EP2927338B1 - HOT-ROLLED STEEL PLATE FOR HIGH-STRENGTH LINE PIPE AND HAVING TENSILE STRENGTH OF AT LEAST 540 MPa - Google Patents

HOT-ROLLED STEEL PLATE FOR HIGH-STRENGTH LINE PIPE AND HAVING TENSILE STRENGTH OF AT LEAST 540 MPa Download PDF

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EP2927338B1
EP2927338B1 EP14742727.2A EP14742727A EP2927338B1 EP 2927338 B1 EP2927338 B1 EP 2927338B1 EP 14742727 A EP14742727 A EP 14742727A EP 2927338 B1 EP2927338 B1 EP 2927338B1
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steel
microstructure
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French (fr)
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EP2927338A4 (en
EP2927338A1 (en
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Sota GOTO
Shunsuke Toyoda
Takatoshi Okabe
Yukihiko OKAZAKI
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JFE Steel Corp
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JFE Steel Corp
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • 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
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/50—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for welded joints
    • 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
    • C22C38/02—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
    • 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
    • C22C38/24—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
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite

Definitions

  • the present invention relates to a hot-rolled steel sheet having hydrogen induced cracking resistance (hereinafter, called HIC resistance) and a strength of X70 or more in accordance with API (American Petroleum Institute) standards which can suitably be used as a material for an electric resistance welded steel pipe for a linepipe for transporting energy resources such as crude oil and a natural gas and to a method for manufacturing the steel sheet.
  • HIC resistance hydrogen induced cracking resistance
  • API American Petroleum Institute
  • UOE steel pipes have been mainly used for linepipes to date from the viewpoint of transport efficiency, because steel pipes having a large diameter and a large thickness can be manufactured using a UOE steel pipe.
  • high strength electric resistance welded steel pipes which are manufactured from hot-rolled steel sheets in a coil shape (hot-rolled steel strips) that are less expensive and have high productivity as a material, are being increasingly used for linepipes instead of UOE steel pipes nowadays.
  • Electric resistance welded steel pipes have an advantage in that they are superior to UOE steel pipes in terms of deviation of a wall thickness and roundness in addition to cost advantage.
  • the pipe production method for electric resistance welded steel pipes involves cold roll forming, the method is characteristic of much more plastic strain being given to steel pipes than to a UOE steel pipe when pipe production is performed.
  • HIC is a phenomenon in which hydrogen ions having been generated by a corrosion reaction become hydrogen atoms on the surface of a steel, and the hydrogen atoms enter into the steel, accumulate around inclusions such as MnS, carbides having a large grain diameter such as NbC, and a second hard phase so as to increase internal pressure and cause the steel material to eventually crack.
  • inclusions such as MnS, carbides having a large grain diameter such as NbC, and a second hard phase so as to increase internal pressure and cause the steel material to eventually crack.
  • a steel material is given plastic strain, many dislocations are formed around the inclusions, carbides, and the second hard phase mentioned above, and hydrogen atoms are more likely to accumulate, which results in HIC being more likely to occur.
  • Patent Literature 1 discloses a method for improving HIC resistance in which inclusions, which become the origins of HIC, are rendered harmless by controlling the total contents of chemical elements which combine respectively with S, O (oxygen), and N to form inclusions to be 0.01% or less or by controlling the maximum diameter of inclusions to be 5 ⁇ m or less, and in which the hardness of a center segregation part is controlled to be Hv 330 or less.
  • Patent Literature 2 discloses a method for decreasing the area ratio of HIC by decreasing the size of TiN grains, which become the origin of HIC. Specifically, the size of Al-Ca-based sulfides in molten steel is decreased by controlling a weight ratio CaO/Al 2 O 3 to be 1.2 to 1.5 by adjusting the added contents of Al and Ca, and the grain diameter of Al-Ti-Ca-based complex inclusions which are formed using the sulfides as nuclei is controlled to be 30 ⁇ m or less.
  • Patent Literature 3 discloses a method in which the formation of carbonitrides of Nb and Ti, which become the origins of HIC, is less likely to occur by controlling Nb concentration to be 0.060% or less and Ti concentration to be 0.025% or less in a region located at a distance in the thickness direction of 5% of the thickness from the central part in the thickness direction.
  • Patent Literature 4 discloses a method for manufacturing a high strength linepipe excellent in terms of HIC resistance in which HIC resistance is improved by decreasing the degree of center segregation as a result of decreasing Mn content added in steel and in which Cr and Mo, which are comparatively less likely to undergo center segregation, are utilized.
  • Patent Literature 1 to Patent Literature 3 Although it is possible to render the origins of HIC harmless to some extent using the methods disclosed in Patent Literature 1 to Patent Literature 3, there is an increase in sensitivity for HIC in the case of a high strength steel sheet of X70 or more in accordance with API standards in particular, and therefore a sufficient effect is not realized only by controlling the amount and size of inclusions.
  • the present invention has been completed in view of the situation described above, and an object of the present invention is to provide a hot-rolled steel sheet for a high strength linepipe excellent in terms of HIC resistance which can suitably be used as a raw material of a high strength electric resistance welded linepipe of X70 or more in accordance with API standards.
  • the present invention has been completed on the idea that, in the case of a hot-rolled steel sheet for a high strength linepipe having a TS of 540 MPa or more where there is an increase in sensitivity for CHIC, a crack length ratio CLR is controlled to be small even in the presence of some amount of inclusions which become the origins of the occurrence of HIC, by improving propagation resistance of HIC as a result of decreasing the grain diameter of a microstructure in a center segregation part through an improvement in the hardenability of the center segregation part by controlling the chemical composition of steel. That is to say, the subject matter of the present invention is as follows.
  • a method for manufacturing a hot-rolled steel sheet for a high strength linepipe having a tensile strength of 540 MPa or more and excellent HIC resistance, which does not form part of the present invention is also disclosed, the method including heating a steel slab having the chemical composition according to item [1] at a temperature of 1100°C or higher and 1300°C or lower, performing rough rolling on the steel slab, thereafter performing finish rolling on the rough-rolled steel under condition that cumulative rolling reduction ratio is 20% or more in a temperature range of 930°C or lower, performing accelerated cooling on the finish-rolled steel sheet to a temperature of 380°C or higher and 600°C or lower at an average cooling rate of 10°C/s or more and 100°C/s or less in terms of the temperature of the central part in the thickness direction, and coiling the cooled steel sheet into a coil shape.
  • the present invention even in the presence of some amount of inclusions, it is possible to suppress HIC by controlling to refine a microstructure in a center segregation part to be small and to manufacture a high strength hot-rolled steel sheet excellent in terms of HIC resistance which can suitably be used for an electric resistance welded steel pipe for a linepipe of X70 or more in accordance with API standards which can be used without causing any problem even in a harsh environment equivalent to a NACE solution.
  • the hot-rolled steel sheet manufactured using the present invention can also be used for a spiral steel pipe for a linepipe of X70 or more in accordance with API standards.
  • the C is a chemical element which significantly contributes to an increase in the strength of steel, and such an effect is realized in the case where the C content is 0.02% or more, but, in the case where the C content is more than 0.06%, since a second phase such as a pearlite microstructure is easy to be formed, there is a deterioration in HIC resistance. Therefore, the C content is set to be 0.02% or more and 0.06% or less, or preferably 0.03% or more and 0.05% or less.
  • Si 0.05% or more and 0.25% or less
  • Si is a chemical element which is added for solute strengthening and decreasing scale-off quantity when hot rolling is performed, and such an effect is realized in the case where the Si content is 0.05% or more, but, in the case where the Si content is more than 0.25%, since red scale excessively grows, cooling ununiformity occurs when hot rolling is performed, which results in a deterioration in the appearance and the uniformity of material properties. Therefore, the Si content is set to be 0.05% or more and 0.25% or less, or preferably 0.10% or more and 0.25% or less.
  • Si be added so that the ratio Mn/Si is 4.0 or more and 12 or less.
  • Mn 0.60% or more and 1.10% or less
  • Mn is a chemical element which contributes to an improvement in strength and toughness as a result of refining of a steel microstructure, and such an effect is realized in the case where the Mn content is 0.60% or more.
  • the Mn content is set to be 0.60% or more and 1.10% or less, preferably 0.80% or more and 1.10% or less, or more preferably 0.80% or more and 1.05% or less.
  • the P content be as small as possible, but a P content of 0.008% or less is acceptable. Moreover, since there is an increase in cost due to an increase in refining time in order to markedly decrease the P content, it is preferable that the P content be 0.002% or more.
  • S is, like P, a chemical element which is inevitably contained in steel, and since S forms MnS in steel, it is preferable that the S content be as small as possible, but a S content of 0.0010% or less is acceptable.
  • the S content is preferably 0.0006% or less.
  • Nb 0.020% or more and 0.060% or less
  • Nb is a chemical element which contributes to an increase in the strength of steel as a result of precipitating in the form of fine Nb carbonitrides in a coiling process when hot rolled steel sheets are manufactured. Also, Nb is a chemical element which contributes to an improvement in the toughness of a weld zone as a result of suppressing the growth of austenite grains when electric resistance welding is performed. Such effects are realized in the case where the Nb content is 0.020% or more. On the other hand, in the case where the Nb content is more than 0.060%, Nb carbonitrides having a large grain diameter, which become the origins of HIC, are more likely to be formed. Therefore, the Nb content is set to be 0.020% or more and 0.060% or less, or preferably 0.030% or more and 0.050% or less.
  • Ti is a chemical element which is added in order to render N, which significantly deteriorates the toughness of steel, harmless by fixing N in the form of TiN. Such an effect is realized in the case where the Ti content is more than 0.001%.
  • the Ti content is set to be 0.001% or more and 0.020% or less, or preferably 0.005% or more and 0.015% or less.
  • Al 0.01% or more and 0.08% or less
  • the Al content is set to be 0.01% or more and 0.08% or less, or preferably 0.01% or more and 0.05% or less.
  • Ca is a chemical element which is effective for improving HIC resistance by shape control of sulfide-based inclusions, and such an effect is realized in the case where the Ca content is 0.0005% or more.
  • the Ca content is set to be 0.0005% or more and 0.0050% or less, or preferably 0.0010% or more and 0.0030% or less.
  • one or more selected from among Cu, Ni, Cr, Mo, and V may be further added in the amounts described below.
  • Cu is a chemical element which contributes to an improvement in the toughness and strength of steel through an improvement in hardenability, and, since Cu is less likely to be concentrated in a center segregation part than Mn and Mo which have similar effect as Cu, Cu can increase the strength of steel without decreasing HIC resistance. Therefore, Cu is added in accordance with the strength grade of steel. Such an effect is realized in the case where the Cu content is 0.05% or more, but, in the case where the Cu content is more than 0.50%, the effect becomes saturated and there is an unnecessary increase in cost in such case. Therefore, the Cu content is 0.50% or less, or preferably 0.40% or less.
  • Ni is, like Cu, a chemical element which contributes to an improvement in the toughness and strength of steel through an improvement in hardenability, and, since Ni is less likely to be concentrated in a center segregation part than Mn and Mo which have a similar effect, Ni can increase the strength of steel without deteriorating HIC resistance. Therefore, Ni is added in accordance with the strength grade. Such an effect is realized in the case where the Ni content is 0.05% or more, but, in the case where the Ni content is more than 0.50%, the effect becomes saturated and there is an unnecessary increase in cost in such case. Therefore, the Ni content is 0.50% or less, or preferably 0.40% or less.
  • Cr is a chemical element which is effective for improving the toughness and strength of steel by improving hardenability, and such an effect is realized in the case where the Cr content is 0.05% or more.
  • Cr significantly deteriorates the toughness of a weld zone as a result of forming Cr oxides when electric resistance welding is performed.
  • the Cr content is set to be 0.50% or less, or preferably 0.30% or less.
  • Mo is a chemical element which is very effective for improving the toughness and strength of steel by improving hardenability, and such an effect is realized in the case where the Mo content is 0.05% or more, but, in the case where the Mo content is more than 0.50%, the effect becomes saturated and there is an unnecessary increase in cost in such case. Therefore, the Mo content is set to be 0.50% or less, or preferably 0.30% or less.
  • V 0.10% or less
  • V is a chemical element which contributes to an increase in the strength of steel through solute strengthening and precipitation strengthening in the case where the V content is 0.005% or more, but, in the case where the V content is more than 0.10%, since there is an increase in the hardness of a center segregation part, there is a deterioration in HIC resistance. Therefore, the V content is set to be 0.10% or less, or preferably 0.080% or less.
  • the CP value is an index indicating the hardenability of a center segregation part. It is possible to obtain a fine bainitic-ferrite microstructure having a grain diameter of 8.0 ⁇ m or less in the center segregation part by controlling the chemical composition of steel so that the CP value is 0.60 or more. On the other hand, in the case where the CP value is more than 0.90, there is an excessive improvement in hardenability, and therefore there is an increase in the hardness of a center segregation part.
  • the CP value is set to be 0.70 or more and 0.90 or less.
  • a fine martensite microstructure which is formed in a center segregation part deteriorates HIC resistance.
  • the chemical elements which contribute to the formation of a fine martensite microstructure are Mn, Mo, Cr, and Ni, and the degree of influence of these chemical elements on the amount of a fine martensite microstructure formed is numerically represented by a CM value. It is necessary that the value of CM shown below satisfy relational expression (2) below in order to control the area fraction of a fine martensite microstructure which is formed in a center segregation part to be less than 5%.
  • CM CM ⁇ 3.05
  • the remainder of the chemical composition other than constituents described above is Fe and inevitable impurities.
  • other small amounts of elements may be added as long as the effects of the present invention are not decreased.
  • the metallographic structure of the present invention be a bainitic-ferrite microstructure having excellent toughness.
  • other kinds of microstructures such as a fine martensite microstructure, an upper bainite microstructure, and a pearlite microstructure are present in a bainitic-ferrite microstructure, since these other kinds of microstructures become hydrogen trapping sites, there is a deterioration in HIC resistance. Therefore, it is preferable that the fractions of the microstructures other than a bainitic-ferrite microstructure be as small as possible.
  • the microstructures other than a bainitic-ferrite microstructure may be included to some extent. Specifically, a case where the total area fraction of the steel microstructures (such as a fine martensite microstructure, an upper bainite microstructure, and a pearlite microstructure) other than a bainitic-ferrite microstructure in the center segregation part is 5% or less is included in the present invention.
  • Average grain diameter of a bainitic-ferrite microstructure 8.0 ⁇ m or less
  • the average grain diameter of a bainitic-ferrite microstructure be 8.0 ⁇ m or less in order to achieve sufficient toughness (vTrs ⁇ -80°C) for a steel sheet used for a linepipe. Also, it is desirable that the average grain diameter of a bainitic-ferrite microstructure be 8.0 ⁇ m or less in order to improvement the crack propagation resistance of HIC. It is preferable that the average grain diameter of a bainitic-ferrite microstructure be 6.0 ⁇ m or less.
  • a slab heating temperature is set to be 1100°C or higher and 1300°C or lower.
  • the temperature is lower than 1100°C, since the temperature is not high enough for carbides, which are formed in steel when continuous casting is performed, to be solid-solute completely, the required strength is not achieved.
  • the temperature is higher than 1300°C, since there is a marked coarsening of austenite grain, there is a deterioration in toughness.
  • this temperature refers to the temperature of the interior of the heating furnace, and the center of the slab is presumed to be heated to this temperature.
  • the finish rolling step it is necessary that finish rolling be performed under the condition that cumulative rolling reduction ratio is 20% or more in a temperature range of 930°C or lower.
  • the cumulative rolling reduction ratio is less than 20%, since there are an insufficient number of nucleation sites of a bainitic-ferrite microstructure, the microstructure becomes coarse, which results in a deterioration in toughness.
  • the upper limit of cumulative rolling reduction ratio be 80% or less.
  • the average cooling rate of the central part in the thickness direction of a steel sheet is set to be 10°C/s or more and 100°C/s or less.
  • the cooling rate is less than 10°C/s
  • the area fractions of a ferrite microstructure and/or a pearlite microstructure become more than 5% even if hardenability increasing chemical elements such as Cu, Ni, and Cr are added. Therefore, it is necessary that the cooling rate be 10°C/s or more.
  • the cooling rate is more than 100°C/s, the area fraction of a martensite microstructure becomes more than 5%.
  • the cooling rate of the central part in the thickness direction of a steel sheet was calculated by using the temperature history of the central part in the thickness direction of the steel sheet by performing heat-transfer calculation using the cooling capacity and heat-transfer coefficient of a run-out, which had been investigated in advance, and the surface temperature of the steel sheet, which had been determined using a radiation thermometer on the run-out.
  • the cooling stop temperature is set to be 380°C or higher and 600°C or lower. In the case where the cooling stop temperature is higher than 600°C, since there is coarsening of precipitation strengthening grains such as Nb carbonitrides, there is a decrease in strength. Moreover, since there is an enhancement of increase in the concentration of carbon in a center segregation part, a fine martensite microstructure, an upper bainite microstructure, and a pearlite microstructure tend to be formed.
  • the cooling stop temperature is lower than 380°C, since there is an improvement in the deformation resistance of a steel sheet, it is difficult to coil the steel sheet into a coil shape, and there is a decrease in strength due to precipitation strengthening grains such as Nb carbonitrides not being precipitated.
  • Test pieces were collected from the obtained hot-rolled steel sheets, and by performing microstructure observation, a tensile test, a Charpy impact test, hardness determination, and a HIC resistance test, tensile properties, toughness, and HIC resistance were evaluated.
  • a tensile test piece was collected from the obtained hot-rolled steel sheet so that the longitudinal direction was at a right angle to the rolling direction (C direction), and a tensile test was performed at room temperature in accordance with API-5L specification in order to determine yield stress YS (deformation stress for a nominal strain of 0.5%) and tensile stress TS.
  • a V-notched test piece was collected from the central part in the thickness direction of the obtained hot-rolled steel sheet so that the longitudinal direction was at a right angle to the rolling direction (C direction), and absorbed energy and a percent brittle fracture were determined by performing Charpy impact tests at temperatures in the range of -140°C to 0°C in accordance with JIS Z 2242 in order to determine a temperature (fracture transition temperature) at which the percent brittle fracture was 50%.
  • three test pieces were used for one temperature in order to obtain the respective arithmetic averages of the determined absorbed energy and percent brittle fracture.
  • a HIC test piece having the thickness of the steel sheet, a width of 20 mm, and a length of 100 mm was collected from the obtained hot-rolled steel sheet so that the longitudinal direction was the rolling direction of the steel sheet, and a HIC resistance test was performed using an A solution in accordance with NACE TM 0284 in order to evaluate HIC resistance.
  • 10 test pieces were used for one coil, and a compressive strain of 10% was applied in the width direction to the test pieces in advance in order to simulate influence of plastic strain applied to a steel sheet in a process of forming an electric resistance welded steel pipe. From the test results, in the case where the crack length ratios (CLR) of all the test pieces for one coil were 15% or less, the coil was judged as satisfactory (O) in terms of HIC resistance. In the case where the crack length ratios of one or more of the test pieces for one coil were more than 15%, the coil was judged as unsatisfactory (x) in terms of HIC resistance.
  • An underlined portion indicates a value out of the range according to the present invention.
  • the examples of the present inventions are all steel sheets having a high strength of 540 MPa or more and excellent HIC resistance.
  • the comparative examples, which were out of the range according to the present invention did not achieve the desired properties as a hot rolled steel sheet for high strength electric resistance welded steel pipes excellent in terms of HIC resistance, because the desired strength or toughness was not achieved, or because there was a deterioration in HIC resistance.
EP14742727.2A 2013-01-24 2014-01-23 HOT-ROLLED STEEL PLATE FOR HIGH-STRENGTH LINE PIPE AND HAVING TENSILE STRENGTH OF AT LEAST 540 MPa Active EP2927338B1 (en)

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JP2013010977 2013-01-24
PCT/JP2014/000319 WO2014115548A1 (ja) 2013-01-24 2014-01-23 引張強さ５４０ＭＰａ以上の高強度ラインパイプ用熱延鋼板

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EP2927338A4 EP2927338A4 (en) 2015-12-16
EP2927338B1 true EP2927338B1 (en) 2016-11-02

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US20150368737A1 (en) 2015-12-24
CN104937124A (zh) 2015-09-23
WO2014115548A1 (ja) 2014-07-31
EP2927338A4 (en) 2015-12-16
EP2927338A1 (en) 2015-10-07
JPWO2014115548A1 (ja) 2017-01-26
JP5884201B2 (ja) 2016-03-15
KR20150088320A (ko) 2015-07-31

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