EP1026273A1 - Acier inoxydable en martensite a haute resistance a la corrosion - Google Patents

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

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Publication number
EP1026273A1
EP1026273A1 EP98932588A EP98932588A EP1026273A1 EP 1026273 A1 EP1026273 A1 EP 1026273A1 EP 98932588 A EP98932588 A EP 98932588A EP 98932588 A EP98932588 A EP 98932588A EP 1026273 A1 EP1026273 A1 EP 1026273A1
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EP
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Prior art keywords
elements
steel
following
inequalities
group elements
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Application number
EP98932588A
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German (de)
English (en)
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EP1026273B1 (fr
EP1026273A4 (fr
Inventor
Masakatsu Sumitomo Metal Ind. Ltd. UEDA
Hideki Sumitomo Metal Ind. Ltd. TAKABE
Kunio Sumitomo Metal Ind. Ltd. KONDO
Kazuhiro Sumitomo Metal Ind. Ltd. OGAWA
Hisashi Sumitomo Metal Ind. Ltd. AMAYA
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Nippon Steel Corp
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Sumitomo Metal Industries Ltd
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Publication of EP1026273A4 publication Critical patent/EP1026273A4/fr
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Publication of EP1026273B1 publication Critical patent/EP1026273B1/fr
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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
    • 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

  • This invention relates to a high-corrosion-resistant martensitic stainless steel for use under cathodic protection.
  • This stainless steel has excellent corrosion resistance in atmospheres, which contain carbon dioxide, and, therefore, it is suitable for use in line-pipes for transporting oil and natural gas, which contain carbon dioxide. Even if the pipe is used in a welded condition in the sea with cathodic protection, there is no risk that the pipe will suffer cracking.
  • the stainless steel of this invention is preferably used as a material for seamless pipes, resistance welded pipes, laser welded pipes, submerged arc welded (SAW) pipes and the like.
  • this stainless steel may also be used as a material for various types of equipment exposed to atmospheres, which contain carbon dioxide.
  • Such equipment includes, e.g., piping for decarbonating facilities, piping for geothermal power generation, and tanks for carbon dioxide-containing liquids.
  • the stainless steel according to this invention can be used in environments, which contain a slight amount of hydrogen sulfide together with carbon dioxide.
  • the pipes themselves are inexpensive, but the inhibitors are expensive and could cause environmental pollution.
  • the duplex stainless steels in the second method (2) are expensive.
  • Martensitic stainless steels are comparatively inexpensive, exhibit high strength and excellent corrosion resistance, and can be used without inhibitors.
  • the martensitic stainless steel needs to be subjected to cathodic protection for the prevention of corrosion to the outer surface, and when subjected to the cathodic protection, there arises a serious problem which is never encountered by carbon steels and duplex stainless steels.
  • Cathodic protection is a corrosion prevention method in which the corrosion current is cancelled by producing a protective current using a steel material to be corroded as the cathode. During this process, hydrogen is produced by the cathodic reaction, and the produced hydrogen is absorbed into the steel material.
  • the welding heat affected zone of a 13Cr martensitic stainless steel has a quenched structure as welded, and exhibits an extreme hardness. When hydrogen is absorbed into such a zone, it suffers cracking due to hydrogen embrittlement.
  • One of the objects of this invention is to provide a martensitic stainless steel having all of the following properties (a) to (d).
  • Another object of this invention is to provide a steel tube, which is made of a martensitic stainless steel, having the above-described properties as a material.
  • This steel pipe includes seamless pipes, and welded pipes such as resistance welded pipes, laser welded pipes, and SAW pipes.
  • the basic chemical composition of the martensitic stainless steel according to this invention is as follows.
  • the martensitic stainless steel of this invention has the basic composition described in (2) or (3) above, and further satisfies any of the following inequalities (1)-1 to (1)-4, and the following inequality (2).
  • M 98+47C-1.1Cr+1.4Ni-150Al ⁇ 50
  • M 98+47C-1.1Cr+1.4Ni-150Al-200Nb-50Ti-200Zr ⁇ 50
  • M 98+47C-1.1Cr+1.4Ni-150Al-22(Mo+0.5W) ⁇ 50
  • M 98+47C-1.1Cr+1.4Ni-150Al-200Nb-50Ti-200Zr-22(Mo+0.5W) ⁇ 50
  • M 98+47C-1.1Cr+1.4Ni-150Al-200Nb-50Ti-200Zr-22(Mo+0.5W) ⁇ 50
  • a stainless steel of this invention has the properties described previously in (a) to (c), as a combined effect of the previously described basic compositions, and the conditions specified by the inequalities (1) and (2).
  • the most significant characteristic feature is that the steel of this invention has no risk of cracking, even if subjected to cathodic protection, as welded. Thus, this feature will be described first.
  • a welding heat affected zone is heated through a weld heat input, and is thereafter rapidly cooled by the chill effect of the base metal. Its heat pattern is substantially the same as that for quenching. Therefore, the inventors thought, on the assumption that the steel would be used as welded, that the phenomena of corrosion and cracking due to cathodic protection observed at the welding heat affected zone could be evaluated in terms of the phenomena observed in a steel as quenched. Hence, specimens of a 13Cr martensitic stainless steel as quenched were prepared and their metallographic structure, corrosion resistance to carbon dioxide, and a tendency toward cracking due to cathodic protection, were investigated. As a result, it was clarified that in order to prevent carbon dioxide corrosion and cracking due to cathodic protection, the following conditions 1 and 2 need to be satisfied at the same time.
  • the rate of martensite is less than 95% means that the steel has a structure other than martensite, e.g., austenite or ferrite mixed in a large amount, and in this case, cracking tends to occur under cathodic protection. This is due to corrosion being promoted at regions other than the martensitic structure, and thus hydrogen is produced by the corrosion reaction, which in turn increases the amount of hydrogen absorbed into the steel.
  • martensite e.g., austenite or ferrite mixed in a large amount
  • a structure which is quenched at a rate of martensite of 95% or more can be obtained by adjusting the chemical composition of the steel.
  • a specific condition for the adjustment of the chemical composition is the previously described inequality (1). That inequality is an empirical formula obtained from the results of a number of tests conducted by the inventors.
  • FIG. 1 is a diagram showing the results of carbon dioxide corrosion tests and cracking tests under cathodic protection, which will later be described in "Example”.
  • the base steel consists of C: 0.01-0.039%, Si: 0.31-0.36%, Mn: 1.09-2.60%, S: 0.003-0.005%, Cr: 11.7-12.2%, Ni: 1.8-2.1%, Al: 0.08-0.11%, and the balance of Fe. Test specimens were prepared from the base steel by varying the P content and the hardness as quenched in varying degrees.
  • test specimens were obtained by adjusting the chemical compositions so as to become structures whose rate of martensite is 95% or more as quenched (so as to satisfy the previously described inequality (1)), with their hardness varied by adjusting the contents of C and Mn.
  • the content of C exceeds 0.04%, the hardness of a steel as quenched, whose rate of martensite is 95% or more, becomes too high to suffer cracking under cathodic protection.
  • the lower the C content the better. Therefore, the C content is set at 0.04% or less.
  • the lower the C content is, the more satisfactory the toughness of the heat affected zone of the steel as welded becomes, therefore, the desirable upper limit of the C content is 0.025%, and the more desirable upper limit is 0.015%. Note that the lower limit is on the order of 0.001% from the viewpoint of manufacturing the steel economically.
  • Silicon is an element necessary to deoxidize steels. When its content exceeds 1.0%, hot workability is degraded. Therefore, its upper limit is set at 1.0%. No deoxidizing effect can be obtained when the Si content is less than 0.01%.
  • Chromium is an element for improving corrosion resistance to carbon dioxide and no sufficient corrosion resistance to carbon dioxide can be obtained when the Cr content is less than 7%.
  • the Cr content is set between 7 and 15%. Preferably, it is between 9 and 13%.
  • the Ni content of a steel needs to be in the range of 0.7-8.0%, because when the Ni content is less than 0.7%, the formation of ferrite is promoted and when it exceeds 8.0%, the amount of austenite is increased.
  • the preferable Ni content is in the range of 0.7-7.0%. Note that excellent properties can be obtained even if the Ni content is within such a low range of 0.7 to less than 4.0%, and thus a possible reduction in the material costs is one of the characteristic features of the steel according to this invention.
  • Al is a necessary element as a deoxidizer in the steel making process.
  • its content is less than 0.001%, no desired deoxidizing effect can be obtained.
  • its content exceeds 0.20%, nonmetallic inclusions increase and thus the corrosion resistance is degraded.
  • the Al content was set between 0.001 and 0.20%.
  • Cu has the effect of suppressing the corrosion of steels and reducing the production of hydrogen to thereby prevent cracking under cathodic protection, and thus Cu can be added whenever necessary.
  • its content exceeds 2%, its effect gets saturated. Therefore, even if Cu is added, it is desirable that its content is up to 2%.
  • the content of N exceeds 0.05%, the hardness of the welding heat affected zone of a steel as quenched, becomes so high that the steel is susceptible to cracking under cathodic protection. Therefore, the N content should be kept at 0.05% or lower.
  • Sulfur is also present as an impurity in steels. Since S impairs hot workability when its content exceeds 0.01%, its upper limit is set at 0.01%. The less, the better. However, the lower limit, permitting economical manufacture, is on the order of 0.0007%.
  • Nb, Ti and Zr are added whenever necessary in order to fix C and reduce fluctuations in strength. Content of each of these elements, in an amount of less than 0.005%, is not effective. Content of each in an amount exceeding 0.10% cannot achieve a rate of martensite of 95% or more, and the hardness of a steel as quenched also becomes so high that the risk of cracking, due to cathodic protection, is increased. Note that these elements may be added singly or in combination of two or more.
  • the first group elements are not essential, none of them need be added at all. However, some addition of them in slight amounts, provides the effect of fixing C, so it is desirable to add them, considering the economy, in the range of less than 5 x C (%) Nb, less than 4 x C(%)Ti, and less than 10 x C(%)Zr.
  • Molybdenum and tungsten are elements that prevent localized corrosion in carbon dioxide environments, while present with Cr, therefore, for steels used in particularly severe corrosive environments, it is desirable that the steel contains one or both Mo and W in amounts ranging from 0.2 to 3.0% in terms of "Mo+0.5W.” No sufficient improvement of localized corrosion resistance is observed with their contents being less than 0.2%, while there is little increase in their effect when the amounts exceed 0.3%.
  • All of Ca, Mg, La and Ce are effective in improving the hot workability of steels. Therefore, to obtain this effect, one, or two or more of them may be selected and added. However, the above-described effect cannot be obtained when content of any of these elements is less than 0.001%. On the other hand, a content exceeding 0.05% produces coarse oxides, which reduce the corrosion resistance of steels, therefore, when these elements are added, each of the contents should be between 0.001 and 0.05%. Note that Ca and La are particularly preferable among these elements.
  • the martensitic stainless steel of this invention is used after subjected it to a quenching-tempering heat treatment.
  • This heat treatment may be carried out under ordinary conditions; for example, a water quenching process from the temperature of Ar 3 point or higher and a subsequent tempering process at 600-670°C, for 5-60 minutes, may be performed.
  • a water quenching process from the temperature of Ar 3 point or higher and a subsequent tempering process at 600-670°C, for 5-60 minutes may be performed.
  • the steel of this invention is given a proof stress of 550MPa or more and an excellent toughness.
  • the heat affected zone that comes in contact with the weld metal is brought to a quenched state, and thus it has an extreme hardness. Even in this state, the heat affected zone of the steel, according to this invention, is satisfactory in toughness and corrosion resistance with its rate of martensite being 95% or more, and also has no risk of cracking under cathodic protection. Note that it is, of course, further desirable to subject the steel to a heat treatment (PWHT) for the purpose of softening the heat affected zone, after welding.
  • PWHT heat treatment
  • Steels whose chemical compositions are as shown in FIGS. 2 and 3 were prepared by melting with an ordinary electric furnace and by refining with an argon-oxygen decarburizing furnace (AOD furnace) for desulfurization.
  • the steels were cast into 500-mm-diameter ingots, and billets having 150 mm in diameter were obtained by hot forging the ingots at 1200°C.
  • test materials were prepared from the above described seamless steel pipes.
  • the welding of the pipes of (c) was effected in accordance with ASTM 1G by a gas-tungsten arc welding method (GTAW) or a shield metal arc welding method (SMAW), using a welding material made of a 25Cr duplex stainless steel.
  • GTAW gas-tungsten arc welding method
  • SMAW shield metal arc welding method
  • Test specimens having 4.0-mm-diameter and 20-mm-long parallel portion were obtained from the quenched-tempered material previously described in (b). These test specimens were subjected to a tensile test, at ambient temperature, to obtain 0.2% proof stresses.
  • Test specimens measured 22 mm (w) x 3 mm (t) x 76 mm (1), which were cut out of the as-welded test material previously described in (c), polished with an emery paper No.600, and thereafter degreased and dried, were used. The test specimens were cut out of locations including the welding heat affected zone and the weld metal.
  • test specimens were immersed for 720 hours in a 5%NaCl aqueous solution (the temperature of the solution was 125°C and the flow velocity was 3.5 m/s) in which CO 2 was saturated at a pressure of 30 atm.
  • test specimens cut out of locations including the welding heat affected zone and the weld metal of the as-welded test material previously described in (c) were conducted under the following conditions.
  • the test Nos. 1 to 44 shown in FIGS. 2 and 3 are stainless steels according to this invention.
  • the rates of martensite of these steels as-quenched and their values M calculated from the previously described inequality (1) are shown in FIGS. 4 and 5.
  • the allowable upper limits of hardness (HRC) calculated from the previously described inequality (2), i.e., the values of (0.046-P)/0.0008 are also presented in these drawings.
  • Test Nos. 45 to 62 steels of FIG. 3 were prepared as comparative examples. In these steels, Nos. 53 to 55 steels and Nos. 60 to 62 steels, whose chemical compositions are outside the range specified by this invention are, as shown in FIG. 5, inferior in part or in whole in their properties as welded.
  • Test Nos. 45, 48 to 52 and 56 to 59 steels do not satisfy the condition specified by the previously described inequality (2). That is, their hardnesses after quenching exceed the allowable upper limits calculated from the inequality (2). These steels suffer cracking under cathodic protection.
  • Test Nos. 46 and 47 steels have their M values less than 50 and these steels have low rates of martensite after quenching, and thus poor in toughness, and suffer cracking under cathodic protection.
  • the martensitic stainless steel of this invention is a high-strength, high-toughness steel, excellent in corrosion resistance to carbon dioxide, and has no risk of cracking even if used as welded under cathodic protection.
  • This steel is extremely suitable for use as linepipe for transporting crude oil and the like, which contain carbon dioxide, particularly, while subjected to cathodic protection in the sea. Since this steel requires no heat treatment after welded, it can exhibit the economy of a martensitic stainless steel at a satisfactory level, and thus has a significant practical advantage.

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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 Articles (AREA)
  • Arc Welding In General (AREA)
  • Heat Treatment Of Steel (AREA)
  • Prevention Of Electric Corrosion (AREA)
EP98932588A 1997-07-18 1998-07-17 Acier inoxydable martensitique a haute resistance a la corrosion Expired - Lifetime EP1026273B1 (fr)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
JP19400097 1997-07-18
JP19400097 1997-07-18
PCT/JP1998/003243 WO1999004052A1 (fr) 1997-07-18 1998-07-17 Acier inoxydable en martensite a haute resistance a la corrosion

Publications (3)

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EP1026273A1 true EP1026273A1 (fr) 2000-08-09
EP1026273A4 EP1026273A4 (fr) 2005-12-14
EP1026273B1 EP1026273B1 (fr) 2007-12-19

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EP98932588A Expired - Lifetime EP1026273B1 (fr) 1997-07-18 1998-07-17 Acier inoxydable martensitique a haute resistance a la corrosion

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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 (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2003033754A1 (fr) * 2001-10-18 2003-04-24 Sumitomo Metal Industries, Ltd. Acier inoxydable martensitique
EP1306458A2 (fr) * 2001-10-25 2003-05-02 Mitsubishi Heavy Industries, Ltd. Rotor de turbine en acier allié au 12 chrome
EP1403391A1 (fr) * 2001-06-01 2004-03-31 Sumitomo Metal Industries, Ltd. Acier inoxydable martensitique
EP1584699A1 (fr) * 2002-12-20 2005-10-12 Sumitomo Metal Industries, Ltd. Acier inoxydable martensitique a haute resistance presentant une excellente resistance a la corrosion du gaz carbonique et a la fissuration par corrosion sous contrainte due au sulfure
EP1717328A1 (fr) * 2004-01-30 2006-11-02 JFE Steel Corporation Tube en acier inoxydable martensitique
EP1826285A1 (fr) * 2004-11-19 2007-08-29 Sumitomo Metal Industries, Ltd. Acier inoxydable martensitique

Families Citing this family (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2058412A4 (fr) 2006-08-31 2016-02-17 Nippon Steel & Sumitomo Metal Corp Acier inoxydable martensitique pour structure soudee
EP2322679B1 (fr) * 2008-09-04 2020-02-26 JFE Steel Corporation Tuyau continu en acier inoxydable martensitique pour un tuyau de puits de pétrole et processus de production associé
JP5053213B2 (ja) * 2008-09-12 2012-10-17 新日本製鐵株式会社 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

Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0273279A2 (fr) * 1986-12-30 1988-07-06 Nisshin Steel Co., Ltd. Procédé pour la fabrication de rubans d'acier inoxydable au chrome à structure biphasée ayant une résistance et un allongement élevés ainsi qu'une anisotropie réduite
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

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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
JP2962098B2 (ja) * 1993-04-09 1999-10-12 日本鋼管株式会社 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の製造法
JP3156170B2 (ja) * 1994-07-26 2001-04-16 住友金属工業株式会社 ラインパイプ用マルテンサイト系ステンレス鋼
JP3588380B2 (ja) * 1995-01-30 2004-11-10 新日本製鐵株式会社 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

Patent Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0273279A2 (fr) * 1986-12-30 1988-07-06 Nisshin Steel Co., Ltd. Procédé pour la fabrication de rubans d'acier inoxydable au chrome à structure biphasée ayant une résistance et un allongement élevés ainsi qu'une anisotropie réduite
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

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
PATENT ABSTRACTS OF JAPAN vol. 018, no. 430 (C-1236), 11 August 1994 (1994-08-11) & JP 06 128632 A (NIPPON STEEL CORP), 10 May 1994 (1994-05-10) *
See also references of WO9904052A1 *

Cited By (15)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1403391A1 (fr) * 2001-06-01 2004-03-31 Sumitomo Metal Industries, Ltd. Acier inoxydable martensitique
EP1403391A4 (fr) * 2001-06-01 2004-08-25 Sumitomo Metal Ind Acier inoxydable martensitique
US7361236B2 (en) 2001-06-01 2008-04-22 Sumitomo Metal Industries, Ltd. Martensitic stainless steel
WO2003033754A1 (fr) * 2001-10-18 2003-04-24 Sumitomo Metal Industries, Ltd. Acier inoxydable martensitique
US8157930B2 (en) 2001-10-18 2012-04-17 Sumitomo Metal Industries, Ltd. Martensitic stainless steel
EP1306458A2 (fr) * 2001-10-25 2003-05-02 Mitsubishi Heavy Industries, Ltd. Rotor de turbine en acier allié au 12 chrome
EP1306458A3 (fr) * 2001-10-25 2003-08-27 Mitsubishi Heavy Industries, Ltd. Rotor de turbine en acier allié au 12 chrome
EP1584699A4 (fr) * 2002-12-20 2009-06-03 Sumitomo Metal Ind Acier inoxydable martensitique a haute resistance presentant une excellente resistance a la corrosion du gaz carbonique et a la fissuration par corrosion sous contrainte due au sulfure
EP1584699A1 (fr) * 2002-12-20 2005-10-12 Sumitomo Metal Industries, Ltd. Acier inoxydable martensitique a haute resistance presentant une excellente resistance a la corrosion du gaz carbonique et a la fissuration par corrosion sous contrainte due au sulfure
NO337858B1 (no) * 2002-12-20 2016-07-04 Sumitomo Metal Ind Høyfast martensittisk rustfritt stål utmerket for korrosjonsmotstand mot karbondioksidgass og sulfid spenningskorrosjonssprekkingsmotstand.
EP1717328A1 (fr) * 2004-01-30 2006-11-02 JFE Steel Corporation Tube en acier inoxydable martensitique
EP1717328A4 (fr) * 2004-01-30 2012-03-28 Jfe Steel Corp Tube en acier inoxydable martensitique
US8168008B2 (en) * 2004-01-30 2012-05-01 Jfe Steel Corporation Martensitic stainless steel pipe
EP1826285A4 (fr) * 2004-11-19 2009-04-08 Sumitomo Metal Ind Acier inoxydable martensitique
EP1826285A1 (fr) * 2004-11-19 2007-08-29 Sumitomo Metal Industries, Ltd. Acier inoxydable martensitique

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
WO1999004052A1 (fr) 1999-01-28
CA2296349A1 (fr) 1999-01-28
DE69838879D1 (de) 2008-01-31
NO20000232L (no) 2000-03-06

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