WO2006035735A1 - マルテンサイト系ステンレス鋼管の製造方法 - Google Patents
マルテンサイト系ステンレス鋼管の製造方法 Download PDFInfo
- Publication number
- WO2006035735A1 WO2006035735A1 PCT/JP2005/017675 JP2005017675W WO2006035735A1 WO 2006035735 A1 WO2006035735 A1 WO 2006035735A1 JP 2005017675 W JP2005017675 W JP 2005017675W WO 2006035735 A1 WO2006035735 A1 WO 2006035735A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- less
- steel pipe
- stainless steel
- producing
- strength
- Prior art date
Links
Classifications
-
- 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
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/002—Heat treatment of ferrous alloys containing Cr
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
-
- 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
- C22C38/001—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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
-
- 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
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
-
- 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 a method for manufacturing a martensitic stainless steel pipe, and more particularly to a method for manufacturing a martensitic seamless stainless steel pipe having a high yield ratio.
- 13Cr steel containing about 0.2% C and about 13% Cr (hereinafter referred to simply as "13Cr steel”) Is highly resistant to infiltration carbon dioxide and has a low C content! /, And is cheaper than Super 13Cr steel and duplex stainless steel, so it is often used as an oil well pipe.
- This seamless steel pipe of 13Cr steel is made into a product by quenching and annealing after it is made from billet by hot working.
- Patent Document 1 discloses a method for improving toughness by a direct quenching method (DQT) in which 13Cr steel is made into a blank by hot working and then quenched. This method is superior in terms of productivity and cost because it does not reheat and quench the cooled tube.
- DQT direct quenching method
- Patent Document 1 Japanese Patent Laid-Open No. 2-277720
- Patent Document 1 focuses only on toughness as a mechanical property, and does not describe any corrosion resistance. Therefore, this method of controlling only toughness has recently been required! Satisfies the hardness (HRC) of 22 or less of the American Petroleum Institute (API) standard 13CrL80 grade, which is an indicator of high strength, high yield ratio and high corrosion resistance. It is difficult to manufacture 13Cr steel pipe.
- HRC hardness
- API American Petroleum Institute
- an object of the present invention is to provide an inexpensive and high-productivity manufacturing method of a corrosion-resistant martensitic seamless steel pipe having a high strength and a high yield ratio.
- the yield strength (YP) is 552 to 656 MPa
- the tensile strength (TS) is 657 MPa or more
- the yield ratio is 75% or more
- the toughness is 0 ° C at the fracture surface transition temperature in the Charpy impact test.
- TS tensile strength
- HRC hardness is 22 or less. It is to provide a manufacturing method of martensitic seamless stainless steel pipe.
- the inventors who can solve this problem can produce a 13Cr steel pipe having high strength and high yield ratio and high corrosion resistance at low cost and high productivity. Based on the prediction, various conditions in the direct quenching method were examined.
- FIG. 1 is a graph showing the results of Examples.
- the present invention defines the chemical composition and heat treatment conditions of the steel as described above. Explain why. In this specification, “%” indicating the chemical composition of steel is “% by mass” unless otherwise specified.
- the range of C needs to be limited in order to obtain an appropriate strength / yield ratio / hardness. If it is less than 0.15%, the predetermined strength is not obtained. On the other hand, if it exceeds 0.21%, the strength becomes too high and it becomes difficult to adjust the yield ratio and hardness. Therefore, it is set to 0.15 to 0.21%.
- Si is added as a steel deoxidizer. To obtain the effect, add 0.16% or more. However, the upper limit is 1.0% to prevent toughness deterioration. Preferably it is 0.16 to 0.50%.
- Mn like Si
- the upper limit is made 1.0% or less.
- Cr is a basic component for obtaining necessary corrosion resistance. 10. Add 5% or more to improve corrosion resistance against pitting corrosion and crevice corrosion, and to reduce CO
- the content should be 0.020% or less.
- A1 amount is set to 0.025-0.
- the hot finishing temperature is 850 ° C or higher
- the lower limit of A1 can be lowered to 0.005%. This is because if the finishing temperature of the final rolling is high, the yield ratio increases because the influence of rolling hardly remains in the material after rolling. Also in this case, the preferable lower limit is 0.025%.
- the preferred upper limit is 0.050% in any embodiment.
- the steel of the present invention comprises Fe and impurities other than the above.
- the amount of N as an impurity is not particularly limited, but if the amount of N exceeds 0.100%, the toughness decreases, so it is preferable to set it to 0.100% or less. Further, it may contain 0.15% or less of Ni and 0.08% or less of Ti as impurities.
- At least one of the following elements may be contained instead of a part of Fe.
- Mo may or may not be added. When added, it has the effect of increasing strength and improving corrosion resistance. For that purpose, it is preferable to add 0.02% or more. However, if the Mo content exceeds 2.0%, the martensitic transformation becomes difficult, so the upper limit is made 2.0%.
- V 0.50% or less
- Nb 0.50% or less
- Nb may not be added. If added, the strength is increased. For that purpose, it is preferable to add 0.002% or more. However, if the Nb content exceeds 0.50%, the toughness is lowered, so the upper limit is made 0.50%.
- the chemical composition of the steel is limited as described above, and at the same time, the finishing temperature of the final hot rolling is set within a predetermined range. Since the hot working at this time is hot rolling in a normal pipe making method, the hot working will be described below by taking hot rolling as an example.
- the finishing temperature of the final rolling is less than 800 ° C, the effect of hot working remains on the steel, and the yield ratio and toughness deteriorate.
- the finishing temperature of the final rolling is over 960 ° C, the crystal grains become coarse, and in this case as well, the toughness and corrosion resistance deteriorate. Therefore, the final rolling finishing temperature should be 800 ° C or higher and 960 ° C or lower.
- the finishing temperature of the final hot rolling process is limited to 850 ° C or more and 960 ° C or less, the required strength * toughness and corrosion resistance are ensured even if the amount of A1 is less than the above range. be able to. Specifically, the strength 'toughness' and corrosion resistance can be ensured when A1 is in the range of 0.005 to 0.05%.
- the hot rolling referred to in the present invention is, for example, as follows.
- the molten steel is adjusted to have a predetermined component, and then a billet is produced by a conventional method such as continuous forging.
- a steel pipe having a predetermined outer diameter and inner thickness that is, a raw pipe, is manufactured by heating it to 1200 ° C or higher and then piercing with a piercer or the like and then hot rolling with a mandrel mill 'reducer or the like.
- the hot rolling may be performed by a plug mill or the like.
- the manufacturing conditions such as hot rolling are adjusted so that the temperature force of the raw material at the end of hot rolling falls within a predetermined range.
- the raw tube is cooled. Usually, it should be cooled to room temperature by air cooling!
- the martensite structure is obtained even when air-cooled.
- tempering is performed so as to obtain predetermined mechanical characteristics. For example, heat up to 700-750 ° C and cool.
- the cooling rate in this case is not particularly limited, and it is usually sufficient to cool at a cooling rate higher than air cooling, for example, 2 ° CZsec or higher.
- the product thus obtained is further subjected to inspection, threading and the like to obtain a product.
- the dimensions of the raw tube are not limited, but an outer diameter of 88. lmm and a wall thickness of 6.95 mm are exemplified.
- the operation and effect of the present invention will be specifically described by way of examples.
- the heating conditions and rolling conditions in the reheating furnace were adjusted. Thereafter, the tube was cooled to room temperature in 2 ° CZ seconds, and then tempered at 700 to 750 ° C. Table 1 shows the finishing temperature and tempering temperature for each test steel.
- a test piece was cut out from the base tube manufactured in this way based on the API 5CT standard, and the tensile strength and yield strength, HRC hardness, Charpy impact test (shape: 2) using an arc-shaped test piece. The transition temperature by mmV notch 10 X 5 mm) was measured.
- the evaluation method is that the tensile strength is API L80 ⁇ V— (YP: 552 to 656 MPa, TS: 657 MPa or more), HRC hardness is 22 or less, fracture surface transition temperature (vTrs) force in Charpy impact test, force SO Satisfaction that the temperature was below ° C was a necessary condition.
- FIG. 1 is a graph showing the results of Table 1.
- the “ ⁇ ” and “X” in the force diagram are as follows.
- a martensitic stainless steel pipe made of 13Cr steel can be produced with high productivity and low cost by the direct quenching method. it can.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
Description
Claims
Priority Applications (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
CN2005800328265A CN101031663B (zh) | 2004-09-28 | 2005-09-27 | 马氏体类不锈钢管的制造方法 |
EP05787771.4A EP1813687B1 (en) | 2004-09-28 | 2005-09-27 | Method for producing martensitic stainless steel pipe |
US11/727,467 US8366843B2 (en) | 2004-09-28 | 2007-03-27 | Method of manufacturing a martensitic stainless steel pipe |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2004-281711 | 2004-09-28 | ||
JP2004281711A JP4380487B2 (ja) | 2004-09-28 | 2004-09-28 | マルテンサイト系ステンレス鋼管の製造方法 |
Related Child Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US11/727,467 Continuation US8366843B2 (en) | 2004-09-28 | 2007-03-27 | Method of manufacturing a martensitic stainless steel pipe |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2006035735A1 true WO2006035735A1 (ja) | 2006-04-06 |
Family
ID=36118880
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2005/017675 WO2006035735A1 (ja) | 2004-09-28 | 2005-09-27 | マルテンサイト系ステンレス鋼管の製造方法 |
Country Status (5)
Country | Link |
---|---|
US (1) | US8366843B2 (ja) |
EP (1) | EP1813687B1 (ja) |
JP (1) | JP4380487B2 (ja) |
CN (1) | CN101031663B (ja) |
WO (1) | WO2006035735A1 (ja) |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN103045835A (zh) * | 2011-10-17 | 2013-04-17 | 宝山钢铁股份有限公司 | 一种L80-13Cr油管的制造方法 |
US8795462B2 (en) | 2007-12-20 | 2014-08-05 | Cima Nanotech Israel Ltd. | Transparent conductive coating with filler material |
JP2017031493A (ja) * | 2015-08-05 | 2017-02-09 | 新日鐵住金株式会社 | ステンレス鋼管の製造方法 |
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JP2007270191A (ja) * | 2006-03-30 | 2007-10-18 | Sumitomo Metal Ind Ltd | マルテンサイト系ステンレス鋼管の製造方法 |
JP5211552B2 (ja) * | 2007-05-31 | 2013-06-12 | Jfeスチール株式会社 | 拡管性に優れる油井用ステンレス鋼管およびその製造方法 |
JP5211708B2 (ja) * | 2008-01-17 | 2013-06-12 | Jfeスチール株式会社 | 拡管性に優れる油井用ステンレス鋼管およびその製造方法 |
US9181610B2 (en) * | 2008-03-27 | 2015-11-10 | Nippon Steel & Sumitomo Metal Corporation | Air cooling equipment for heat treatment process for martensitic stainless steel pipe or tube |
CN102172626B (zh) * | 2010-12-29 | 2012-07-25 | 天津钢管集团股份有限公司 | φ48-89mm超级13Cr油管的热轧生产方法 |
CN102345999A (zh) * | 2011-06-27 | 2012-02-08 | 苏州方暨圆节能科技有限公司 | 换热器冷却扁管的不锈钢材料 |
JP5907083B2 (ja) * | 2013-01-31 | 2016-04-20 | Jfeスチール株式会社 | 靭性に優れた継目無鋼管の製造方法及び製造設備 |
CN104099527B (zh) * | 2013-04-08 | 2016-06-01 | 宝山钢铁股份有限公司 | 一种超级13Cr加厚钻杆的制造方法 |
JP6406075B2 (ja) * | 2015-03-12 | 2018-10-17 | Jfeスチール株式会社 | マルテンサイト系高Cr鋼の継目無鋼管の製造方法 |
CN111315906A (zh) * | 2017-11-02 | 2020-06-19 | 日本制铁株式会社 | 穿轧机顶头及其制造方法 |
CN110643895B (zh) * | 2018-06-27 | 2021-05-14 | 宝山钢铁股份有限公司 | 一种马氏体不锈钢油套管及其制造方法 |
CN115404417B (zh) * | 2021-05-28 | 2023-10-13 | 宝武特种冶金有限公司 | 一种高性能马氏体耐热钢及其制备方法 |
Citations (9)
Publication number | Priority date | Publication date | Assignee | Title |
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JPS63293111A (ja) | 1987-05-26 | 1988-11-30 | Sumitomo Metal Ind Ltd | マルテンサイト系ステンレス鋼継目無管の製造方法 |
GB2230024A (en) | 1989-02-28 | 1990-10-10 | Mannesmann Ag | An heat treatment for seamless steel pipes |
JPH0672261B2 (ja) * | 1986-11-05 | 1994-09-14 | 住友金属工業株式会社 | ステンレス鋼継目無し管の製造方法 |
JPH0678571B2 (ja) * | 1987-11-07 | 1994-10-05 | 住友金属工業株式会社 | ステンレス鋼継目無し管の製造方法 |
JP2705416B2 (ja) * | 1991-12-19 | 1998-01-28 | 住友金属工業株式会社 | マルテンサイト系ステンレス鋼と製造方法 |
JPH11310822A (ja) * | 1998-04-30 | 1999-11-09 | Nippon Steel Corp | 低温靭性に優れた高強度マルテンサイト系ステンレス鋼管の製造法 |
EP1288316A1 (en) | 2001-08-29 | 2003-03-05 | Kawasaki Steel Corporation | Method for making high-strength high-toughness martensitic stainless steel seamless pipe |
JP2003105441A (ja) | 2001-09-28 | 2003-04-09 | Kawasaki Steel Corp | 高強度・高靭性13Crマルテンサイト系ステンレス鋼継目無管の製造方法 |
JP4110420B2 (ja) | 2005-06-23 | 2008-07-02 | 株式会社富士通ゼネラル | 空気調和機 |
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JPS63238217A (ja) * | 1987-03-26 | 1988-10-04 | Kawasaki Steel Corp | 低温靭性および耐応力腐食割れ性に優れたマルテンサイト系ステンレス継目無鋼管の製造方法 |
JPH01123024A (ja) * | 1987-11-05 | 1989-05-16 | Sumitomo Metal Ind Ltd | ステンレス鋼継目無し管の製造方法 |
JPH0672262B2 (ja) * | 1987-11-06 | 1994-09-14 | 住友金属工業株式会社 | ステンレス鋼継目無し管の製造方法 |
JP2979604B2 (ja) * | 1990-08-31 | 1999-11-15 | 住友金属工業株式会社 | マルテンサイト系ステンレス鋼継目無管の製造方法 |
JP2996245B2 (ja) * | 1998-02-23 | 1999-12-27 | 住友金属工業株式会社 | 酸化スケ―ル層付きマルテンサイト系ステンレス鋼材およびその製造方法 |
WO2000070112A1 (fr) * | 1999-05-18 | 2000-11-23 | Sumitomo Metal Industries, Ltd. | Acier inoxydable martensitique pour tube en acier sans soudure |
-
2004
- 2004-09-28 JP JP2004281711A patent/JP4380487B2/ja active Active
-
2005
- 2005-09-27 EP EP05787771.4A patent/EP1813687B1/en not_active Expired - Fee Related
- 2005-09-27 CN CN2005800328265A patent/CN101031663B/zh not_active Expired - Fee Related
- 2005-09-27 WO PCT/JP2005/017675 patent/WO2006035735A1/ja active Application Filing
-
2007
- 2007-03-27 US US11/727,467 patent/US8366843B2/en active Active
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JPH0672261B2 (ja) * | 1986-11-05 | 1994-09-14 | 住友金属工業株式会社 | ステンレス鋼継目無し管の製造方法 |
JPS63293111A (ja) | 1987-05-26 | 1988-11-30 | Sumitomo Metal Ind Ltd | マルテンサイト系ステンレス鋼継目無管の製造方法 |
JPH0678571B2 (ja) * | 1987-11-07 | 1994-10-05 | 住友金属工業株式会社 | ステンレス鋼継目無し管の製造方法 |
GB2230024A (en) | 1989-02-28 | 1990-10-10 | Mannesmann Ag | An heat treatment for seamless steel pipes |
JPH02277720A (ja) | 1989-02-28 | 1990-11-14 | Mannesmann Ag | シームレスオイルパイプライン管を製作する方法 |
JP2705416B2 (ja) * | 1991-12-19 | 1998-01-28 | 住友金属工業株式会社 | マルテンサイト系ステンレス鋼と製造方法 |
JPH11310822A (ja) * | 1998-04-30 | 1999-11-09 | Nippon Steel Corp | 低温靭性に優れた高強度マルテンサイト系ステンレス鋼管の製造法 |
EP1288316A1 (en) | 2001-08-29 | 2003-03-05 | Kawasaki Steel Corporation | Method for making high-strength high-toughness martensitic stainless steel seamless pipe |
JP2003105441A (ja) | 2001-09-28 | 2003-04-09 | Kawasaki Steel Corp | 高強度・高靭性13Crマルテンサイト系ステンレス鋼継目無管の製造方法 |
JP4110420B2 (ja) | 2005-06-23 | 2008-07-02 | 株式会社富士通ゼネラル | 空気調和機 |
Non-Patent Citations (1)
Title |
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See also references of EP1813687A4 |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US8795462B2 (en) | 2007-12-20 | 2014-08-05 | Cima Nanotech Israel Ltd. | Transparent conductive coating with filler material |
CN103045835A (zh) * | 2011-10-17 | 2013-04-17 | 宝山钢铁股份有限公司 | 一种L80-13Cr油管的制造方法 |
JP2017031493A (ja) * | 2015-08-05 | 2017-02-09 | 新日鐵住金株式会社 | ステンレス鋼管の製造方法 |
Also Published As
Publication number | Publication date |
---|---|
CN101031663B (zh) | 2010-09-08 |
US20070246136A1 (en) | 2007-10-25 |
EP1813687A4 (en) | 2010-05-05 |
US8366843B2 (en) | 2013-02-05 |
JP2006097051A (ja) | 2006-04-13 |
EP1813687A1 (en) | 2007-08-01 |
EP1813687B1 (en) | 2018-11-14 |
JP4380487B2 (ja) | 2009-12-09 |
CN101031663A (zh) | 2007-09-05 |
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