EP3124639B1 - Stahlblech für hochfestes leitungsrohr mit hervorragender tieftemperaturzähigkeit und stahlrohr für hochfestes leitungsrohr - Google Patents

Stahlblech für hochfestes leitungsrohr mit hervorragender tieftemperaturzähigkeit und stahlrohr für hochfestes leitungsrohr Download PDF

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EP3124639B1
EP3124639B1 EP15770365.3A EP15770365A EP3124639B1 EP 3124639 B1 EP3124639 B1 EP 3124639B1 EP 15770365 A EP15770365 A EP 15770365A EP 3124639 B1 EP3124639 B1 EP 3124639B1
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steel plate
content
line pipe
steel
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French (fr)
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EP3124639A1 (de
EP3124639A4 (de
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Yoshiyuki Kobayashi
Haruya KAWANO
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Kobe Steel Ltd
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Kobe Steel 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • 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
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/10—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
    • C21D9/14—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes wear-resistant or pressure-resistant pipes
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—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
    • C22C38/06—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
    • 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 steel plate for a high-strength line pipe and to a steel tube for a high-strength line pipe manufactured from the steel plate for a high-strength line pipe.
  • the present invention relates to a steel plate for a high-strength line pipe having an excellent critical CTOD (Crack Tip Opening Displacement) value and to a steel tube for a high-strength line pipe.
  • CTOD Critical Tip Opening Displacement
  • Line pipes used for transportation of natural gas and oil tend to undergo high pressure as an operating pressure for the purpose of improving the transportation efficiency.
  • Steel plates for such line pipes are required to have higher strength. Additionally, in terms of safety, steel plates are required to exhibit excellent CTOD properties in a CTOD test, which is an assessment index of fracture toughness as a characteristics of brittle fracture occurrence prevention.
  • dislocation strengthening which involves strengthening the material by increasing the dislocation density, can be exhibited by increasing a cumulative rolling reduction ratio in the so-called dual-phase temperature range, where part of an austenite single-phase microstructure is transformed into ferrite in a rolling step of the manufacturing procedure of a steel plate.
  • the dislocation strengthening mechanism can be applied more easily, compared to other strengthening mechanisms.
  • Patent Document 2 has proposed the application of special rolling conditions in which a steel plate is on standby while being air-cooled in rolling until its temperature decreases by 80°C or more in order to avoid the rolling in a temperature range that causes separation.
  • Patent Document 3 has proposed a technique that involves setting the upper limit of S content lower to decrease the amount of MnS formed, which would cause the separation, thereby suppressing the occurrence of separation.
  • Patent Documents 1 and 2 are very useful in enabling suppression of the occurrence of separation and increasing the critical CTOD value.
  • these techniques require the solid solution strengthening by the addition of expensive elements, the complicated manufacturing steps incorporating the combination of the water-cooling equipment and heating equipment on line, and the adoption of the special rolling conditions, which inevitably leads to an increase in costs and a decrease in productivity.
  • Patent Document 3 cannot eliminate MnS completely, which is not sufficient as a technique of suppressing the occurrence of separation.
  • EP3018231 A1 , EP2980238 A1 and JP2013213242 A disclosed a steel plate with excellent hydrogen-induced cracking resistance.
  • JP2012072472 A and JP2003096517 A disclosed a steel plate for a high-strength line pipe.
  • the present invention has been made in view of the foregoing circumstances, and it is an object of the present invention to provide a steel plate for a high-strength line pipe with excellent low temperature toughness that can ensure the high critical CTOD value even when separation occurs, and can be easily manufactured at low cost, as well as a steel tube for a high-strength line pipe produced by using such a steel plate for a high- strength line pipe.
  • a steel plate for a high-strength line pipe according to the present invention that can solve the above-mentioned problems is defined in claim 1.
  • the present invention also includes a steel tube for a high-strength line pipe having excellent low temperature toughness manufactured by using the above-mentioned steel plate for a high-strength line pipe.
  • the present invention appropriately defines a chemical composition of the steel plate, and sets the average grain size of the steel plate in the t/4 position where t is the thickness of the steel plate as well as the separation index SI measured on the fracture surface of a Charpy specimen at a specified temperature, in respective appropriate ranges.
  • the present invention can achieve the steel plate for a high-strength line pipe that has excellent low temperature toughness and a tensile strength of 520 MPa or more and that can obtain the excellent critical CTOD value even when separation occurs in the CTOD test.
  • Fig. 1 is a schematic diagram of a fracture surface of a Charpy specimen for explaining a measurement method of a separation index SI.
  • the inventors have aimed to create a steel plate for a high-strength line pipe that can obtain the excellent critical CTOD value while allowing for the occurrence of separation to some extent without completely shutting out the occurrence of separation, and they have studied about the relationship between the occurrence of the separation in the CTOD test and the microstructure of the steel plate.
  • the critical CTOD value measured in the CTOD test has a correlation with the separation index SI in the Charpy test, and that to ensure the excellent low-temperature toughness, ensuring the toughness of the steel plate as a base material by refining the grain is effective.
  • the average grain size In terms of ensuring the excellent low temperature toughness, it is necessary to attain the adequate toughness of a base material by refining the grains. To ensure the target low temperature toughness, the average grain size needs to be 10 ⁇ m or less in the t/4 position, which is the representative position for evaluating the steel plate properties.
  • the average grain size is preferably 8.0 ⁇ m or less, and more preferably 7.0 ⁇ m or less. The smaller average grain size is better, but the lower limit of the grain size is approximately 4 ⁇ m or more.
  • the separation index SI of the fracture surface of the Charpy specimen of the steel plate at the specified temperature is set at 0.30 mm/mm 2 or less, thereby making it possible to ensure the target critical CTOD value even when separation occurs in the CTOD test.
  • the target critical CTOD value is equal to or more than 0.15 mm when a testing temperature is set at -10°C.
  • the above-mentioned specified temperature can be determined from the following equation (1). That is, the testing temperature (specified temperature) for performing the Charpy test varies depending on the thickness of the steel plate. To evaluate the target critical CTOD value which is supposed at the testing temperature of -10°C, it is also necessary to consider this specified temperature (T 1 ).
  • T 1 T 2 ⁇ 6 ⁇ t 1 / 2 + 20
  • T 1 is a Charpy testing temperature (°C)
  • T 2 is a CTOD testing temperature (°C), which is -10°C in the present specification
  • t is a thickness (mm) of the steel plate.
  • the separation index SI can be determined by dividing the total length of separations occurring in the direction perpendicular to the plate thickness direction on a fracture surface of the Charpy specimen by an area (cross-sectional area) of the fracture surface of the specimen (see Fig. 1 to be mentioned later).
  • SI ⁇ L n / S A where L n indicates a length (mm) of an n-th separation, and S A is a cross-sectional area (mm 2 ) of the fracture surface of the specimen.
  • the separation index SI determined as mentioned above needs to be 0.30 mm/mm 2 or less.
  • the separation index SI is preferably 0.20 mm/mm 2 or less, and more preferably 0.15 mm/mm 2 or less. Note that from the purpose that even though separation occurs, the high critical CTOD value is exhibited, the separation index SI is not necessarily 0 mm/mm 2 .
  • the separation index SI is preferably 0.05 mm/mm 2 or more, and more preferably 0.10 mm/mm 2 or more.
  • the chemical composition of the steel plate for a high-strength line pipe according to the present invention also needs to be adjusted as appropriate.
  • the reason for setting the ranges of the respective chemical components in the composition will be mentioned below.
  • the term % as used herein means % by mass.
  • Carbon (C) is an element essential to ensure the strengths of a steel plate as a base material and a weld zone.
  • the C content needs to be 0.02% or more.
  • the C content is preferably 0.03% or more, and more preferably 0.05% or more. Any excessive C content, however, is more likely to form a martensitic island (MA: Martensite-Austenite constituent), decreasing the toughness of a heat affected zone (HAZ) of the steel plate, and degrading the weldability. From this perspective, the C content needs to be 0.20% or less. Further, the C content is preferably 0.15% or less, and more preferably 0.12% or less.
  • Silicon (Si) has a deoxidation function and is effective in improving the strength of the steel plate as the base material and a weld zone. To exhibit these effects, the Si content is set at 0.02% or more. The Si content is preferably 0.05% or more, and more preferably 0.15% or more. However, any excessive Si content degrades the weldability and toughness. Accordingly, the Si content needs to be suppressed to 0.50% or less. The Si content is preferably 0.45% or less, and more preferably 0.35% or less.
  • Manganese (Mn) is an element that is effective in improving the strengths of a steel plate as a base material and a weld zone. To exhibit these effects, the Mn content is more than 1.2%. However, any excessive Mn content not only promotes the occurrence of the separation because of the formation of MnS, but also degrades the HAZ toughness and weldability of the steel plate. Thus, the upper limit of the Mn content is set at 2.0% or less. The Mn content is preferably 1. 9% or less and more preferably 1.8% or less.
  • Phosphorus (P) is an element inevitably contained in a steel plate.
  • the P content exceeds 0.02%, the base material toughness and the HAZ toughness of the steel plate are drastically degraded.
  • the P content is 0.010% or less.
  • the P content is preferably reduced as much as possible, but it is difficult to industrially set the P content at 0%.
  • the upper limit of S content is set at 0.01% or less.
  • the S content is preferably 0.008% or less, more preferably 0.0060% or less, and further preferably 0.0050% or less.
  • the S content is desirably set small, but it is difficult to industrially set the S content to less than 0.0001%.
  • the lower limit of the S content is approximately 0.0001% or more.
  • Aluminum (Al) is a strong deoxidation element. To obtain the deoxidation effect, the Al content needs to be 0 .010% or more. Thus, the Al content is preferably 0.020% or more, and more preferably 0.030% or more. On the other hand, any excessive Al content forms a large amount of AlN to decrease the amount of TiN precipitates, degrading the HAZ toughness. Thus, the Al content needs to be 0.080% or less. The Al content is preferably 0.060% or less, and more preferably 0.050% or less.
  • Niobium (Nb) is an element effective in enhancing the strength and the base material toughness of the steel plate without degrading its weldability. To exhibit such effects, the Nb content needs to be 0.002% or more.
  • the Nb content is preferably 0.005% or more, and more preferably 0.010% or more. However, when the Nb content becomes excessive to exceed 0.060%, the toughness of the base material and HAZ is degraded. Thus, the upper limit of Nb content is set to 0.060% or less.
  • the Nb content is preferably 0.050% or less, and more preferably 0.040% or less.
  • Titanium (Ti) precipitates as TiN in a steel.
  • Ti is an element required to improve the base material toughness by the suppression of coarsening of austenite grains during heating of a slab and to improve the HAZ toughness by the coarsening of austenite grains in the HAZ during welding.
  • the Ti content needs to be 0. 003% or more.
  • the Ti content is preferably 0.005% or more, and more preferably 0. 010% or more.
  • any excessive Ti content degrades the base material and HAZ toughness, because of solute Ti and precipitated TiC.
  • the Ti content needs to be 0.030% or less.
  • the Ti content is preferably 0.025% or less, and more preferably 0.020% or less.
  • Calcium (Ca) serves to control the form of a sulfide and has an effect of suppressing the formation of MnS by forming CaS. To exhibit such an effect, the Ca content needs to be 0.0003% or more.
  • the Ca content is preferably 0.0005% or more, and more preferably 0.0010% or more.
  • the upper limit of the Ca content is 0.0060% or less.
  • the Ca content is preferably 0.0050% or less, and more preferably 0.0040% or less.
  • N Nitrogen
  • the N content is set at 0.0010% or more.
  • the N content is preferably 0.0030% or more, and more preferably 0. 0040% or more. Any excessive N content, however, degrades the HAZ toughness by the presence of the solid-solution N. Thus, the N content needs to be 0.010% or less.
  • the N content is preferably 0.0080% or less, and more preferably 0.0060% or less.
  • a rare earth element is an element effective in controlling the form of a sulfide and has an effect of suppressing the formation of MnS by forming REMS.
  • the REM content needs to be 0.0001% or more.
  • the REM content is preferably 0.0003% or more, and more preferably 0.0005% or more.
  • the upper limit of the REM content is 0.0300% or less. Note that in the present invention, REM means 15 lanthanoid elements from La to Lu, scandium Sc and yttrium Y.
  • Zirconium (Zr) contributes to improving the HAZ toughness by forming an oxide and dispersing it finely in the steel. To exhibit such an effect, the Zr content needs to be 0.0001% or more.
  • the Zr content is preferably 0.0003% or more, and more preferably 0.0005% or more.
  • any excessive Zr content forms coarse inclusions to degrade the base material toughness.
  • the Zr content needs to be 0.0200% or less.
  • the Zr content is preferably 0.0100% or less, and more preferably 0.0050% or less.
  • the chemical composition of the steel plate for a high-strength line pipe according to the present invention has been mentioned above in terms of its essential elements.
  • the balance of the steel plate is substantially iron.
  • inevitable impurities are allowed to be brought and contained in the steel, depending on the situations, including raw materials, construction materials, facilities and the like.
  • the above-mentioned inevitable impurities can include, for example, As, Sb, Sn, O, H and the like.
  • the steel plate for a line pipe according to the present invention also preferably further contains one or more elements selected from the group consisting of Cu, Ni, Cr, Mo and V in the following amounts as needed.
  • the reasons for setting ranges when allowing the steel plate to contain these optional elements are as follows.
  • Copper (Cu) is an element effective in enhancing the strength of the steel plate. To exhibit such an effect, the Cu content needs to be 0.01% or more.
  • the Cu content is more preferably 0.05% or more, and further preferably 0.10% or more. Any excessive Cu content, however, degrades the base material toughness.
  • the Cu content is preferably set at 1.50% or less.
  • the Cu content is more preferably 1.0% or less, and further preferably 0.50% or less.
  • Nickel (Ni) is an element effective in improving the strength and toughness of the base material and weld zone. To exhibit such effects, the Ni content needs to be 0.01% or more. Accordingly, the Ni content is more preferably 0.05% or more, and further preferably 0.10% or more. A large content of Ni, however, makes the structural steel plate extremely expensive. From the economic point of view, the Ni content is preferably 1.50% or less. The Ni content is more preferably 1.0% or less, and further preferably 0.50% or less.
  • Chrome (Cr) is an element effective in improving the strength of the steel plate.
  • the Cr content is preferably 0.01% or more.
  • the Cr content is more preferably 0.05% or more, and further preferably 0.10% or more.
  • the Cr content is preferably 1.50% or less.
  • the Cr content is more preferably 1.0% or less, and further preferably 0.50% or less.
  • Molybdenum (Mo) is an element effective in improving the strength and toughness of the base material. To exhibit such effects, the Mo content needs to be 0. 01% or more.
  • the Mo content is more preferably 0.05% or more, and further preferably 0.10% or more. However, when the Mo content exceeds 1.50%, the HAZ toughness and weldability of the steel plate are degraded.
  • the Mo content is preferably 1.50% or less, more preferably 1.0% or less, and further preferably 0.50% or less.
  • Vanadium (V) is an element effective in improving the strength of the steel plate. To obtain such an effect, the V content is preferably 0.003% or more. The V content is more preferably 0.010 % or more. On the other hand, when the V content exceeds 0.1%, the weldability of the steel plate and the base material toughness thereof are degraded. Thus, the V content is preferably 0.1% or less, and more preferably 0.08% or less.
  • Cu, Ni, Cr, Mo and V are elements that improve the strength and toughness of the base material and the HAZ, and may be used individually, or alternatively two or more of these elements may be used together, as needed.
  • the steel plate does not have the following composition in percent by mass: C: 0.07%, Si: 0.32%, Mn: 1.44%, P: 0.006%, S: 0.0009%, Al: 0.025%, Ca: 0.0036%, N: 0.0047%, O: 0.0021%, Ti: 0.011%, Cu: 0.15%, Ni: 0.23%, Cr: 0.26%, Mo: 0.09%, Nb: 0.010%, REM: 0.0021%, and Zr: 0.0011%, with the balance being iron and inevitable impurities.
  • REM and Ca need to be added after the steel plate is deoxidized by Al and Zr, that is, after Al 2 O 3 and ZrO are formed by Al and Zr.
  • Ca is apt to form an oxide.
  • Ca is more likely to form an oxide (CaO) rather than a sulfide (CaS) .
  • the time until the completion of casting is required to be restricted.
  • a cast steel should be produced such that solidification is completed within 200 minutes after the addition of Ca. Further, the time from the sufficient formation of the REMS by the addition of REM to the addition of Ca, which has a higher sulfide formation capability than REM, should be four minutes or more.
  • Ca and REM are present in the form of sulfides without forming any oxide.
  • the slab is reheated at a heating temperature of 1,050 to 1,250°C, which is a normal temperature range, followed by a predetermined rough rolling.
  • the rolled slab is hot-rolled in a temperature range of an Ar 3 transformation point to 950°C (hereinafter referred to as an "Ar 3 point to 950°C”) in such a manner that a cumulative rolling reduction ratio is 50% or more.
  • the cumulative rolling reduction ratio is preferably 55% or more, and more preferably 60% or more.
  • the upper limit of the cumulative rolling reduction ratio is approximately 80% or less in terms of actual operation.
  • the cumulative rolling reduction ratio is preferably 10% or more, and more preferably 15% or more.
  • the cumulative rolling reduction ratio exceeds 35%, the texture is developed, resulting in an increase in the separation index SI.
  • the cumulative rolling reduction ratio should be 35% or less.
  • the cumulative rolling reduction ratio is preferably 30% or less, and more preferably 25% or less.
  • Cumulative rolling reduction ratio means a value determined by calculation from the following equation (3).
  • the above-mentioned temperature is defined as an average temperature determined by calculation from the surface temperature of the slab or steel plate, taking into consideration the plate thickness and the like.
  • Cumulative Rolling Reduction Ratio t 0 ⁇ t 1 / t 2 ⁇ 100 where in the equation (3) above, t 0 is a rolling start thickness (mm) of the steel plate when the average temperature is within the rolling temperature range; t 1 is a rolling end thickness (mm) of the steel plate when the average temperature is within the rolling temperature range; and t 2 is a thickness of a cast piece (e.g., slab) before the rolling.
  • Ar 3 point for use is a point determined by the equation (4) below. The same goes for values shown in Table 2 as will be mentioned later.
  • Ar 3 ° C 910 ⁇ 310 ⁇ C ⁇ 80 ⁇ Mn ⁇ 20 ⁇ Cu ⁇ 15 ⁇ Cr ⁇ 55 ⁇ Ni ⁇ 80 ⁇ Mo + 0.35 ⁇ t ⁇ 8
  • [C], [Mn], [Cu], [Cr], [Ni] and [Mo] indicate the contents (% by mass) of C, Mn, Cu, Cr, Ni and Mo, respectively
  • t is a plate thickness (mm) when measuring the temperature.
  • the plate thickness of the steel plate for a high-strength line pipe according to the present invention is not specifically limited, but when using the steel plate as the material for the line pipe, the plate thickness is preferably at least 6 mm or more, and more preferably 10 mm or more.
  • the upper limit of the plate thickness of the steel plate is preferably 30 mm or less, and more preferably 25 mm or less.
  • the steel plate for a high-strength line pipe according to the present invention is formed into a steel tube for a line pipe thereafter.
  • the obtained steel tube reflects the properties of the steel plate as raw material and thus has excellent low temperature toughness.
  • the obtained slab was reheated at a heating temperature of 1,080 to 1,180°C shown in Table 2, followed by the predetermined rough rolling.
  • the rough-rolled steel was further hot-rolled at a cumulative rolling reduction ratio shown in Table 2 below at the temperature of Ar 3 point to 950°C.
  • the hot-rolled steel was further rolled at a cumulative rolling reduction ratio shown in Table 2 below in the so-called dual-phase temperature range from (Ar 3 - 60°C) to Ar 3 point, and was then allowed to cool, thereby producing a steel plate of each steel.
  • the rolling conditions are shown in Table 2 below together with the plate thickness t after the rolling, steel and Ar 3 point (samples No. 1 to 18). [Table 2] Test No.
  • a specimen of each sample was used in which its cross-sectional surface (L cross-sectional surface) perpendicular to the steel plate surface and in parallel with the rolling direction was polished and corroded with nital.
  • the average ferrite grain size in each specimen was determined using an intercept method on photomicrographs that were taken at a magnification of 400x in the t/4 position as the measurement position where t is a thickness plate.
  • an yield stress and a tensile strength of the respective samples were measured using a full thickness tensile specimen of each sample in conformity with API-5L standard by test methods based on the standard. In this way, the tensile properties of the samples were evaluated.
  • FIG. 1 is a schematic diagram of a fracture surface of the Charpy specimen when measuring the separation index SI. Referring to Fig.
  • reference numeral 1 denotes a separation
  • 2 denotes a fracture surface
  • 3 denotes a 2 mm V notch
  • 4 denotes the plate thickness direction.
  • the separation index SI of each sample was determined by measuring lengths L 1 to L 3 of the separations generated at the fracture surface of the Charpy specimen of each sample and dividing the total length by the cross-sectional area of the fracture surface of the specimen according to the above equation (2).
  • a three-point bending CTOD specimen with B x 2B geometry of each sample in conformity with BS7448 standard was used to evaluate the CTOD properties by a test method based on the standard.
  • the CTOD test was performed on two tests of each steel plate at -10°C. One of them with the lower CTOD value was adopted as the critical CTOD value.
  • Sample Nos. 1 to 12 satisfied all the chemical composition, the average grain size and the separation index SI specified by the present invention. It is found that the critical CTOD values of the sample Nos. 1 to 12 satisfied the target value range of 0.15 mm or more, even though separation occurred at the testing temperature of -10°C in the CTOD test.
  • sample Nos. 13 to 18 did not satisfy at least one of the requirements defined by the present invention, and as a result, the critical CTOD values of these samples did not reach the target value.
  • the cumulative rolling reduction ratios in the dual-phase temperature range became high, developing the textures, leading to large separation indexes SI. As a result, their critical CTOD values were small.
  • the cumulative rolling reduction ratio in the range of Ar 3 point to 950°C became lower, increasing the average grain size to degrade the base material toughness.
  • its critical CTOD value did not reach the target value.
  • the sample No. 16 used the steel plate made of the steel I that contained Mn in an excessive amount by way of example.
  • MnS was supposed to be formed in the center segregation part of the steel plate, leading to a large separation index SI.
  • its critical CTOD value did not reach the target value.
  • the sample No. 17 used the steel plate made of the steel J that contained P in an excessive amount by way of example, which degraded its base material toughness. As a result, its critical CTOD value did not reach the target value.
  • the sample No. 18 used the steel plate made of the steel K that contained S in an excessive amount by way of example. Thus, like the sample No. 16, MnS was supposed to be formed in the center segregation part of the steel plate, leading to a large separation index SI. As a result, its critical CTOD value did not reach the target value.

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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)

Claims (2)

  1. Stahlblech für ein hochfestes Leitungsrohr mit hervorragender Tieftemperaturzähigkeit, umfassend, in Massenprozent:
    C: 0,02 bis 0,20 %,
    Si: 0,02 bis 0,50 %,
    Mn: mehr als 1,2 % bis 2,0 %,
    P: 0 % überschreitend und 0,010 % oder weniger,
    S: 0 % überschreitend und 0,01 % oder weniger,
    AI: 0,010 bis 0,080 %,
    Nb: 0,002 bis 0,060 %,
    Ti: 0,003 bis 0,030 %,
    Ca: 0,0003 bis 0,0060 %,
    N: 0,0010 bis 0,010 %,
    REM: 0,0001 bis 0,0300 %, und
    Zr: 0,0001 bis 0,0200 %,
    gegebenenfalls weiter umfassend ein oder zwei oder mehrere Elemente, ausgewählt aus der Gruppe, bestehend aus, in Massenprozent:
    Cu: 0 % überschreitend und 1,50 % oder weniger,
    Ni: 0 % überschreitend und 1,50 % oder weniger,
    Cr: 0 % überschreitend und 1,50 % oder weniger,
    Mo: 0 % überschreitend und 1,50 % oder weniger, und
    V: 0 % überschreitend und 0,1 % oder weniger,
    worin der Rest Eisen und unvermeidliche Verunreinigungen ist, wobei eine durchschnittliche Korngröße des Stahlblechs 10 µm oder weniger in einer t/4-Position beträgt, worin t eine Dicke des Stahlblechs ist, und
    ein Trennungsindex SI, gemessen auf einer Bruchoberfläche einer 2 mm V-gekerbten Charpy-Probe des Stahlblechs in Übereinstimmung mit Standard ASTM-A370 bei einer vorgegebenen Temperatur, 0 mm/mm2 überschreitet und 0,30 mm/mm2 oder weniger beträgt,
    wobei das Stahlblech nicht die nachstehende Zusammensetzung in Massenprozent aufweist:
    C: 0,07 %, Si: 0,32 %, Mn: 1,44 %, P: 0,006 %, S: 0,0009 %, Al: 0,025 %, Ca: 0,0036 %, N: 0,0047 %, O: 0,0021 %, Ti: 0,011 %, Cu: 0,15 %, Ni: 0,23 %, Cr: 0,26 %, Mo: 0,09 %, Nb: 0,010 %, REM: 0,0021 %, und Zr: 0,0011 %, worin der Rest Eisen und unvermeidliche Verunreinigungen ist.
  2. Stahlröhre für ein hochfestes Leitungsrohr mit hervorragender Tieftemperaturzähigkeit, hergestellt unter Verwendung des Stahlblechs für ein hochfestes Leitungsrohr nach Anspruch 1.
EP15770365.3A 2014-03-28 2015-03-25 Stahlblech für hochfestes leitungsrohr mit hervorragender tieftemperaturzähigkeit und stahlrohr für hochfestes leitungsrohr Active EP3124639B1 (de)

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PCT/JP2015/059122 WO2015147055A1 (ja) 2014-03-28 2015-03-25 低温靭性に優れた高強度ラインパイプ用鋼板および高強度ラインパイプ用鋼管

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JPH0920921A (ja) * 1995-06-30 1997-01-21 Kobe Steel Ltd セパレーションを利用する高靱性鋼板の製造方法
JPH1171615A (ja) * 1997-08-29 1999-03-16 Nippon Steel Corp 低温靱性に優れた厚鋼板の製造方法
JP4660034B2 (ja) * 2001-08-27 2011-03-30 新日本製鐵株式会社 高い衝撃吸収エネルギーを有する板厚１５ｍｍ以下のＸ７０級鋼板の非水冷型製造方法。
JP4705287B2 (ja) * 2001-09-20 2011-06-22 新日本製鐵株式会社 高い吸収エネルギーを有する薄手高強度鋼板の非水冷型製造方法
JP5472423B2 (ja) 2005-03-29 2014-04-16 Ｊｆｅスチール株式会社 耐切断割れ性に優れた高強度・高靱性厚鋼板
JP5131714B2 (ja) * 2009-09-02 2013-01-30 新日鐵住金株式会社 低温靭性に優れた高強度ラインパイプ用鋼板及び高強度ラインパイプ用鋼管
JP5747398B2 (ja) * 2009-11-20 2015-07-15 国立研究開発法人物質・材料研究機構 高強度鋼
JP5621478B2 (ja) * 2010-09-29 2014-11-12 Ｊｆｅスチール株式会社 高靱性かつ高変形性高強度鋼管用鋼板およびその製造方法
JP5472071B2 (ja) * 2010-12-13 2014-04-16 新日鐵住金株式会社 ラインパイプ用鋼材
JP5741483B2 (ja) 2012-02-27 2015-07-01 新日鐵住金株式会社 現地溶接性に優れるラインパイプ用高強度熱延鋼板およびその製造方法
JP5824401B2 (ja) * 2012-03-30 2015-11-25 株式会社神戸製鋼所 耐水素誘起割れ性に優れた鋼板およびその製造方法
CN102851587B (zh) * 2012-09-06 2014-02-12 江苏沙钢集团有限公司 抗变形x80-x100管线钢板
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EP3124639A1 (de) 2017-02-01
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