EP0851037B1 - High-chromium and high-nickel alloy with hydrogen sulfide corrosion resistance - Google Patents
High-chromium and high-nickel alloy with hydrogen sulfide corrosion resistance Download PDFInfo
- Publication number
- EP0851037B1 EP0851037B1 EP96917716A EP96917716A EP0851037B1 EP 0851037 B1 EP0851037 B1 EP 0851037B1 EP 96917716 A EP96917716 A EP 96917716A EP 96917716 A EP96917716 A EP 96917716A EP 0851037 B1 EP0851037 B1 EP 0851037B1
- Authority
- EP
- European Patent Office
- Prior art keywords
- hydrogen sulfide
- alloy
- content
- corrosion resistance
- alloys
- 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.)
- Expired - Lifetime
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
- C22C38/18—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
Definitions
- This invention relates to austenitic high-Cr and high-Ni alloys and more particularly, to high-Cr and high-Ni alloys which exhibit a good corrosion resistance when placed in an aqueous solution having a relatively low hydrogen sulfide concentration at a partial pressure of hydrogen sulfide gas of 1 atm., or below.
- the examples of alloys which are employed in environments where they are in contact with hydrogen sulfide-containing liquids include drill pipes, pipes for flow lines from oil wells, oil country tubular goods for oil and natural gas wells, plate members for natural steam power stations, plate members for installation for desulfurization from exhaust gases, and the like. Especially, drilling of oil wells, exploitation and production of natural gas involve corrosive environments which are severe.
- alloys which are to be employed in an environment containing hydrogen sulfide should have a good resistance to stress corrosion cracking.
- Known alloys which are used in an environment such as of a hydrogen sulfide-containing oil well wherein a partial pressure of hydrogen sulfide is as high as approximately 10 atm. include Ni-Cr-Mo-Fe Ni-based alloys which contain Ni in amounts as great as 30 -50% (Japanese Laid-open Patent Application Nos. 57-131340, 57-134544 and 57-134545).
- Japanese Laid-open Patent Application No. 57-131340 proposes an alloy which comprises, aside from Ni, Cr, Mo and W, Cu and Co, if necessary, in order to improve the resistance to stress corrosion cracking.
- alloys for oil wells are so designed as to improve the corrosion resistance to hydrogen sulfide including a resistance to stress corrosion cracking. More particularly, the corrosion resistance to hydrogen sulfide is greatly influenced by the content of hydrogen sulfide present in raw oil and the temperature of the raw oil. Accordingly, when used in such an environment of hydrogen sulfide as having set out above, the alloy is so designed that a corrosion-resistant film is formed on the surfaces of the alloy.
- the corrosion-resistant film should have a two-layer structure including an outer layer consisting of a Ni sulfide film and an inner layer consisting of a Cr oxide film. In order to facilitate the growth of the inner layer of the Cr oxide film, at least one of Mo and W is incorporated in the alloy.
- the reason why the corrosion-resistant film is designed to have a double-layer structure is so that hydrogen sulfide is prevented from entering into the inner layer by means of the outer layer of the Ni sulfide film thereby preventing the breakage of the Cr oxide inner film with the hydrogen sulfide.
- the Cr oxide inner film is able to suppress the dissolution of the alloy and thus, acts to improve the corrosion resistance, ensuring a good corrosion resistance to hydrogen sulfide.
- the invention has for its object the provision of a high-Cr and high-Ni alloy which overcomes the problems involved in the prior art, which is imparted with good corrosion resistance to hydrogen sulfide under environmental conditions of a partial pressure of hydrogen sulfide of 1 atm., or below and a temperature of about 150°C, and which is low in cost.
- the high-Cr and high-Ni alloy of the invention has a good corrosion resistance to hydrogen sulfide under environmental conditions of a partial pressure of hydrogen sulfide of 1 atm., or below and a temperature of about 150 °C.
- the alloy is free of Mo and W which are expensive elements and is thus low in cost, and is mass-producible.
- the alloy of the invention has the following chemical composition on the basis of percent by weight: Si: 0.05 - 1.0% Mn: 0.1 - 1.5% Cr: 20 - 30% Ni: 20 - 40% sol.
- the contents of C, P and S in the incidental impurities should, respectively, be 0.05% or below, 0.03% or below and 0.01% or below.
- REM, Y, Mg and Ca do not have to be added at all, however, if these elements are used, it is sufficient to add at least one of REM, Y, Mg and Ca.
- Preferable contents of these elements are as follows: REM 0.001 - 0.10% Y 0.001 - 0.20% Mg 0.001 - 0.10% Ca 0.001 - 0.10%
- Si is an element necessary for deoxidation of molten steel at the time of refining.
- the content should be 0.05% or above.
- the content of Si is in the range of 0.05 - 1.0%, preferably 0.2 - 0.5%.
- Mn is an element necessary for deoxidation of molten steel.
- the content of Mn should be 0.1% or above.
- the content of Mn is in the range of 0.1 - 1.5%, preferably 0.5 - 0.75%.
- Cr is an element which is effective for improving the corrosion resistance to hydrogen sulfide (especially, resistance to stress corrosion cracking) in co-existence with other major components of Ni and N. If the content is less than 20%, such an effect cannot be obtained satisfactorily. Cr tends to worsen hot workability. If the content is reduced to a range of less than 20%, no significant effect of improving the hot workability may be obtained. On the other hand, where the content of Cr exceeds 30%, any further improvement of the corrosion resistance to hydrogen sulfide cannot be attained using a higher content of Cr within the above range. Moreover, in the case where the content of Cr exceeds 30%, good hot workability cannot be expected even if the content of S is reduced. Accordingly, the content of Cr is in the range of 20 - 30%, preferably 22 - 27%.
- Ni is effective in improving the corrosion resistance to hydrogen sulfide. This effect is shown when the content of Ni is 20% or above. However, when the content exceeds 40%, any further effect is not expected using a higher content within the above range. Where Ni (which is expensive) is contained in amounts higher than required, the resultant alloy becomes expensive, thus being economically poor. Accordingly, the content of Ni is in the range of 20 - 40%, preferably 22 - 30%.
- Al like Si and Mn, is an element necessary for the deoxidation of molten steel.
- the deoxidation effect is shown when the content of sol. Al (i.e.. Al contained in alloy and soluble in hydrochloric acid) is 001% or above.
- the content of sol. Al exceeds 0.3%, hot workability is impeded. Accordingly, the content of sol. Al is in the range of 0.01 - 0.3%, preferably 0.1 - 0.15%.
- Cu is the most important element for the invention which constitutes a characteristic feature of the high-Cr and high-Ni alloy of the invention.
- Cu serves to remarkably improve the corrosion resistance to hydrogen sulfide in an environment of hydrogen sulfide gas whose partial pressure is as low as 1 atm., or below. In order to achieve this improvement, 0.5% or above of Cu should be present. However, if Cu is added in excess of 5.0%, no further improvement is expected. Additionally, when the content exceeds 5.0%, hot workability is degraded. Accordingly, the content of Cu is in the range of 0.5 - 5.0%, preferably 1.0 - 3.0%.
- the alloy of the invention may contain one or more of REM (rare earth elements), Y, Mg and Ca in order to improve hot workability. These elements are effective in improving hot workability as in the case where the alloy is hot-worked under severe conditions.
- each element is less than 0.001%, any significant effect of improving the hot workability is not obtained.
- contents of the respective elements exceed the defined upper limits, coarse oxides are formed, thus impeding hot workability.
- Major incidental impurities include C, P and S.
- the content of C should preferably be not more than 0.05%.
- the content of C exceeds 0.05% and Nb or V co-exist as an impurity, coarse carbide is formed along with the co-existing element, and Cr carbide is formed at grain boundaries in a contiguous state.
- the formation of these carbides causes Cr depletion zones, so that stress corrosion cracking is liable to occur along the grain boundaries.
- the upper limit of the content of C is determined at 0.05%, and the content of C is preferably 0.03% or below.
- the content of P exceeds 0.03, the susceptibility to stress corrosion cracking in an environment of hydrogen sulfide increases. Accordingly, the upper limit is 0.03%.
- the content is preferably 0.02% or below.
- the content of S When the content of S exceeds 0.01%, hot workability is considerably impeded. Accordingly, the content of S is defined to be not more than 0.01. If the content of S is so great, hot workability is considerably impeded as set out above. In this connection, if the content of S is as low as about 0.0007% or below, hot workability is improved. Accordingly, if good hot workability under severe conditions is essential, it is preferred to reduce the content of S to a level of 0.0007% or below.
- the incidental impurity elements may further comprise, aside from the above-stated C, P and S, 0.10% or below of B, Sn, As, Sb, Bi, Pb and Zn.
- the impurities present in such amounts as set out above exerts little influence on the characteristics of the alloy of the invention.
- the alloy of the invention and articles such as alloy pipes made of the alloy of the invention as a base metal can be made using manufacturing apparatus and methods which are employed for ordinary commercial manufacture. For instance, melting of the alloy may be conducted by utilizing electric furnaces, argon-oxygen decarburization furnaces (AOD furnaces), vacuum-oxygen decarburization furnaces (VOD furnaces) and the like.
- the molten metal may be cast into ingots or may be cast into rod-shaped billets according to a continuous casting technique.
- an extrusion pipe making processes such as the Ugine Sejournet process, or the Mannesman pipe making process.
- the pipe making conditions such as a heating temperature of billets prior to pipe making may be those of the case using conventional high-Cr and high-Ni alloys.
- each ingot was heated to 1250°C and subjected to hot forging at 1200°C to obtain a rod with a diameter of 150 mm.
- the rod was cut into pieces having a length of 1000 mm to obtain billets for extrusion pipe making.
- the billet was shaped into a pipe having a diameter of 60 mm, a thickness of 5 mm and a length of about 20 m according to the Ugine Sejournet hot extrusion pipe making process. Only one pipe was made for each alloy indicated in Table 1.
- a sample piece was taken out from each pipe and subjected to a corrosion test in a hydrogen sulfide environment to check corrosion resistance to hydrogen sulfide.
- the corrosion test in the hydrogen sulfide environment was conducted in the following manner. It should be noted that the hot workability was evaluated in terms of the presence (symbol "x” in Table 1) or the absence (symbol "o” in Table 1) of defects through visual observation of defects on the inner surfaces of a pipe obtained by extrusion pipe making. Two sample pieces for each alloy were used for the corrosion test in the hydrogen sulfide environment.
- Table 1 the results of the corrosion test in the hydrogen sulfide environment and the results of evaluation of the hot workability are shown in Table 1. With respect to the corrosion resistance to hydrogen sulfide, where either pitting corrosion or cracking was not observed at all, this resistance is indicated as "o”. Where either of pitting corrosion or cracking was observed, this is indicated as "x”.
- alloys of the inventive example (alloy Nos. 1 - 12), wherein the chemical compositions are within the range of the invention, were not recognized with respect to the pitting corrosion and the cracking in the corrosion test in the hydrogen sulfide environment. Moreover, no defect on the inner surface of the pipes obtained after pipe making was found.
- the alloys of the invention are excellent in the corrosion resistance to hydrogen sulfide and hot workability.
- the hot workability is better than that of the case where such an element is not added at all.
- Comparative alloy Nos. 16 - 18 contain either or both of Mo and W and those alloys have been hitherto accepted as showing good corrosion resistance to hydrogen sulfide in an environment where a partial pressure of hydrogen sulfide gas is high. Nevertheless, as will be apparent from this example, these alloys were poor in corrosion resistance to hydrogen sulfide. These results revealed that where the partial pressure of hydrogen sulfide gas was low, like those conditions of this example, Mo and W did not serve to improve the corrosion resistance to hydrogen sulfide.
- alloy No. 2 of the invention was further subjected to another corrosion test in the hydrogen sulfide environment where a partial pressure of hydrogen gas in the testing atmosphere was set at 0.8 atm., with the other conditions being the same as in Example 1.
- a partial pressure of hydrogen gas in the testing atmosphere was set at 0.8 atm.
- the inventive alloy was excellent in corrosion resistance to hydrogen sulfide.
- the alloys of the invention exhibit an excellent corrosion resistance to hydrogen sulfide in an environment where a partial pressure of hydrogen sulfide gas is as low as about 1 atm., or below, along with good hot workability. Since it is not necessary to add Mo and W(which are expensive), the cost of raw materials for alloys making decreases. Moreover, the alloys of the invention can be made by use of manufacturing apparatus and method which have been conventionally used for the manufacture, thus making it possible to mass-produce the alloy inexpensively.
- the alloy of the invention is employed, for example as a material for pipes which are in contact with a hydrogen sulfide-containing corrosive fluid produced from oil wells, good corrosion resistance is ensured.
- the alloy of the invention thus has very high practical value for use as a material which is used in an environment where a partial pressure of hydrogen sulfide gas is relatively low.
Description
Si: | 0.05 - 1.0% |
Mn: | 0.1 - 1.5% |
Cr: | 20 - 30% |
Ni: | 20 - 40% |
sol. | Al: 0.01 - 0.3% |
Cu: | 0.5 - 5.0% |
REM: | 0 - 0.10% |
Y: | 0 - 0.20% |
Mg: | 0 - 0.10% |
Ca: | 0 - 0.10% |
Balance: | Fe and incidental impurities |
REM | 0.001 - 0.10% |
Y | 0.001 - 0.20% |
Mg | 0.001 - 0.10% |
Ca | 0.001 - 0.10% |
with a 0.25 mm U-shaped notch (made at the center of a test piece)
(the stress was added by 10 mm at the central portion of the test piece according to a four-point supporting method.)
Claims (6)
- A high-Cr and high-Ni alloy having good corrosion resistance to hydrogen sulfide, which has the following chemical composition on the basis of percent by weight:
Si: 0.05 - 1.0%; Mn: 0.1 - 1.5%; Cr: 20 - 30%; Ni: 20 - 40%; sol. Al: 0.01 - 0.3%; Cu: 0.5 - 5.0%; REM: 0 - 0.10%; Y: 0 - 0.20%; Mg: 0 - 0.10%; Ca: 0 - 0.10%; and balance: Fe and incidental impurities, - A high-Cr and high-Ni alloy according to Claim 1, wherein said alloy contains, on the basis of percent by weight, at least one of REM: 0.001 - 0.10%, Y: 0.001 - 0.20%, Mg: 0.001 - 0.10%, and Ca: 0.001 - 0.10%.
- A high-Cr and high-Ni alloy according to Claim 1 or 2, wherein, on the basis of percent by weight, the content of Cu ranges between 1.0 - 3.0%.
- A high-Cr and high-Ni alloy according to Claim 1 or 2, wherein, on the basis of percent by weight, the content of Cr ranges between 22 - 27%.
- A high-Cr and high-Ni alloy according to Claim 1 or 2, wherein, on the basis of percent by weight, the content of Ni ranges between 22 - 30%.
- A high-Cr and high-Ni alloy according to Claim 1 or 2, wherein, on the basis of percent by weight, the content of Cu ranges between 1.0 - 3.0%, the content of Cr ranges between 22 - 27%, and the content of Ni ranges between 22 - 30%.
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
PCT/JP1996/001672 WO1997048830A1 (en) | 1996-06-17 | 1996-06-17 | High-chromium and high-nickel alloy with hydrogen sulfide corrosion resistance |
CA002212346A CA2212346C (en) | 1996-06-17 | 1996-06-17 | Hydrogen sulfide corrosion resistant high-cr and high ni alloys |
Publications (3)
Publication Number | Publication Date |
---|---|
EP0851037A1 EP0851037A1 (en) | 1998-07-01 |
EP0851037A4 EP0851037A4 (en) | 1999-12-01 |
EP0851037B1 true EP0851037B1 (en) | 2002-09-04 |
Family
ID=56289695
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP96917716A Expired - Lifetime EP0851037B1 (en) | 1996-06-17 | 1996-06-17 | High-chromium and high-nickel alloy with hydrogen sulfide corrosion resistance |
Country Status (2)
Country | Link |
---|---|
EP (1) | EP0851037B1 (en) |
AU (1) | AU696908B2 (en) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2007124996A1 (en) * | 2006-04-27 | 2007-11-08 | Evonik Degussa Gmbh | Reaction vessel for the production of hydrogen sulphide |
Families Citing this family (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
SE527319C2 (en) | 2003-10-02 | 2006-02-07 | Sandvik Intellectual Property | Alloy for high temperature use |
US20080196797A1 (en) * | 2007-02-16 | 2008-08-21 | Holmes Kevin C | Flow formed high strength material for safety systems and other high pressure applications |
Family Cites Families (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US3926620A (en) * | 1970-07-14 | 1975-12-16 | Sumitomo Metal Ind | Low carbon ni-cr alloy steel having an improved resistance to stress corrosion cracking |
US4816217A (en) * | 1984-03-16 | 1989-03-28 | Inco Alloys International, Inc. | High-strength alloy for industrial vessels |
US4816218A (en) * | 1984-11-01 | 1989-03-28 | Inco Alloys International, Inc. | Process of using an iron-nickel-chromium alloy in an oxidation attacking environment |
DE3716665A1 (en) * | 1987-05-19 | 1988-12-08 | Vdm Nickel Tech | CORROSION RESISTANT ALLOY |
JPH03103842A (en) * | 1989-09-19 | 1991-04-30 | Seiko Epson Corp | Projection type liquid crystal display device |
KR20050057098A (en) * | 2002-09-05 | 2005-06-16 | 코닌클리케 필립스 일렉트로닉스 엔.브이. | Recordable optical record carrier comprising two sub-grooves |
-
1996
- 1996-06-17 AU AU60175/96A patent/AU696908B2/en not_active Expired
- 1996-06-17 EP EP96917716A patent/EP0851037B1/en not_active Expired - Lifetime
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2007124996A1 (en) * | 2006-04-27 | 2007-11-08 | Evonik Degussa Gmbh | Reaction vessel for the production of hydrogen sulphide |
Also Published As
Publication number | Publication date |
---|---|
EP0851037A4 (en) | 1999-12-01 |
AU6017596A (en) | 1998-01-07 |
AU696908B2 (en) | 1998-09-24 |
EP0851037A1 (en) | 1998-07-01 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
EP0545753B1 (en) | Duplex stainless steel having improved strength and corrosion resistance | |
US6623869B1 (en) | Metal material having good resistance to metal dusting | |
EP2725112B1 (en) | Carburization-resistant metal material and uses of the carburization-resistant metal material | |
WO2018020886A1 (en) | High strength seamless stainless steel pipe for oil wells and production method therefor | |
AU2006311988B2 (en) | High strength corrosion resistant alloy for oil patch applications | |
WO2017010036A1 (en) | High strength seamless stainless steel pipe and manufacturing method therefor | |
WO2018155041A1 (en) | High strength seamless stainless steel pipe for oil well and production method therefor | |
US8163233B2 (en) | Martensitic stainless steel for welded structures | |
JP6156609B1 (en) | High strength stainless steel seamless steel pipe for oil well and method for producing the same | |
KR20100060026A (en) | Austenitic stainless steel | |
EP2194152B1 (en) | High-strength cr-ni alloy product and seamless oil well pipes made by using the same | |
MXPA04009375A (en) | Low alloy steel. | |
JP3608743B2 (en) | Martensitic stainless steel with excellent hot workability and resistance to sulfide stress cracking | |
JP3650951B2 (en) | Seamless steel pipe for oil wells with excellent stress corrosion cracking resistance | |
NO336990B1 (en) | Martensitic stainless steel | |
GB2049729A (en) | Method for producing steel plate having excellent resistance to hydrogen induced cracking | |
JP2004197150A (en) | Metal dusting resistant metallic material having excellent high temperature strength | |
EP0851037B1 (en) | High-chromium and high-nickel alloy with hydrogen sulfide corrosion resistance | |
US5879619A (en) | Hydrogen sulfide corrosion resistant high-Cr and high-Ni alloys | |
CA2212346C (en) | Hydrogen sulfide corrosion resistant high-cr and high ni alloys | |
JP7207557B2 (en) | Stainless seamless steel pipe for oil country tubular goods and manufacturing method thereof | |
JPH07136748A (en) | Production of high corrosion resistance steel for resistance welded steel tube | |
CN111344426A (en) | Duplex stainless steel and method for producing duplex stainless steel | |
JP3933089B2 (en) | Low alloy steel | |
JP3470418B2 (en) | High strength austenitic alloy with excellent seawater corrosion resistance and hydrogen sulfide corrosion resistance |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
PUAI | Public reference made under article 153(3) epc to a published international application that has entered the european phase |
Free format text: ORIGINAL CODE: 0009012 |
|
17P | Request for examination filed |
Effective date: 19980422 |
|
AK | Designated contracting states |
Kind code of ref document: A1 Designated state(s): DE DK FR GB IT SE |
|
A4 | Supplementary search report drawn up and despatched |
Effective date: 19991020 |
|
AK | Designated contracting states |
Kind code of ref document: A4 Designated state(s): DE DK FR GB IT SE |
|
GRAG | Despatch of communication of intention to grant |
Free format text: ORIGINAL CODE: EPIDOS AGRA |
|
17Q | First examination report despatched |
Effective date: 20010904 |
|
GRAG | Despatch of communication of intention to grant |
Free format text: ORIGINAL CODE: EPIDOS AGRA |
|
GRAH | Despatch of communication of intention to grant a patent |
Free format text: ORIGINAL CODE: EPIDOS IGRA |
|
GRAH | Despatch of communication of intention to grant a patent |
Free format text: ORIGINAL CODE: EPIDOS IGRA |
|
GRAA | (expected) grant |
Free format text: ORIGINAL CODE: 0009210 |
|
AK | Designated contracting states |
Kind code of ref document: B1 Designated state(s): DE DK FR GB IT SE |
|
REG | Reference to a national code |
Ref country code: GB Ref legal event code: FG4D |
|
REF | Corresponds to: |
Ref document number: 69623488 Country of ref document: DE Date of ref document: 20021010 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: DK Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20021204 |
|
ET | Fr: translation filed | ||
PLBE | No opposition filed within time limit |
Free format text: ORIGINAL CODE: 0009261 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT |
|
26N | No opposition filed |
Effective date: 20030605 |
|
REG | Reference to a national code |
Ref country code: GB Ref legal event code: 732E Free format text: REGISTERED BETWEEN 20131010 AND 20131016 |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: TP Owner name: NIPPON STEEL & SUMITOMO METAL CORPORATION, JP Effective date: 20131108 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R082 Ref document number: 69623488 Country of ref document: DE Representative=s name: BOCKHORNI & KOLLEGEN PATENT- UND RECHTSANWAELT, DE |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R082 Ref document number: 69623488 Country of ref document: DE Representative=s name: BOCKHORNI & KOLLEGEN PATENT- UND RECHTSANWAELT, DE Effective date: 20140402 Ref country code: DE Ref legal event code: R081 Ref document number: 69623488 Country of ref document: DE Owner name: NIPPON STEEL & SUMITOMO METAL CORPORATION, JP Free format text: FORMER OWNER: SUMITOMO METAL INDUSTRIES, LTD., OSAKA, JP Effective date: 20140402 |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: PLFP Year of fee payment: 20 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: DE Payment date: 20150609 Year of fee payment: 20 Ref country code: GB Payment date: 20150617 Year of fee payment: 20 Ref country code: SE Payment date: 20150611 Year of fee payment: 20 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: FR Payment date: 20150608 Year of fee payment: 20 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: IT Payment date: 20150625 Year of fee payment: 20 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R071 Ref document number: 69623488 Country of ref document: DE |
|
REG | Reference to a national code |
Ref country code: GB Ref legal event code: PE20 Expiry date: 20160616 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: GB Free format text: LAPSE BECAUSE OF EXPIRATION OF PROTECTION Effective date: 20160616 |
|
REG | Reference to a national code |
Ref country code: SE Ref legal event code: EUG |