WO2019065116A1 - 油井管用マルテンサイト系ステンレス継目無鋼管およびその製造方法 - Google Patents
油井管用マルテンサイト系ステンレス継目無鋼管およびその製造方法 Download PDFInfo
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- 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
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- 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
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- 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
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
Definitions
- the present invention relates to a martensitic stainless steel seamless steel pipe for oil well used for oil wells and gas wells of crude oil or natural gas (hereinafter simply referred to as oil wells) and a method for producing the same.
- the present invention relates to improvement of sulfide stress corrosion cracking resistance (SSC resistance) in an environment containing hydrogen sulfide (H 2 S).
- Patent Document 1 C is significantly reduced compared to the prior art, containing 13% Cr steel as a basic composition, Ni, Mo and Cu are contained, Cr + 2Ni + 1.1Mo + 0.7Cu ⁇ 32.5 is satisfied, and Nb: 0.20% or less , V: 0.20% or less of which one or two kinds are contained so as to satisfy the condition of Nb + V% 0.05%, yield stress: high strength of 965 MPa or more, and Charpy at -40 ° C It has high toughness of 50 J or more, and it can maintain good corrosion resistance.
- Patent Document 2 describes a component system 13% Cr-based martensitic stainless steel pipe containing an extremely low C amount of 0.015% or less and Ti of 0.03% or more, and a high strength of yield stress 95 ksi class, It has low hardness of less than 27 in HRC, and has excellent SSC resistance.
- Patent Document 3 describes a martensitic stainless steel satisfying 6.0 ⁇ Ti / C ⁇ 10.1 because Ti / C has a correlation with a value obtained by subtracting yield stress from tensile stress. According to the technology described above, the value obtained by subtracting the yield stress from the tensile stress is 20.7 MPa or more, and the variation in hardness that reduces the SSC resistance can be suppressed.
- the amount of Mo in the steel is defined as Mo2.32.3 ⁇ 0.89 Si + 32.2 C, and the metal structure is mainly tempered martensite, carbide precipitated during tempering, and Laves precipitated finely during tempering.
- a martensitic stainless steel composed of intermetallic compounds such as phase and ⁇ phase is described. According to the described technology, it is said that the 0.2% proof stress of the steel becomes high strength of 860 MPa or more, and can have excellent carbon dioxide gas corrosion resistance and sulfide stress corrosion cracking resistance.
- JP 2007-332442 A JP, 2010-242163, A International Publication 2008/023702 International Publication 2004/057050
- Patent Document 2 it is considered that sulfide stress cracking resistance can be maintained under a condition that a stress of 655 MPa is applied under an atmosphere adjusted to pH: 3.5 with 5% NaCl aqueous solution (H 2 S: 0.10 bar).
- Patent Document 3 describes an aqueous solution of 20% NaCl aqueous solution (H 2 S: 0.03 bar, CO 2 bal.) Adjusted to pH: 4.5
- Patent Document 4 an aqueous 25% NaCl solution (H 2 S: 0.03
- the steel is considered to have resistance to sulfide stress cracking under an atmosphere adjusted to pH: 4.0 bar, CO 2 bal).
- sulfide stress corrosion cracking resistance under an atmosphere other than the above has not been studied, and it can not be said to have sulfide stress corrosion cracking resistance that can withstand the current severe corrosion environment.
- An object of the present invention is to provide a martensitic stainless steel seamless steel pipe for oil well pipe having high strength and excellent resistance to sulfide stress corrosion cracking and a method for producing the same.
- high strength here shall be yield stress: 758 Mpa (110 ksi) or more.
- the yield stress is 896 MPa or less.
- excellent resistance to sulfide stress corrosion cracking refers to a test solution: 0.165 mass% NaCl aqueous solution (liquid temperature: 25 ° C., H 2 S: 1 bar, CO 2 bal), sodium acetate + hydrochloric acid
- the test piece is immersed in an aqueous solution adjusted to pH: 3.5, the immersion time is 720 hours, 90% of the yield stress is applied as an applied stress, the test is performed, and the test piece after the test is cracked It shall mean the case of not doing.
- the present inventors have resistance to sulfide stress corrosion cracking in a corrosive environment containing 13% Cr-based stainless steel pipe as a basic composition, CO 2 , Cl ⁇ and H 2 S.
- the effects of various alloying elements on SSC resistance) were studied intensively.
- the steel contains each component in a predetermined range, and C, Mn, Cr, Cu, Ni, Mo, W, Nb, N, and Ti are adjusted to satisfy appropriate relational expressions and ranges.
- the present invention has been completed based on the above-mentioned findings, with further studies. That is, the gist of the present invention is as follows. [1] mass%, C: 0.0010 to 0.0094%, Si: 0.5% or less, Mn: 0.05 to 0.5%, P: 0.030% or less, S: 0.005% or less, Ni: 4.6 to 7.3%, Cr: 10.0 to 14.5%, Mo: 1.0 to 2.7%, Al: 0.1% or less, V: 0.2% or less, N: 0.1% or less Ti: 0.01 to 0.50%, Cu: 0.01 to 1.0%, Co: 0.01 to 1.0% A martensitic stainless steel seamless steel pipe for oil well pipes, containing the following values (1) and (2) and satisfying the following expression (3) and having a yield stress of 758 MPa or more consisting of balance Fe and unavoidable impurities.
- Nb 0.25% or less by mass%
- W A martensitic stainless steel seamless steel pipe for oil well tubes according to [1], which has a composition containing one or two or more selected from the following: 1.1% or less.
- Ca 0.010% or less
- REM 0.010% or less
- Mg 0.010% or less
- B A martensitic stainless steel seamless steel pipe for oil well tubes according to [1] or [2], which has a composition containing one or more selected from 0.010% or less.
- the present invention has excellent sulfide stress corrosion cracking resistance (SSC resistance) in a corrosive environment containing CO 2 , Cl ⁇ and further H 2 S, and yield stress YS: 758 MPa (110 ksi)
- SSC resistance sulfide stress corrosion cracking resistance
- composition limitation reason of the steel pipe of the present invention will be described.
- mass% is simply described as% unless otherwise specified.
- C is an important element related to the strength of martensitic stainless steel, and is effective for improving the strength.
- a content of 0.0010% or more is required.
- the content is more than 0.0094%, the corrosion resistance is lowered because Cr carbonitride is formed. Therefore, in the present invention, C is limited to 0.0010 to 0.0094%. Preferably, it is 0.0050 to 0.0094%.
- Si 0.5% or less Since Si acts as a deoxidizer, it is desirable to contain 0.05% or more. On the other hand, the content exceeding 0.5% reduces carbon dioxide corrosion resistance and hot workability. For this reason, Si was limited to 0.5% or less. The preferred range is 0.10 to 0.30%.
- Mn 0.05 to 0.5%
- Mn is an element that improves the hot workability, and contains 0.05% or more in order to ensure the required strength. On the other hand, even if the content of Mn exceeds 0.5%, the effect is saturated and the cost is increased. Therefore, Mn was limited to 0.05 to 0.5%. Preferably, it is 0.4% or less.
- P 0.030% or less
- P is an element that reduces both carbon dioxide gas corrosion resistance, pitting corrosion resistance, and sulfide stress corrosion cracking resistance, and in the present invention, it is desirable to reduce as much as possible.
- extreme reductions increase manufacturing costs. Therefore, P was limited to 0.030% or less as an industrially inexpensively practicable range within a range that does not cause an extreme decrease in the characteristics.
- Preferably it is 0.020% or less.
- S 0.005% or less Since S is an element that significantly reduces the hot workability, it is desirable to reduce it as much as possible. By reducing the S content to 0.005% or less, it becomes possible to produce a pipe in a normal process, so S in the present invention is limited to 0.005% or less. In addition, Preferably it is 0.003% or less.
- Ni 4.6 to 7.3%
- Ni is an element which strengthens the protective film to improve the corrosion resistance and further increases the strength of the steel by solid solution. In order to obtain such an effect, the content needs to be 4.6% or more. On the other hand, when the Ni content exceeds 7.3%, the stability of the martensitic phase decreases and the strength decreases. Therefore, Ni was limited to 4.6 to 7.3%.
- Cr 10.0 to 14.5%
- Cr is an element which forms a protective film and improves corrosion resistance, and by containing 10.0% or more, the corrosion resistance necessary for oil well pipes can be secured. On the other hand, if the content exceeds 14.5%, the formation of ferrite becomes easy, so that the martensite phase can not be stably ensured. Therefore, Cr is limited to 10.0 to 14.5%. Preferably, it is 11.0 to 13.5%.
- Mo 1.0 to 2.7% Mo is an element that improves the resistance to pitting corrosion by Cl ⁇ , and needs to be 1.0% or more in order to obtain the corrosion resistance necessary for a severe corrosive environment.
- Mo when the content of Mo exceeds 2.7%, in addition to the saturation of the above effects, the corrosion resistance is lowered due to the increase in hardness.
- Mo since Mo is an expensive element, it causes a rise in manufacturing cost. Therefore, Mo was limited to 1.0 to 2.7%. Preferably, it is 1.5 to 2.5%.
- Al 0.1% or less Since Al acts as a deoxidizer, a content of 0.01% or more is effective to obtain such an effect. However, since the content exceeding 0.1% adversely affects the toughness, Al in the present invention is limited to 0.1% or less. Preferably, it is 0.01 to 0.03%.
- V 0.2% or less V improves the strength of the steel by precipitation strengthening and also improves the resistance to sulfide stress corrosion cracking, so a content of 0.005% or more is desirable.
- the V content in the present invention is limited to 0.2% or less, since the toughness is lowered when the content exceeds 0.2%.
- V is 0.01 to 0.08%.
- N 0.1% or less N is an element that significantly improves pitting resistance. However, when the N content exceeds 0.1%, various nitrides are formed to reduce the toughness, so the N in the present invention is limited to 0.1% or less. Preferably, it is 0.004 to 0.08%, and more preferably 0.005 to 0.05%.
- Ti 0.01 to 0.50%
- Ti is an element which forms Ti carbide by bonding with C and extremely reduces C, and in order to obtain such an effect, the content thereof needs to be 0.01% or more.
- the content exceeds 0.50%, coarse carbides are generated which is a cause of lowering the toughness and the resistance to sulfide stress corrosion cracking. Therefore, Ti is limited to 0.01 to 0.50%.
- the preferred range is 0.05 to 0.15%.
- Cu 0.01 to 1.0% At a content of 0.01% or more, Cu strengthens the protective film and suppresses active dissolution to improve resistance to sulfide stress corrosion cracking. On the other hand, when the content exceeds 1.0%, CuS precipitates to reduce the hot workability. Therefore, Cu was limited to 0.01 to 1.0%.
- Co 0.01 to 1.0%
- Co is an element that reduces the hardness and improves the pitting resistance by raising the Ms point and promoting the ⁇ transformation. In order to acquire such an effect, 0.01% or more needs to be contained. On the other hand, excessive content may lower the toughness and further increase the material cost. Therefore, Co in the present invention is limited to 0.01 to 1.0%.
- the following value (1) and value (2) satisfy each of the following expression (3): Contains elements.
- the value (1) is an equation correlating to the amount of residual ⁇ , and by reducing the value of the value (1), retained austenite is reduced, the hardness is reduced, and the sulfide stress corrosion cracking resistance is improved.
- the value (2) is an equation correlating to the pitting potential, and C, Mn, Cr, Cu, Ni, Mo, W, N so that the value (2) satisfies the range of the following equation (3)
- the occurrence of pitting corrosion which is the starting point of sulfide stress corrosion cracking is suppressed, and the resistance to sulfide stress corrosion cracking is remarkably improved.
- a value (1) causes a rise in hardness when it is 10 or more, when the value (2) satisfies the range of the following equation (3), the occurrence of pitting corrosion appears prominently, and sulfide stress corrosion resistance Crackability is improved.
- Nb can reduce solid solution carbon and reduce hardness by forming carbides.
- excessive content may lower toughness.
- W is an element improving the pitting resistance, but an excessive content may lower the toughness and further increase the material cost. Therefore, in the case of containing Nb: 0.25% or less, W: 1.1% or less.
- Ca 0.010% or less
- REM 0.010% or less
- Mg 0.010% or less
- B One or more selected from 0.010% or less
- Ca, REM, Mg and B are all elements which improve corrosion resistance through shape control of inclusions. To get this effect, Ca: 0.0005% or more, REM: 0.0005% or more, Mg: 0.0005% or more, B: It is desirable to contain 0.0005% or more. on the other hand, Ca: 0.010%, REM: 0.010%, Mg: 0.010%, B: 0.010% If the content is more than the above, the toughness and the carbon dioxide corrosion resistance decrease. Therefore, when it contains, Ca: 0.010% or less, REM: 0.010% or less, Mg: 0.010% or less, B: Limited to 0.010% or less.
- the balance other than the above-mentioned component composition consists of Fe and unavoidable impurities.
- a steel pipe material having the above composition is used, but the method of manufacturing a stainless steel seamless steel pipe, which is a steel pipe material, is not particularly limited, and any known method of manufacturing a seamless pipe can be applied.
- the molten steel of the above composition is melted by a melting method such as a converter and made into a steel pipe material such as billet by a method such as continuous casting or ingot-slab rolling. Subsequently, these steel tube materials are heated, hot worked and piped in a pipe forming process of Mannesman-plug mill method or Mannesman-mandrel mill method which is a known pipe forming method, and a joint having the above composition No steel pipe.
- the treatment after forming the steel pipe material into the steel pipe is not particularly limited, but preferably, the steel pipe is heated to a temperature above the Ac 3 transformation point and then quenched to a cooling stop temperature of 100 ° C. or less And a tempering treatment for tempering at a temperature below the Ac 1 transformation point.
- the steel pipe is further reheated to a temperature above the Ac 3 transformation point, preferably held for 5 minutes or more, and then cooled to a cooling stop temperature of 100 ° C. or less.
- a cooling stop temperature 100 ° C. or less.
- cooling is performed by air cooling (cooling rate 0.05 ° C./s or more and 20 ° C./s or less) or water cooling (cooling rate 5 ° C./s or more and 100 ° C./s or less). It is not limited.
- tempering treatment is applied to the steel pipe subjected to the quenching treatment.
- the tempering treatment is a treatment for heating a steel pipe to a temperature below the Ac 1 transformation point, preferably holding it for 10 minutes or more, and cooling it.
- the tempering temperature becomes higher than the Ac 1 transformation point, a martensitic phase precipitates after tempering, and desired high toughness and excellent corrosion resistance can not be secured. Therefore, the tempering temperature is limited to the Ac 1 transformation point or less.
- the above-mentioned Ac 3 transformation point (° C.) and Ac 1 transformation point (° C.) give a temperature history of heating and cooling to the test piece and detect the transformation point from minute displacement of expansion and contraction by the Fourmaster test It can be measured.
- this billet After melting the molten steel of the component shown in Table 1 with a converter, it casts into a billet (steel pipe material) by a continuous casting method. Further, this billet was formed by hot working using a model seamless rolling mill and then cooled by air cooling or water cooling to obtain a seamless steel pipe having an outer diameter of 83.8 mm and a thickness of 12.7 mm.
- test material was cut out from the obtained seamless steel pipe, and the test material was subjected to quenching and tempering treatment under the conditions shown in Table 2. After a test piece for observation of structure was collected from a test material subjected to quenching and tempering treatment and polished, the amount of retained austenite ( ⁇ ) was measured by X-ray diffraction method.
- an API arc-shaped tensile test specimen is collected from a test material subjected to quenching treatment and tempering treatment, and a tensile test is performed according to the specification of API to determine tensile characteristics (yield stress YS, tensile stress TS).
- yield stress YS yield stress YS
- tensile stress TS tensile stress characteristics
- the SSC test was performed according to NACE TM0177 Method A.
- the test environment used was prepared by adding 0.41 g / L CH 3 COONa + HCl to a 0.165 mass% NaCl aqueous solution (liquid temperature: 25 ° C., H 2 S: 1 bar, CO 2 bal) as a test solution to adjust the pH to 3.5.
- the test was carried out with a hydrogen sulfide partial pressure of 0.1 MPa, an immersion time of 720 hours, and 90% of the yield stress as the applied stress.
- produce in the test piece after a test was set as pass, and the case where a crack generate
- the martensitic stainless steel seamless steel pipe having excellent SSC resistance all of which have high strength of yield stress of 758 MPa or more and no generation of cracking even when stressed in an environment containing H 2 S according to the present invention. It has become.
- the comparative example out of the range of the present invention although the desired high strength is obtained, the excellent SSC resistance can not be secured.
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Abstract
Description
[1]質量%で、
C:0.0010~0.0094%、
Si:0.5%以下、
Mn:0.05~0.5%、
P:0.030%以下、
S:0.005%以下、
Ni:4.6~7.3%、
Cr:10.0~14.5%、
Mo:1.0~2.7%、
Al:0.1%以下、
V:0.2%以下、
N:0.1%以下、
Ti:0.01~0.50%、
Cu:0.01~1.0%、
Co:0.01~1.0%
を含有し、かつ下記値(1)および値(2)が下記(3)式を満足し、残部Feおよび不可避的不純物からなる758MPa以上の降伏応力を有する油井管用マルテンサイト系ステンレス継目無鋼管。
-109.37C+7.307Mn+6.399Cr+6.329Cu+11.343Ni-13.529Mo+1.276W+2.925Nb
+196.775N-2.621Ti-120.307 ・・・(1)
-1.324C+0.0533Mn+0.0268Cr+0.0893Cu+0.00526Ni+0.0222Mo-0.0132W-0.473N-0.5Ti-0.514 ・・・(2)
ここで、C、Mn、Cr、Cu、Ni、Mo、W、Nb、N、Ti:各元素の含有量(質量%)(但し、含有しない元素は0(零)%とする。)
-35.0≦値(1)≦45 且つ -0.40≦値(2)≦0.070 ・・・(3)
[2]前記組成に加えてさらに、質量%で
Nb:0.25%以下、
W:1.1%以下
のうちから選ばれた1種または2種を含有する組成とする[1]に記載の油井管用マルテンサイト系ステンレス継目無鋼管。
[3]前記組成に加えてさらに、質量%で、
Ca:0.010%以下、
REM:0.010%以下、
Mg:0.010%以下、
B:0.010%以下
のうちから選ばれた1種または2種以上を含有する組成とする[1]または[2]に記載の油井管用マルテンサイト系ステンレス継目無鋼管。
[4][1]~[3]のいずれかに記載の組成を有する鋼管素材を造管し鋼管としたのち、該鋼管をAc3変態点以上に加熱し、続いて100℃以下の冷却停止温度まで冷却する焼入れ処理と、ついでAc1変態点以下の温度で焼き戻しをする焼戻処理とを施す油井管用マルテンサイト系ステンレス継目無鋼管の製造方法。
Cはマルテンサイト系ステンレス鋼の強度に関係する重要な元素であり、強度向上に有効である。本発明における所望の強度を得るためには、0.0010%以上の含有を必要とする。一方、0.0094%を超える含有量では、Cr炭窒化物を生成するため、耐食性が低下する。このため、本発明では、Cは0.0010~0.0094%に限定した。好ましくは0.0050~0.0094%である。
Siは、脱酸剤として作用するため、0.05%以上含有することが望ましい。一方で、0.5%を超える含有は、耐炭酸ガス腐食性および熱間加工性を低下させる。このため、Siは0.5%以下に限定した。なお、好ましくは0.10~0.30%である。
Mnは、熱間加工性を向上させる元素であり、必要な強度を確保するためには0.05%以上含有する。一方、0.5%を超えてMnを含有しても、その効果が飽和し、かえってコストの高騰を招く。よって、Mnは0.05~0.5%に限定した。好ましくは、0.4%以下である。
Pは、耐炭酸ガス腐食性、耐孔食性、耐硫化物応力腐食割れ性をともに低下させる元素であり、本発明ではできるだけ低減させることが望ましい。しかしながら、極端な低減は製造コストを高騰させる。よって、特性の極端な低下を招かない範囲で、かつ工業的に安価に実施可能な範囲として、Pは0.030%以下に限定した。なお、好ましくは0.020%以下である。
Sは、熱間加工性を著しく低下させる元素であるため、できるだけ低減させることが望ましい。S含有量を0.005%以下に低減することで、通常工程でのパイプ製造が可能となるため、本発明におけるSは0.005%以下に限定した。なお、好ましくは0.003%以下である。
Niは、保護被膜を強固にして耐食性を向上させ、更に固溶することで鋼の強度を増加させる元素である。このような効果を得るためには、4.6%以上の含有を必要とする。一方、Ni含有量が7.3%を超えると、マルテンサイト相の安定性が低下して、強度が低下する。よって、Niは4.6~7.3%に限定した。
Crは、保護被膜を形成して耐食性を向上させる元素であり、10.0%以上の含有で油井管用として必要な耐食性を確保できる。一方、含有量が14.5%を超えるとフェライトの生成が容易となるため、マルテンサイト相の安定確保ができなくなる。よって、Crは10.0~14.5%に限定した。なお、好ましくは11.0~13.5%である。
Moは、Cl-による孔食に対する抵抗性を向上させる元素であり、厳しい腐食環境に必要な耐食性を得るためには、1.0%以上の含有が必要である。一方、2.7%を超えるMoの含有は、上記の効果が飽和することに加え、硬度が高くなることで耐食性が低下する。また、Moは高価な元素であるため、製造コストの高騰を招く。よって、Moは1.0~2.7%に限定した。なお、好ましくは1.5~2.5%である。
Alは、脱酸剤として作用するため、このような効果を得るためには、0.01%以上の含有が有効である。しかしながら、0.1%を超える含有は、靱性に悪影響を及ぼすため、本発明におけるAlは0.1%以下に限定した。なお、好ましくは0.01~0.03%である。
Vは、析出強化によって鋼の強度を向上させ、更に耐硫化物応力腐食割れ性も向上させるため、0.005%以上の含有が望ましい。一方、0.2%を超える含有は、靱性が低下するため、本発明におけるVは0.2%以下に限定した。好ましくは、Vは0.01~0.08%である。
Nは、耐孔食性を著しく向上させる元素である。しかしながら、N含有量が0.1%超えでは、種々の窒化物を形成して靱性を低下させるため、本発明におけるNは0.1%以下に限定した。好ましくは0.004~0.08%であり、さらに好ましくは0.005~0.05%である。
Tiは、Cと結合することでTi炭化物を形成し、極低C化する元素であり、このような効果を得るためには0.01%以上の含有が必要となる。一方、0.50%を超える含有では、靱性や耐硫化物応力腐食割れ性を低下させる原因である粗大な炭化物が生成する。よって、Tiは0.01~0.50%に限定した。なお、好ましくは0.05~0.15%である。
Cuは、0.01%以上の含有で、保護皮膜を強固にすると共に活性溶解を抑制し、耐硫化物応力腐食割れ性を向上させる。一方、1.0%を超える含有は、CuSが析出して熱間加工性を低下させる。よって、Cuは0.01~1.0%に限定した。
Coは、Ms点を上昇させα変態を促進することで、硬さを低減すると共に、耐孔食性を向上させる元素である。このような効果を得るためには、0.01%以上の含有を必要とする。一方、過剰な含有は靱性を低下させる場合があり、更に材料コストを高騰させる。よって、本発明におけるCoは0.01~1.0%に限定した。
-109.37C+7.307Mn+6.399Cr+6.329Cu+11.343Ni-13.529Mo+1.276W+2.925Nb
+196.775N-2.621Ti-120.307 ・・・(1)
-1.324C+0.0533Mn+0.0268Cr+0.0893Cu+0.00526Ni+0.0222Mo-0.0132W-0.473N-0.5Ti-0.514 ・・・(2)
ここで、C、Mn、Cr、Cu、Ni、Mo、W、Nb、N、Ti:各元素の含有量(質量%)(但し、含有しない元素は0(零)%とする。)
-35.0≦値(1)≦45 且つ -0.40≦値(2)≦0.070 ・・・(3)
更に、必要に応じて選択元素として、Nb:0.25%以下、W:1.1%以下のうちから選ばれた1種または2種を含有することができる。
Ca:0.010%以下、
REM:0.010%以下、
Mg:0.010%以下、
B:0.010%以下
のうちから選ばれた1種または2種以上することができる。
Ca:0.0005%以上、
REM:0.0005%以上、
Mg:0.0005%以上、
B:0.0005%以上
含有することが望ましい。一方、
Ca:0.010%、
REM:0.010%、
Mg:0.010%、
B:0.010%
を超えて含有すると、靱性および耐炭酸ガス腐食性を低下させる。よって、含有する場合には、
Ca:0.010%以下、
REM:0.010%以下、
Mg:0.010%以下、
B:0.010%以下
に限定した。
本発明では、更に鋼管を、Ac3変態点以上の温度に再加熱し、好ましくは5min以上保持し、続いて100℃以下の冷却停止温度まで冷却する。これによって、マルテンサイト相の微細化と高靱化が得られる。焼入れ加熱温度がAc3変態点未満では、組織がオーステナイト単相域とならないため、その後の冷却で十分なマルテンサイト組織が得られず、所望の高強度を達成できない。よって、焼入れ加熱温度はAc3変態点以上に限定する。なお、冷却方法は限定しないが、一般に空冷(冷却速度0.05℃/s以上20℃/s以下)または水冷(冷却速度5℃/s以上100℃/s以下)により冷却し、冷却速度の条件も限定されない。
続いて、焼入れ処理を施した鋼管に、焼戻処理を施す。焼戻処理は、鋼管をAc1変態点以下に加熱し、好ましくは10min以上保持し、冷却する処理である。焼戻温度がAc1変態点より高温になると、焼戻後にマルテンサイト相が析出し、所望の高靱性および優れた耐食性を確保できない。よって、焼戻温度はAc1変態点以下に限定する。なお、上記のAc3変態点(℃)、Ac1変態点(℃)については、試験片に加熱および冷却の温度履歴を与え、膨張および収縮の微小変位から変態点を検出するフォーマスター試験により測定することができる。
γ(体積率)=100/(1+(IαRγ/IγRα))
ここで、Iα:αの積分強度
Rα:αの結晶学的理論計算値
Iγ:γの積分強度
Rγ:γの結晶学的理論計算値
を用いて換算した。
Claims (4)
- 質量%で、
C:0.0010~0.0094%、
Si:0.5%以下、
Mn:0.05~0.5%、
P:0.030%以下、
S:0.005%以下、
Ni:4.6~7.3%、
Cr:10.0~14.5%、
Mo:1.0~2.7%、
Al:0.1%以下、
V:0.2%以下、
N:0.1%以下、
Ti:0.01~0.50%、
Cu:0.01~1.0%、
Co:0.01~1.0%
を含有し、かつ下記値(1)および値(2)が下記(3)式を満足し、残部Feおよび不可避的不純物からなる組成を有し、758MPa以上の降伏応力を有する油井管用マルテンサイト系ステンレス継目無鋼管。
記
-109.37C+7.307Mn+6.399Cr+6.329Cu+11.343Ni-13.529Mo+1.276W+2.925Nb
+196.775N-2.621Ti-120.307 ・・・(1)
-1.324C+0.0533Mn+0.0268Cr+0.0893Cu+0.00526Ni+0.0222Mo-0.0132W-0.473N-0.5Ti-0.514 ・・・(2)
ここで、C、Mn、Cr、Cu、Ni、Mo、W、Nb、N、Ti:各元素の含有量(質量%)(但し、含有しない元素は0(零)%とする。)
-35.0≦値(1)≦45 且つ -0.40≦値(2)≦0.070 ・・・(3) - 前記組成に加えてさらに、質量%で
Nb:0.25%以下、
W:1.1%以下
のうちから選ばれた1種または2種を含有する組成とする請求項1に記載の油井管用マルテンサイト系ステンレス継目無鋼管。 - 前記組成に加えてさらに、質量%で、
Ca:0.010%以下、
REM:0.010%以下、
Mg:0.010%以下、
B:0.010%以下
のうちから選ばれた1種または2種以上を含有する組成とする請求項1または2に記載の油井管用マルテンサイト系ステンレス継目無鋼管。 - 請求項1~3のいずれかに記載の組成を有する鋼管素材を造管し鋼管としたのち、該鋼管をAc3変態点以上に加熱し、続いて100℃以下の冷却停止温度まで冷却する焼入れ処理と、ついでAc1変態点以下の温度で焼き戻しをする焼戻処理とを施す油井管用マルテンサイト系ステンレス継目無鋼管の製造方法。
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2018
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- 2018-09-04 JP JP2018564433A patent/JP6540922B1/ja active Active
- 2018-09-04 US US16/646,354 patent/US11401570B2/en active Active
- 2018-09-04 MX MX2020002864A patent/MX2020002864A/es unknown
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Also Published As
Publication number | Publication date |
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EP3690072A1 (en) | 2020-08-05 |
MX2020002864A (es) | 2020-07-24 |
JPWO2019065116A1 (ja) | 2019-11-14 |
US11401570B2 (en) | 2022-08-02 |
EP3690072A4 (en) | 2020-08-05 |
US20200270715A1 (en) | 2020-08-27 |
JP6540922B1 (ja) | 2019-07-10 |
AR113184A1 (es) | 2020-02-05 |
BR112020004809A2 (pt) | 2020-09-24 |
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