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EP1995341A1 - Conduite de puits de pétrole pour dilatation dans un puits et acier inoxydable à deux phases destiné à être utilisé en tant que conduite de puits de pétrole pour dilatation - Google Patents

Conduite de puits de pétrole pour dilatation dans un puits et acier inoxydable à deux phases destiné à être utilisé en tant que conduite de puits de pétrole pour dilatation Download PDF

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Publication number
EP1995341A1
EP1995341A1 EP08722143A EP08722143A EP1995341A1 EP 1995341 A1 EP1995341 A1 EP 1995341A1 EP 08722143 A EP08722143 A EP 08722143A EP 08722143 A EP08722143 A EP 08722143A EP 1995341 A1 EP1995341 A1 EP 1995341A1
Authority
EP
European Patent Office
Prior art keywords
stainless steel
expansion
country tubular
oil country
duplex stainless
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Withdrawn
Application number
EP08722143A
Other languages
German (de)
English (en)
Other versions
EP1995341A4 (fr
Inventor
Hideki Takabe
Masakatsu Ueda
Kunio Kondo
Taro Ohe
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Nippon Steel Corp
Original Assignee
Sumitomo Metal Industries Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Sumitomo Metal Industries Ltd filed Critical Sumitomo Metal Industries Ltd
Publication of EP1995341A1 publication Critical patent/EP1995341A1/fr
Publication of EP1995341A4 publication Critical patent/EP1995341A4/fr
Withdrawn legal-status Critical Current

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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
    • C22C38/004—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
    • C22C38/001—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
    • C22C38/18—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
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—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

Definitions

  • the present invention relates to an oil country tubular good and duplex stainless steel, and more specifically, to an oil country tubular good to be expanded in a well and duplex stainless steel to be used for such an oil country tubular good for expansion.
  • a conventional method of constructing a well is as follows. To start with, when a well is drilled for a prescribed distance, a first casing is inserted. Then, when the well is further drilled for a prescribed distance, a second casing having an outer diameter smaller than the inner diameter of the first casing is inserted. In this way, according to the conventional construction method, the outer diameters of casings to be inserted are sequentially reduced as the well is drilled deeper. Therefore, as the oil well is deeper, the inner diameters of casings used in the upper part of the well (near the surface of the ground) increase. As a result, the drilling area increases, which pushes up the drilling cost.
  • a new technique for reducing the drilling area and thus reducing the drilling cost is disclosed by JP 7-567610 A and the pamphlet of International Publication WO 98/00626 .
  • the technique disclosed by these documents is as follows.
  • a casing C3 having a smaller outer diameter than the inner diameter ID1 of casings C1 and C2 already provided in a well is inserted into the well.
  • the inserted casing C3 is expanded, so that its inner diameter is equal to the inner diameter ID1 of the previously provided casings C1 and C2 as shown in Fig. 1 .
  • the casing is expanded inside the well and therefore it is not necessary to increase the drilling area if the oil well to construct is deep. Therefore, the drilling area can be reduced.
  • the number of necessary steel pipes can be reduced because large size casings are not necessary.
  • pipe expansion characteristic a uniformly deforming characteristic when expanded (hereinafter referred to as "pipe expansion characteristic.")
  • the deforming characteristic without local constriction during working is required, in other words, uniform elongation that can be evaluated by tensile testing must be high.
  • the pipe expansion ratio is maximized.
  • the uniform elongation of the oil country tubular good for expansion is preferably more than 20%.
  • JP 2005-146414 A discloses a seamless oil country tubular good for expansion.
  • the structure of the disclosed oil country tubular good includes a ferrite transformation phase and low temperature transformation phases (such as bainite, martensite, and bainitic ferrite), and has a high pipe expansion characteristic.
  • the uniform elongation of each test piece in the disclosed embodiment is not more than 20% (see JP 2005-146414 A , u-E1 in Tables 2-1 and 2-2). Therefore, the bell part described above may not deform uniformly.
  • the inventors examined the uniform elongation of various types of steel. As a result, the inventors have found that duplex stainless steel having prescribed chemical components has a uniform elongation significantly higher than those of carbon steel and martensitic stainless steel.
  • the inventors have further studied and found that in order to produce an oil country tubular good having a uniform elongation more than 20%, the following requirements must be fulfilled.
  • An oil country tubular good for expansion according to the invention is expanded in a well.
  • the oil country tubular good for expansion according to the invention is formed of duplex stainless steel having a composition containing, in percentage by mass, 0.005% to 0.03% C, 0.1% to 1.0% Si, 0.2% to 2.0% Mn, at most 0.04% P, at most 0.015% S, 18.0% to 27.0% Cr, 4.0% to 9.0% Ni, at most 0.040% Al, and 0.05% to 0.40% N, and the balance consisting of Fe and impurities, and a structure including an austenite ratio in the range from 40% to 90%.
  • the oil country tubular good has a yield strength from 256 MPa to 655 MPa, and a uniform elongation more than 20%.
  • the "uniform elongation" means the distortion (%) at the maximum load point in a tensile test.
  • the austenite ratio is an austenite area ratio.
  • the duplex stainless steel may further contain at most 2.0% Cu.
  • the duplex stainless steel may further contain one or more selected from the group consisting of at most 4.0% Mo and at most 5.0% W.
  • the duplex stainless steel may further contain one or more selected from the group consisting of at most 0.8% Ti, at most 1.5% V, and at most 1.5% Nb.
  • the duplex stainless steel may further contain one or more selected from the group consisting of at most 0.02% B, at most 0.02% Ca and at most 0.02% Mg.
  • duplex stainless steel according to the invention is used for the above-described oil country tubular good for expansion.
  • An oil country tubular good according to an embodiment of the invention is formed of duplex stainless steel having the following chemical composition and metal structure.
  • % related to elements means “% by mass.”
  • the C content is not less than 0.005%. Meanwhile, if the C content exceeds 0.03%, carbide is more easily precipitated, which lowers the grain boundary corrosion resistance. Therefore, the C content is from 0.005% to 0.03%.
  • the Si content is not less than 0.1%. Meanwhile, if the Si content exceeds 1.0%, intermetallic compounds are acceleratingly generated, which lowers the hot workability. Therefore, the Si content is from 0.1% to 1.0%.
  • Phosphorus is an impurity that promotes central segregation and degrades the sulfide stress cracking resistance. Therefore, the P content is preferably as small as possible. Therefore, the P content is not more than 0.04%.
  • the S content is preferably as small as possible.
  • the S content is therefore not more than 0.015%.
  • Chromium improves the carbon dioxide corrosion resistance.
  • the Cr content is not less than 18.0%. Meanwhile, if the Cr content exceeds 27.0%, intermetallic compounds are acceleratingly generated, which lowers the hot workability. Therefore, the Cr content is from 18.0% to 27.0%, preferably from 20.0% to 26.0%.
  • Aluminum is effective as a deoxidizing agent. However, if the Al content exceeds 0.040%, inclusions in the steel increase, which degrades the toughness and the corrosion resistance. Therefore, the Al content is not more than 0.040%.
  • the N content is not less than 0.05%. Meanwhile, if the N content exceeds 0.40%, a defect attributable to a generated blow hole is caused. The toughness and corrosion resistance of the steel are degraded as well. Therefore, the N content is from 0.05% to 0.40%, preferably from 0.1% to 0.35%.
  • the balance of the duplex stainless steel according to the invention consists of Fe and impurities.
  • duplex stainless steel for an oil country tubular good for expansion according to the embodiment further contains Cu in place of part of Fe if necessary.
  • the Cu content is not more than 2.0%. Note that in order to effectively secure the above-described effect, the Cu content is preferably not less than 0.2%. However, if the Cu content is less than 0.2%, the above-described effect can be obtained to some extent.
  • duplex stainless steel for an oil country tubular good for expansion according to the embodiment further contains one or more selected from the group consisting of Mo and W in place of part of Fe if necessary.
  • Molybdenum and tungsten are optional elements. These elements improve the pitting corrosion resistance and the deposit corrosion resistance. However, an excessive Mo content and/or an excessive W content causes a ⁇ phase to be more easily precipitated, which embrittles the steel. Therefore, the Mo content is not more than 4.0% and the W content is not more than 5.0%. In order to effectively secure the above described effect, the Mo content is preferably not less than 2.0% and the W content is preferably not less than 0.1%. However, if the Mo content and the W content are less than the described lower limits, the above-described effect can be obtained to some extent.
  • duplex stainless steel for an oil country tubular good for expansion according to the embodiment further contains one or more selected from the group consisting of Ti, V, and Nb in place of part of Fe if necessary.
  • Titanium, vanadium, and niobium are optional elements. These elements improve the strength of the steel. However, if the contents of these elements are excessive, the hot workability is lowered. Therefore, the Ti content is 0.8% or less, the V content is 1.5% or less, and the Nb content is 1.5% or less. In order to more effectively secure the above-described effect, the Ti content is preferably not less than 0.1%, and the V content is preferably not less than 0.05%. The Nb content is preferably not less than 0.05%. However, if the Ti, V, and Nb contents are less than the above-described lower limits, the above effect can be obtained to some extent.
  • the duplex stainless steel for an oil country tubular good according to the embodiment further contains one or more selected from the group consisting of B, Ca, and Mg in place of part of Fe.
  • B content, the Ca content, and the Mg content are each not more than 0.02%.
  • the B content, the Ca content, and the Mg content are each preferably not less than 0.0002%.
  • the above-described effect can be obtained to some extent.
  • the duplex stainless steel that forms an oil country tubular good for expansion according to the invention has a metal structure including a ferrite phase and an austenite phase. It is considered that the austenite phase as a soft phase contributes to improvement of the uniform elongation.
  • the austenite ratio in the steel is from 40% to 90%.
  • the austenite ratio is an area ratio measured by the following method. A sample is taken from an arbitrary position of an oil country tubular good for expansion and mechanically polished, and then the polished sample is subjected to electrolytic etching in a 30 mol% KOH solution. The etched surface of the sample is observed using a 400X optical microscope with a 25 grating ocular lens, and the austenite ratio is measured by the point count method according to ASTM E562.
  • the austenite ratio is less than 40%, the uniform elongation is reduced to 20% or less. Meanwhile, if the austenite ratio exceeds 90%, the corrosion resistance of the steel is degraded. Therefore, the austenite ratio is from 40% to 90%.
  • the austenite ratio is preferably from 40% to 70%, more preferably from 45% to 65%.
  • the oil country tubular good for expansion according to the invention is produced by the following method.
  • Molten steel having the above-described composition is cast and then formed into billets.
  • the produced billet is subjected to hot working and made into an oil country tubular good for expansion.
  • the hot working for example, the Mannesmann method is carried out.
  • hot extrusion may be carried out, or hot forging may be carried out.
  • the produced oil country tubular good for expansion may be a seamless pipe or a welded pipe.
  • the oil country tubular good for expansion after the hot working is subjected to solution treatment.
  • the solution treatment temperature at the time is from 1000°C to 1200°C. If the solution treatment temperature is less than 1000°C, a ⁇ phase is precipitated, which embrittles the steel. The yield strength is raised and exceeds 655 MPa because of the precipitation of the ⁇ phase, and therefore the uniform elongation is 20% or less. On the other hand, if the solution treatment temperature exceeds 1200°C, the austenite ratio is significantly lowered and becomes less than 40%.
  • the solution treatment temperature is preferably from 1000°C to 1175°C, more preferably from 1000°C to 1150°C.
  • the oil country tubular good for expansion according to the invention is in an as-solution-treated state (so-called as-solution-treated material). More specifically, the tubular good is used as a product right after the solution treatment without being subjected to other heat treatment and cold working (such as cold reduction or pilger rolling) except for cold straightening.
  • the yield strength may be in the range from 276 MPa to 655 MPa (40 ksi to 95 ksi). It is considered that in this way, the uniform elongation exceeds 20% and a high expansion characteristic is obtained even in a well. Note that if the yield strength exceeds 655 MPa, the uniform elongation is 20% or less.
  • the oil country tubular good for expansion needs strength in a certain level, and the yield strength is 276 MPa or more.
  • the yield strength exceeds 655 MPa. Therefore, the uniform elongation is less than 20%.
  • a plurality of steel products having the chemical compositions in Table 1 were cast and formed into billets.
  • the produced billets were subjected to hot forging and hot rolling and a plurality of steel plates for testing having a thickness of 30 mm, a width of 120 mm, and a length of 300 mm were formed.
  • Steel plates with test Nos. 1 to 23 were subjected to heat treatment as described in the "heat treatment” column and cold working in Table 1. More specifically, the steel plates with test Nos. 1 to 11 were subjected to solution treatment in the temperature range from 1050°C to 1150°C ("ST" in the "heat treatment” column in Table 1). The solution treatment temperature for each of the steel plates is shown in the "ST temperature” in Table 1. The steel plates with test Nos. 1 to 11 were each a so-called as-solution-treated material without being subjected to other heat treatment or cold working such as cold reduction after the solution treatment.
  • the steel plates with test Nos. 12 to 20 were quenched at 920°C and then tempered in the temperature range from 550°C to 730°C ("QT" in the "heat treatment” column in Table 1).
  • the steel plate with test No. 21 was subjected to solution treatment at a temperature less than 1000°C
  • the steel plate with test No. 22 was subjected to solution treatment at a temperature higher than 1200°C.
  • the steel plates with test Nos. 21 and 22 are as-solution-treated materials.
  • the steel plate with test No. 23 was subjected to solution treatment at 1085°C followed by cold drawing.
  • the austenite ratio was obtained after the heat treatment. More specifically, a test piece was taken from each of these steel plates. The sampled test pieces were mechanically polished and the polished test pieces were subjected to electrolytic etching in a 30 mol% KOH solution. The etched surfaces of the samples were observed using a 400X optical microscope with 25 grating ocular lens in 16 fields. The austenite ratio (%) was obtained for each of the observed fields. The austenite ratios were obtained by the point count method according to ASTM E562. The average of the austenite ratios (%) obtained for each of the fields is given in the " ⁇ " column in Table 1.
  • a round bar specimen having an outer diameter of 6.35 mm, and a parallel part length of 25.4 mm was taken from each of the steel plates 1 to 23 in the lengthwise direction and subjected to a tensile test at room temperature.
  • the yield strengths (MPa) obtained by the tensile tests are given in the "YS” column in Table 1
  • the tensile strengths (MPa) are given in the "TS” column in Table 1
  • the uniform elongations (%) are given in the "UE” column in Table 1.
  • the 0.2% proof stress according to the ASTM standard was defined as the yield strength (YS).
  • the distortion of a specimen at the maximum load point was defined as the uniform elongation (%).
  • the steel plates with test Nos. 1 to 11 each had a chemical composition, a metal structure and a yield strength within the ranges defined by the invention, and therefore their uniform elongations all exceeded 20%.
  • the steel plates with test Nos. 12 to 20 were not made of duplex stainless steel and therefore their uniform elongations were not more than 20%.
  • the steel plate with test No. 21 is made of duplex stainless steel and has a chemical composition within the range defined by the invention, but its solution-treatment temperature was less than 1000°C. Therefore, the yield strength exceeded the upper limit by the invention and the uniform elongation was not more than 20%. It was probably because the solution-treatment temperature was low and therefore a ⁇ phase was precipitated, which raised the yield strength.
  • the austenite ratio was less than 40% and the uniform elongation was not more than 20%.
  • the steel plate with test No. 23 was not an as-solution-treated material, but subjected to cold working after the solution-treatment. Therefore, the yield strength exceeded the upper limit of the range defined by the invention and the uniform elongation was not more than 20%.
  • the oil country tubular good for expansion and duplex stainless steel according to the invention are applicable to an oil country tubular good and particularly applicable as an oil country tubular good for expansion in a well.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Articles (AREA)
  • Metal Extraction Processes (AREA)
EP08722143A 2007-03-26 2008-03-14 Conduite de puits de pétrole pour dilatation dans un puits et acier inoxydable à deux phases destiné à être utilisé en tant que conduite de puits de pétrole pour dilatation Withdrawn EP1995341A4 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2007078691 2007-03-26
PCT/JP2008/054747 WO2008117680A1 (fr) 2007-03-26 2008-03-14 Conduite de puits de pétrole pour dilatation dans un puits et acier inoxydable à deux phases destiné à être utilisé en tant que conduite de puits de pétrole pour dilatation

Publications (2)

Publication Number Publication Date
EP1995341A1 true EP1995341A1 (fr) 2008-11-26
EP1995341A4 EP1995341A4 (fr) 2010-03-10

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EP08722143A Withdrawn EP1995341A4 (fr) 2007-03-26 2008-03-14 Conduite de puits de pétrole pour dilatation dans un puits et acier inoxydable à deux phases destiné à être utilisé en tant que conduite de puits de pétrole pour dilatation

Country Status (12)

Country Link
US (1) US20090032246A1 (fr)
EP (1) EP1995341A4 (fr)
JP (1) JPWO2008117680A1 (fr)
CN (1) CN101541997A (fr)
AR (1) AR067233A1 (fr)
AU (1) AU2008207596A1 (fr)
BR (1) BRPI0802616A2 (fr)
CA (1) CA2638289C (fr)
EA (1) EA013146B1 (fr)
MX (1) MX2008012238A (fr)
UA (1) UA90217C2 (fr)
WO (1) WO2008117680A1 (fr)

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CN101935808A (zh) * 2010-09-19 2011-01-05 天津钢管集团股份有限公司 130ksi钢级低温高韧抗腐蚀的钻杆及其制造方法
EP2177634A4 (fr) * 2007-07-20 2016-01-20 Nippon Steel & Sumitomo Metal Corp Procédé de production de tubes en acier inoxydable duplex
US9758850B2 (en) 2012-06-21 2017-09-12 Jfe Steel Corporation High strength stainless steel seamless pipe with excellent corrosion resistance for oil well and method of manufacturing the same
US9803267B2 (en) 2011-05-26 2017-10-31 Upl, L.L.C. Austenitic stainless steel
US10151011B2 (en) 2012-12-21 2018-12-11 Jfe Steel Corporation High-strength stainless steel seamless tube or pipe for oil country tubular goods, and method of manufacturing the same
EP4137590A4 (fr) * 2020-06-02 2023-10-25 JFE Steel Corporation Acier inoxydable duplex et tuyau en acier inoxydable duplex sans soudure

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EP2220261B1 (fr) 2007-11-29 2018-12-26 ATI Properties LLC Acier inoxydable austénitique pauvre
KR101467616B1 (ko) 2007-12-20 2014-12-01 에이티아이 프로퍼티즈, 인코퍼레이티드 내부식성 린 오스테나이트계 스테인리스 강
WO2009082498A1 (fr) 2007-12-20 2009-07-02 Ati Properties, Inc. Acier inoxydable austénitique à faible teneur en nickel contenant des éléments stabilisants
US8337749B2 (en) 2007-12-20 2012-12-25 Ati Properties, Inc. Lean austenitic stainless steel
JP2013129879A (ja) * 2011-12-22 2013-07-04 Jfe Steel Corp 耐硫化物応力割れ性に優れた油井用高強度継目無鋼管およびその製造方法
UA111115C2 (uk) 2012-04-02 2016-03-25 Ейкей Стіл Пропертіс, Інк. Рентабельна феритна нержавіюча сталь
JP6405078B2 (ja) * 2012-05-07 2018-10-17 株式会社神戸製鋼所 二相ステンレス鋼材および二相ステンレス鋼管
CN103266281B (zh) * 2013-05-24 2015-02-04 无锡鑫常钢管有限责任公司 一种超级双相不锈钢管及其生产工艺
FI125466B (en) * 2014-02-03 2015-10-15 Outokumpu Oy DUPLEX STAINLESS STEEL
AR101904A1 (es) * 2014-09-29 2017-01-18 Nippon Steel & Sumitomo Metal Corp Material de acero y tuberías expansibles para la industria del petróleo
CN105478524B (zh) * 2016-01-06 2017-07-28 河北华通线缆集团股份有限公司 一种双相不锈钢连续油管的制造方法
CN111057967A (zh) * 2019-12-31 2020-04-24 九牧厨卫股份有限公司 一种高耐蚀抗刮擦不锈钢板、不锈钢水槽及其制备方法
CN110983191A (zh) * 2019-12-31 2020-04-10 九牧厨卫股份有限公司 一种高耐蚀不锈钢板、不锈钢水槽及其制备方法
US20230220511A1 (en) * 2022-01-11 2023-07-13 Daido Steel Co., Ltd. Additive manufacturing wire, additively-manufactured object, and additive manufacturing method

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CN101935808A (zh) * 2010-09-19 2011-01-05 天津钢管集团股份有限公司 130ksi钢级低温高韧抗腐蚀的钻杆及其制造方法
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JPWO2008117680A1 (ja) 2010-07-15
MX2008012238A (es) 2008-11-28
BRPI0802616A2 (pt) 2011-08-30
WO2008117680A1 (fr) 2008-10-02
EP1995341A4 (fr) 2010-03-10
AR067233A1 (es) 2009-10-07
EA200870307A1 (ru) 2009-02-27
CN101541997A (zh) 2009-09-23
CA2638289A1 (fr) 2008-09-26
EA013146B1 (ru) 2010-02-26
CA2638289C (fr) 2011-08-30
AU2008207596A1 (en) 2008-10-16
UA90217C2 (ru) 2010-04-12

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