EP2803741B1 - Verfahren zur wärmenachbehandlung eines niedriglegierten stahlrohres - Google Patents

Verfahren zur wärmenachbehandlung eines niedriglegierten stahlrohres Download PDF

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EP2803741B1
EP2803741B1 EP12864721.1A EP12864721A EP2803741B1 EP 2803741 B1 EP2803741 B1 EP 2803741B1 EP 12864721 A EP12864721 A EP 12864721A EP 2803741 B1 EP2803741 B1 EP 2803741B1
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heat treatment
weld heat
low alloy
alloy steel
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EP2803741A1 (de
EP2803741A4 (de
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Hiroyuki Hirata
Tomohiko Omura
Kenji Kobayashi
Kaori Kawano
Kota TOMATSU
Kazuhiro Ogawa
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Nippon Steel Corp
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Nippon 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
    • 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
    • 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
    • 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
    • C22C38/08—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/18—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
    • C22C38/48—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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron

Definitions

  • the present invention relates to a method of post weld heat treatment of a low alloy steel pipe. More particularly, it relates to a low alloy steel pipe in which a weld heat affected zone that has been subjected to postweld heat treatment has excellent resistance to embrittlement attributable to hydrogen, such as stress corrosion cracking in wet hydrogen sulfide environments.
  • a steel pipe called a riser, flowline, or trunkline is used for transmission of crude oil or natural gas between an oil well or gas well located at the bottom of the sea and a platform on the sea or between the platform and a refinery station on the land.
  • a riser, flowline, or trunkline is used for transmission of crude oil or natural gas between an oil well or gas well located at the bottom of the sea and a platform on the sea or between the platform and a refinery station on the land.
  • HIC hydrogen induced cracking
  • SSC sulfide stress cracking
  • Patent Document 1 JP5-255746A proposes a steel provided with excellent HIC resistance by defining the heat history and heat treatment conditions at the production time without substantially containing Ni, Cu and Ca.
  • Patent Document 2 JP6-336639A proposes a steel provided with HIC resistance and SSC resistance by essentially adding Cr, Ni and Cu.
  • Patent Document 3 JP2002-60894A proposes a steel in which the HIC resistance and SSC resistance are enhanced by defining the specific ranges of amounts of C, Ti, N, V and O.
  • Patent Document 4 JP2010-24504A
  • a high-strength steel in which, by reducing the amounts of C and Mn and by containing 0.5% or more of Mo, the hardening of weld heat affected zone is restrained, and both of HIC resistance and SSC resistance of base metal and HAZ are achieved.
  • Patent Document 5 JP2007-321228A proposes a low alloy steel containing 0.5% or more of Cr assuming that PWHT of one hour per one-inch wall thickness.
  • Patent Document 6 JP2008-274405A provides a high-strength steel containing, by mass%, 0.03%-0.10% C, 0.01-0.5% Si, 1.5-2.5% Mn, 0.1-0.5% Mo, 0.08% or less Al, and one or more elements of Ti, Nb and V and the balance being Fe and unavoidable impurities.
  • the steel is subjected to post weld SR processing at 650°C for 2 hours.
  • Patent Document 7 provides a method for manufacturing high tensile strength steel plate consisting essentially of 0.02 to 0.18% C, 0.05 to 0.5% Si, 0.5 to 2.0% Mn, 0.005 to 0.1% Al, 0.0005 to 0.008% N, 0.03% or less P, 0.03% or less S, by mass, and the balance of Fe and inevitable impurities.
  • PWHT is applied under the condition of 580°C to 690C for 1 hour to 24 hours.
  • Patent Document 8 JP2007-270194A provides a method of producing a high-strength steel containing, by mass, 0.03-0.07% C, 0.01-0.5% Si, 1.5-2.5% Mn, 0.1-0.5% Mo, ⁇ 0.08% Al and one or more kinds of 0.005-0.035% Ti, 0.005-0.07% Nb, 0.005-0.1% V. Tempering is applied at 650°C for 2 hours.
  • Patent Document 9 provides a high strength line pipe steel containing, in terms of percent by weight, 0.05 to 0.10% C, 0.6% or less Si, 1.7 to 2.5% Mn, 0.015% or less P, 0.003% or less S, 0.1 to 1.0% Ni, 0.15 to 0.6% Mo, 0.01 to 0.10% Nb, 0.005 to 0.030% Ti, 0.06% or less Al, 0.001 to 0.006% N, and the balance of Fe and unavoidable impurities.
  • One example of steel pipe was subjected to tempering at 550°C to 20 minutes.
  • Patent Document 10 JP H11-77350A provides a method for producing a welded steel pipe for a line pipe, excellent in HIC resistance, SSC resistance and low temperature toughness.
  • the pipe is subjected to tempering at 500°C to 700°C.
  • Patent Document 11 JP H09-194995A ) provides a steel tube with high strength and high toughness, having mechanical properties, in a weld zone, comparable to those in a base material part.
  • the steel tube is subjected to tempering at 500°C to 750°C.
  • Non-Patent Document 1 Masanori Kowaka, Corrosion damage and anticorrosion engineering of metal, August 25, 1983, issued by Agne Corporation, p.198
  • Patent Document 4 it is described that the hardening of weld heat affected zone is restrained, and both of HIC resistance and SSC resistance of base metal and HAZ can be achieved.
  • Mo is an expensive element, there has been desired a method for improving hydrogen embrittlement resistance of HAZ without requiring much cost.
  • PWHT brings about a certain effect.
  • importance is attached to efficiency in laying line pipes so that welding work is performed, for example, on a ship on the sea, it is generally desirable that PWHT be eliminated, or, even if being performed, the PWHT be performed for a very short period of time.
  • An objective of the present invention is to provide a low alloy steel in which a HAZ subjected to PWHT, especially short-time PWHT, has excellent hydrogen embrittlement resistance in wet hydrogen sulfide environments or the like.
  • the present inventors To enhance the hydrogen embrittlement resistance of HAZ of a steel subjected to PWHT, the present inventors first examined hydrogen embrittlement of as-welded HAZ to clarify necessary conditions. As a result, it is considered that the hydrogen embrittlement of HAZ is produced by the mechanism described below.
  • the dislocations and vacancies in which hydrogen is trapped exist densely as compared with a thermally refined base metal, and cementite also disperses. For this reason, it is considered that the HAZ is highly susceptible to hydrogen embrittlement as compared with the base metal.
  • Each of the elements of Ti, V and Nb has a high affinity for carbon as compared with iron, and therefore forms fine MX-type carbides in the process of PWHT.
  • the MX-type carbides have a high consistency with a parent phase as compared with cementite, so that the lattice strain of interface with the matrix is small, and the amount of occlusion of diffusible hydrogen in the carbides is large. Therefore, it is considered that, when hydrogen intrudes due to corrosion reaction, the accumulation site of diffusible hydrogen is dispersed, whereby remarkable hydrogen accumulation and formation of embrittlement starting point due to this accumulation are restrained, and embrittlement is resultantly alleviated.
  • the present invention has been made based on the above-described findings, and is directed to the method of post weld heat treatment according to claims 1 to 4, and the use of a low alloy steel according to claims 5 to 8.
  • a low alloy steel in which a HAZ subjected to PWHT, especially short-time PWHT, has excellent hydrogen embrittlement resistance in wet hydrogen sulfide environments or the like.
  • C carbon
  • C is an element effective in enhancing the hardenability of steel and increasing the strength thereof. In order to achieve these effects, 0.01% or more of C must be contained. However, if the content of C exceeds 0.15%, when PWHT is performed, a large amount of cementite is precipitated, and the hydrogen embrittlement susceptibility of HAZ is enhanced. Therefore, the C content is set to 0.01 to 0.15%.
  • the lower limit of the C content is preferably 0.03%.
  • the C content is preferably 0.12% or less.
  • Si silicon is an element effective for deoxidation, but brings about a decrease in toughness if being contained excessively. Therefore, the Si content is set to 3% or less.
  • the Si content is preferably 2% or less.
  • the lower limit of the Si content is not particularly defined; however, even if the Si content is decreased, the deoxidizing effect decreases, the cleanliness of steel is deteriorated, and an excessive decrease in the Si content leads to an increase in production cost. Therefore, the Si content is preferably 0.01% or more.
  • Mn manganese
  • Mn manganese
  • the Mn content is set to 3% or less.
  • the lower limit of the Mn content is not particularly defined; however, in order to achieve the strength increasing effect of Mn, 0.2% or more of Mn is preferably contained.
  • the lower limit thereof is further preferably 0.4%, and the preferable upper limit thereof is 2.8%.
  • Al is an element effective for deoxidation, but if being contained excessively, the effect is saturated, and also the toughness is decreased. Therefore, the Al content is set to 0.08% or less.
  • the Al content is preferably 0.06% or less.
  • the lower limit of the Al content is not particularly defined; however, an excessive decrease in the Al content does not sufficiently achieve the deoxidizing effect, deteriorates the cleanliness of steel, and also increases the production cost. Therefore, 0.001% or more of Al is preferably contained.
  • the Al content in the present invention means the content of acid soluble Al (so-called "sol.Al").
  • Ti titanium
  • V vanadium
  • Nb niobium
  • the low alloy steel in accordance with the present invention contains the above-described elements, and the balance consists of Fe and impurities.
  • the "impurities” mean components that are mixed on account of various factors including raw materials such as ore or scrap when a steel material is produced on an industrial scale. Of the impurities, concerning the elements described below, the content thereof must be restricted stringently.
  • N nitrogen
  • the N content must be restricted to 0.01% or less.
  • the N content is preferably 0.008% or less.
  • the lower limit of the N content is not particularly defined; however, an excessive decrease in the N content leads to a remarkable increase in production cost. Therefore, the lower limit of the N content is preferably 0.0001%.
  • P phosphorus
  • HAZ tungsten carbide
  • the P content is restricted to 0.05% or less.
  • the lower limit of the P content is not particularly defined; however, an excessive decrease in the P content leads to a remarkable increase in production cost. Therefore, the lower limit of the P content is preferably 0.001%.
  • S sulfur
  • S sulfur
  • the lower limit of the S content is not particularly defined; however, an excessive decrease in the S content leads to a remarkable increase in production cost. Therefore, the lower limit of the S content is preferably 0.0001%.
  • the O content exists in the steel as an impurity. If much O is contained, large amounts of oxides are formed, and the workability and ductility are deteriorated. Therefore, the O content must be set to 0.03% or less.
  • the O content is preferably 0.025% or less.
  • the lower limit of the O content need not particularly be defined; however, an excessive decrease in the O content leads to a remarkable increase in production cost. Therefore, the O content is preferably 0.0005% or more.
  • the low alloy steel in accordance with the present invention may contain the elements described below in lieu of a part of Fe.
  • At least one of Cr (chromium) and Mo (molybdenum) may be contained because these elements enhance the hardenability and contribute to the improvement in strength. However, if the contents thereof are excessively high, these elements precipitate as carbides to hinder the carbides of Ti and the like and to enhance the hydrogen embrittlement susceptibility. Therefore, if Cr and/or Mo are contained, the contents thereof are set to 1.5% or less in total.
  • the lower limit of the contents of Cr and/or Mo is preferably 0.02%, further preferably 0.05%.
  • the upper limit thereof is preferably 1.2%.
  • At least one of Ni (nickel) and Cu (copper) may be contained because these elements enhance the hardenability and contribute to the improvement in strength. However, even if these elements are contained excessively, not only the effects are saturated, but also the cost is increased. Therefore, if Ni and/or Cu are contained, the contents thereof are set to 0.8% or less in total.
  • the lower limit of the contents of Ni and/or Cu, if added, is preferably 0.02%, further preferably 0.05%.
  • the upper limit thereof is preferably 0.7%.
  • At least one of Ca (calcium) and Mg (magnesium) may be contained because these elements improve the hot workability of steel. However, if the contents thereof are excessively high, these elements combine with oxygen to remarkably decrease the cleanliness, so that the hot workability may rather be deteriorated. Therefore, if at least one kind of these elements is contained, the contents thereof are set to 0.05% or less in total.
  • the lower limit of the contents of Ca and/or Mg is preferably 0.0005%, further preferably 0.001%.
  • the upper limit thereof is preferably 0.03%.
  • B (boron) may be contained because it segregates at the grain boundaries, so that it restrains the precipitation of ferrite from the grain boundaries, thereby enhancing the hardenability indirectly, and contributes to the improvement in strength.
  • B boron
  • the content of B is preferably in the range satisfying Formula (2).
  • the lower limit of the B content is preferably 0.0001%, further preferably 0.0005%.
  • the conditions of PWHT performed for the low alloy steel in accordance with the present invention are not subject to any special restriction. However, when PWHT is performed under the condition satisfying Formula (3), the low alloy steel in accordance with the present invention achieves excellent effects: 8000 ⁇ T ⁇ 20 + log t / 3600 ⁇ 15000 where, T is treatment temperature (°C) of postweld heat treatment, and t is treatment time (sec) of postweld heat treatment.
  • T ⁇ ⁇ 20 + log(t/3600) ⁇ is less than 8000, there is a possibility that the hydrogen embrittlement resistance of HAZ of steel material consisting of the low alloy steel in accordance with the present invention cannot be enhanced.
  • T ⁇ ⁇ 20 + log(t/3600) ⁇ exceeds 15000, the coarsening of fine MX-type carbides consisting of Ti or the like advances, so that sufficient hydrogen embrittlement resistance cannot be obtained, and also the strength of steel including the weld zone is decreased remarkably. Therefore, the PWHT performed for the low alloy steel in accordance with the present invention is preferably carried out under the condition satisfying Formula (3).
  • the PWHT is preferably carried out in the temperature range of 500 to 750°C for 30 to 600 seconds.
  • the reason for this is that fine MX-type carbides are formed stably by short-time PWHT, whereby the hydrogen embrittlement resistance is enhanced, and also an extreme increase in cost caused by long-time PWHT in actual work is restrained.
  • the PWHT time is preferably set to 300 seconds or shorter.
  • the low alloy steel of the present invention preferably has a yield strength (YS) of 552 MPa or higher.
  • YS yield strength
  • test material was prepared by machining a 12 mm-thick low alloy steel plate having the chemical composition given in Table 1 into a 12 mm square and a 100 mm length. This test material was subjected to HAZ-simulated thermal cycle in which the test material was heated to a temperature of 1350°C, at which the hardening of HAZ was remarkable, for 3 seconds by high-frequency induction heating, and thereafter was rapidly cooled. By using this test material, the tests described below were conducted.
  • test specimen having a thickness of 2 mm, a width of 10 mm, and a length of 75 mm was sampled from the obtained test material, and the SCC resistance was evaluated by a four-point bending test in conformity to EFC16 specified by the European Federation of Corrosion.
  • the test specimen was immersed in a 5% common salt + 0.5% acetic acid aqueous solution of normal temperature (24°C), in which 1 atm hydrogen sulfide gas is saturated, for 336 hours, whereby the presence of occurrence of SSC was examined.
  • Test No. in which SSC did not occur was made acceptable, and test No. in which SSC occurred was made unacceptable.
  • test Nos. X1 to X12 the occurrence of SSC was not recognized in the four-point bending test. Contrarily, in test Nos. Y1 and Y2, although the chemical components met the requirements of the present invention, since PWHT was not performed, MX-type carbides did not precipitate, and SSC occurred. In test Nos. Y3 and Y4, since the addition amounts of Ti, Nb and V, which were constituent elements of MX-type carbides contained in the steel, were small, and the predetermined relationship with C was not satisfied, sufficient amounts of MX-type carbides did not precipitate, and SSC occurred. In test No.
  • a method of post weld heat treatment for a low alloy steel pipe in which a HAZ is subjected to especially short-time PWHT in which a HAZ is subjected to especially short-time PWHT.
  • the steel pipe has excellent hydrogen embrittlement resistance in wet hydrogen sulfide environments or the like.

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Claims (4)

  1. Verfahren zur Wärmebehandlung nach dem Schweißen, wobei ein zum Übertragen von Rohöl oder Erdgas verwendetes niedriglegiertes Stahlrohr einer Wärmebehandlung nach einem Schweißen für eine Rohrleitungsverlegung unterzogen wird, wobei das niedriglegierte Stahlrohr in Masseprozent besteht aus:
    C: 0,01 bis 0,15 %;
    Si: 3 % oder weniger;
    Mn: 3 % oder weniger;
    Al: 0,08 % oder weniger;
    B: dem Formel (2) erfüllenden Bereich;
    einer oder mehreren Art/en von Elementen, die aus Ti, V und Nb ausgewählt sind: dem Formel (1) erfüllenden Bereich; optional
    Cr und/oder Mo: 1,5 % oder weniger insgesamt;
    Ni und/oder Cu: 0,8 % oder weniger insgesamt;
    Ca und/oder Mg: 0,05 % oder weniger insgesamt; und
    es sich bei dem Rest um Fe und Verunreinigungen handelt, wobei es sich bei den Verunreinigungen handelt um
    Ni: 0,01 % oder weniger,
    P: 0,05 % oder weniger;
    S: 0,03 % oder weniger; und
    O: 0,03 % oder weniger,
    die Wärmebehandlung nach dem Schweißen unter der Formel (3) erfüllenden Bedingung erfolgt: 0,1 × C % ≤ Ti % + V % + 0,5 × Nb % ≤ 0,2
    Figure imgb0009
     B % < 0,1 × C %
    Figure imgb0010
     8000 ≤ T × 20 + log t / 3600 ≤ 15000
    Figure imgb0011
    worin das Elementsymbol in der Formel den Gehalt (Masse-%) an jedem Element darstellt, T die Behandlungstemperatur (°C) der Wärmebehandlung nach dem Schweißen ist, und t die Behandlungszeit (s) der Wärmebehandlung nach dem Schweißen ist, wobei die Behandlungstemperatur im Bereich von 500 bis 750°C liegt und die Behandlungszeit 30 bis 600 Sekunden beträgt.
  2. Verfahren zur Wärmebehandlung nach einem Schweißen nach Anspruch 1, wobei das niedriglegierte Stahlrohr in Masseprozent enthält:
    Cr und/oder Mo: 0,02 bis 1,5 % insgesamt.
  3. Verfahren zur Wärmebehandlung nach dem Schweißennach Anspruch 1 oder 2, wobei das niedriglegierte Stahlrohr in Masseprozent enthält:
    Ni und/oder Cu: 0,02 bis 0,8 % insgesamt.
  4. Verfahren zur Wärmebehandlung nach dem Schweißen nach einem der Ansprüche 1 bis 3, wobei das niedriglegierte Stahlrohr in Masseprozent enthält:
    Ca und/oder Mg: 0,0005 bis 0,05 % insgesamt.
EP12864721.1A 2012-01-12 2012-12-17 Verfahren zur wärmenachbehandlung eines niedriglegierten stahlrohres Active EP2803741B1 (de)

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