WO1999004052A1 - Acier inoxydable en martensite a haute resistance a la corrosion - Google Patents

Acier inoxydable en martensite a haute resistance a la corrosion Download PDF

Info

Publication number
WO1999004052A1
WO1999004052A1 PCT/JP1998/003243 JP9803243W WO9904052A1 WO 1999004052 A1 WO1999004052 A1 WO 1999004052A1 JP 9803243 W JP9803243 W JP 9803243W WO 9904052 A1 WO9904052 A1 WO 9904052A1
Authority
WO
WIPO (PCT)
Prior art keywords
less
group
mass
elements
steel
Prior art date
Application number
PCT/JP1998/003243
Other languages
English (en)
Japanese (ja)
Inventor
Masakatsu Ueda
Hideki Takabe
Kunio Kondo
Kazuhiro Ogawa
Hisashi Amaya
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.
Priority to CA002296349A priority Critical patent/CA2296349C/fr
Priority to EP98932588A priority patent/EP1026273B1/fr
Priority to JP2000503256A priority patent/JP3555579B2/ja
Priority to DE69838879T priority patent/DE69838879T2/de
Publication of WO1999004052A1 publication Critical patent/WO1999004052A1/fr
Priority to NO20000232A priority patent/NO20000232L/no

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
    • C22C38/001—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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium

Definitions

  • the present invention relates to a high corrosion resistant martensitic stainless steel used under force sword protection.
  • This stainless steel has excellent corrosion resistance in an atmosphere containing carbon dioxide gas. Therefore, it is suitable for use as a line pipe for transporting oil and natural gas containing carbon dioxide. Even if the pipe is used as welded with anticorrosion in seawater, there is no risk of cracking.
  • the stainless steel of the present invention is suitable as a material for seamless steel pipes, ERW steel pipes, laser-welded steel pipes, submerged-arc-welded (SAW) pipes, and the like.
  • a steel product it can also be used as a material for various devices exposed to an atmosphere containing carbon dioxide gas. Examples of such equipment include piping for a decarbonation facility, piping for geothermal power generation, and a tank for a liquid containing carbon dioxide.
  • the stainless steel according to the present invention can be used even in an environment containing a trace amount of hydrogen sulfide together with carbon dioxide. Background art
  • the pipe itself is inexpensive, but the inhibitor is expensive and may cause environmental pollution.
  • the duplex stainless steel (2) itself is expensive.
  • carbon dioxide corrosion resistance There are many research reports on the corrosion resistance of steel to carbon dioxide (hereinafter referred to as carbon dioxide corrosion resistance). For example, A. Ikeda. Et al .: Corrosion / 83, NACE Houston. Paper No. 45, 1983 states that by increasing the content of Cr to 7% or more, it is possible to use a high-temperature aqueous solution containing carbon dioxide at about 100 ° C. It has been reported that carbon dioxide corrosion can be prevented at high temperatures. Also, M. Ueda, et al .: Corrosion / 92, NA CE Houston. Paper No.55, 1992 shows that the addition of Mo and / or W to 13Cr martensitic stainless steel improves local corrosion performance. Is disclosed.
  • 13Cr martensite stainless steel for example, SUS410 steel
  • SUS410 steel has attracted attention as a carbon dioxide corrosion resistant piping material.
  • This type of steel is used after heat treatment of quenching and tempering.
  • PWHT post-weld heat treatment
  • Martensite stainless steel is relatively inexpensive, has high strength and excellent corrosion resistance, and can be used without any inhibition. However, when used in seawater, for example, as a submarine pipeline, force sword protection must be carried out to protect the outer surface. Big problems that stainless steel does not have Occurs.
  • Kasode corrosion protection is a corrosion protection method that uses corrosion-resistant steel as a force sword to generate a corrosion protection current and counteract the corrosion current. At this time, hydrogen is generated by the cathodic reaction, and this hydrogen enters the steel material.
  • the heat affected zone of the 13Cr martensitic stainless steel has a hardened structure as it is welded, and has high hardness. If hydrogen penetrates into such a part, it causes cracking due to hydrogen embrittlement.
  • An object of the present invention is to provide a martensitic stainless steel having the following characteristics (a) to ().
  • Another object of the present invention is to provide a steel pipe made of martensitic stainless steel having the above characteristics.
  • the steel pipes include seamless steel pipes and welded steel pipes such as ERW pipes, laser welded pipes, and SAW pipes.
  • the basic chemical composition of the martensitic stainless steel of the present invention is as follows.
  • component (2) further includes one or more alloying elements selected from at least one group of the following first group elements, second group elements, and third group elements: composition.
  • Group 1 elements Nb: 0.005 to 0.10%, Ti: 0.005 to 0.10% and
  • Group 2 element Mo and W that become 0.2-3.0% at MO + 0.5W
  • Group 3 elements Ca: 0.001 to 0.05%
  • Mg 0.001 to 0.05%
  • the martensitic stainless steel of the present invention has the basic composition of the above (2) or (3), and further satisfies any of the following formulas (1) to (4) and formula (4).
  • Fig. 1 is a diagram showing the relationship between the P (adjacent) content and the hardness of as-quenched steel and the corrosion resistance in martensitic stainless steel.
  • FIG. 2 is a table showing the chemical composition of the test materials used in the examples.
  • FIG. 3 is a table showing the chemical compositions of the test materials used in the examples.
  • FIG. 4 is a table showing the test results of the examples.
  • FIG. 5 is a table showing the test results of the example.
  • BEST MODE FOR CARRYING OUT THE INVENTION The stainless steel of the present invention has the following characteristics as the overall effect of the basic composition and the conditions defined by the formulas (1) and (2). Is provided. Among them, the most significant feature of the steel of the present invention is that there is no risk of cracking even if the force-sword corrosion protection is performed as it is. Therefore, First, this feature will be described.
  • the weld heat affected zone is heated by the welding heat input and then rapidly cooled by the chill effect of the base metal. Its heat history is almost the same as the heat history of quenching. Therefore, the inventors of the present invention have assumed that, assuming that the steel is used as welded, the phenomena of corrosion of the heat-affected zone of the weld and cracking caused by corrosion of the power source are similar to those of the as-quenched steel. I thought it could be evaluated. Therefore, samples of as-quenched 13 Cr martensitic stainless steel were prepared, and their metallographic structure, corrosion resistance to carbon dioxide gas, and the tendency of cracking due to force-sword corrosion were investigated. As a result, it became clear that the following conditions 1 and 2 must be satisfied simultaneously in order to prevent cracking due to carbon dioxide gas corrosion and force sword corrosion protection.
  • the as-quenched metal structure must have a martensite ratio of 95% or more.
  • the martensite ratio is less than 95% means that there is a large amount of non-martensite tissues, such as austenite or ferrite, in which case cracking occurs under cathodic protection. Will occur. This is because corrosion is promoted in parts other than the martensite structure, and hydrogen is generated by the corrosion reaction, so that the amount of hydrogen absorbed in the steel also increases.
  • Figure 1 shows C: 0.01 to 0.039%, Si: 0.31 to 0.36%, Mn: 1.09 to 2.60%, S: 0.003 to 0.005%, Cr: 11.7 to 12.2%, Ni: 1.8 to 2.1%, A1: 0.08- 0.1%, the balance was Fe steel, and test pieces were prepared with various changes in the P content and hardness as quenched. It is a figure which shows the result of having performed the crack test below. The test pieces were prepared by quenching and adjusting the composition so that the martensite ratio was 95% or more (to satisfy the above formula (1)). The hardness was determined by the content of C and Mn. Changed by adjustment.
  • the C content exceeds 0.04%, the hardness of as-quenched steel with a martensite ratio of 95% or more becomes too high, causing cracking under force-sword corrosion protection.
  • the lower the C% the better. Therefore, C is set to 0.04% or less.
  • the lower the C% the better the toughness of the heat-affected zone as it is welded. Therefore, the desirable upper limit is 0.025%, and more desirable is 0.015%. In consideration of economical production, the lower limit is about 0.001%.
  • Si is a necessary component for deoxidizing steel, but if its content exceeds 1.0%, hot workability deteriorates. Therefore, the upper limit was set at 1.0%. If it is less than 0.01%, a deoxidizing effect cannot be obtained.
  • Mn is also a necessary component as a deoxidizing agent for steel, but if its content exceeds 1.5%, hot workability deteriorates. Therefore, the upper limit was set at 1.5%. If it is less than 0.1%, no deoxidizing effect can be obtained.
  • Cr is a component that improves carbon dioxide gas corrosion resistance. If it is less than 7%, sufficient carbon dioxide gas corrosion resistance cannot be obtained. On the other hand, if it exceeds 15%, it is difficult to obtain a martensite ratio of 95% or more with quenching, so the Cr content was set to 7 to 15%. Preferred is 9-; 13%.
  • Ni needs to be contained in the range of 0.7-8.0% in order to obtain a martensite ratio of 95% or more as-quenched. If it is less than 0.7%, ferrite generation increases, and if it exceeds 8.0%, the amount of austenite increases.
  • the content of Ni is preferably 0.7 to 7.0%.
  • One of the features of the steel of the present invention is that excellent properties can be obtained even in a low Ni content range of 0.7 to less than 4.0, so that the cost of the material can be reduced.
  • A1 is an element necessary as a deoxidizing agent in the steelmaking process, similar to Si described above, but if its content is less than 0.001%, the desired deoxidizing effect cannot be obtained. Conversely, if the content exceeds 0.20%, the non-metallic inclusions increase and the corrosion resistance deteriorates. Therefore, the A1 content was set to 0.001 to 0.20%.
  • Cu is not an essential component, but it has the effect of suppressing steel corrosion, reducing hydrogen generation and preventing cracking under cathodic protection, and can be added as necessary. However, if the content exceeds 2%, the effect is saturated. Therefore, even when Cu is added, its content is preferably 2% or less.
  • N should be kept below 0.05%.
  • the P content is regulated in relation to the hardness of the as-quenched steel (HRC).
  • HRC as-quenched steel
  • Nb, Ti and Zr are added as necessary to fix C and reduce the variation in strength. If each is less than 0.005%, there is no effect, and if it exceeds 0.10%, it is not possible to realize a martensite ratio of 95% or more with quenching, and the hardness as quenched becomes too high. The risk of cracking due to corrosion protection increases. These elements may be added alone or in combination of two or more.
  • This first group element is not an essential component and does not need to be added at all. However, since the addition of a small amount has the effect of fixing C, Nb is less than 5 XC (%), Ti is less than 4 x C (%), and Zr is less than 10 x C (%). It is desirable to include it in the range.
  • Mo and W coexist with Cr to prevent local corrosion in a carbon dioxide gas environment. Therefore, it is desirable for steel used in an environment where corrosion conditions are particularly severe to contain either 0.2 or 3.0% of Mo and / or W calculated as “Mo + 0.5W”. If it is less than 0.2%, sufficient improvement in local corrosion resistance cannot be obtained. On the other hand, even if the content exceeds 3.0%, the effect is hardly increased.
  • Group 3 elements (Ca, Mg, La, Ce):
  • Ca, Mg, La and Ce are all effective for improving the hot workability of steel. Therefore, to obtain the effect, one or more of these can be selected and added. However, if the content of each element is less than 0.001%, the above effects cannot be obtained. On the other hand, when the content exceeds 0.05%, coarse oxides are generated which lower the corrosion resistance of steel. Therefore, when they are added, their contents should be 0.001 to 0.05%, respectively. Particularly preferred among these elements are Ca and La.
  • the martensite stainless steel of the present invention is used after being subjected to a heat treatment of quenching and tempering. The heat treatment may be performed under ordinary conditions.
  • the steel of the present invention becomes a steel material having a yield strength of 550 MPa or more and excellent toughness.
  • the affected zone in contact with the weld metal is in a quenched state and has the highest hardness. Even in such a state, the weld heat affected zone of the steel of the present invention has a martensite ratio of 95% or more, has sufficient strength, toughness, and corrosion resistance, and has a crack under force-sword corrosion protection. There is no danger. Needless to say, it is more desirable to perform heat treatment (PWHT) after welding for the purpose of softening the heat affected zone.
  • PWHT heat treatment
  • the molten metal with the chemical composition shown in Fig. 2 and Fig. 3 is melted in a normal electric furnace, refined using an argon-oxygen decarburizing furnace (A0D furnace) for desulfurization, The ingot was subjected to hot forging at 1200 ° C. to obtain a bill with a diameter of 150 employees. From this billet, a seamless steel pipe with an outer diameter of 168 mm and a thickness of 12 thighs was manufactured by the Mannesmann pipe manufacturing method.
  • test materials were prepared from the above seamless steel pipes.
  • (c) is performed by gas-tungsten-arc welding (GTAW) or covered arc welding (Shield Metal Arc Welding, SMAW for short) using 25Cr duplex stainless steel welding material.
  • GTAW gas-tungsten-arc welding
  • SMAW covered arc welding
  • 25Cr duplex stainless steel welding material 25Cr duplex stainless steel welding material.
  • a cross section perpendicular to the longitudinal direction was cut out from the as-quenched pipe (a), and the HRC hardness was measured.
  • a cross section perpendicular to the longitudinal direction is cut out from the as-quenched pipe of (a), and a 100-times microscopic metallographic structure is observed with an optical microscope in 10 visual fields to measure the martensite ratio (area ratio). I asked.
  • test piece having a parallel part length of 20 mm was sampled at a diameter of 4.0 hall and subjected to a tensile test at room temperature to find 0.2% resistance to heat.
  • test piece having a width of 22 thighs and a thickness of 76 thighs and a length of 76 thighs was cut out from the as-welded test material (c), polished with No. 600 emery paper, degreased and dried. Specimens were taken from locations including the heat affected zone and the weld metal.
  • test piece was immersed in a 5% NaCl aqueous solution (liquid temperature: 125 ° C, flow rate: 3.5 m / s) saturated with CO 2 gas at 30 atm for 720 hours.
  • the specimen was visually inspected for the occurrence of local corrosion, and the corrosion loss of the specimen (the value obtained by subtracting the weight of the specimen after the test from the weight of the specimen before the test) was measured. It was converted to the corrosion rate (thigh / year).
  • test was conducted under the following conditions using a test piece taken from the position including the weld heat affected zone and the weld metal of the test material as-welded in (c) above.
  • ⁇ The temperature at which the brittle fracture ratio is 50% is lower than 130 ° C.
  • the corrosion rate is 0.05 thigh / year or less and no local corrosion is observed.
  • Corrosion rate exceeds 0.05 ⁇ / year, and local corrosion occurs or corrodes Local corrosion occurred at a speed of 0.05 m / year or less.
  • Test Nos. 1 to 44 shown in FIGS. 2 and 3 are the stainless steels of the present invention.
  • the as-quenched martensite ratios of these steels and the values of M calculated by the above equation (1) are shown in FIGS.
  • the allowable upper limit value of the hardness (IffiC) calculated from the above equation, that is, the value of (0.046-P) /0.0008 is also shown in these figures.
  • the excellent properties as described above include the fact that the basic chemical composition is appropriate, that by satisfying the above formula, the quenched steel has a martensite ratio of 95% or more, and that the P content and The relationship of hardness (HRC) is brought about by the overall function and effect of satisfying the above equation (2).
  • the steels of test Nos. 45 to 62 in Fig. 3 were produced as comparative examples. Of these, the steels of Nos. 53 to 55 and Nos. 60 to 62 whose basic compositions were out of the range specified in the present invention had some or all of the as-welded properties as shown in FIG. Part is inferior.
  • test steels 45, 48-52, and 56-59 are steels that do not satisfy the conditions of the above formula. That is, the as-quenched hardness exceeds the allowable upper limit calculated by equation (2). All of these steels cracked under force sword protection.
  • the steels of Test Nos. 46 and 47 have ⁇ values less than 50. These have low as-quenched martensite rates, which Poor toughness, cracking under force sword protection. Industrial applicability
  • the martensitic stainless steel of the present invention is a high-strength, high-toughness steel excellent in carbon dioxide corrosion resistance. And it is a steel that does not have the possibility of cracking when used as it is under corrosion protection by force. This steel is extremely suitable for use as a line pipe for transporting crude oil containing carbon dioxide gas, especially while performing power sword protection in the sea. Since this steel does not require heat treatment after welding, it can fully demonstrate the economics of martensitic stainless steel and has a great practical advantage.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Articles (AREA)
  • Arc Welding In General (AREA)
  • Heat Treatment Of Steel (AREA)
  • Prevention Of Electric Corrosion (AREA)

Abstract

L'invention concerne un acier inoxydable en martensite possédant une haute résistance à la corrosion par dioxyde de carbone, une haute résistance mécanique et une haute ténacité, l'acier ne présentant pas de possibilité de fissuration même lorsqu'il est soudé et muni d'un système de protection cathodique; l'acier présente la composition de base suivante (1) au plus 0,04 % en masse de C, 7 à 15 % en masse de Cr, 0,7 à 8,0 % en masse de Ni, 0,001 à 0,20 % en masse de Al et une quantité spécifiée d'au moins un type d'élément sélectionné dans le groupe formé par Si, Mn, Cu, S, Nb, Ti, Zr, Mo, W, Ca, Mg, et La; et remplit les conditions suivantes (2) M=98+47C-1.1Cr+1.4Ni-150Al-200Nb-50Ti-200Zr-22(Mo+0,5W)≥50 (1) P≤0,046-0,0008HRC (2) les symboles d'éléments dans les formules (1)-1 à (1)-4 et (2) représentant la teneur (% en masse) des éléments respectifs, et HRC dans la formule (2), la dureté Rockwell de l'acier trempé.
PCT/JP1998/003243 1997-07-18 1998-07-17 Acier inoxydable en martensite a haute resistance a la corrosion WO1999004052A1 (fr)

Priority Applications (5)

Application Number Priority Date Filing Date Title
CA002296349A CA2296349C (fr) 1997-07-18 1998-07-17 Acier inoxydable en martensite a haute resistance a la corrosion
EP98932588A EP1026273B1 (fr) 1997-07-18 1998-07-17 Acier inoxydable martensitique a haute resistance a la corrosion
JP2000503256A JP3555579B2 (ja) 1997-07-18 1998-07-17 高耐食性マルテンサイト系ステンレス鋼
DE69838879T DE69838879T2 (de) 1997-07-18 1998-07-17 Martensitischer rostfreier stahl mit hohem korrosionswiderstand
NO20000232A NO20000232L (no) 1997-07-18 2000-01-17 Martensittisk rustfritt stål med høy korrosjonsresistens

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP9/194000 1997-07-18
JP19400097 1997-07-18

Publications (1)

Publication Number Publication Date
WO1999004052A1 true WO1999004052A1 (fr) 1999-01-28

Family

ID=16317312

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP1998/003243 WO1999004052A1 (fr) 1997-07-18 1998-07-17 Acier inoxydable en martensite a haute resistance a la corrosion

Country Status (6)

Country Link
EP (1) EP1026273B1 (fr)
JP (1) JP3555579B2 (fr)
CA (1) CA2296349C (fr)
DE (1) DE69838879T2 (fr)
NO (1) NO20000232L (fr)
WO (1) WO1999004052A1 (fr)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2010026672A1 (fr) * 2008-09-04 2010-03-11 Ｊｆｅスチール株式会社 Tuyau continu en acier inoxydable martensitique pour un tuyau de puits de pétrole et processus de production associé
JP2010065301A (ja) * 2008-09-12 2010-03-25 Nippon Steel Corp 海岸地区における塗装時の耐食性に優れた高強度鋼およびその製造法

Families Citing this family (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP4240189B2 (ja) * 2001-06-01 2009-03-18 住友金属工業株式会社 マルテンサイト系ステンレス鋼
JP4144283B2 (ja) * 2001-10-18 2008-09-03 住友金属工業株式会社 マルテンサイト系ステンレス鋼
JP3905739B2 (ja) * 2001-10-25 2007-04-18 三菱重工業株式会社 タービンロータ用１２Ｃｒ合金鋼、その製造方法及びタービンロータ
AR042494A1 (es) * 2002-12-20 2005-06-22 Sumitomo Chemical Co Acero inoxidable martensitico de alta resistencia con excelentes propiedades de resistencia a la corrosion por dioxido de carbono y resistencia a la corrosion por fisuras por tensiones de sulfuro
JP4400423B2 (ja) * 2004-01-30 2010-01-20 Ｊｆｅスチール株式会社 マルテンサイト系ステンレス鋼管
JP4337712B2 (ja) * 2004-11-19 2009-09-30 住友金属工業株式会社 マルテンサイト系ステンレス鋼
EP2058412A4 (fr) 2006-08-31 2016-02-17 Nippon Steel & Sumitomo Metal Corp Acier inoxydable martensitique pour structure soudee

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH04268019A (ja) * 1991-02-22 1992-09-24 Nippon Steel Corp マルテンサイト系ステンレス鋼ラインパイプの製造方法
JPH06299301A (ja) * 1993-04-09 1994-10-25 Nkk Corp １１０Ｋｓｉ グレードの高強度耐食性マルテンサイト系ステンレス鋼管
JPH0841599A (ja) * 1994-07-26 1996-02-13 Sumitomo Metal Ind Ltd 溶接部の耐食性が優れたマルテンサイト系ステンレス鋼
JPH08199236A (ja) * 1995-01-30 1996-08-06 Nippon Steel Corp ラインパイプ用マルテンサイト系ステンレス鋼板の製造方法

Family Cites Families (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
ES2044905T3 (es) * 1986-12-30 1994-01-16 Nisshin Steel Co Ltd Proceso para la produccion de una banda de acero inoxidable al cromo de una estructura doble que tiene una alta resistencia y alargamiento asi como una mejor anistropia plana.
JPH06128632A (ja) * 1992-10-13 1994-05-10 Nippon Steel Corp 耐蝕性に優れたマルテンサイト系ステンレス鋼の製造方法

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH04268019A (ja) * 1991-02-22 1992-09-24 Nippon Steel Corp マルテンサイト系ステンレス鋼ラインパイプの製造方法
JPH06299301A (ja) * 1993-04-09 1994-10-25 Nkk Corp １１０Ｋｓｉ グレードの高強度耐食性マルテンサイト系ステンレス鋼管
JPH0841599A (ja) * 1994-07-26 1996-02-13 Sumitomo Metal Ind Ltd 溶接部の耐食性が優れたマルテンサイト系ステンレス鋼
JPH08199236A (ja) * 1995-01-30 1996-08-06 Nippon Steel Corp ラインパイプ用マルテンサイト系ステンレス鋼板の製造方法

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of EP1026273A4 *

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2010026672A1 (fr) * 2008-09-04 2010-03-11 Ｊｆｅスチール株式会社 Tuyau continu en acier inoxydable martensitique pour un tuyau de puits de pétrole et processus de production associé
JP2010065301A (ja) * 2008-09-12 2010-03-25 Nippon Steel Corp 海岸地区における塗装時の耐食性に優れた高強度鋼およびその製造法

Also Published As

Publication number Publication date
CA2296349C (fr) 2004-11-02
EP1026273B1 (fr) 2007-12-19
JP3555579B2 (ja) 2004-08-18
DE69838879T2 (de) 2008-12-04
EP1026273A4 (fr) 2005-12-14
NO20000232D0 (no) 2000-01-17
CA2296349A1 (fr) 1999-01-28
DE69838879D1 (de) 2008-01-31
NO20000232L (no) 2000-03-06
EP1026273A1 (fr) 2000-08-09

Similar Documents

Publication Publication Date Title
EP0864663B1 (fr) Structures en acier soude presentant une excellente resistance a la corrosion
AU2003289437B2 (en) High-strength martensitic stainless steel with excellent resistances to carbon dioxide gas corrosion and sulfide stress corrosion cracking
JP3271262B2 (ja) 耐食性にすぐれた二相ステンレス鋼
JP6969666B2 (ja) オーステナイト系ステンレス鋼溶接継手
WO2011132765A1 (fr) Tuyau d'acier contenant du chrome pour une canalisation ayant une excellente résistance à la fissuration par corrosion intergranulaire sous contrainte dans la partie affectée par la chaleur de soudage
JP4462005B2 (ja) 耐食性に優れたラインパイプ用高強度ステンレス鋼管およびその製造方法
US6159310A (en) Wire for welding high-chromium steel
WO2005073419A1 (fr) Tube en acier inoxydable martensitique
JP3555579B2 (ja) 高耐食性マルテンサイト系ステンレス鋼
JP2001279392A (ja) マルテンサイト系ステンレス鋼および製造方法
JP2007321181A (ja) マルテンサイト系ステンレス鋼材溶接部の形成方法
EP0546549A1 (fr) Tube pour pipeline, avec bonne résistance à la corrosion et bonne soudabilité
JP2002105604A (ja) 耐食性および溶接性に優れたラインパイプ用高Ｃｒマルテンサイト系ステンレス鋼管およびその製造方法
JP3156170B2 (ja) ラインパイプ用マルテンサイト系ステンレス鋼
JP2002226947A (ja) 耐歪み時効性に優れたマルテンサイト系ステンレス鋼溶接継手
JP3620319B2 (ja) 耐食性と溶接性に優れたマルテンサイト系ステンレス鋼
JP2004107773A (ja) 耐食性に優れたラインパイプ用ステンレス鋼管
JP2000015447A (ja) マルテンサイト系ステンレス鋼の溶接方法
US9352369B2 (en) Equipment for use in corrosive environments and methods for forming thereof
JPS6160866A (ja) 耐サワ−性に優れたラインパイプ用鋼材
JP2575250B2 (ja) 耐食性および溶接性の優れたラインパイプ
JPH04224656A (ja) 油井管用マルテンサイト系ステンレス鋼
El-Mahallawi et al. Welding-associated failures in power boilers
JP3890821B2 (ja) 耐応力腐食割れ性に優れた高強度高靱性ステンレス鋼
Sagara et al. New Duplex Stainless Steel for Line Pipe Material in Slightly Sour Environment

Legal Events

Date Code Title Description
AK Designated states

Kind code of ref document: A1

Designated state(s): CA JP NO US

AL Designated countries for regional patents

Kind code of ref document: A1

Designated state(s): AT BE CH CY DE DK ES FI FR GB GR IE IT LU MC NL PT SE

DFPE Request for preliminary examination filed prior to expiration of 19th month from priority date (pct application filed before 20040101)
121 Ep: the epo has been informed by wipo that ep was designated in this application
WWE Wipo information: entry into national phase

Ref document number: 09482328

Country of ref document: US

ENP Entry into the national phase

Ref document number: 2296349

Country of ref document: CA

Ref country code: CA

Ref document number: 2296349

Kind code of ref document: A

Format of ref document f/p: F

WWE Wipo information: entry into national phase

Ref document number: 1998932588

Country of ref document: EP

WWP Wipo information: published in national office

Ref document number: 1998932588

Country of ref document: EP

WWG Wipo information: grant in national office

Ref document number: 1998932588

Country of ref document: EP