,0001 bis 0,01%,
    Mg: 0,0001 bis 0,01%,
    Y: 0,0001 bis 0,005%,
    Hf: 0,0001 bis 0,005% und
    Re: 0,0001 bis 0,005%
    enthält.
  7. Ein Verfahren zur Herstellung eines Stahlrohres zur Verwendung für ein hochfestes Leitungsrohr mit hervorragender Beständigkeit gegen wasserstoffinduzierte Rissbildung nach Anspruch 1, wobei das Verfahren die Schritte umfasst:
    zuerst Ausführen des Verfahrens nach Anspruch 5 zum Herstellen eines Stahlblechs, gefolgt von den Schritten:
    einen Schritt des Formens des Stahlblechs zu einer Röhrenform; und
    einen Schritt des Verschweißens beider abgeschrägten Blechkanten;
    wobei eine Dicke "t" [mm] des Stahlblechs und ein Außendurchmesser D [mm] des Stahlrohres nach der Rohrherstellung
    t≥25 und
    t/D≥0,035
    erfüllen.
EP13768001.3A 2012-03-30 2013-03-29 Hochfestes stahlrohr für leitungsrohr mit hervorragender beständigkeit gegen wasserstoffinduzierte rissbildung, hochfestes stahlblech für ein leitungsrohr damit und verfahren zur herstellung davon Active EP2832879B1 (de)

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CN104024461B (zh) 2016-04-06
BR112014019281A2 (de) 2017-06-20
JP5392441B1 (ja) 2014-01-22
EP2832879A1 (de) 2015-02-04
BR112014019281A8 (pt) 2017-07-11
KR101615842B1 (ko) 2016-04-26
EP2832879A4 (de) 2016-01-13
KR20140116913A (ko) 2014-10-06
JPWO2013147197A1 (ja) 2015-12-14
WO2013147197A1 (ja) 2013-10-03

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