WO2004001082A1 - 油井用ステンレス鋼管およびその製造方法 - Google Patents
油井用ステンレス鋼管およびその製造方法 Download PDFInfo
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- WO2004001082A1 WO2004001082A1 PCT/JP2003/007709 JP0307709W WO2004001082A1 WO 2004001082 A1 WO2004001082 A1 WO 2004001082A1 JP 0307709 W JP0307709 W JP 0307709W WO 2004001082 A1 WO2004001082 A1 WO 2004001082A1
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Classifications
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C37/00—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
- B21C37/06—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of tubes or metal hoses; Combined procedures for making tubes, e.g. for making multi-wall tubes
- B21C37/08—Making tubes with welded or soldered seams
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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
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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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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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
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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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
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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
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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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
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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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
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
Definitions
- the present invention relates to an oil well steel pipe used for a crude oil or natural gas oil well or gas well.
- carbon dioxide (C0 2) the improvement of corrosion resistance under extreme Umate severe corrosive environments containing chlorine ions (C) or the like.
- An improved martensitic stainless steel (or steel pipe) has been proposed in which the corrosion resistance of Cr martensitic stainless steel (or steel pipe) is improved.
- the technique described in Japanese Patent Application Laid-Open No. 8-120345 is a method for producing a martensite stainless steel seamless steel pipe having excellent corrosion resistance.
- the steel composition of the 13% Cr martensite stainless steel pipe is limited to 0.005 to 0.05% of C, Ni: 2.4 to 6% and Cu: 0.2 to 4%, and Mo is added to 0.5 to 0.5%.
- the technique described in Japanese Patent Application Laid-Open No. 9-268349 is a method for producing a martensitic stainless steel excellent in sulfide stress corrosion cracking resistance.
- the composition is adjusted to 13% Cr martensite containing C: 0.005 to 0.05%, N: 0.005 to 0.1%, Ni: 3.0 to 6.0%, Cu: 0.5 to 3%, Mo: 0.5 to 3%.
- Stainless steel composition is heated to (Ac ⁇ point + 10 ° C) to (Ac ⁇ point + 40 ° C) and held for 30 to 60 minutes.
- the structure After cooling to a temperature below the Ac point, the structure becomes a mixed structure of tempered martensite and r phase of 20% by volume or more. According to this technology, the phase is contained at 20% by volume or more. It is stated that the use of a tempered martensite structure significantly improves sulfide stress corrosion cracking resistance.
- the technique described in Japanese Patent Application Laid-Open No. 10-1755 is a martensitic stainless steel containing 10 to 15% Cr having excellent corrosion resistance and sulfide stress corrosion cracking resistance.
- This martensitic stainless steel has a Cr content of 10 to 15%, a C content of 0.005 to 0.05%, i: 4.0% or more, Cu: 0.5 to 3%, and a Mo content of 1.0 to 3.0%.
- Japanese Patent No. 2814528 relates to a martensitic stainless steel material for oil wells having excellent sulfide stress corrosion cracking resistance.
- This steel material contains more than 15% and less than 19% Cr, C: 0.05% or less, N: 0.1% or less, Ni: 3.5-8.0%, Mo: 0.1-4.0%, and 30Cr + It has a steel composition that simultaneously satisfies 36Mo + 14Si-28Ni ⁇ 455 (%), 21Cr + 25Mo + 17Si + 35 ⁇ 731 (%). It states that the steel will have excellent corrosion resistance even in harsh oil well environments where chloride ions, carbon dioxide gas and trace amounts of hydrogen sulfide gas are present.
- Japanese Patent No. 3251648 relates to a precipitation hardening type martensitic stainless steel excellent in strength and toughness.
- This martensite stainless steel contains 10.0 to 17% Cr, contains C: 0.08% or less, N: 0.015% or less, Ni: 6.0 to 10.0%, and Cu: 0.5 to 2.0%.
- Mo 0.5 and steel composition you containing 3.0%, by annealing the inter least 35% cold work, particle size 5 average crystal grain size were precipitated during bird box below 25 m X 10- 2/2 m having the above precipitates was suppressed to 6 X 10 6 cells Z wicked person 2 or less tissue.
- the present invention has been made in view of such circumstances in the related art.
- the present invention is inexpensive, excellent in hot workability, and C0 2, containing Cr or the like, excellent in corrosion resistance showing the excellent C0 2 corrosion resistance even at severe corrosive environment of a high temperature exceeding 180 ° C
- An object of the present invention is to provide a stainless steel pipe for an oil well, preferably a high-strength stainless steel pipe for an oil well.
- the gist of the present invention is as follows.
- Nb 0.20% or less by mass%
- Ti A stainless steel pipe for oil wells with excellent corrosion resistance, characterized by containing one or two selected from 0.30% or less.
- any one of (1) to (4) it must have a structure consisting of a residual austenite phase of 5 to 25% by volume, a ferrite phase of 5% or less, and a residual martensite phase.
- the quenching treatment is a treatment of heating to a temperature in the range of 800 to 1100, followed by cooling to room temperature at a cooling rate of air cooling or higher, and the tempering treatment is performed at 500 to 630 ° C.
- a method for producing a stainless steel pipe for an oil well characterized by performing a tempering treatment at a temperature within a range.
- the quenching treatment is a treatment of heating to a temperature in the range of 800 to 1100 ° C and subsequently cooling to room temperature at a cooling rate of air cooling or higher.
- high strength refers to a strength equal to or higher than that of a normal 13% Cr martensite stainless steel oil well pipe (yield strength: 550 MPa or more), and preferably a strength having a yield strength of 654 MPa or more. Shall refer to the case.
- the composition of the improved 13% Cr martensitic stainless steel base to Ichisu comprises C0 2, CI ", etc., high temperatures up to 230 beyond 180
- the intense study was carried out on the effect of alloying elements on the corrosion resistance of steel in a corrosive environment.
- C was significantly reduced and Ni, Mo, and Cu were contained in appropriate amounts, and the following equations (1) and (2) were used.
- the present invention has been completed based on the above-mentioned findings and further studies.
- C is an important element related to the strength of martensitic stainless steel, but if it exceeds 0.05%, sensitization during tempering due to the inclusion of Ni increases. In order to prevent sensitization during tempering, C is limited to 0.05% or less in the present invention. Also, from the viewpoint of corrosion resistance, it is preferable that the amount is as small as possible. Incidentally, the content is preferably 0.03% or less. More preferably, it is 0.01 to 0.03%.
- Si is an element which acts as a deoxidizing agent, but is preferably a child containing 0.05% or more in the present invention, the content exceeding 0.50% reduces the resistance to C0 2 corrosion, more hot workability Also reduce. For this reason, Si was limited to 0.50% or less. Preferably, it is 0.10 to 0.30%.
- Mn is an element that increases the strength of steel, and secures the desired strength in the present invention. To be contained, it must be contained at least 0.20%. On the other hand, if the content exceeds 1.80%, the toughness is adversely affected. For this reason, Mn was limited to the range of 0.20 to 1.80%. In addition, it is preferably 0 ⁇ 20 to 1.00%. More preferably, it is 0.20 to 0.80%.
- P is resistant C0 2 corrosion resistance, co 2 stress corrosion cracking resistance, an element which both deteriorate the pitting corrosion resistance and sulfide stress corrosion cracking resistance, it is desirable to reduce as much as possible in the present invention
- extreme reduction leads to increased manufacturing costs.
- S is an element that significantly degrades hot workability in the pipe manufacturing process, and is desirably as small as possible. If it is reduced to 0.005% or less, it becomes possible to manufacture pipes by the normal process.
- the content is preferably 0.003% or less.
- Cr is a protective coating is an element improving the corrosion resistance is formed on the steel surface, in particular resistance to C0 2 corrosion, an element which contributes to the improvement of resistance to C0 2 stress corrosion cracking resistance.
- the content of 14.0% or more is required from the viewpoint of improving corrosion resistance at high temperatures.
- a content exceeding 18.0% deteriorates hot workability. Therefore, in the present invention, Cr is limited to the range of 14.0 to 18.0%.
- the content is preferably 14.5% to 17.5%.
- Ni has to strengthen the protective coating of steel surfaces, resistance to C0 2 corrosion resistance, C0 2 stress corrosion cracking resistance, the effect of improving the pitting corrosion resistance and sulfide stress corrosion cracking resistance, further, a solid solution strength It is an element that increases the strength of steel by chemical conversion. Such an effect is observed when the content is 5. Q% or more, but when the content exceeds 8.0%, the stability of the martensite structure is reduced and the strength is reduced. Therefore, Ni is limited to the range of 5.0 to 8.0%.
- the content is preferably 5.5 to 7.0%.
- Mo is an element that increases resistance to pitting corrosion by c.
- the content is 1.5 to 2.5%.
- Cu is an element that strengthens the protective coating on the steel surface, suppresses the intrusion of hydrogen into the steel, and enhances sulfide stress corrosion cracking resistance. Such an effect is exhibited when the content is 0.5% or more, but when the content exceeds 3.5%, CuS is precipitated at the grain boundary, and the hot workability is reduced. For this reason, Cu was limited to the range of 0.5 to 3.5%. Incidentally, the content is preferably 0.5 to 2.5%.
- A1 0.05% or less
- A1 is a strong deoxidizing element, but its content exceeding 0.05% adversely affects the toughness of steel. For this reason, A1 was limited to 0.05% or less. Note that the content is preferably 0.01 to 0.03%.
- V 0.20% or less
- V has the effect of increasing the strength of steel and improving stress corrosion cracking resistance. Such effects become remarkable when the content is 0.03% or more, but when the content exceeds 0.20%, the paddy properties deteriorate. For this reason, V is limited to 0.20% or less. In addition, Or 0.03 to 0.08%.
- ⁇ is an element that significantly improves pitting resistance. Such an effect is recognized at a content of 0.01% or more, but a content of more than 0.15% forms various nitrides and deteriorates toughness. Therefore, ⁇ was limited to 0.01 to 0.15%. Preferably, it is 0.03 to 0.15%, more preferably 0.03 to 0.08%.
- ⁇ is present as an oxide in steel and adversely affects various properties, so that ⁇ is preferably reduced as much as possible.
- the ⁇ content is increased beyond 0.006%, the hot workability, resistance to C0 2 stress corrosion cracking resistance, pitting corrosion resistance, significantly reduces the resistance to sulfide stress corrosion cracking Oyo Pi toughness. Therefore, in the present invention, ⁇ is limited to 0.006% or less.
- one or two selected from Nb: 0.20% or less and Ti: 0.30% or less can be further contained in addition to the above basic composition.
- Both Nb and Ti are elements that have the effect of increasing the strength and also improving the toughness, and in particular, significantly increase the strength by tempering at a relatively low temperature range of 500 to 630 ° C. . Such effects become remarkable when Nb: 0.02% or more and Ti: 0.01% or more. On the other hand, if the content exceeds Nb: 0.20% and Ti: 0.30%, respectively, the toughness decreases. Ti also has an effect of improving stress corrosion cracking resistance. For this reason, it is preferable to limit the content to Nb: 0.20% or less and Ti: 0.30% or less.
- one or more selected from among Zr: 0.20% or less, B: 0.01% or less, W: 3.0% or less can be contained in addition to the above-mentioned respective compositions. .
- Zr, B, and W all have the effect of increasing the strength, and one or more of them can be selected and contained as needed. Also, Zr, B, and W add to the increase in strength. In addition, it has the effect of improving the stress corrosion cracking resistance. Such effects are remarkable when Zr: 0.01% or more, B: 0.0005% or more, and W: 0.1% or more. On the other hand, if the content of Zr exceeds 0.20%, the content of B exceeds 0.01%, and the content of W exceeds 3.0%, the toughness deteriorates. For this reason, it is preferable to limit to Zr: 0.20% or less, B: 0.01% or less, and W: 3.0% or less.
- Ca: 0.0005 to 0.01% can be further contained in addition to the above-described compositions.
- Ca has the effect of fixing S as CaS and spheroidizing sulfide inclusions, thereby reducing the lattice distortion of the matrix around the inclusions and reducing the hydrogen trapping ability of the inclusions. Having. Such effect is that pronounced and Do at content of not less than 0.0005%, the content exceeding 0.01% causes an increase in CaO, resistance C0 2 corrosion, pitting corrosion resistance is low under. For this reason, Ca is preferably limited to the range of 0.0005 to 0.01%. In addition to satisfying the range of each component described above, in the present invention, it is necessary to further satisfy the following expressions (1) and (2).
- the balance other than the above components is Fe and inevitable impurities.
- the steel pipe of the present invention preferably has a structure composed of 5 to 25% by volume of a residual austenite phase and a residual martensite phase.
- the steel pipe of the present invention has a structure composed of 5 to 25% by volume of a residual austenite phase, 5% or less of a ferrite phase, and a balance of a martensite phase.
- the structure of the steel pipe according to the present invention is basically a structure mainly composed of a martensite phase.However, in the martensite phase, a residual austenite phase having a volume fraction of 5 to 25%, or a volume fraction of 5% to 25%. It is preferable to contain 5% or less of a ferrite phase.
- High toughness can be obtained by containing 5% by volume or more of the residual magnesium oxide phase.
- the content of the residual austenite phase exceeds 25% by volume, the strength is reduced.
- the residual austenite phase is preferably set to 5 to 25% by volume.
- molten steel having the above composition is smelted by a commonly known smelting method such as a converter, an electric furnace, a vacuum melting furnace, etc. It is preferable to use a steel pipe material such as Next, these steel pipe materials are heated, hot-worked and formed using a normal Mannesmann-Plug Mill or Mannesmann-Mandrel Mill manufacturing process to form seamless steel pipes of desired dimensions. It is preferable that the seamless steel pipe after pipe formation is cooled to room temperature at a cooling rate higher than air cooling. In the case of a seamless steel pipe having a steel composition within the scope of the present invention described above, the hot-working process is followed by cooling to room temperature at a cooling rate equal to or higher than air cooling, so that the martensite phase is mainly formed.
- the quenched seamless steel pipe is then preferably heated to a temperature below the transformation point and tempered.
- a temperature below the transformation point preferably above 400 ° C
- the structure becomes a structure consisting of a tempered martensite phase, or further a retained austenite phase, and in some cases, a smaller amount of a ferrite phase.
- a seamless steel pipe having desired high strength, desired toughness, and desired excellent corrosion resistance can be obtained.
- an electric steel pipe and a UOE steel pipe can be manufactured in accordance with a normal process to obtain a steel pipe for an oil well.
- electric resistance welded steel pipe, the U_ ⁇ E steel, the steel pipe after pipe a quenching treatment to cool to room temperature in air or a cooling rate after reheating the A c 3 transformation point or above the temperature, at Ide A c It is preferable to perform a tempering process of tempering at a temperature below the transformation point.
- the quenching treatment is performed by heating to a temperature in the range of 800 to 1100 ° C, followed by air cooling.
- the cooling is performed to the room temperature at the above cooling rate.
- the tempering is preferably performed at a temperature in the range of 500 to 630 ° C.
- the heating temperature in the quenching process is less than 800 ° C, the quenching effect is small and Difficult to get. On the other hand, if it exceeds 1100 ° C, the crystal grains become coarse and the toughness of the steel decreases. If the tempering temperature is less than 500, a sufficient amount of precipitates will not be deposited, while if it exceeds 630 ° C, the strength of the steel will be significantly reduced.
- the resulting seamless steel pipe was visually inspected for cracks on the inner and outer surfaces while being air-cooled after pipe making, and hot workability was evaluated.
- a test piece material was cut out from the obtained seamless steel pipe, heated at 920 ° C for lh, and then cooled with water. Further, tempering treatment was performed at 600 ° C for 30 minutes. It has been confirmed that the employed quenching temperature is above the Ac 3 transformation point in all steels, and the adopted tempering temperature is below the ACl transformation point. From the test piece material thus quenched and tempered, a corrosion test piece of 3 mm thick x 30 mm wide x 40 mm long was prepared by machining, and a corrosion test was performed. For some steel pipes, quenching was not performed and only tempering was performed.
- the weight of the test piece after the corrosion test was measured, and the corrosion rate calculated from the weight loss before and after the corrosion test was obtained.
- the corrosion test specimens after the test were examined for the occurrence of pitting corrosion on the test specimen surface using a rule with a magnification of 10 times.
- Table 2 shows the obtained results.
- Equation (2) (Cr) + (Mo) +0.3 (Si) -43.5 (C) -0.4 (n) (Ni) -0.3 (Cu) — 9 (N)
- test piece material was cut out from the obtained seamless steel pipe, and quenched and tempered under the conditions shown in Table 4.
- An API arc-shaped tensile test specimen was sampled from the quenched and tempered specimen material and subjected to a tensile test to determine the tensile properties (yield strength YS, tensile strength TS).
- a corrosion test specimen of thickness 3 mm x width 30 nim x length 40 mm was sampled from the quenched and tempered test specimen material by machining, and the corrosion test was performed.
- test liquid retained in: 20% NaC l aqueous solution: during (liquid temperature 230 ° C, of 30 atm C0 2 gas atmosphere), it was immersed corrosion test pieces were conducted between immersion ⁇ as two weeks.
- the weight of the test piece after the corrosion test was measured, and the corrosion rate calculated from the weight loss before and after the corrosion test was obtained.
- the corrosion test specimens after the test were examined for the occurrence of pitting corrosion on the test specimen surface using a loupe with a magnification of 10 times.
- Equation (1) (Cr) +0.65 (Ni) +0.6 (o) +0.55 (Cu)-20 (C)
- Equation (2) (Cr) + (Mo) +0.3 (Si) -43.5 (C) -0.4 (n) one (Mi) -0.3 (Cu) -9 (N)
- Cooling F & Cooling Y S T S Cracking Corrosion rate Pitting corrosion
- a test specimen material was cut out from the obtained seamless steel pipe, and quenched and tempered under the conditions shown in Table 6. It has been confirmed that the employed quenching temperatures are all above the Ac 3 transformation point, and the employed tempering temperatures are all below the ACl transformation point. From the quenched and tempered test specimen material, a test specimen for tissue observation is taken, and the test specimen for tissue observation is corroded with aqua regia and the tissue is imaged with a scanning electron microscope (1000x). The tissue fraction (volume%) of the ferrite phase was calculated using an image analyzer. The structural fraction of the residual austenite phase was measured using X-ray diffraction.
- Example 2 In the same manner as in Example 1, an API arc-shaped tensile test specimen was sampled from the quenched and tempered specimen material and subjected to a tensile test to determine the tensile properties (yield strength YS, tensile strength TS ). In addition, a V-notch test specimen (thickness: 5 mm) was sampled from the quenched and tempered test specimen material in accordance with the provisions of JISZ 2202, and in accordance with the provisions of ISZ 2242. A Charpy impact test was performed and the absorbed energy at 40 ° C VE- 4 . ( J).
- a corrosion test specimen with a thickness of 3 mm x a width of 30 dragons and a length of 40 strokes was sampled from the quenched and tempered test specimen material by machining, and a corrosion test was performed in the same manner as in Example 2. Carried out.
- the weight of the test piece after the corrosion test was measured, and the corrosion rate calculated from the weight loss before and after the corrosion test was obtained. Further, the corrosion test specimen after the test was observed for occurrence of pitting corrosion on the test specimen surface by using a loupe with a magnification of 10 times.
- the corrosion resistance that put by 5 to 25 body product% residual Osutenai preparative phase or even 5% or less by volume of tissue containing a ferrite phase, the harsh corrosive environment at a high temperature of 230 ° C comprises C0 2 Excellent.
- it has high strength with a yield strength of 654 MPa or more and high toughness with an absorbed energy of 60 J or more at 40 ° C.
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Priority Applications (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP03733478A EP1514950B1 (en) | 2002-06-19 | 2003-06-18 | Stainless-steel pipe for oil well and process for producing the same |
US10/488,980 US20040238079A1 (en) | 2002-06-19 | 2003-06-18 | Stainless-steel pipe for oil well and process for producing the same |
JP2004530921A JP4363327B2 (ja) | 2002-06-19 | 2003-06-18 | 油井用ステンレス鋼管およびその製造方法 |
US12/416,996 US7842141B2 (en) | 2002-06-19 | 2009-04-02 | Stainless-steel pipe for oil well and process for producing the same |
Applications Claiming Priority (6)
Application Number | Priority Date | Filing Date | Title |
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JP2002-178974 | 2002-06-19 | ||
JP2002178974 | 2002-06-19 | ||
JP2003-114775 | 2003-04-18 | ||
JP2003114775 | 2003-04-18 | ||
JP2003156234 | 2003-06-02 | ||
JP2003-156234 | 2003-06-02 |
Related Child Applications (2)
Application Number | Title | Priority Date | Filing Date |
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US10488980 A-371-Of-International | 2003-06-18 | ||
US12/416,996 Continuation US7842141B2 (en) | 2002-06-19 | 2009-04-02 | Stainless-steel pipe for oil well and process for producing the same |
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WO2004001082A1 true WO2004001082A1 (ja) | 2003-12-31 |
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PCT/JP2003/007709 WO2004001082A1 (ja) | 2002-06-19 | 2003-06-18 | 油井用ステンレス鋼管およびその製造方法 |
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Country | Link |
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US (2) | US20040238079A1 (ja) |
EP (1) | EP1514950B1 (ja) |
JP (1) | JP4363327B2 (ja) |
WO (1) | WO2004001082A1 (ja) |
Cited By (16)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2006307287A (ja) * | 2005-04-28 | 2006-11-09 | Jfe Steel Kk | 拡管性に優れる油井用ステンレス鋼管 |
WO2006117926A1 (ja) * | 2005-04-28 | 2006-11-09 | Jfe Steel Corporation | 拡管性に優れる油井管用ステンレス鋼管 |
JP2007169776A (ja) * | 2005-11-28 | 2007-07-05 | Jfe Steel Kk | 拡管性に優れた油井管用ステンレス鋼管およびその製造方法 |
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JP2006307287A (ja) * | 2005-04-28 | 2006-11-09 | Jfe Steel Kk | 拡管性に優れる油井用ステンレス鋼管 |
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Also Published As
Publication number | Publication date |
---|---|
EP1514950B1 (en) | 2011-09-28 |
JP4363327B2 (ja) | 2009-11-11 |
JPWO2004001082A1 (ja) | 2005-10-20 |
US7842141B2 (en) | 2010-11-30 |
EP1514950A4 (en) | 2005-07-20 |
US20090272469A1 (en) | 2009-11-05 |
EP1514950A1 (en) | 2005-03-16 |
US20040238079A1 (en) | 2004-12-02 |
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