[go: up one dir, main page]

EP0998591B1 - Tube de canalisation et acier de construction produits par coulee continue a grande vitesse - Google Patents

Tube de canalisation et acier de construction produits par coulee continue a grande vitesse Download PDF

Info

Publication number
EP0998591B1
EP0998591B1 EP98921241A EP98921241A EP0998591B1 EP 0998591 B1 EP0998591 B1 EP 0998591B1 EP 98921241 A EP98921241 A EP 98921241A EP 98921241 A EP98921241 A EP 98921241A EP 0998591 B1 EP0998591 B1 EP 0998591B1
Authority
EP
European Patent Office
Prior art keywords
steel
linepipe
steels
manganese
cracking
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
Application number
EP98921241A
Other languages
German (de)
English (en)
Other versions
EP0998591A1 (fr
Inventor
John Malcolm Gray
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Cbmm Technology Suisse Sa
Original Assignee
American Cast Iron Pipe Co
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
Priority claimed from US08/879,331 external-priority patent/US5993570A/en
Application filed by American Cast Iron Pipe Co filed Critical American Cast Iron Pipe Co
Publication of EP0998591A1 publication Critical patent/EP0998591A1/fr
Application granted granted Critical
Publication of EP0998591B1 publication Critical patent/EP0998591B1/fr
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

Images

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
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium

Definitions

  • the present invention is directed to a high-strength linepipe and structural steel that is resistant to hydrogen-induced cracking (HIC) in sour service.
  • HIC hydrogen-induced cracking
  • High strength linepipe for this sour service has heretofore been produced from low carbon-manganese steel, and strengthened by the addition of niobium and/or vanadium.
  • Manganese levels for such steels have typically been in the range of 0.90 to 1.20 weight percent, when it is expected that the linepipe will be used in the most severe service conditions.
  • manganese levels in the aforesaid range of 0.90-1.20 weight percent will be referred to as being "relatively high" manganese contents for low carbon-manganese steels.
  • JP2267241 discloses a steel for line pipe applications having a high corrosion resistance.
  • steels within the above ranges demonstrate excellent impact strengths (high energy impact valves) and Chapry V-notch transition temperatures.
  • FIG. 1 is a graph depicting the results of a NACE TM0284-96 stepwise cracking test, plotting the weight percent of manganese against the yield strengths of the samples.
  • a composition that yields a high-strength, high toughness steel, without relying on the use of a relatively high manganese content to provide the relatively high strength characteristics is provided.
  • the manganese content in the steels according to the present invention can be very low, such as 0.15 weight percent or less, thereby virtually eliminating manganese segregation and the tendency of the steel to form manganese sulfide. Further, the low manganese-to-sulfur ratio present in the steels, which is preferably approximately 3,000:1 to 5,000:1, minimizes the tendency of any MnS that may be formed, to form into stringers.
  • the steel of the present invention relies on the addition of niobium to provide the high strength characteristics, and, optionally, any one or more of vanadium, molybdenum, chromium, boron, copper and nickel, used in combination with the niobium. These elements combine to lower the austenite-to-ferrite ( ⁇ ) transformation temperature and to prevent the formation of coarse ferrite grains at the very low manganese and carbon levels employed in the steel. The benefits derived from these strengthening mechanisms are enhanced or maximized by water cooling the steel after the strip or plate rolling.
  • the steel can be more consistently produced due to the reliance on niobium, and optionally also vanadium, precipitation hardening, and on control of the austenite to ferrite transformation temperature.
  • the normally- experienced variations in mechanical properties in coiled product resulting from coiling temperature variations and head-to-tail (leading end to trailing end) temperature variations are minimized or eliminated by the strengthening elements (principally niobium) and mechanisms used in producing this steel.
  • the steel of the present invention can be treated with calcium or rare earth metals for sulfide inclusion shape control, as in conventional practice.
  • the use of titanium reduces manganese sulfide plasticity, especially at low manganese and nitrogen contents, and when the manganese-to-sulfur ratio is very low, which are both features of the steel of the present invention.
  • the very-low carbon and manganese contents in the steel maximize delta (6) ferrite formation during solidification and facilitate solute redistribution. Tolerance for phosphorous impurity is increased and there is a virtual absence of pearlite banding.
  • the steels can be rolled on plate mills or strip mills using either direct hot charging or conventional reheating practices.
  • the manganse : sulphur ratio is between 3,000 : 1 and 5,000 : 1.
  • Steels having compositions within the ranges set forth above can be cast at high castings speeds, in the range of 0.8 to 3.0 m/min, that are desired for production efficiency, by conventional (200 to 300 mm thick) or thin (50-90 mm thick) slab caster.
  • the steels cast at such high speeds exhibit low segregation intensity, and, as noted previously, high strength, high toughness, and resistance to degradation or failure in sour service applications.
  • the steels of the present invention have the notable advantage of providing excellent resistance to stepwise cracking and sulfide stress cracking even when calcium and/or copper are not employed in the steel. Further, the high strength properties can be obtained in the absence of molybdenum. When molybdenum is present within the stated range, the high strength and excellent resistance to stepwise cracking and sulfide stress corrosion cracking can be obtained in the absence of calcium.
  • Table V presents the results of the Charpy v-notch impact tests conducted on triplicate samples prepared from steel heats A-D, with the Charpy test samples being 2/3 of the standard specimen size. As can be seen in the table, the fracture energies are very high, even at sub-zero (°F.) temperatures, with Steel Heat B demonstrating remarkable impact resistance down to -80°F.
  • Table VI below presents data from drop weight tear testing, as well as the 50% and 85% values for brittle/ductile fracture transition temperatures as demonstrated in the Charpy V-notch impact tests and in the drop weight tear tests (DWTT). Again, the steels demonstrate excellent notch toughness characteristics with the pipe made from Heat B demonstrating truly out standing results.
  • yield strengths and ultimate tensile strengths of tensile specimens from heats A-D, as well as from heats E-G are reported in Table VII below.
  • the desired range for yield strength is about 248-552 MPa (36-80 ksi)
  • the desired range of ultimate tensile strengths is 310-621 MPa (45-90 ksi). These would be considered as high-strength steels, as the term "high strength" is used herein.
  • Resistance to sulfide stress cracking is normally assessed, in accordance with the level of skill in the art, by the test methods set forth in NACE Standard TM0177.
  • tests were conducted on heats E-G in accordance with this NACE standard, modified to include a test period of 96 hours at 80% percent of the specified minimum yield strength (SMYS). No cracking was evidenced in these tests, indicating an acceptable level of resistance to sulfide stress cracking. It is notable that these heats tested for resistance to sulfide stress cracking had manganese contents toward the upper end of the range of manganese content desired for the present invention. It is expected that steels having lower manganese contents, in the more preferred range set forth in Table III above, will exhibit the same or even an improved level of resistance to sulfide stress cracking.
  • the examples of the invention are those having a manganese content in the range of about 0.10-0.60 wt.% and having a yield strength in the range of about 379-483 MPa (55-70 ksi). Steels meeting those criteria fall within the shaded region of FIG. 1. Because steels having both 0.60 wt.% manganese and a yield strength of 483 MPa (70 ksi) would fall close to the crack/no crack boundary 100, a more conservative set of criteria would include a decreasing maxinun yield strength from 483 MPa (70 ksi) to 469 MPa (68 ksi) maximum as the manganese content increases from 0.50 wt.% to 0.60 wt.t.
  • FIG. 1 results presented in FIG. 1 are based on tests conducted using the Solution A (pH 5.2) standard test solution defined in NACE TM 0284-96. Additional tests were conducted in accordance with the standard, but using the lower pH, more severely corrosive, Solution B defined in the standard. Samples from heats A-D, as well as four other samples falling within the steel composition of the present invention, were tested using Solution B in the NACE test, and all samples passed the test, demonstrating a complete absence of stepwise cracking, even under these more severely corrosive conditions.
  • Solution A pH 5.2
  • API American Petroleum Institute
  • tubular products such as line pipe
  • API Specification 5LX is directed to high-strength welded or seamless steel line pipe for oil or gas transmission, a use for which the steel of the present invention is especially well suited.
  • API 5LX is hereby incorporated by reference in its entirety. Included in API 5LX are several material grades, such as X46, X52, X56, X60, X65 and X70. The numbers following the "X" in these designations are the minimum yield strengths in MPa (ksi) for materials of the respective grades. Each material grade further has certain conipositional requirements and tensile strength requirements.
  • the API 5LX material grades are specified when alloy steel pipe is to be used in gas or sour gas service.
  • Steels of the present invention having compositions falling within the ranges set forth in Table I meet all compositional limitations set forth in API 5LX, and, as can be seen by the yield strength results set forth in Table VII, steels can be produced to meet the requirements of all grades up through the X70 grade. Accordingly, the steels made in accordance with the present invention can be used as line pipe virtually across the entire spectrum of the API 5LX linepipe specification. Further, with the demonstrated increased resistance to hydrogen-induced cracking over steels currently supplied under the 5LX specification, the steels of the present invention will be especially well suited for use as 5LX linepipe (e.g. X52) in instances where, in addition to the material grade specification, requirements for resistance to hydrogen-induced cracking are specified or imposed.
  • 5LX linepipe e.g. X52
  • the low carbon/low manganese steels of the present invention possess the desirable properties for use in linepipe applications, especially in sour gas service. Because of its high strength and toughness, the steel is also well suited to being used as structural steel.
  • the particular embodiments and compositions discussed above are for illustrative purposes, and the invention is not intended to be limited to specific examples. Accordingly, reference should be made to the appended claims to determine the scope of the invention.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Articles (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
  • Rigid Pipes And Flexible Pipes (AREA)

Claims (6)

  1. Acier à haute résistance comprenant : Elément Gamme (% en poids) C 0,015 à 0,080 Mn 0,10 à 0,55 Nb 0,005 à 0,15 Ti 0,005 à 0,030 N 0,001 à 0,01 et facultativement Cr ≤ 0,50 Ni ≤ 0,95 Mo ≤ 0,60 B ≤ 0,0025 S ≤ 0,008 Ca ≤ 0,005 Si ≤ 0,210 P ≤ 0,025 Cu ≤ 0,25 Al ≤ 0,063 V ≤ 0,007
    le reste étant du fer et des impuretés, l'acier ayant une microstructure sensiblement dépourvue de ferrite à gros grains, une limite d'élasticité dans la gamme de 36 à 80 ksi et étant résistant à une dégradation par H2S.
  2. Acier à haute résistance selon la revendication 1, et comprenant : Elément Gamme (% en poids) C 0,015 à 0,050 Mn 0,10 à 0,55 Nb 0,03 à 0,09 Ti 0,015 à 0,025 N 0,001à 0,005 Mo ≤ 0,10 B ≤ 0,0025 S ≤ 0,003 Ca ≤ 0,0025 P ≤ 0,008
    le reste étant du fer et des impuretés, l'acier ayant une microstructure sensiblement dépourvue de ferrite à gros grains, une limite d'élasticité dans la gamme de 36 à 80 ksi et étant résistant à une dégradation par H2S.
  3. Procédé de formation d'un acier, le procédé comprenant la coulée en continu d'un acier ayant une composition selon l'une quelconque des revendications précédentes à une vitesse de coulée comprise entre 0,8 et 3,0 m/min, moyennant quoi l'acier présente une faible intensité de ségrégation de manganèse et une résistance à la fissuration par étape dans un environnement de H2S.
  4. Tube de canalisation formé à partir d'un acier à haute résistance comprenant : Elément Gamme (% en poids) C 0,015 à 0,080 Mn 0,10 à 1,0 Nb 0,005 à 0,15 Ti 0,005 à 0,030 N 0,001 à 0,01 et facultativement Cr ≤ 0,50 Ni ≤ 0,95 Mo ≤ 0,60 B ≤ 0,0025 S ≤ 0,008 Ca ≤ 0,005 Si ≤ 0,210 P ≤ 0,025 Cu ≤ 0,25 Al ≤ 0,063 V ≤ 0,007
    le reste étant du fer et des impuretés.
  5. Tube de canalisation selon la revendication 4, dans lequel l'acier comprend : Elément Gamme (% en poids) C 0,015 à 0,050 Mn 0,10 à 0,55 Nb 0,03 à 0,09 Ti 0,015 à 0,025 Mo ≤ 0,10 B ≤ 0,0009 S ≤ 0,003 N 0,001 à 0,005 Ca ≤ 0,0025 P ≤ 0,008
    le reste étant du fer et des impuretés.
  6. Tube de canalisation selon la revendication 4 ou la revendication 5, dans lequel l'acier a une limite d'élasticité de 36 à 80 Ksi, et le tube de canalisation satisfait les critères de la spécification 5LX de l'API.
EP98921241A 1997-05-19 1998-05-15 Tube de canalisation et acier de construction produits par coulee continue a grande vitesse Expired - Lifetime EP0998591B1 (fr)

Applications Claiming Priority (7)

Application Number Priority Date Filing Date Title
US4694197P 1997-05-19 1997-05-19
US46941P 1997-05-19
US4869497P 1997-06-06 1997-06-06
US48694P 1997-06-06
US08/879,331 US5993570A (en) 1997-06-20 1997-06-20 Linepipe and structural steel produced by high speed continuous casting
US879331 1997-06-20
PCT/US1998/010034 WO1998053110A1 (fr) 1997-05-19 1998-05-15 Tube de canalisation et acier de construction produits par coulee continue a grande vitesse

Publications (2)

Publication Number Publication Date
EP0998591A1 EP0998591A1 (fr) 2000-05-10
EP0998591B1 true EP0998591B1 (fr) 2006-03-29

Family

ID=27367024

Family Applications (1)

Application Number Title Priority Date Filing Date
EP98921241A Expired - Lifetime EP0998591B1 (fr) 1997-05-19 1998-05-15 Tube de canalisation et acier de construction produits par coulee continue a grande vitesse

Country Status (8)

Country Link
EP (1) EP0998591B1 (fr)
JP (1) JP2002515093A (fr)
KR (1) KR100540686B1 (fr)
AT (1) ATE321897T1 (fr)
BR (1) BR9809852A (fr)
CA (1) CA2289084C (fr)
DE (1) DE69834031T2 (fr)
WO (1) WO1998053110A1 (fr)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20220299425A1 (en) * 2021-03-19 2022-09-22 Saudi Arabian Oil Company Development of Control Samples to Enhance the Accuracy of HIC Testing
US11788951B2 (en) 2021-03-19 2023-10-17 Saudi Arabian Oil Company Testing method to evaluate cold forming effects on carbon steel susceptibility to hydrogen induced cracking (HIC)

Families Citing this family (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR100584748B1 (ko) * 2001-12-22 2006-05-30 주식회사 포스코 내 수소 유기 균열성이 우수한 라인 파이프용 연주 주편
JP4613579B2 (ja) * 2004-10-25 2011-01-19 Ｊｆｅスチール株式会社 鋼の鋳造方法
AU2006214807B2 (en) * 2005-02-21 2011-11-03 Bluescope Steel Limited Linepipe steel
CN101142336A (zh) 2005-02-21 2008-03-12 布卢斯科普钢铁有限公司 管线钢
US20080226396A1 (en) * 2007-03-15 2008-09-18 Tubos De Acero De Mexico S.A. Seamless steel tube for use as a steel catenary riser in the touch down zone
KR101174970B1 (ko) 2010-02-26 2012-08-23 현대제철 주식회사 라인파이프용 고강도 강판 및 그 제조 방법

Family Cites Families (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5980752A (ja) * 1982-10-28 1984-05-10 Nippon Kokan Kk <Nkk> 硫化水素環境で溶接部の耐水素割れ性及び耐硫化物応力腐食割れ性に優れた鋼
JP2655911B2 (ja) * 1989-04-07 1997-09-24 川崎製鉄株式会社 耐水素誘起割れ性および耐硫化物応力腐食割れ性に優れるラインパイプ用鋼
JP2870830B2 (ja) * 1989-07-31 1999-03-17 日本鋼管株式会社 耐ｈｉｃ特性に優れた高張力高靭性鋼板の製造方法
JPH0681034A (ja) * 1992-08-31 1994-03-22 Sumitomo Metal Ind Ltd 耐ｈｉｃ性に優れた鋼管用熱延鋼帯の製造方法
JPH06220577A (ja) * 1993-01-26 1994-08-09 Kawasaki Steel Corp 耐ｈｉｃ特性に優れた高張力鋼及びその製造方法
JP2770718B2 (ja) * 1993-09-03 1998-07-02 住友金属工業株式会社 耐ｈｉｃ性に優れた高強度熱延鋼帯とその製造方法

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20220299425A1 (en) * 2021-03-19 2022-09-22 Saudi Arabian Oil Company Development of Control Samples to Enhance the Accuracy of HIC Testing
US11656169B2 (en) * 2021-03-19 2023-05-23 Saudi Arabian Oil Company Development of control samples to enhance the accuracy of HIC testing
US20230251181A1 (en) * 2021-03-19 2023-08-10 Saudi Arabian Oil Company Development of Control Samples to Enhance the Accuracy of HIC Testing
US11788951B2 (en) 2021-03-19 2023-10-17 Saudi Arabian Oil Company Testing method to evaluate cold forming effects on carbon steel susceptibility to hydrogen induced cracking (HIC)
US12072278B2 (en) * 2021-03-19 2024-08-27 Saudi Arabian Oil Company Development of control samples to enhance the accuracy of HIC testing

Also Published As

Publication number Publication date
CA2289084C (fr) 2007-03-13
JP2002515093A (ja) 2002-05-21
KR100540686B1 (ko) 2006-01-10
DE69834031T2 (de) 2007-01-11
DE69834031D1 (de) 2006-05-18
WO1998053110A1 (fr) 1998-11-26
BR9809852A (pt) 2000-06-27
CA2289084A1 (fr) 1998-11-26
EP0998591A1 (fr) 2000-05-10
ATE321897T1 (de) 2006-04-15
KR20010012235A (ko) 2001-02-15

Similar Documents

Publication Publication Date Title
US5993570A (en) Linepipe and structural steel produced by high speed continuous casting
CA2280923C (fr) Acier a resistance elevee a la rupture et procede de production
US11628512B2 (en) Clad steel plate and method of producing the same
JP6198937B2 (ja) 超高度の靭性および優れた溶接性を伴うｈｔ５５０鋼板ならびにその製造方法
EP1435399B1 (fr) Procédé de soudage pour améliorer une résistance à la fissuration à froid
JP5846311B2 (ja) 溶接熱影響部ｃｔｏｄ特性に優れた厚肉高張力鋼およびその製造方法
EP3235921B1 (fr) Tôle d&#39;acier présentant une bonne résistance à la fatigue et à la croissance de fissures et son procédé de fabrication
KR20140117547A (ko) 용접부 인성이 우수한 고인성 클래드 강판의 모재 및 그 클래드 강판의 제조 방법
JPH10503809A (ja) 熱間加工性に優れた耐硫化物応力割れ性を有するマルテンサイト系ステンレス鋼
CA3094517C (fr) Composition d&#39;acier selon la specification api 5l psl-2 pour qualite x-65 a resistance amelioree a la fissuration induite par l&#39;hydrogene (hic) et procede de fabrication de son ac ier
EP0998591B1 (fr) Tube de canalisation et acier de construction produits par coulee continue a grande vitesse
JP4276574B2 (ja) 大入熱溶接熱影響部の靭性に優れた厚鋼板
JP2647302B2 (ja) 耐水素誘起割れ性の優れた高強度鋼板の製造方法
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
US3574002A (en) Stainless steel having improved corrosion and fatigue resistance
JPH07292416A (ja) 超高強度ラインパイプ用鋼板の製造方法
JP3579307B2 (ja) 溶接性及び歪時効後の靭性に優れた６０キロ級直接焼入れ焼戻し鋼
CN112760567A (zh) 一种韧性优异的高速列车转向架用钢板及其制造方法
JPH09272956A (ja) 耐海水用析出強化型高合金鋼及びその製造方法
JPH09194990A (ja) 溶接熱影響部靱性の優れた高張力鋼
JP2002018593A (ja) 低合金耐熱鋼用溶接材料および溶接金属
JP2705946B2 (ja) 耐ｓｓｃ性の優れた高張力鋼板の製造法
JP3823628B2 (ja) 溶接性及び歪時効後の靭性に優れた６０キロ級高張力鋼の製造方法
JPH08269566A (ja) Ｓｒ特性に優れた高強度・高靱性ｕｏｅ鋼管の製造方法
JP3975674B2 (ja) 低合金鋼材の製造方法

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: 19991217

AK Designated contracting states

Kind code of ref document: A1

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

17Q First examination report despatched

Effective date: 20010419

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

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

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LI

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: 20060329

Ref country code: CH

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: 20060329

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20060515

REF Corresponds to:

Ref document number: 69834031

Country of ref document: DE

Date of ref document: 20060518

Kind code of ref document: P

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MC

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20060531

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SE

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: 20060629

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20060629

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: 20060629

RAP2 Party data changed (patent owner data changed or rights of a patent transferred)

Owner name: MICROALLOYING INTERNATIONAL LP

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: ES

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: 20060710

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: PT

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: 20060829

NLT2 Nl: modifications (of names), taken from the european patent patent bulletin

Owner name: MICROALLOYING INTERNATIONAL LP

Effective date: 20060705

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

ET Fr: translation filed
NLS Nl: assignments of ep-patents

Owner name: MICROALLOYING INTERNATIONAL LP

Effective date: 20061101

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20060629

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: 20070102

BECA Be: change of holder's address

Owner name: *MICROALLOYING INTERNATIONAL LP10175 HARWIN, SUITE

Effective date: 20060329

BECH Be: change of holder

Owner name: *MICROALLOYING INTERNATIONAL LP

Effective date: 20060329

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GR

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: 20060630

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: FI

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: 20060329

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CY

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: 20060329

BECA Be: change of holder's address

Owner name: CBMM TECHNOLOGY SUISSE S.A.

Effective date: 20121129

Owner name: RUE DE HESSE 16, CH-1204 GENEVE

Effective date: 20121129

BECH Be: change of holder

Owner name: CBMM TECHNOLOGY SUISSE S.A.

Effective date: 20121129

BECN Be: change of holder's name

Owner name: CBMM TECHNOLOGY SUISSE S.A.

Effective date: 20121129

REG Reference to a national code

Ref country code: NL

Ref legal event code: TD

Effective date: 20130401

Ref country code: NL

Ref legal event code: SD

Effective date: 20130401

REG Reference to a national code

Ref country code: DE

Ref legal event code: R082

Ref document number: 69834031

Country of ref document: DE

Representative=s name: PATENTANWAELTE LIPPERT, STACHOW & PARTNER, DE

REG Reference to a national code

Ref country code: AT

Ref legal event code: PC

Ref document number: 321897

Country of ref document: AT

Kind code of ref document: T

Owner name: CBMM TECHNOLOGY SUISSE SA, CH

Effective date: 20130118

REG Reference to a national code

Ref country code: DE

Ref legal event code: R082

Ref document number: 69834031

Country of ref document: DE

Representative=s name: WUESTHOFF & WUESTHOFF, PATENTANWAELTE PARTG MB, DE

Effective date: 20130201

Ref country code: DE

Ref legal event code: R082

Ref document number: 69834031

Country of ref document: DE

Representative=s name: WUESTHOFF & WUESTHOFF PATENT- UND RECHTSANWAEL, DE

Effective date: 20130201

Ref country code: DE

Ref legal event code: R082

Ref document number: 69834031

Country of ref document: DE

Representative=s name: PATENTANWAELTE LIPPERT, STACHOW & PARTNER, DE

Effective date: 20130201

Ref country code: DE

Ref legal event code: R081

Ref document number: 69834031

Country of ref document: DE

Owner name: CBMM TECHNOLOGY SUISSE SA, CH

Free format text: FORMER OWNER: MICROALLOYING INTERNATIONAL LP, HOUSTON, TEX., US

Effective date: 20130201

Ref country code: DE

Ref legal event code: R081

Ref document number: 69834031

Country of ref document: DE

Owner name: CBMM TECHNOLOGY SUISSE SA, CH

Free format text: FORMER OWNER: MICROALLOYING INTERNATIONAL LP, HOUSTON, US

Effective date: 20130201

REG Reference to a national code

Ref country code: FR

Ref legal event code: TP

Owner name: CBMM TECHNOLOGY SUISSE SA, CH

Effective date: 20130724

Ref country code: FR

Ref legal event code: RM

Effective date: 20130724

Ref country code: FR

Ref legal event code: CJ

Effective date: 20130724

Ref country code: FR

Ref legal event code: CD

Owner name: CBMM TECHNOLOGY SUISSE SA, CH

Effective date: 20130724

Ref country code: FR

Ref legal event code: CA

Effective date: 20130724

REG Reference to a national code

Ref country code: DE

Ref legal event code: R082

Ref document number: 69834031

Country of ref document: DE

Representative=s name: WUESTHOFF & WUESTHOFF, PATENTANWAELTE PARTG MB, DE

Ref country code: DE

Ref legal event code: R082

Ref document number: 69834031

Country of ref document: DE

Representative=s name: WUESTHOFF & WUESTHOFF PATENT- UND RECHTSANWAEL, DE

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 18

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 19

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: NL

Payment date: 20160523

Year of fee payment: 19

Ref country code: LU

Payment date: 20160524

Year of fee payment: 19

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: DE

Payment date: 20160527

Year of fee payment: 19

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: FR

Payment date: 20160530

Year of fee payment: 19

Ref country code: BE

Payment date: 20160523

Year of fee payment: 19

Ref country code: AT

Payment date: 20160518

Year of fee payment: 19

Ref country code: IT

Payment date: 20160524

Year of fee payment: 19

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20170531

REG Reference to a national code

Ref country code: DE

Ref legal event code: R119

Ref document number: 69834031

Country of ref document: DE

REG Reference to a national code

Ref country code: NL

Ref legal event code: MM

Effective date: 20170601

REG Reference to a national code

Ref country code: AT

Ref legal event code: MM01

Ref document number: 321897

Country of ref document: AT

Kind code of ref document: T

Effective date: 20170515

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: AT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20170515

REG Reference to a national code

Ref country code: FR

Ref legal event code: ST

Effective date: 20180131

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: NL

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20170601

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20170515

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20170531

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: DE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20171201

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20170515

Ref country code: FR

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20170531

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: BE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20170531