WO2011132765A1 - Tuyau d'acier contenant du chrome pour une canalisation ayant une excellente résistance à la fissuration par corrosion intergranulaire sous contrainte dans la partie affectée par la chaleur de soudage - Google Patents

Tuyau d'acier contenant du chrome pour une canalisation ayant une excellente résistance à la fissuration par corrosion intergranulaire sous contrainte dans la partie affectée par la chaleur de soudage Download PDF

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WO2011132765A1
WO2011132765A1 PCT/JP2011/059891 JP2011059891W WO2011132765A1 WO 2011132765 A1 WO2011132765 A1 WO 2011132765A1 JP 2011059891 W JP2011059891 W JP 2011059891W WO 2011132765 A1 WO2011132765 A1 WO 2011132765A1
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steel pipe
corrosion cracking
stress corrosion
welding
phase
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PCT/JP2011/059891
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English (en)
Japanese (ja)
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宮田　由紀夫
木村　光男
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Ｊｆｅスチール株式会社
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Priority to CN2011800195748A priority Critical patent/CN102859019A/zh
Priority to BR112012026595A priority patent/BR112012026595A2/pt
Priority to EP11772096.1A priority patent/EP2562284B1/fr
Publication of WO2011132765A1 publication Critical patent/WO2011132765A1/fr

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—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
    • C22C38/18—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
    • 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
    • C21D2211/001—Austenite
    • 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
    • C21D2211/008—Martensite

Definitions

  • the present invention is suitable as a steel pipe for line pipe used in a pipeline for transporting crude oil or natural gas produced in an oil well or a gas well. It is related to Cr containing steel pipe, especially corrosion resistance in extremely severe corrosion environment (corrosion resistance) and welded heat affected zone (cemented zone stress corrosion resistance sigmoid stress corrosion resistance) to intergranular stress corrosion cracking or resistan On the improvement of e to IGSCC).
  • corrosion resistance extremely severe corrosion environment
  • welded heat affected zone cemented zone stress corrosion resistance sigmoid stress corrosion resistance
  • Pipelines for transporting crude oil and natural gas produced in such oil and gas fields have high strength, high toughness, excellent corrosion resistance, and laying of pipelines From the viewpoint of reducing the cost of laying, it is required to use a steel pipe that also has excellent weldability.
  • Patent Document 1 discloses that intergranular stress corrosion cracking (intergranular stress) occurs in a heat affected zone without performing post-weld heat treatment suitable for a line pipe.
  • a martensitic stainless steel pipe that can prevent corrosion cracking (abbreviated as IGSCC) and has excellent resistance to intergranular stress corrosion cracking at the weld heat-affected zone (martensitic stainless steel pipe).
  • the martensitic stainless steel pipe described in Patent Document 1 is mass%, C: less than 0.0100%, N: less than 0.0100%, Cr: 10-14%, Ni: 3-8%, Si: 0.05 to 1.0%, Mn: 0.1 to 2.0%, P: 0.03% or less, S: 0.010% or less, Al: 0.001 to 0.10%, and One or more selected from Cu: 4% or less, Co: 4% or less, Mo: 4% or less, W: 4% or less, and Ti: 0.15% or less, Nb: 0.10 % Or less, V: 0.10% or less, Zr: 0.10% or less, Hf: 0.20% or less, Ta: 0.20% or less.
  • Csol which is an effective content of dissolved carbon (Csol), which effectively acts on the formation of Cr carbide (carbide) is made less than 0.0050%.
  • Csol dissolved carbon
  • Patent Document 2 describes a high-strength stainless steel pipe for line pipes having excellent corrosion resistance.
  • the high-strength stainless steel pipe described in Patent Document 2 is mass%, C: 0.001 to 0.015%, N: 0.001 to 0.015%, Cr: 15 to 18%, Ni: 0.00.
  • JP 2005-336601 A (WO 2005/073419 A1) JP 2005-336599 A
  • the present invention solves the problems of the prior art, and has the desired high strength, toughness, corrosion resistance, resistance to sulfide stress corrosion cracking, and intergranular stress resistance of the weld heat affected zone. It aims at providing the Cr containing steel pipe for line pipes excellent in corrosion cracking property.
  • the steel pipe targeted by the present invention is an X65 to X80 grade steel pipe (steel pipe having a yield strength (YS) of 448-651 MPa).
  • “excellent toughness” means that the absorbed energy E ⁇ 40 (J) at ⁇ 40 ° C. in the Charpy impact test is 50 J or more.
  • Excellent corrosion resistance means that the corrosion rate (mm / year) (hereinafter abbreviated as mm / y) in a 200 g / liter NaCl aqueous solution at 150 ° C. saturated with 3.0 MPa of carbon dioxide gas is 0. .10 mm / y or less.
  • the “steel pipe” includes a seamless steel pipe and a welded steel pipe.
  • the inventors of the present invention have made a ferritic / martensitic stainless steel pipe containing 16 to 17% of Cr, resistant to the heat affected zone in a corrosive environment containing carbon dioxide and chlorine ions.
  • the various factors affecting the intergranular stress corrosion cracking property have been intensively studied.
  • intergranular stress corrosion cracking is caused by the formation of coarse ferrite grains in the heat-affected zone during the heating cycle during welding, and subsequent cooling. It has been found that this is because Cr carbide precipitates at the grain boundaries of the coarse ferrite grains during the cycling cycle and a Cr-depleted layer is formed at the grain boundaries.
  • the present inventors have found that at least the ferrite ( ⁇ ) ⁇ austenite ( ⁇ ) from the grain boundary before Cr carbide precipitates at the grain boundary of coarse ferrite grains. If transformation can be caused and most grain boundaries can be occupied by austenite, precipitation of Cr carbides at the grain boundaries can be prevented, formation of Cr-deficient layers can be suppressed, and the occurrence of intergranular stress corrosion cracking can be prevented. I came up with it.
  • the composition range is expressed by the following formula (1) 11.5 ⁇ Cr + Mo + 0.4W + 0. 3Si-43.5C-0.4Mn-Ni-0.3Cu-9N ⁇ 13.3 (1) It was found that the composition range needs to be optimized so as to satisfy the above.
  • the grain boundary is obtained by setting the composition such that ⁇ Cr + Mo + 0.4W + 0.3Si-43.5C-0.4Mn-Ni-0.3Cu-9N ⁇ is 13.3 or less. It was newly found that carbides (Cr carbides) hardly precipitate, and therefore, a Cr-deficient layer is hardly formed, and it is possible to prevent intergranular stress corrosion cracking.
  • the U-bending stress corrosion cracking test was a test in which the test piece was bent into a U shape with an inner radius of 8.0 mm as shown in FIG.
  • the corrosive solution used was a 50 g / l NaCl solution having a liquid temperature of 100 ° C., a CO 2 pressure of 0.1 MPa, and a pH of 2.0. The test period was 168h. After the test, the cross section of the test piece was observed with a 100-fold optical microscope, and the presence or absence of cracks was investigated.
  • FIG. 3 shows the relationship with 4W + 0.3Si-43.5C-0.4Mn-Ni-0.3Cu-9N ⁇ .
  • the gist of the present invention is as follows. (1) In mass%, C: 0.001 to 0.015%, Si: 0.05 to 0.50%, Mn: 0.10 to 2.0%, P: 0.020% or less, S: 0.010% or less, Al: 0.001 to 0.10%, Cr: 15.0 to 18.0%, Ni: 2.0 to 6.0%, Mo: 1.5 to 3.5%, V: 0.001 to 0.20%, N: 0.015% or less, the following formula (1) 11.5 ⁇ Cr + Mo + 0.4W + 0.3Si-43.5C-0.4Mn-Ni-0.3Cu-9N ⁇ 13.3 (1) (Here, Cr, Mo, W, Si, C, Mn, Ni, Cu, N: content of each element (mass%)) And having a composition consisting of the balance Fe and unavoidable impurities, heated to the ferrite single-phase temperature range at the time of welding, and the cooled weld heat affected zone in a ratio to the total
  • composition in addition to the above-mentioned composition, it is further one of mass%, selected from Cu: 0.01 to 3.5%, W: 0.01 to 3.5%, or 2 A Cr-containing steel pipe for line pipes, characterized by comprising a seed-containing composition.
  • mass% selected from Cu: 0.01 to 3.5%, W: 0.01 to 3.5%, or 2 A Cr-containing steel pipe for line pipes, characterized by comprising a seed-containing composition.
  • a Cr-containing steel pipe for line pipes having excellent intergranular stress corrosion cracking resistance of the weld heat affected zone can be manufactured at low cost, and has a remarkable industrial effect.
  • steel pipe structures, such as a pipeline can be constructed without performing post-weld heat treatment, and there is also an effect that construction costs can be significantly reduced, such as shortening the construction period.
  • C 0.001 to 0.015%
  • C is an element that contributes to an increase in strength. In the present invention, it is necessary to contain 0.001% or more. On the other hand, if the content exceeds 0.015%, the toughness of the weld heat affected zone is deteriorated. If it is contained in a large amount, it becomes difficult to prevent intergranular stress corrosion cracking in the weld heat affected zone. For this reason, C is limited to the range of 0.001 to 0.015%. Preferably, the content is 0.002 to 0.010%.
  • Si 0.05 to 0.50%
  • Si is an element that acts as a deoxidizing agent and increases the strength by solid solution. In the present invention, it is necessary to contain 0.05% or more. However, a large content exceeding 0.50% lowers the toughness of the base metal and the weld heat affected zone. For this reason, Si was limited to the range of 0.05 to 0.50%. Note that the content is preferably 0.10 to 0.40%.
  • Mn 0.10 to 2.0%
  • Mn is a solid solution that contributes to increasing the strength of the steel and is an austenite-generating element that suppresses the formation of ferrite and improves the toughness of the base material and the weld heat affected zone.
  • Such an effect requires the content of 0.10% or more, but even if the content exceeds 2.0%, the effect is saturated and an effect commensurate with the content cannot be expected. For this reason, Mn was limited to the range of 0.10 to 2.0%. Note that the content is preferably 0.20 to 0.90%.
  • P 0.020% or less
  • P is an element that deteriorates corrosion resistance such as carbon dioxide corrosion resistance (CO 2 corrosion resistance) and sulfide stress corrosion cracking resistance, and can be reduced as much as possible in the present invention. Although desirable, extreme reduction results in increased manufacturing costs.
  • P is limited to 0.020% or less as a range that can be industrially implemented at a relatively low cost and does not deteriorate the corrosion resistance. In addition, Preferably it is 0.015% or less.
  • S 0.010% or less
  • S is an element that significantly deteriorates the hot workability in the pipe manufacturing process, and is preferably as small as possible, but if it is reduced to 0.010% or less, the pipe in the normal process Since production is possible, S is limited to 0.010% or less. In addition, Preferably it is 0.004% or less.
  • Al: 0.001 to 0.10% Al is an element having a strong deoxidizing action, and in order to obtain such an effect, it is necessary to contain 0.001% or more. However, if it exceeds 0.10%, the toughness is adversely affected. Effect. For this reason, Al was limited to 0.10% or less. In addition, Preferably it is 0.05% or less.
  • Cr 15.0 to 18.0% Cr is an element that forms a protective film and improves corrosion resistance such as carbon dioxide corrosion resistance and sulfide stress corrosion cracking resistance.
  • the content of 15.0% or more is required for the purpose of improving the corrosion resistance in a particularly severe corrosive environment.
  • it contains exceeding 18.0% hot workability will fall. For this reason, Cr was limited to the range of 15.0 to 18.0%.
  • Ni 2.0-6.0%
  • Ni is an element that has a function of strengthening the protective coating, enhances corrosion resistance such as carbon dioxide corrosion resistance and sulfide stress corrosion cracking resistance, and contributes to an increase in strength.
  • the content of 2.0% or more is required.
  • the content exceeding 6.0% decreases the hot workability and decreases the strength.
  • Ni was limited to the range of 2.0 to 6.0%.
  • Preferably it is 3.0 to 5.0%.
  • Mo 1.5-3.5%
  • Mo is an element that has an effect of increasing resistance to pitting corrosion caused by Cl ⁇ (chlorine ions) and effectively acts to improve corrosion resistance. In order to acquire such an effect, it is necessary to contain 1.5% or more. On the other hand, if the content exceeds 3.5%, the hot workability is lowered and the production cost is increased. For this reason, Mo was limited to the range of 1.5 to 3.5%. Note that the content is preferably 1.8 to 3.0%.
  • V 0.001 to 0.20%
  • V is an element that contributes to an increase in strength and has an effect of improving stress corrosion cracking resistance. Such an effect becomes remarkable when the content is 0.001% or more, but the content exceeding 0.20% lowers the toughness. For this reason, V is limited to a range of 0.001 to 0.20%. Note that the content is preferably 0.010 to 0.10%.
  • N 0.015% or less N is an element that has an effect of improving pitting corrosion resistance but significantly reduces weldability. In the present invention, N can be reduced as much as possible. Although desirable, extreme reduction results in increased manufacturing costs.
  • the upper limit was set to 0.015% as a range that can be industrially implemented at a relatively low cost and does not deteriorate the weldability.
  • the above-mentioned components are basic components, but in addition to the basic composition, Cu: 0.01 to 3.5%, W: 0.01 to 3.5% 1 is selected as a selective element.
  • Two or more kinds and / or one or two kinds selected from Ca: 0.0005 to 0.0100% and REM: 0.0005 to 0.0100% can be selected and contained as necessary. .
  • Cu is an element that improves the carbon dioxide gas corrosion resistance and contributes to an increase in strength.
  • it is desirable to contain 0.01% or more, but even if it exceeds 3.5%, the effect is saturated, and an effect commensurate with the content cannot be expected, and it is economical. Disadvantageous. For this reason, when it contains, it is preferable to limit Cu to 0.01 to 3.5% of range. More preferably, it is 0.30 to 2.0%.
  • W is an element that improves the corrosion resistance of carbon dioxide gas and also improves the resistance to stress corrosion cracking, and further the resistance to sulfide stress corrosion cracking and pitting corrosion. In order to obtain such an effect, it is desirable to contain 0.01% or more, but even if it exceeds 3.5%, the effect is saturated, and an effect commensurate with the content cannot be expected, and it is economical. Disadvantageous. For this reason, when contained, W is preferably limited to a range of 0.01 to 3.5%. More preferably, it is 0.30 to 2.0%.
  • Ti, Nb, Zr are Both are elements that have a strong tendency to form carbides compared to Cr, have the effect of suppressing the precipitation of Cr carbides at grain boundaries during cooling, and can be selected as needed to contain one or more. .
  • Ti 0.01-0.20%
  • Nb 0.01-0.20%
  • Zr 0.01-0.20%
  • Ti 0.02 to 0.10%
  • Nb 0.02 to 0.10%
  • Zr 0.02 to 0.10%.
  • Ca and REM are morphological control of inclusions.
  • the content of each component is adjusted so as to satisfy the following formula (1) within the range of the components described above.
  • the median ⁇ Cr + Mo + 0.4W + 0.3Si-43.5C-0.4Mn-Ni-0.3Cu-9N ⁇ of the formula (1) is an index for evaluating hot workability and further resistance to intergranular stress corrosion cracking.
  • the content of each element is adjusted within the above range so as to be in the range of 11.5 to 13.3 that satisfies the expression (1).
  • the median of the formula (1) is less than 11.5, the hot workability is insufficient, the hot workability necessary and sufficient for the production of the seamless steel pipe cannot be ensured, and the production of the seamless steel pipe becomes difficult.
  • the median value of the formula (1) is larger than 13.3, the intergranular stress corrosion cracking resistance is lowered as described above. For these reasons, the content of each element is adjusted within the above-described range and so as to satisfy the expression (1).
  • the steel pipe of the present invention has the above-described composition, and further has a structure including a martensite phase as a base phase and a ferrite phase having a volume ratio of 10 to 50% and an austenite phase having a volume ratio of 30% or less.
  • the martensite phase includes a tempered martensite phase (tempered martensite phase).
  • the martensite phase is preferably contained in a volume ratio of 25% or more in order to ensure a desired strength.
  • the ferrite phase is a soft structure that improves workability, and is preferably contained in a volume ratio of 10% or more from the viewpoint of improving workability.
  • the desired high strength (X65, YS: 448 MPa or more) cannot be secured.
  • the austenite phase is a structure that improves toughness, but if it exceeds 30%, it is difficult to ensure strength.
  • the austenite phase does not completely transform into a martensite phase during the quenching process, and a part of the austenite phase remains, and a part of the martensite phase and the ferrite phase during the tempering process reversely transforms and is stable. And may remain as an austenite phase after cooling.
  • the composition range of the steel of the present invention is a ferrite single-phase temperature range at 1300 ° C. or higher.
  • molten steel having the above composition is melted by a conventional melting method such as a converter, an electric furnace, a vacuum melting furnace, and the like, and a continuous casting method. It is preferable to use a steel material such as a billet by a conventional method such as (continuous casting method) or a slabbing-mill method for rolling an ingot. Subsequently, these steel materials are heated and hot-rolled using a normal Mannesmann-plug mill method or Mannesmann-mandrel mill method manufacturing process. The pipe is made into a seamless steel pipe having a desired size.
  • the seamless steel pipe after pipe forming is subjected to accelerated cooling (air-cooling rate) or more, preferably accelerated cooling (cooling to room temperature at a cooling rate of 0.5 ° C./s or more at an average of 800 to 500 ° C.). It is preferable to apply.
  • it is a steel pipe which has a composition within the composition range of this invention, it can be set as the structure
  • the cooling rate is less than 0.5 ° C./s, it becomes impossible to obtain a structure based on the martensite phase as described above.
  • the structure based on the martensite phase means that the martensite phase is a structure having the largest volume ratio or a volume ratio substantially equal to the volume ratio of another structure having the largest volume Li.
  • reheating quenching
  • tempering tempering
  • the quenching treatment it is reheated to 800 ° C. or higher, held at that temperature for 10 minutes or more, and then cooled to 100 ° C. or lower at a cooling rate of 0.5 ° C./s or higher on average by air cooling or 800 to 500 ° C. It is preferable to set it as a treatment.
  • the reheating temperature is less than 800 ° C., it becomes impossible to secure a structure based on a desired martensite phase.
  • the tempering treatment after the quenching treatment, heating to a temperature of 500 ° C. or more and 700 ° C. or less, more preferably 580 ° C. or more and 680 ° C. or less, holding for a predetermined time, and then air cooling is preferable. Thereby, desired high strength, desired high toughness, and desired excellent corrosion resistance can be combined. So far, the seamless steel pipe has been described as an example, but the present invention is not limited to this.
  • a steel pipe material steel plate having the above-described composition, an electric-welded steel pipe and a UOE steel pipe can be manufactured by a normal process to obtain a steel pipe for a line pipe.
  • the above-described quenching and tempering treatment is applied to the steel pipe material (steel plate) or the steel pipe to make the steel pipe having the above-described structure also for the ERW steel pipe and the UOE steel pipe.
  • the above-described steel pipe of the present invention can be welded to form a welded structure (steel pipe structure).
  • the welding joining of this invention steel pipe shall include the case where welding joining of this invention steel pipe and another kind of steel pipe is included.
  • the welded heat-affected zone that is heated and cooled to a ferrite single-phase temperature range of 1300 ° C. or higher at welding is preferably the entire length of the old ferrite grain boundary. Therefore, 50% or more of the old ferrite grain boundary has a weld heat affected zone having a structure occupied by the martensite phase and / or austenite phase. Thereby, intergranular stress corrosion cracking is suppressed, and the intergranular stress corrosion cracking resistance of the weld heat affected zone is improved without performing post-weld heat treatment.
  • Molten steel having the composition shown in Table 1 was melted and degassed in a vacuum melting furnace, cast into a 100 kgf steel ingot, and made into a steel pipe material of a predetermined size by hot forging. These steel pipe materials are heated and then piped by hot working using a model seamless mill (small laboratory seamless rolling mill) to produce a seamless steel pipe (outer diameter 65 mm ⁇ x wall thickness 5.5 mm). ). About the obtained seamless steel pipe, the presence or absence of the crack generation
  • test material was collected from the obtained seamless steel pipe, and the test material (steel pipe) was quenched and tempered under the conditions shown in Table 2.
  • a test piece is taken from a test material (steel pipe) that has been subjected to quenching treatment and tempering treatment, and the structure is observed (microstructure observation), tensile test (impact test), impact test (corrosion test), and corrosion test (corrosion test).
  • a sulfide stress corrosion cracking test and a U bending stress corrosion cracking test were conducted.
  • the test method was as follows. (1) Structure observation A test piece for structure observation was collected from the obtained test material (steel pipe).
  • SSC Sulfide stress corrosion cracking
  • the applied stress was YS (yield strength) of the base material, and the test period was 720 hour (hereinafter abbreviated as h).
  • the broken piece was evaluated as x, and the broken piece was evaluated as o.
  • tissue observation was extract
  • the U bending stress corrosion cracking test was a test in which a test piece was bent into a U shape with an inner radius of 8.0 mm and immersed in a corrosive solution.
  • the corrosive solution used was a 50 g / liter NaCl solution having a liquid temperature of 100 ° C., a CO 2 pressure of 0.1 MPa, and a pH of 2.0. The test period was 168h.
  • Each of the inventive examples is excellent in hot workability, YS: high strength of 448 MPa (65 ksi) or more, high toughness of vE- 40 : 50 J or more, corrosion rate: high corrosion resistance of 0.12 mm / y or less.
  • YS high strength of 448 MPa (65 ksi) or more
  • high toughness of vE- 40 50 J or more
  • corrosion rate high corrosion resistance of 0.12 mm / y or less
  • sulfide stress corrosion cracking there is no occurrence of intergranular stress corrosion cracking in the weld heat affected zone heated to 1300 ° C or higher, and the intergranular stress corrosion cracking resistance of the weld heat affected zone is improved. It is an excellent steel pipe.
  • Comparative examples outside the scope of the present invention are hot workability is reduced, toughness is reduced, corrosion resistance is reduced, sulfide stress cracking resistance is reduced, or welding heat influence The intergranular stress corrosion cracking resistance of the part is reduced.
  • Patent Document 2 Inventive steel No. 1 disclosed in the examples of JP-A-2005-336599.
  • Patent Document 2 steel pipes (steel pipe Nos. 27 to 31) manufactured using F, G, M, N, and O (steel Nos. U, V, W, X, and Y) have individual elements.
  • composition range of the present invention satisfies the scope of the present invention, since all the formulas (1) defined in the present invention exceed 13.3, as shown in Table 3, the old ferrite grain boundary
  • the ratio of the length occupied by the martensite phase and / or austenite phase relative to the total length is all less than 50%, and all the intergranular stress corrosion cracking occurs.
  • the effect of the intergranular stress corrosion cracking resistance of the weld heat affected zone is completely unexpected from Japanese Patent Application Laid-Open No. 2005-336599 (Patent Document 2).

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  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
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Abstract

L'invention concerne un tuyau d'acier contenant du chrome pour une canalisation, qui présente une résistance mécanique élevée de grade X65 à X80, une excellente ténacité, une résistance à la corrosion, une résistance à la fissuration par corrosion sous contrainte par les sulfures, et une excellente résistance à la fissuration par corrosion intergranulaire sous contrainte au niveau d'une partie affectée par la chaleur de soudage. Spécifiquement, on utilise une composition contenant, en pourcentage massique, 0,001-0,015 % de C, 0,05-0,50 % de Si, 0,10-2,0 % de Mn, 0,001-0,10 % d'Al, 15,0-18,0 % de Cr, 2,0-6,0 % de Ni, 1,5-3,5 % de Mo, 0,001-0,20 % de V, et pas plus de 0,015 % de N, de manière à satisfaire l'équation Cr+Mo+0,4W+0,3Si-43,5C-0,4Mn-Ni-0,3Cu-9N = 11,5-13,3. En conséquence, la partie affectée par la chaleur de soudage, qui a été chauffée pendant le soudage dans la région de température de la phase ferritique, qui est d'au moins 1300 °C, puis refroidie prend une configuration dans laquelle au moins 50 % des anciens joints de grains de ferrite sont occupés par une phase martensitique et/ou une phase austénitique. Dans le tuyau d'acier ainsi obtenu, la formation d'une couche déficiente en carbure de chrome est supprimée, et la résistance à la fissuration par corrosion intergranulaire sous contrainte de la partie affectée par la chaleur de soudage est considérablement améliorée. Le besoin d'effectuer un traitement thermique post-soudage est supprimé, et le temps de fabrication de structures à tuyaux soudés est fortement réduit.
PCT/JP2011/059891 2010-04-19 2011-04-15 Tuyau d'acier contenant du chrome pour une canalisation ayant une excellente résistance à la fissuration par corrosion intergranulaire sous contrainte dans la partie affectée par la chaleur de soudage WO2011132765A1 (fr)

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CN2011800195748A CN102859019A (zh) 2010-04-19 2011-04-15 焊接热影响部的耐晶间应力腐蚀开裂性优异的线管用含Cr钢管
BR112012026595A BR112012026595A2 (pt) 2010-04-19 2011-04-15 tubo de aço contendo cr para tubo para condução excelente em resistência a rachaduras por corrosão sob tensão intergranular em zona termicamente afetada soldada
EP11772096.1A EP2562284B1 (fr) 2010-04-19 2011-04-15 Tuyau d'acier contenant du chrome pour une canalisation ayant une excellente résistance à la fissuration par corrosion intergranulaire sous contrainte dans la partie affectée par la chaleur de soudage

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JP2010095860 2010-04-19
JP2010-095860 2010-04-19

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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2013161089A1 (fr) 2012-04-26 2013-10-31 Ｊｆｅスチール株式会社 TUBE D'ACIER CONTENANT DU Cr DESTINÉ À UN TUBE DE CANALISATION EXCELLENT EN TERMES DE RÉSISTANCE À LA FISSURATION INTERGRANULAIRE PAR CORROSION SOUS TENSION D'UNE ZONE SOUDÉE TOUCHÉE PAR LA CHALEUR
JP2015110822A (ja) * 2012-12-21 2015-06-18 Ｊｆｅスチール株式会社 耐食性に優れた油井用高強度ステンレス継目無鋼管およびその製造方法

Families Citing this family (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP5924256B2 (ja) 2012-06-21 2016-05-25 Ｊｆｅスチール株式会社 耐食性に優れた油井用高強度ステンレス鋼継目無管およびその製造方法
CN103233180A (zh) * 2013-05-17 2013-08-07 宝山钢铁股份有限公司 一种高强度双相不锈钢管及其制造方法
JP6171834B2 (ja) * 2013-10-21 2017-08-02 Ｊｆｅスチール株式会社 厚肉鋼材製造用装置列
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BR102014005015A8 (pt) * 2014-02-28 2017-12-26 Villares Metals S/A aço inoxidável martensítico-ferrítico, produto manufaturado, processo para a produção de peças ou barras forjadas ou laminadas de aço inoxidável martensítico-ferrítico e processo para a produção de tudo sem costura de aço inoxidável martensítico-ferrítico
JP6137082B2 (ja) * 2014-07-31 2017-05-31 Ｊｆｅスチール株式会社 低温靭性に優れた油井用高強度ステンレス継目無鋼管およびその製造方法
WO2016113794A1 (fr) * 2015-01-15 2016-07-21 Ｊｆｅスチール株式会社 Tube d'acier inoxydable sans soudure pour puits de pétrole, et son procédé de fabrication
JP6206423B2 (ja) * 2015-01-22 2017-10-04 Ｊｆｅスチール株式会社 低温靭性に優れた高強度ステンレス厚鋼板およびその製造方法
JP6432683B2 (ja) 2015-08-04 2018-12-05 新日鐵住金株式会社 ステンレス鋼及び油井用ステンレス鋼材
CN105177255B (zh) * 2015-10-15 2017-06-13 东北大学 一种铁素体‑奥氏体双相不锈钢的热处理工艺方法
CN110763612B (zh) * 2018-07-25 2022-10-11 中国石油化工股份有限公司 一种研究马氏体对奥氏体钢应力腐蚀开裂性能影响的方法
CN115807190A (zh) * 2022-11-28 2023-03-17 攀钢集团攀枝花钢铁研究院有限公司 一种输油用高强度耐腐蚀不锈钢无缝管及其制造方法

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2001115238A (ja) * 1999-08-06 2001-04-24 Sumitomo Metal Ind Ltd マルテンサイト系ステンレス鋼溶接鋼管
JP2001279392A (ja) * 2000-03-30 2001-10-10 Sumitomo Metal Ind Ltd マルテンサイト系ステンレス鋼および製造方法
JP2002060910A (ja) * 2000-08-11 2002-02-28 Sumitomo Metal Ind Ltd 高Ｃｒ溶接鋼管
WO2005073419A1 (fr) 2004-01-30 2005-08-11 Jfe Steel Corporation Tube en acier inoxydable martensitique
JP2005336599A (ja) 2003-10-31 2005-12-08 Jfe Steel Kk 耐食性に優れたラインパイプ用高強度ステンレス鋼管およびその製造方法

Family Cites Families (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS558404A (en) * 1978-06-30 1980-01-22 Nippon Steel Corp Manufacture of austenitic stainless steel used in atmosphere of high-temperature and high-pressure water
CN100497705C (zh) * 2003-10-31 2009-06-10 杰富意钢铁株式会社 耐腐蚀性优良的管线管用高强度不锈钢管及其制造方法
WO2005042793A1 (fr) * 2003-10-31 2005-05-12 Jfe Steel Corporation Tuyau en acier inoxydable haute resistance pour une canalisation presentant une excellente resistance a la corrosion, et procede de production associe
US20100116382A1 (en) * 2007-04-27 2010-05-13 Japan Atomic Energy Agency Austenitic stainless steel excellent in intergranular corrosion resistance and stress corrosion cracking resistance, and method for producing austenitic stainless steel material

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2001115238A (ja) * 1999-08-06 2001-04-24 Sumitomo Metal Ind Ltd マルテンサイト系ステンレス鋼溶接鋼管
JP2001279392A (ja) * 2000-03-30 2001-10-10 Sumitomo Metal Ind Ltd マルテンサイト系ステンレス鋼および製造方法
JP2002060910A (ja) * 2000-08-11 2002-02-28 Sumitomo Metal Ind Ltd 高Ｃｒ溶接鋼管
JP2005336599A (ja) 2003-10-31 2005-12-08 Jfe Steel Kk 耐食性に優れたラインパイプ用高強度ステンレス鋼管およびその製造方法
WO2005073419A1 (fr) 2004-01-30 2005-08-11 Jfe Steel Corporation Tube en acier inoxydable martensitique
JP2005336601A (ja) 2004-01-30 2005-12-08 Jfe Steel Kk マルテンサイト系ステンレス鋼管

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2013161089A1 (fr) 2012-04-26 2013-10-31 Ｊｆｅスチール株式会社 TUBE D'ACIER CONTENANT DU Cr DESTINÉ À UN TUBE DE CANALISATION EXCELLENT EN TERMES DE RÉSISTANCE À LA FISSURATION INTERGRANULAIRE PAR CORROSION SOUS TENSION D'UNE ZONE SOUDÉE TOUCHÉE PAR LA CHALEUR
CN104254625A (zh) * 2012-04-26 2014-12-31 杰富意钢铁株式会社 焊接热影响部的耐晶界应力腐蚀破裂性优良的管线管用含Cr钢管
JP2015110822A (ja) * 2012-12-21 2015-06-18 Ｊｆｅスチール株式会社 耐食性に優れた油井用高強度ステンレス継目無鋼管およびその製造方法

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EP2562284A1 (fr) 2013-02-27
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