EP2172573B1 - Nahtloses rohr aus martensitischem nichtrostendem stahl für ölbohrungsrohr und herstellungsverfahren dafür - Google Patents

Nahtloses rohr aus martensitischem nichtrostendem stahl für ölbohrungsrohr und herstellungsverfahren dafür Download PDF

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EP2172573B1
EP2172573B1 EP07829943.5A EP07829943A EP2172573B1 EP 2172573 B1 EP2172573 B1 EP 2172573B1 EP 07829943 A EP07829943 A EP 07829943A EP 2172573 B1 EP2172573 B1 EP 2172573B1
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cooling
air cooling
temperature
treatment
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French (fr)
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EP2172573A1 (de
EP2172573A4 (de
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Yukio Miyata
Mitsuo Kimura
Masahito Tanaka
Ken Shimamoto
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JFE Steel Corp
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JFE Steel Corp
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
    • C21D9/14—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes wear-resistant or pressure-resistant pipes
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C21D1/22—Martempering
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with 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
    • C22C38/18—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
    • C21D2211/008—Martensite
    • 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

Definitions

  • the present invention relates to a martensitic stainless steel seamless pipe for oil country tubular goods, and in more particular relates to a seamless steel pipe for oil country tubular goods which has a high strength, such as a yield strength of 758 MPa or more, (110 ksi grade) and a superior low temperature toughness and to a method for manufacturing the martensitic stainless steel seamless pipe.
  • Oil country tubular goods used in the environments as described above are required to include a material which simultaneously has a high strength, a superior corrosion resistance, and also a superior toughness.
  • Patent Document 1 martensitic stainless steel suitably used for oil country tubular goods has been proposed which contains 0.01% to 0.1% of C, 9% to 15% of Cr, and 0.1% or less of N, and which has a high toughness even though having a relatively high C content and a high strength.
  • Patent Document 1 when the amount of carbides present in prior-austenite grain boundaries is decreased to 0.5 volume percent or less, the maximum minor axis of the carbides is set to 10 and 200 nm, the ratio between an average Cr concentration and an average Fe concentration in the carbides is set to 0.4 or less, a M 23 C 6 type carbide is suppressed from being precipitated, and a M 3 C type carbide is positively precipitated, the toughness can be significantly improved.
  • Patent Document 2 discloses a steel containing 0.02 to 0.05% C, 0.50% or lower Si, 0.03% or lower P, 0.01 % or lower S, 11 to 17% Cr, 1.5 to 5.0% Ni, 0.5 to 2.0% Mo, 0.05% or lower Al and 0.02 to 0.1 % N or, furthermore, 0.5 to 2.0% Cu, satisfying the relation C+0.8N>0.06, and the balance being Fe with inevitable impurities, which is subjected to hot working and is naturally air-cooled to a room temperature. Next, it is heated to the Ac3 point +10 °C or above to the Ac3 point + 200 °C or below and is cooled from this heating temperature-800 °C to 600-350 °C at 2 °C/s or a higher rate.
  • the steel is cooled to a room temperature at a rate of air cooling or above and is thereafter tempered at the Ac1 point or below.
  • the precipitation of intergranular carbides is controlled to improve its toughness and stress corrosion cracking resistance.
  • the present invention is made to solve the related technical problems described above, and an object of the present invention is to propose a seamless steel pipe for oil country tubular goods which simultaneously has a high yield strength of 758-862 MPa (a 110 ksi grade of yield strength) and a superior low temperature toughness and a stable method for manufacturing the seamless steel pipe.
  • the "superior low temperature toughness" of the present invention indicates the case in which the fracture transition temperature vTrs in a Charpy impact test is -60°C or less.
  • the inventors of the present invention carried out an intensive research on the influences of component compositions and heat treatment conditions upon the change in toughness with an increase in strength of a 13 Cr martensitic stainless steel pipe.
  • the Cr content is set to a relatively low content, such as approximately 11% of Cr
  • the Ni content is also set to a relatively low content, such as 4.0% or less
  • a quenching treatment is performed, when an appropriate tempering treatment is performed in which heating is performed to a tempering temperature in the range of 450°C to 550°C, and cooling is then performed, even if Mo is not added, a high yield strength of 758-862 MPa (a 110 ksi grade of yield) strength can be ensured, and a high toughness having a vTrs of -60°C or less can also be obtained.
  • a tempering treatment was then performed in such a way that heating was performed to a temperature in the range of 425°C to 575°C, and spontaneous cooling was then performed. In addition, in the cooling of the tempering treatment, a correctional treatment was performed.
  • tensile test and a Charpy impact test were performed on the obtained seamless steel pipe, so that tensile characteristics (yield strength YS, and tensile strength TS) and the low temperature toughness (fracture transition temperature vTrs) were measured.
  • the obtained results are shown in Fig. 1 . From Fig. 1 , according to this component system, it is found that when tempering is performed at a temperature in the range of 450°C to 550°C after a quenching treatment, a high toughness and a high strength can be simultaneously obtained.
  • a seamless steel pipe for oil country tubular goods which simultaneously has a high yield strength of 758-862 MPa (a 110 ksi grade of yield strength) and a superior low temperature toughness having a fracture transition temperature vTrs of -60°C or less can be easily and also stably manufactured, and significant industrial advantages can be obtained.
  • Fig. 1 is a graph showing the relationship of the tempering temperature with the yield strength YS, tensile strength TS, and fracture transition temperature vTrs.
  • a method for manufacturing a seamless steel pipe for oil country tubular goods will be described.
  • a stainless steel seamless pipe which has a composition according to claims 1-2, containing less than 0.010% of C, 1.0% or less of Si, 0.1% to 2.0% of Mn, 0.020% or less of P, 0.010% or less of S, 0.10% or less of Al, 10% to 14% of Cr, 0.1% to 4.0% of Ni, 0.05% or less of N, and the balance being Fe and inevitable impurities.
  • “mass percent” is simply represented by "%”.
  • the content is an important element relating to the strength of martensitic stainless steel, and in order to ensure a desired strength, the content is preferably 0.003% or more; however, when the content is 0.010% or more, the toughness and also the corrosion resistance are liable to be degraded. Hence, in the present invention, the C content is limited to less than 0.010%. In addition, in order to stably ensure the strength and the toughness, the content is preferably in the range of 0.003% to 0.008%.
  • the Si is an element functioning as a deoxidizing agent in a normal steelmaking process, and in the present invention, the content is preferably 0.1% or more; however, when the content is more than 1.0%, the toughness is degraded, and hot workability is also degraded. Hence, the Si content is limited to 1.0% or less. In addition, the content is preferably in the range of 0.1% to 0.3%.
  • Mn is an element to increase the strength, and in order to ensure a strength necessary as a steel pipe for oil country tubular goods, the content must be 0.1% or more in the present invention; however, when the content is more than 2.0%, the toughness is adversely influenced. Hence, the Mn content is limited in the range of 0.1% to 2.0%. In addition, the content is preferably in the range of 0.5% to 1.5%.
  • the P is an element to degrade the corrosion resistance, such as CO 2 corrosion resistance, and is preferably decreased as small as possible in the present invention; however, an excessive decrease may cause an increase in cost.
  • the P content is limited to 0.020% or less. In addition, the content is preferably 0.015% or less.
  • S is an element to considerably degrade the hot workability in a pipe manufacturing process and is preferably decreased as small as possible; however, when the content is decreased to 0.010% or less, pipe manufacturing can be performed by a normal process, and hence the S content is limited to 0.010% or less. In addition, the content is preferably 0.003% or less.
  • the content is an element having a strong deoxidizing function, and in order to obtain this effect, the content is preferably 0.001% or more; however, when the content is more than 0.10%, the toughness is adversely influenced. Hence the Al content is limited to 0.10% or less. In addition, the content is preferably 0.05% or less.
  • Cr is an element to improve the corrosion resistance by forming a passivation film and is also an element to particularly contribute to an effective improvement in CO 2 corrosion resistance and resistance to CO 2 stress corrosion cracking.
  • the content is 10% or more, corrosion resistance required for oil country tubular goods can be ensured, and hence the lower limit is set to 10% in the present invention.
  • the content is large, such as more than 14%, since ferrite is easily generated, a large amount of an expensive austenite generation element must be added in order to stably ensure a martensitic phase or to prevent degradation of the hot workability, so that economical problems may arise.
  • the Cr content is limited in the range of 10% to 14%.
  • the content is preferably in the range of 10.5% to 11.5%.
  • Ni has a function to strengthen a passivation film and is an element to improve the corrosion resistance, such as CO 2 corrosion resistance.
  • the content In order to obtain the effect as described above, the content must be 0.1% or more. On the other hand, when the content is more than 4.0%, the improvement effect is saturated, and as a result, a manufacturing cost is inevitably increased. Hence, the Ni content is limited in the range of 0.1% to 4.0%. In addition, the content is preferably in the range of 1.5% to 3.0%.
  • N is an element to significantly improve pitting resistance, and when the content is 0.003% or more, the effect described above becomes significant. On the other hand, when the content is more than 0.05%, various nitrides are formed, and as a result, the toughness is degraded. Hence, the N content is limited to 0.05% or less. In addition, the content is preferably in the range of 0.01% to 0.02%.
  • the components described above are basic components of the starting material, according to the present invention, besides those basic components described above, at least one selected from the group consisting of 2.0% or less of Cu and 2.0% or less of Mo and/or at least one selected from the group consisting of 0.10% or less of V, 0.10% or less of Nb, and 0.10% or less of Ti may also be contained.
  • Cu and Mo are elements each having a function to improve the corrosion resistance and, whenever necessary, at least one of them may be selected and contained.
  • Cu is an element having a function to improve the pitting resistance by strengthening a passivation film, and in order to obtain the effect as described above, the content is preferably 0.2% or more.
  • the content is more than 2.0%, Cu is partly precipitated, and as a result, the toughness is degraded.
  • the content thereof is limited to 2.0% or less.
  • the content is in the range of 0.2% to 1.0%.
  • Mo is an element having a function to increase the resistance against pitting caused by Cl - , and in order to obtain the above effect, the content is preferably 0.2% or more.
  • the content is more than 2.0%, the strength is not only decreased, but a material cost is also increased.
  • the Mo content is limited to 2.0% or less.
  • the content is in the range of 0.2% to 1.0%.
  • V, Nb, and Ti are components to increase the strength, and whenever necessary, at least one of them may be selected and contained.
  • At least one of 0.02% or more of V, 0.01% or more of Nb, and 0.02% or more of Ti is preferably contained.
  • the toughness is degraded.
  • the contents of V, Nb, and Ti are each limited to 0.10% or less.
  • the V content is 0.02% to 0.05%
  • the Nb content is 0.01% to 0.05%
  • the Ti content is 0.02% to 0.05%.
  • the balance other than those components described above is Fe and inevitable impurities, which may contain, 0.010% or less of O.
  • a method for manufacturing a starting material having the above composition is not particularly limited, it is preferable that after molten steel having the above composition is formed by a commonly known steelmaking method, for example, using a converter, an electrical furnace, a vacuum melting furnace, and the like, a steel pipe material, such as a billet, be formed by a common method, such as a continuous casting method, or an ingot-making and blooming method. Subsequently, the steel pipe material is heated and is processed by hot working using a common Mannesmann-plug mill type or Mannesmann-mandrel mill type manufacturing process to form a seamless steel pipe having a desired dimension, and this seamless steel pipe is preferably used as the starting material.
  • a seamless steel pipe may also be manufactured by press type hot extrusion.
  • the seamless steel pipe is preferably cooled to room temperature at a cooling rate equivalent to or more than that of air cooling.
  • the starting material (seamless steel pipe) is first processed by a quenching treatment.
  • the quenching treatment of the present invention is a treatment in which after re-heating is performed to a heating temperature for quenching equivalent to or more than the Ac 3 transformation point, cooling is performed from the heating temperature for quenching to a temperature range of 100°C or less at a cooling rate equivalent to or more than that of air cooling.
  • a fine martensitic microstructure can be obtained.
  • a heating temperature for quenching is less than the Ac 3 transformation point, since heating cannot be performed to the austenite single phase region, and a sufficient martensitic microstructure cannot be obtained by subsequent cooling, a desired strength cannot be ensured.
  • the heating temperature for quenching of the quenching treatment is limited to be equivalent to or more than the Ac 3 transformation point.
  • the heating temperature is 950°C or less.
  • the cooling from the quenching heating temperature is performed to a temperature range of 100°C or less at a cooling rate equivalent to or more than that of air cooling. Since the starting material of the present invention has high hardenability, when the cooling is performed to a temperature range of 100°C or less at a cooling rate approximately equivalent to that of air cooling, a sufficiently quenched microstructure (martensitic microstructure) can be obtained.
  • the holding time at the heating temperature for quenching is set to 10 minutes or more in view of uniform heating.
  • the seamless steel pipe processed by the quenching treatment is subsequently processed by a tempering treatment.
  • the tempering treatment is an important treatment to ensure a superior low temperature toughness.
  • the tempering treatment of the present invention is defined as a treatment in which after heating is performed to a tempering temperature in the range of 450°C to 550°C and is maintained for 30 minutes or more, cooling is performed preferably to room temperature preferably at a cooling rate equivalent to or more than that of air cooling.
  • the tempering temperature is less than 450°C, since the tempering is insufficient, the toughness is degraded, and as a result, a high strength and a high toughness cannot be simultaneously obtained.
  • the tempering temperature is more than 550°C, besides a decrease in strength, since the grain boundaries become brittle, the intergranular fracture is liable to occur, and the toughness is also degraded; hence, a high strength and a high toughness cannot be simultaneously obtained.
  • the tempering temperature is preferably in the range of 500°C to 550°C.
  • the holding time at the tempering temperature is set to 30 minutes or more.
  • the cooling from the tempering temperature is performed at a cooling rate equivalent to or more than that of air cooling.
  • a correction treatment for correcting defect in pipe shape may be performed in the cooling of the tempering treatment.
  • the correction treatment is performed in a temperature range of 400°C or more.
  • the temperature of the correction treatment is less than 400°C, a working strain is locally applied to the steel pipe when the correction treatment is performed, and hence variation in mechanical characteristics is liable to be generated.
  • the correction treatment is performed in a temperature range of 400°C or more.
  • a seamless steel pipe manufactured by the above-described manufacturing method is a martensitic stainless steel seamless pipe which has the composition described above and which simultaneously has a high yield strength of 758-862 MPa (a 110 ksi grade of yield strength) and a superior low temperature toughness having a fracture transition temperature vTrs of - 60°C or less in a Charpy impact test.
  • this martensitic stainless steel seamless pipe has a microstructure including a tempered martensitic phase as a primary phase.
  • the seamless steel pipes thus obtained were subjected to a quenching treatment and a tempering treatment, and were further subjected to a correction treatment whenever necessary.
  • V-notch test pieces (10 mm thick) in accordance with JIS Z 2242 standard were obtained from the seamless steel pipes which were subjected to the quenching treatment and the tempering treatment and were further subjected to the correction treatment whenever necessary, a Charpy impact test was carried out to obtain the fracture transition temperature vTrs and absorption energy vE -60 at a temperature of -60°C, so that the toughness was evaluated.
  • a Charpy impact test was performed at a temperature of -60°C, and the variation was evaluated from the average value (ave) and the minimum value (min) of the absorption energy vE -60 .
  • corrosion test pieces having a thickness of 3 mm, a width of 25 mm, and a length of 50 mm were formed from the steel pipes by machining, and a corrosion test was performed.
  • the corrosion test was performed in such a way that the corrosion test pieces were immersed for one week (168 hours) in a test solution, a 20%-NaCl aqueous solution (solution temperature: 80°C, and a CO 2 gas environment at 30 bar pressure), which was placed in an autoclave.
  • the weights of the test pieces subjected to the corrosion test were measured, and corrosion rates were obtained by calculating the weight loss before and after the corrosion test.
  • the surfaces of the test pieces subjected to the corrosion test were observed with a loupe having a magnification of 10 to confirm the pitting generation.
  • the pitting in the case in which at least one pit was observed, it was regarded that pitting occurred, and in the other cases, it was regarded that no pitting occurred.
  • the obtained results are shown in Table 3.
  • a martensitic stainless steel seamless pipe could be obtained which had a sufficient corrosion resistance as oil country tubular goods and which simultaneously had a high yield strength of 758-862 MPa (a 110 ksi grade of YS) and a superior low temperature toughness having a vTrs of -60°C or less.
  • a high yield strength of 758-862 MPa a 110 ksi grade of YS
  • a superior low temperature toughness having a vTrs of -60°C or less.

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  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
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Claims (3)

  1. Nahtloses Rohr aus martensitischem nichtrostendem Stahl für Ölfeldrohre, umfassend: eine Zusammensetzung, die auf Massenprozentbasis aus Folgendem besteht:
    weniger als 0,010 % C, 1,0 % oder weniger an Si,
    0,1 % bis 2,0 % Mn, 0,020 % oder weniger an P,
    0,010 % oder weniger an S, 0,10 % oder weniger an Al,
    10 % bis 14 % Cr, 0,1 % bis 4,0 % Ni,
    0,05 % oder weniger an N,
    optional mindestens einem Element, das aus der Gruppe gewählt wird, die aus 2,0 % oder weniger an Cu und 2,0 % oder weniger an Mo besteht und/oder
    mindestens einem Element, das aus der Gruppe gewählt wird, die aus 0,10 % oder weniger an V, 0,10 % oder weniger an Nb und 0,10 % oder weniger an Ti besteht und
    wobei der Rest Fe und unvermeidbare Verunreinigungen sind, die 0,010 % oder weniger O enthalten können,
    wobei das nahtlose Rohr aus martensitischem nichtrostendem Stahl gleichzeitig eine hohe Streckgrenze von 758 - 862 MPa (eine Streckgrenzenklasse von 110 ksi) und eine hervorragende Tieftemperaturzähigkeit mit einer Bruchübergangstemperatur vTrs von -60 °C oder weniger in einem Charpy-Kerbschlagversuch aufweist.
  2. Verfahren zur Herstellung eines nahtlosen Rohres aus martensitischem nichtrostendem Stahl für Ölfeldrohre, das gleichzeitig eine hohe Streckgrenze von 758 - 862 MPa (eine Streckgrenzenklasse von 110 ksi) und eine hervorragende Tieftemperaturzähigkeit aufweist, umfassend: Durchführen einer Abschreckbehandlung an einem nahtlosen Rohr aus nichtrostendem Stahl, das eine Zusammensetzung aufweist, die auf Massenprozentbasis aus Folgendem besteht:
    weniger als 0,010 % C, 1,0 % oder weniger an Si,
    0,1 % bis 2,0 % Mn, 0,020 % oder weniger an P,
    0,010 % oder weniger an S, 0,10 % oder weniger an Al,
    10 % bis 14 % Cr, 0,1% bis 4,0 % Ni,
    0,05 % oder weniger an N,
    optional mindestens einem Element, das aus der Gruppe gewählt wird, die aus 2,0 % oder weniger an Cu und 2,0 % oder weniger an Mo besteht und/oder
    mindestens einem Element, das aus der Gruppe gewählt wird, die aus 0,10 % oder weniger an V, 0,10 % oder weniger an Nb und 0,10 % oder weniger an Ti besteht und
    wobei der Rest Fe und unvermeidbare Verunreinigungen sind, die 0,010 % oder weniger an O enthalten können, wobei, nachdem das Erwärmen auf eine Erwärmungstemperatur zum Abschrecken gleich oder höher der Ac3-Transformationstemperatur und niedriger als oder gleich 950 °C für zehn Minuten oder länger durchgeführt wurde, das Abkühlen von der Erwärmungstemperatur zum Abschrecken auf einem Temperaturbereich von 100 °C oder weniger bei einer Abkühlgeschwindigkeit gleich oder höher als die der Luftkühlung erfolgt; und Durchführen einer Anlassbehandlung, bei der nach der Abschreckbehandlung eine Erwärmung auf eine Anlasstemperatur in dem Bereich von 450 °C bis 550 °C für 30 Minuten oder länger durchgeführt wird, und anschließend das Abkühlen mit einer Abkühlgeschwindigkeit gleich oder höher als die der Luftkühlung erfolgt.
  3. Verfahren zur Herstellung eines nahtlosen Rohres aus martensitischem nichtrostendem Stahl für Ölfeldrohre nach Anspruch 2, wobei während des Abkühlens der Ablassbehandlung eine Korrekturbehandlung in einem Temperaturbereich von 400 °C oder mehr durchgeführt wird.
EP07829943.5A 2007-06-29 2007-10-10 Nahtloses rohr aus martensitischem nichtrostendem stahl für ölbohrungsrohr und herstellungsverfahren dafür Active EP2172573B1 (de)

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EP2172573A1 (de) 2010-04-07
JP5145793B2 (ja) 2013-02-20
CN101437973B (zh) 2012-09-05
US20100193087A1 (en) 2010-08-05
WO2009004741A1 (ja) 2009-01-08
EP2172573A4 (de) 2011-05-18
RU2431693C1 (ru) 2011-10-20
JP2009007658A (ja) 2009-01-15
RU2010102917A (ru) 2011-08-10
CN101437973A (zh) 2009-05-20

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