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EP3006585B1 - Tube en acier sans soudure destiné à un tube de canalisation utilisé dans un environnement acide - Google Patents

Tube en acier sans soudure destiné à un tube de canalisation utilisé dans un environnement acide Download PDF

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Publication number
EP3006585B1
EP3006585B1 EP14803329.3A EP14803329A EP3006585B1 EP 3006585 B1 EP3006585 B1 EP 3006585B1 EP 14803329 A EP14803329 A EP 14803329A EP 3006585 B1 EP3006585 B1 EP 3006585B1
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seamless steel
steel pipe
content
pipe
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German (de)
English (en)
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EP3006585A1 (fr
EP3006585B8 (fr
EP3006585A4 (fr
Inventor
Kenji Kobayashi
Yuji Arai
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Nippon Steel Corp
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Nippon Steel and Sumitomo Metal 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
    • C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
    • C21D8/105—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D9/085—Cooling or quenching
    • 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
    • C22C38/001—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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—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
    • C22C38/40—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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite

Definitions

  • the present invention relates to a seamless steel pipe. More particularly, it relates to a seamless steel pipe for a line pipe that is used in sour environments containing hydrogen sulfide (H 2 S), which is a corrosive gas.
  • H 2 S hydrogen sulfide
  • Crude oil and natural gas contain hydrogen sulfide and moisture.
  • a wet hydrogen sulfide environment is called a sour environment.
  • Line pipes are used as pipelines for transporting crude oil or natural gas produced from oil wells or gas wells. Therefore, the line pipes are used in sour environments.
  • a line pipe used in sour environments has a problem of hydrogen embrittlement attributable to hydrogen absorbed into a steel because of corrosion in environments containing hydrogen sulfide.
  • the hydrogen embrittlement includes sulfide stress cracking occurring on a steel product under static external stresses and hydrogen induced cracking (hereinafter, referred to as HIC) occurring in the interior of a steel product without external stresses.
  • HIC hydrogen induced cracking
  • the line pipe often has a problem of HIC. Therefore, a steel pipe for a line pipe is especially required to have HIC resistance.
  • a steel pipe for a line pipe includes a welded steel pipe and a seamless steel pipe.
  • the welded steel pipe has a seam part (weld zone) extending in the axial direction or in a spiral form.
  • the steel plate used for the welded steel pipe has a center segregated portion, which is produced at the time of continuous casting, in the center of plate thickness, and the center segregated portion has high HIC susceptibility. Therefore, as a steel pipe for a line pipe especially required to have HIC resistance, the seamless steel pipe is preferably used.
  • Patent Document 1 proposes a seamless steel pipe having a high strength and excellent HIC resistance.
  • the steel product for a line pipe disclosed in Patent Document 1 has a composition consisting, in mass%, of C: 0.03 to 0.15%, Si: 0.05 to 1.0%, Mn: 0.5 to 1.8%, P: 0.015% or less, S: 0.04% or less, O: 0.01% or less, N: 0.007% or less, sol.Al: 0.01 to 0.1%, Ti: 0.024% or less, and Ca: 0.0003 to 0.02%, the balance being Fe and impurities.
  • the size of TiN in the steel product is 30 ⁇ m or less. Patent Document 1 describes that since TiN is fine, excellent HIC resistance can be attained.
  • Patent Document 4 describes a steel slab consisting of 0.02-0.20% C, 0.01-0.50% Si, 0.2-2.5%% Mn, ⁇ 0.025% P, ⁇ 0.02% S, ⁇ 0.1% Al, 0.01-0.10% Nb, and the balance essentially Fe is used as a stock, or, if necessary, one or more kinds among 0.05-0.5% Cu, 0.007-0.07% Ce, 0.001-0.07% Ca, and 0.0020-0.0250% N or further trace amounts of one or more elements among Ti, B, Cr, Mo, and Ni are incorporated to the above steel.
  • the above steels are hot-rolled and then cooled naturally so as to precipitate Nb, V, etc., in the course of cooling.
  • Patent Document 5 describes an ingot consisting of 0.02-0.20wt.% C, 0.01-2.00% Si, 0.2-2.5% Mn, ⁇ 0.025% P, ⁇ 0.02% S, ⁇ 0.1% Al, 0.01-0.1% Nb, 0.005-0.2% Ti, ⁇ 0.0050% N, and the balance substantially Fe is subjected to hot rough rolling.
  • the steel which cools down to the precipitation temperature region of Ti and Nb carbonitrides, etc., in the steel is then heated to the temperature at which a Ti carbide is solutionized and the Nb carbonitride is not solutionized.
  • the heated steel is subjected to the finish rolling, then to the natural cooling.
  • Specific ratios of ⁇ 1 kinds among Cu, Ce, Ca, and V and further ⁇ 1 kinds among B, Cr, Mo, and Ni are incorporated at need into the steel having such composition.
  • the blister is a swell that is generated in the vicinity of the surface of a steel product and extends in the axial direction of the steel product.
  • HIC resistance test for example, NACE TM0284
  • NACE NACE TM0284
  • the occurrence of blister may be observed.
  • HIC blister
  • the blister has not especially posed a problem.
  • An objective of the present invention is to provide a seamless steel pipe which is not subjected to quenching and tempering treatment and in which, in the case where the steel pipe is used in line pipe, which line pipe is used in sour environments, the occurrence of blisters and fine internal cracks can be suppressed.
  • the seamless steel pipe according to an embodiment of the present invention is used for a line pipe used in sour environments.
  • This seamless steel pipe has a chemical composition consisting, in mass%, of C: 0.08 to 0.24%, Si: 0.10 to 0.50%, Mn: 0.3 to 2.5%, P: 0.02% or less, S: 0.006% or less, Nb: 0.04 to 0.12%, Al: 0.005 to 0.100%, Ca: 0.0003 to 0.0050%, N: 0.0100% or less, O: 0.0050% or less, Ti: 0 to 0.1%, V: 0 to 0.03%, Cr: 0 to 0.6%, Mo: 0 to 0.3%, Ni: 0 to 0.4%, Cu: 0 to 0.3%, and B: 0 to 0.005%, the balance being Fe and impurities, has a structure consisting of ferrite and pearlite, and also has a yield strength of 350 to less than 450 MPa, wherein the content (mass%) of Nb is not less than F1 value
  • quenching and tempering treatment is not performed, and even if the strength is low, the occurrence of blisters and fine internal cracks can be suppressed.
  • the present inventors examined and studied the occurrence of blisters in a low-strength seamless steel pipe that is not subjected to quenching and tempering treatment, and obtained the findings described below.
  • a blister occurs through the mechanism described below. Hydrogen accumulates around inclusions in the steel, and forms the starting point of hydrogen swell (blister). If the steel product yields on account of the rise in hydrogen pressure at the starting point, a crack is produced. If the crack is produced, the dislocation and hydrogen further accumulate at the edges of crack, and the crack propagates. Thereby, a blister is formed.
  • the ratio of ferrite having a low yield strength is high. Therefore, it is thought that the ferrite yields and thereby a blister is generated. For this reason, in order to suppress the occurrence of blisters, it is effective to enhance the strength of steel by strengthening the ferrite itself, or by increasing the ratio of pearlite in the steel, or by the like means.
  • FIG. 1 is a graph showing the relationship between the yield strength of a seamless steel pipe and the number of occurring blisters (per 20 cm 2 ).
  • FIG. 1 was obtained by the method described below. Seamless steel pipes having various chemical compositions were produced. At this time, each of the seamless steel pipes subjected to hot working was allowed to cool or cooled at a cooling rate of less than 5°C/s, and the quenching and tempering treatment was not performed.
  • the yield strength was determined in the later-described yield strength test. Further, the number of blisters (per 20 cm 2 ) occurring in each of the seamless steel pipes was determined in the later-described blister number measuring test. Thereby, FIG. 1 was created.
  • the curve of FIG. 1 has an inflection point in the vicinity of the yield strength of 350 MPa. Therefore, if the yield strength is 350 MPa or more, the number of blisters can be kept small.
  • the content of C is increased, the ratio of pearlite in the steel increases, and thereby the yield strength of steel is enhanced. However, if the C content increases, the weldability decreases.
  • the seamless steel pipe for a line pipe is circumferentially welded at the site at which the line pipe is laid. If the C content increases, the toughness of the circumferentially welded joint part decreases, and also sulfide stress cracking (SSC) is liable to occur. Therefore, it is difficult to excessively increase the C content.
  • SSC sulfide stress cracking
  • the strength of seamless steel pipe can be enhanced by performing the quenching and tempering treatment.
  • the quenching and tempering treatment of a low-strength seamless steel pipe leads to an increase in production cost.
  • a welded steel pipe such as a UOE steel tube is subjected to cold working such as pipe making and pipe expanding. Since the strength of welded steel pipe is enhanced by cold working, the number of occurring blisters may possibly be reduced.
  • the seamless steel pipe is suitable as a line pipe used in hostile sour environments. Therefore, it is difficult to raise the strength by means of cold working or the like, and considering the production cost as well, the cold working is unfavorable.
  • the C content is increased, and further the Nb content is increased.
  • the C content is set to 0.08 to 0.24%, and the Nb content is set to 0.04 to 0.12%.
  • the strength thereof can be enhanced, and the occurrence of blisters can be suppressed.
  • Nb content (mass%) is made not less than the F1 value defined by Formula (1).
  • F 1 0.02 + t ⁇ 15 ⁇ 0.001 where, t is the wall thickness (unit: mm) of the seamless steel pipe.
  • the wall thickness of the seamless steel pipe for a line pipe used in sour environments is, for example, 10 to 50 mm. If the wall thickness increases, the cooling condition of the seamless steel pipe after hot-working also changes. The cooling rate decreases, and the strength of steel tends to be degraded. If the Nb content is not less than the F1 value of Formula (1), the strength of steel is 350 MPa or more, and the occurrence of blisters can be suppressed.
  • the seamless steel pipe according to this embodiment is used for a line pipe used in sour environments.
  • This seamless steel pipe has a chemical composition consisting, in mass%, of C: 0.08 to 0.24%, Si: 0.10 to 0.50%, Mn: 0.3 to 2.5%, P: 0.02% or less, S: 0.006% or less, Nb: 0.04 to 0.12%, Al: 0.005 to 0.100%, Ca: 0.0003 to 0.0050%, N: 0.0100% or less, O: 0.0050% or less, Ti: 0 to 0.1%, V: 0 to 0.03%, Cr: 0 to 0.6%, Mo: 0 to 0.3%, Ni: 0 to 0.3%, Cu: 0 to 0.3%, and B: 0 to 0.005%, the balance being Fe and impurities, has a structure consisting of ferrite and pearlite, and also has a yield strength of 350 to less than 450 MPa.
  • Nb content (mass%) is made not less than the F1 value defined by Formula (1).
  • F 1 0.02 + t ⁇ 15 ⁇ 0.001 where, t is the wall thickness (unit: mm) of the seamless steel pipe.
  • the seamless steel pipe according to this embodiment has the chemical composition described below.
  • Carbon (C) enhances the hardenability, and enhances the strength of steel.
  • heat treatment such as quenching and tempering is not performed after pipe making as in the case of the seamless steel pipe of this embodiment
  • the strength of steel decreases excessively.
  • the C content is too low, furthermore, excellent HIC resistance is less liable to be attained.
  • the C content is 0.08% or more, high-strength pearlite dispersedly precipitates in the steel. Therefore, the yield of ferrite is restrained. For this reason, excellent HIC resistance is attained, and the occurrence of blisters is suppressed.
  • the seamless steel pipe of this embodiment is circumferentially welded at the site as a line pipe.
  • the C content is 0.08 to 0.24%.
  • the lower limit of the C content is preferably more than 0.08%, further preferably 0.10%.
  • the upper limit of the C content is preferably less than 0.24%, further preferably 0.15%.
  • Si deoxidizes a steel. If the Si content is too low, this effect cannot be achieved. On the other hand, if the Si content is too high, the toughness of the welding heat affected zone decreases. If the Si content is too high, furthermore, the precipitation of ferrite, which is a softening phase, is promoted. Therefore, the HIC resistance decreases, and blisters are liable to occur. For these reasons, the Si content is 0.10 to 0.50%.
  • the lower limit of the Si content is preferably more than 0.10%, further preferably 0.15%, and still further preferably 0.20%.
  • the upper limit of the Si content is preferably less than 0.50%, further preferably 0.35%, and still further preferably 0.30%.
  • Manganese (Mn) enhances the hardenability of steel, and enhances the strength of steel. Furthermore, Mn enhances the toughness of steel. If the Mn content is too low, these effects cannot be achieved. On the other hand, if the Mn content is too high, HIC is liable to occur due to the hardening of steel caused by Mn segregation and due to the formation of MnS. Therefore, the Mn content is 0.3 to 2.5%.
  • the lower limit of the Mn content is preferably more than 0.3%, further preferably 0.5%, and still further preferably 0.8%.
  • the upper limit of the Mn content is preferably less than 2.5%, further preferably 2.0%, and still further preferably 1.8%.
  • Phosphorus (P) is an impurity. Phosphorus decreases the toughness of steel. Therefore, the P content is 0.02% or less. The P content is preferably less than 0.02%, further preferably 0.01% or less. The P content is preferably as low as possible.
  • S Sulfur
  • S is an impurity. Sulfur forms MnS.
  • MnS serves as the starting point of a blister. Therefore, the S content is preferably as low as possible.
  • the decreasing of the S content incurs high costs.
  • the S content should be 0.006% or less.
  • the S content is preferably as low as possible.
  • the S content is preferably 0.003% or less.
  • Niobium (Nb) dissolves ferrite and enhances the strength of steel. Furthermore, Nb combines with C and N to form carbo-nitrides, and performs grain refinement of steel due to pinning hardening. By the grain refinement, the HIC resistance of steel is enhanced. Furthermore, the grain refinement enhances the toughness of steel. In the case where the seamless steel pipe is made from a steel material containing the above-described range of C and the above-described range of Mn, and not containing Nb, and thereafter heat treatment is not performed (that is, in the case where an as-rolled material, for which quenching and tempering treatment is omitted, is produced), the yield strength of the produced seamless steel pipe is about 250 MPa.
  • the yield strength of the seamless steel pipe rises to 350 MPa or more. Therefore, the occurrence of blisters is suppressed. If the Nb content is too low, the above-described effects are not achieved. On the other hand, if the Nb content is too high, coarse Nb carbo-nitrides are formed. A coarse Nb carbo-nitride serves as the starting point of blister, and further the HIC resistance also decreases. Therefore, the Nb content is 0.04 to 0.12%.
  • the wall thickness of the seamless steel pipe for a line pipe used in sour environments is 10 to 50 mm.
  • the cooling rate of the seamless steel pipe becomes low, and the ferrite grains become coarse, so that the yield strength of steel degrades. Therefore, the lower limit of the Nb content has to be not less than the F1 value (%) defined by the following Formula (1).
  • F 1 0.02 + t ⁇ 15 ⁇ 0.001 where, t is the wall thickness (unit: mm) of the seamless steel pipe.
  • the seamless steel pipe satisfies Formula (1), not only in the base metal but also in the welding heat affected zone formed by circumferential welding between the seamless steel pipes, a sufficient yield strength can be assured, and the occurrence of blisters is suppressed.
  • the welding heat affected zone includes a hardened zone in which the cooling rate after heating is high and which is hardened, and a softened zone in which the cooling rate is low and which is softened by undergoing thermal effects repeatedly. In the case where Formula (1) is satisfied, in the softened zone, a sufficient yield strength is assured.
  • the lower limit of the Nb content is 0.04%.
  • the upper limit of the Nb content is preferably less than 0.12%, further preferably 0.10%, and still further preferably 0.08%.
  • Al deoxidizes a steel. If the Al content is too low, this effect cannot be achieved. On the other hand, if the Al content is too high, coarse cluster-form alumina inclusion particles are formed when the circumferential welding is performed, and thereby the toughness in the welding heat affected zone (HAZ) is decreased. Therefore, the Al content is 0.005 to 0.100%.
  • the lower limit of the Al content is preferably more than 0.005%, further preferably 0.010%, and still further preferably 0.020%.
  • the upper limit of the Al content is preferably less than 0.100%, further preferably 0.060%, and still further preferably 0.040%.
  • the Al content means the content of acid-soluble Al (sol.Al).
  • Ca Calcium
  • MnS which serves as the starting point of HIC, a blister, and a fine internal crack. Therefore, Ca suppresses the occurrence of blisters and fine internal cracks. If the Ca content is too low, these effects are insufficient. On the other hand, if the Ca content is too high, inclusions form a cluster, and the toughness and HIC resistance of steel are decreased. Therefore, the Ca content is 0.0003 to 0.0050%.
  • the lower limit of the Ca content is preferably more than 0.0003%, further preferably 0.0010%, and still further preferably 0.0015%.
  • the upper limit of the Ca content is preferably less than 0.0050%, further preferably 0.0040%, and still further preferably 0.0030%.
  • Nitrogen (N) is an impurity. Nitrogen forms coarse nitrides, and decreases the toughness and SSC resistance of steel. Therefore, the N content is preferably as low as possible. For this reason, the N content is 0.0100% or less. The N content is preferably 0.0080% or less, further preferably 0.0060% or less.
  • Oxygen (O) is an impurity. Oxygen forms coarse oxides or a cluster of oxides, and decreases the toughness and HIC resistance of steel. Therefore, the O content is preferably as low as possible. For this reason, the O content is 0.0050% or less. The O content is preferably 0.0040% or less, further preferably 0.0030% or less.
  • the balance of chemical composition of the seamless steel pipe of this embodiment is Fe and impurities.
  • the impurities referred to in this description mean elements that are mixed from ore and scrap used as steel raw materials or from the environment in the production process or the like.
  • the seamless steel pipe of this embodiment may contain one or more types of elements selected from a group consisting of Ti, V, Cr, Mo, Ni, Cu, and B. Any of these elements enhances the strength of steel.
  • Titanium (Ti) is an optional element. Like Nb, Ti combines with C and N to form carbo-nitrides, and performs grain refinement of steel due to pinning hardening. On the other hand, if the Ti content is too high, this effect is saturated. Therefore, the Ti content is 0 to 0.1%.
  • the lower limit of the Ti content is preferably 0.002%, further preferably 0.005%.
  • the upper limit of the Ti content is preferably less than 0.1%, further preferably 0.05%.
  • Vanadium (V) is an optional element. Vanadium forms carbides to strengthen a steel. On the other hand, if the V content is too high, coarse carbides are formed, and SSC is liable to occur. Therefore, the V content is 0 to 0.03%.
  • the lower limit of the V content is preferably 0.01%, further preferably 0.015%.
  • the upper limit of the V content is preferably less than 0.03%, further preferably 0.025%.
  • Cr chromium
  • Mo molybdenum
  • Ni nickel
  • Cu copper
  • the lower limit of the Mo content is preferably 0.01%, further preferably 0.05%.
  • the lower limit of the Ni content is preferably 0.01%, further preferably 0.05%.
  • the lower limit of the Cu content is preferably 0.01%, further preferably 0.05%.
  • the upper limit of the Cr content is preferably less than 0.6%, further preferably 0.5%.
  • the upper limit of the Mo content is preferably less than 0.3%, further preferably 0.25%.
  • the upper limit of the Ni content is preferably less than 0.4%, further preferably 0.3%, and still further preferably 0.25%.
  • the upper limit of the Cu content is preferably less than 0.3%, further preferably 0.25%.
  • the total content of Cr, Mo, Ni and Cu satisfies the following Formula (2).
  • Boron (B) is an optional element. Boron enhances the hardenability of steel for a low-strength seamless steel pipe, and enhances the HIC resistance for a low-strength steel. On the other hand, if the B content is too high, the SSC resistance of steel decreases. Therefore, the B content is set to 0 to 0.005%.
  • the lower limit of the B content is preferably 0.0001% or more, further preferably 0.0003%.
  • the upper limit of the B content is preferably less than 0.005%, further preferably 0.003%.
  • the seamless steel pipe of this embodiment is not subjected to quenching and tempering treatment after pipe making. That is to say, the seamless steel pipe of this embodiment is a so-called as-rolled material for which the quenching and tempering treatment is omitted. As described later, the seamless steel pipe having been made is allowed to cool or is cooled at a cooling rate of less than 2°C/s. Therefore, the structure of the seamless steel pipe of this embodiment consists of ferrite and pearlite. Most part of the structure is ferrite, and the remaining part thereof is pearlite.
  • the structure referred to in this description means a matrix structure not containing inclusions and precipitates.
  • the seamless steel pipe of this embodiment has a yield strength of 350 MPa or more.
  • the yield strength means a 0.2% yield stress.
  • the preferable yield strength of the seamless steel pipe is 400 MPa or more.
  • the yield strength is less than 450 MPa.
  • a steel having the above-described chemical composition is melted, and is refined by the well-known method.
  • the molten steel is cast into a continuously cast material by the continuous casting process.
  • the continuously cast material is, for example, a slab, a bloom, or a billet.
  • the molten steel may be made an ingot by the ingot-making process.
  • the slab or bloom of the continuously cast material or the ingot is hot-worked to produce a billet.
  • a slab, bloom or an ingot is rolled into a billet using a blloming mill.
  • the produced billet is hot-rolled to produce a seamless steel pipe.
  • the billet is heated in a heating furnace. If the heated billet is hot-rolled in the state in which coarse Nb inclusions remain therein, at the cooling time after hot rolling, the strengthening due to Nb cannot be attained sufficiently. In this embodiment, therefore, the billet is heated to a further high temperature as compared with the time of production of the ordinary seamless steel pipe. Specifically, at the heating time, the billet is heated to a temperature of 1250°C or more.
  • the billet extracted from the heating furnace is hot-worked to produce a seamless steel pipe.
  • piercing-rolling based on the Mannesmann process is performed to produce a hollow shell.
  • the produced hollow shell is further subjected to elongation rolling and sizing by using a mandrel mill, a reducer, a sizing mill, or the like to produce a seamless steel pipe.
  • the produced seamless steel pipe is cooled.
  • the cooling rate in a high-temperature region of 500°C or more, in which Nb carbo-nitrides precipitate is preferably higher. Therefore, until the temperature of seamless steel pipe decreases to 500°C, the seamless steel pipe is cooled at a cooling rate of 0.5 to 5°C/s, and subsequently, it is cooled at a cooling rate of less than 2°C.
  • the cooling at a cooling rate of less than 2°C/s includes the allowing to cool.
  • the cooling rate can be controlled, for example, by regulating the spacing between the adjacent seamless steel pipes at the time of allowing to cool. For example, until the temperature of seamless steel pipe decreases to 500°C, the spacing between the adjacent seamless steel pipes is made distance D1, and at a temperature of 500°C or less, the spacing is regulated to distance D2, which is shorter than distance D1. Thereby, a gentle two-stage cooling rate can be realized.
  • the seamless steel pipe after hot-working is not subjected to quenching and tempering treatment.
  • the occurrence of blisters can be suppressed.
  • the number of blisters in the surface is less than 10 per 20 cm 2 .
  • the number of blisters can be determined by the blister number measuring test described below.
  • NACE National Association of Corrosion Engineers
  • a HIC test using a wet hydrogen sulfide environment is conducted. Specifically, a coupon test specimen measuring plate thickness ⁇ 20 mm wide ⁇ 100 mm long (length in the axial direction of seamless steel pipe) is sampled. This coupon test specimen has a pair of surfaces corresponding to the external surface and internal surface of the seamless steel pipe.
  • the seamless steel pipe according to this embodiment by enhancing the yield strength to 350 MPa or more by means of C and Nb, the occurrence of blisters can be suppressed. Therefore, the HIC resistance is excellent, and furthermore, when a tensile stress is applied, SOHIC is less liable to occur.
  • steels A1, A10, A11, A12 and A13 did not have sufficient yield strength, and showed too many blisters.
  • steels B1 and B3 did not contain Nb, and the Nb content of steel B2 was less than the lower limit of the Nb content of the seamless steel pipe of this embodiment.
  • the C content of each of steels B4 and B5 was less than the lower limit of the C content of the seamless steel pipe of this embodiment.
  • the F2 value of steel B6 did not satisfy Formula (2).
  • the ingots of the steels were hot-forged to produce a plurality of billets of the steels.
  • the billet is piercing-rolled by using a piercing mill (piercer) to produce a seamless steel pipe.
  • piercer piercing mill
  • three kinds of seamless steel pipes having wall thicknesses of 12.7 mm, 25.4 mm, and 38.1 mm were produced.
  • Each of the produced seamless steel pipes was cooled at the first cooling rate given in Table 2 until the temperature of seamless steel pipe decreases to 500°C, and was cooled at the second cooling rate subsequently.
  • Each of the seamless steel pipes having three kinds of wall thicknesses that had been produced for each steel was subjected to a micro-structure observing test.
  • the wall thickness central portion was etched by using nital or the like.
  • One optional visual field (visual field area: 40,000 ⁇ m 2 ) of the etched wall thickness central portion was observed.
  • an optical microscope having a magnification of ⁇ 500 was used.
  • each of all the seamless steel pipes had a structure consisting of ferrite and pearlite.
  • a round-bar tensile test specimen having a parallel part measuring 6 mm in outside diameter and 40 mm in length was sampled.
  • the parallel part was parallel to the axial direction of the seamless steel pipe.
  • a tension test was conducted at normal temperature (25°C) to determine the yield strength YS (0.2% yield stress) (MPa).
  • FIG. 2 is a photographic image of two surfaces (corresponding to the external surface and internal surface of seamless steel pipe) of the coupon test specimen after the blister number measuring test of steel A4 (wall thickness: 20 mm)
  • FIG. 3 is a photographic image of two surfaces of the coupon test specimen after the blister number measuring test of steel B3 (wall thickness: 20 mm).
  • the upper surface corresponds to the external surface of seamless steel pipe
  • the lower surface corresponds to the internal surface of seamless steel pipe.
  • each of the 12.7-mm seamless steel pipes of these steels which had a wall thickness of 15 mm or less, had a yield strength YS of 350 to less than 450 MPa. For this reason, as shown in FIG. 2 , the occurrence of blisters in the surface was suppressed, and the number of blisters was less than 10 per 20 cm 2 .
  • the Nb content of each of steels A2 to A9 A14 and A15 was not less than the F1 value defined by Formula (1). Therefore, even for the seamless steel pipes having a wall thickness of more than 15 mm, a yield strength of 350 to less than 450 MPa was attained, and the number of blisters was less than 10 per 20 cm 2 .
  • the Nb content of each of steels A2 to A9, A14 and A15 was not less than the F1 value. Therefore, even for the seamless steel pipes having a wall thickness of more than 35 mm, a yield strength of 350 to less than 450 MPa was attained, and the number of blisters was less than 10 per 20 cm 2 .
  • the Nb content of each of steels B1 to B3 was too low. Therefore, even for the seamless steel pipes each having a wall thickness of less than 20mm, the yield strength was less than 350 MPa. As the result, many blisters occurred in the surface as shown in FIG. 3 , and the number of blisters was not less than 10 per 20 cm 2 .
  • the C content of each of steels B4 and B5 was too low. Therefore, even for the seamless steel pipes each having a wall thickness of less than 20mm, the yield strength was less than 350 MPa, and the number of blisters was not less than 10 per 20 cm 2 .
  • the F2 value of steel B6 did not satisfy Formula (2). Therefore, the yield strength of steel B6 was more than 450 MPa.

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Claims (5)

  1. Tuyau en acier sans soudure pour une conduite utilisée dans des environnements acides comprenant :
    une composition chimique consistant, en % en masse en,
    C : 0,08 à 0,24 %,
    Si : 0,10 à 0,50 %,
    Mn : 0,3 à 2,5 %,
    P : 0,02 % ou inférieur,
    S : 0,006 % ou inférieur,
    Nb : 0,04 à 0,12 %,
    Al : 0,005 à 0,100 %,
    Ca : 0,0003 à 0,0050 %,
    N : 0,0100 % ou inférieur,
    O : 0,0050 % ou inférieur,
    Ti : 0 à 0,1 %,
    V : 0 à 0,03 %,
    Cr : 0 à 0,6 %,
    Mo : 0 à 0,3 %,
    Ni : 0 à 0,4 %,
    Cu : 0 à 0,3 %, et
    B : 0 à 0,005 %,
    le reste étant Fe et des impuretés ;
    une structure consistant en ferrite et perlite ; et
    une résistance à la traction de 350 à moins de 450 MPa, dans lequel
    la teneur (% en masse) de Nb n'est pas inférieure à la valeur F1 définie par la formule (1) F 1 = 0,02 + t − 15 × 0,001
    Figure imgb0011
     où, t est l'épaisseur de paroi (unité : mm) du tuyau en acier sans soudure.
  2. Tuyau en acier sans soudure selon la revendication 1, dans lequel
    la teneur totale en Cr, Mo, Ni et Cu satisfait la formule (2) suivante : Cr + Mo / 5 + Cu + Ni / 15 < 0,10
    Figure imgb0012
    où, chacun des symboles d'éléments dans la formule est la teneur (% en masse) de l'élément correspondant.
  3. Conduite utilisant le tuyau en acier sans soudure selon l'une quelconque des revendications précédentes.
  4. Utilisation du tuyau en acier sans soudure selon l'une quelconque des revendications 1 à 2 pour une conduite dans des environnements acides.
  5. Procédé de fabrication d'un tuyau en acier sans soudure pour une conduite utilisée dans des environnements acides comprenant :
    la fusion d'un acier ayant une composition chimique consistant,
    en % en masse en,
    C : 0,08 à 0,24 %,
    Si : 0,10 à 0,50 %,
    Mn : 0,3 à 2,5 %,
    P : 0,02 % ou inférieur,
    S : 0,006 % ou inférieur,
    Nb : 0,04 à 0,12 %,
    Al : 0,005 à 0,100 %,
    Ca : 0,0003 à 0,0050 %,
    N : 0,0100 % ou inférieur,
    O : 0,0050 % ou inférieur,
    Ti : 0 à 0,1 %,
    V : 0 à 0,03 %,
    Cr : 0 à 0,6 %,
    Mo : 0 à 0,3 %,
    Ni : 0 à 0,4 %,
    Cu : 0 à 0,3 %, et
    B : 0 à 0,005 %,
    le reste étant Fe et des impuretés ;
    le raffinage et la coulée de l'acier fondu en un matériau coulé en continu par un procédé de coulée continue ou en un lingot par un procédé de fabrication de lingot ;
    l'usinage à chaud du matériau coulé en continu ou du lingot pour produire une billette ;
    le chauffage de la billette à une température de 1 250°C ou supérieure ;
    l'usinage à chaud de la billette chauffée pour produire un tuyau en acier sans soudure ;
    le refroidissement du tuyau en acier sans soudure produit, dans lequel, jusqu'à ce que la température du tuyau en acier sans soudure diminue jusqu'à 500°C, le tuyau en acier sans soudure est refroidi à une vitesse de refroidissement de 0,5 à 5°C/s, et ensuite, refroidi à une vitesse de refroidissement inférieure à 2°C/s.
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