EP2103704B1 - Warmgewalztes Langprodukt und Verfahren zu dessen Herstellung - Google Patents

Warmgewalztes Langprodukt und Verfahren zu dessen Herstellung Download PDF

Info

Publication number
EP2103704B1
EP2103704B1 EP08004335A EP08004335A EP2103704B1 EP 2103704 B1 EP2103704 B1 EP 2103704B1 EP 08004335 A EP08004335 A EP 08004335A EP 08004335 A EP08004335 A EP 08004335A EP 2103704 B1 EP2103704 B1 EP 2103704B1
Authority
EP
European Patent Office
Prior art keywords
hot
long product
content
product according
rolled long
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.)
Active
Application number
EP08004335A
Other languages
German (de)
English (en)
French (fr)
Other versions
EP2103704A1 (de
Inventor
Hans Roelofs
Ulrich Urlau
Mirkka Lembke
Guido Olschewski
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.)
Swiss Steel AG
Original Assignee
Swiss Steel AG
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 Swiss Steel AG filed Critical Swiss Steel AG
Priority to PL08004335T priority Critical patent/PL2103704T3/pl
Priority to ES08004335T priority patent/ES2391312T3/es
Priority to EP08004335A priority patent/EP2103704B1/de
Priority to SI200830770T priority patent/SI2103704T1/sl
Publication of EP2103704A1 publication Critical patent/EP2103704A1/de
Application granted granted Critical
Publication of EP2103704B1 publication Critical patent/EP2103704B1/de
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the invention relates to a hot-rolled long product according to the preamble of claim 1 and a method for its production.
  • tempered steels are generally used. With tempered steels it is possible to achieve tensile strengths of more than 1 000 MPa with simultaneous necking of more than 45%.
  • the necessary heat treatment heat treatment, quenching, tempering
  • expensive post-processing straightening, grinding
  • Pre-tempered steels have significant disadvantages in machining (long chips, low tool life). These processing disadvantages can be somewhat reduced by the addition of a maximum of 0.04 wt.% Sulfur. Higher levels of sulfur degrade the manufacturability and microscopic purity of these Al-alloyed steels.
  • the tempered steels are alloyed with at least 0.015% aluminum.
  • hard and abrasive Al 2 O 3 -containing oxide inclusions are produced during the cutting process, which have a negative effect on tool life.
  • these inclusions In order to achieve good machinability, these inclusions must be converted into less abrasive calcium aluminate inclusions by adding calcium in a complex metallurgical process.
  • ferritic-martensitic dual-phase steels were developed.
  • the structure of these steels is via a thermomechanical Treatment achieved during hot rolling.
  • good toughness properties can only be set as long as the stored martensite islands remain small enough.
  • the achievable tensile strength is thereby limited to below 1'000 MPa.
  • Steels for pipe production must be characterized in particular by good toughness and weldability. For this to be achieved, a low carbon content of less than 0.13 wt% is required.
  • the desired high-strength, tough structure is achieved by accelerated cooling from the rolling heat. In the temperature range of 800 to 500 ° C (range of conversion) cooling rates of 10 to 40 K / s are used.
  • the structure of these steels then consists of allotriomorphic ferrite and bainite (at least 20%).
  • the low carbon content of the accelerated cooling guarantees the avoidance of high martensite content, which enables good toughness properties.
  • the tensile strength is thereby limited to below 1'000 MPa.
  • US 2003 0084 965 discloses a machinable steel with 0.1-0.6 C, 0.01-2.0 Si, and 0.005-0.20 s.
  • EP 0845544 (C ⁇ 0.12%) describes a microalloyed bainitic steel which has a tensile strength of more than 1000 MPa at room temperature. To achieve these properties, the steel is austenitized again after rolling and then quenched at a cooling rate of 17 to 150 K / s. These cooling rates are well above the air cooled long products in conventional rolling mills.
  • An easily machinable bainitic-martensitic complex phase steel for the production of air-cooled conventionally hot-rolled long products in a size range of 5.0 to 70 mm is not yet available.
  • the material concept must be designed in such a way that the dimensional differences in the cooling rate of approx. 0.1 to 8.0 K / s do not lead to any significant fluctuations in the mechanical-technological properties of the final product.
  • the object of the invention is to provide an improved hot-rolled long product, with which in particular the above disadvantages are avoided.
  • Another object of the invention is to provide a process for producing a hot-rolled long product.
  • the alloying components are selected so that at usual cooling rates from the rolling heat of 0.1 to 8.0 K / s a bainitic-martensitic microstructure always results with a tensile strength level of 1'000 to 1400 MPa, without costly alloying elements and / or or special equipment for accelerated cooling from the rolling heat must be used.
  • the lower limit of the carbon content to 0.20% ensures, in combination with manganese and chromium, that only small amounts of ferrite are present in the microstructure. Ferrite levels above 10% affect both the strength level and impact strength of the product.
  • the upper limit of the carbon to 0.25% ensures that the tensile strength does not rise above 1400 MPa. Higher strength values degrade machinability in the downstream drawing or machining process. Higher carbon contents also promote the formation of carbides, which adversely affects ductility.
  • Silicon affects the carbon activity and slows down the precipitation of carbides.
  • the selected silicon concentration allows a one-hour annealing treatment at 400 ° C without degrading the ductility due to carbide precipitations (based on the description of the carbide-free bainite in WO 96/22396 ). Since silicon is an efficient solid solution hardener in bainite, its content must be limited to 1.35% in order not to exceed the maximum desired tensile strength of 1400 MPa.
  • the manganese content is too high, the manganese segregations are pronounced and the microstructure becomes very inhomogeneous. For this reason, the "free”, ie not bound in manganese sulfides, manganese content ( ⁇ total manganese content - 1.72 Sulfur content) to 1.50%.
  • the so determined manganese content is not sufficient to achieve a bainitic-martensitic structure after air cooling from the rolling heat.
  • the product must also contain so much chromium that chromium content + (manganese content - 1.72 sulfur content)> 2.6% by weight applies. Together with a carbon content of at least 0.20%, a bainitic-martensitic microstructure with ⁇ 10% ferrite is ensured.
  • Molybdenum is said to prevent the precipitation of iron carbides at the primary grain boundaries and associated loss of toughness. For cost reasons, the molybdenum content should be as low as necessary: 0.1 to 0.5% molybdenum.
  • the steel should contain at least 0.04%, preferably 0.12 to 0.17% sulfur.
  • the sulfur combines with manganese to form manganese sulfide precipitates, thus improving both chip breaking and tool life. Since these precipitates also reduce the transverse toughness of the hot-rolled long product, the addition of sulfur should be limited to 0.25%.
  • the aluminum content should be limited to 0.01%.
  • oxide inclusions should be set with an Al 2 O 3 content of ⁇ 50%.
  • the metallurgical treatment is carried out so that soft, glassy silicate inclusions are formed with the following relative proportions by weight: 20 to 50% CaO, 35 to 65% SiO 2 and less than 25% Al 2 O 3 . The tool life of the tools used in machining is then significantly extended.
  • the good machinability of the hot-rolled long product produced according to the invention can be further improved according to claim 3 or 4 by the addition of 0.05 to 0.3% lead or 0.05 to 0.3% bismuth.
  • the austenite grain size before the structural transformation and the cooling rate during structural transformation in a temperature range between 800 and 500 ° C. are of crucial importance.
  • a fine austenite grain leads to a finer final structure with better toughness values.
  • the austenite grain after the last forming step according to claim 7 should not be greater than 50 ⁇ m.
  • the cooling rates should be between 0.1 and 8.0 K / s.
  • the upper value is given by the possibilities of conventional cooling of accelerated air.
  • the lower limit of 0.1 K / s is to ensure that no ferrite> 10% occur. Large bar dimensions that cool down inside the bar much slower than 0.1 K / s can not be produced with this technology.
  • a heat treatment for 0.5 to 2 hours at 300 to 500 ° C according to claim 8 may be useful.
  • the high silicon content of the product delays the rearrangement of carbon atoms in the microstructure. This is desirable to suppress the formation of coarse carbide precipitates.
  • also in connection with carbon known aging processes that begin immediately after the hot rolling slowed down. In particular, the maximum ductility of the structure sets in only after a few weeks. In cases where the rolled long product is to be further processed immediately, a heat treatment is therefore recommended.
  • a molten steel was poured and then rolled into bar steel in various dimensions.
  • the molten steel was produced by the electrical steel process with a secondary metallurgical treatment on a ladle and subsequent casting to 150 ⁇ 150 mm 2 sticks in a continuous casting plant.
  • the billets were then reheated in a walking beam oven to 1'150 to 1'200 ° C and then to bar steel in the dimensions 22 (cooling rate is about 1.5 K / s) and 52 mm (cooling rate is about 0.4 K / s) rolled.
  • the cooling of the rods after rolling was carried out in air.
  • the steel was made 0.22% to carbon 0.94% silicon 00:07% nickel 0.14% to molybdenum 00:15% sulfur 0.003% aluminum 0.012% phosphorus ⁇ 0.001% boron 0.011% titanium ⁇ 0.003% lead ⁇ 0.003% bismuth 0.013% nitrogen 1.60% manganese 1:34% Manganese - 1.72 Sulfur 1:54% chrome 2.88% Chromium + (manganese - 1.72 sulfur) and other impurities caused by melting.
  • the high sulfur content of 0.15% ensures good chip breaking and improves tool life.
  • the low aluminum content suppresses the formation of hard, abrasive, clay-containing oxide inclusions.
  • the metallographic micrographs at 200x magnification are in the Fig. 1 shown.
  • the microstructure is a very fine mixed structure.
  • the bainite and martensite fractions could not be reliably quantified.
  • the pictures as well as the obtained strength level show that the structure consists primarily (>> 50%) of bainite.
  • the structure of the 52 mm rod is slightly coarser than the structure of the 22 mm rod due to the low cooling rate from the rolling heat.
  • manganese sulphides which can serve as nucleating sites for ferrite formation
  • isolated ferrite grains can be recognized.
  • the ferrite content is extremely low ( ⁇ 10%).
  • the determination of the residual austenite quantity in the X-ray diffractometer showed 5.1 ⁇ 0.45% for the 22 mm rod and 4.4 ⁇ 1.34% for the 52 mm rod.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
EP08004335A 2008-03-10 2008-03-10 Warmgewalztes Langprodukt und Verfahren zu dessen Herstellung Active EP2103704B1 (de)

Priority Applications (4)

Application Number Priority Date Filing Date Title
PL08004335T PL2103704T3 (pl) 2008-03-10 2008-03-10 Walcowany na gorąco długi produkt i sposób jego wytwarzania
ES08004335T ES2391312T3 (es) 2008-03-10 2008-03-10 Producto longitudinal laminado en caliente y procedimiento para su fabricación
EP08004335A EP2103704B1 (de) 2008-03-10 2008-03-10 Warmgewalztes Langprodukt und Verfahren zu dessen Herstellung
SI200830770T SI2103704T1 (sl) 2008-03-10 2008-03-10 Vroče valjani dolg proizvod in postopek za njegovo izdelavo

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP08004335A EP2103704B1 (de) 2008-03-10 2008-03-10 Warmgewalztes Langprodukt und Verfahren zu dessen Herstellung

Publications (2)

Publication Number Publication Date
EP2103704A1 EP2103704A1 (de) 2009-09-23
EP2103704B1 true EP2103704B1 (de) 2012-07-11

Family

ID=39864799

Family Applications (1)

Application Number Title Priority Date Filing Date
EP08004335A Active EP2103704B1 (de) 2008-03-10 2008-03-10 Warmgewalztes Langprodukt und Verfahren zu dessen Herstellung

Country Status (4)

Country Link
EP (1) EP2103704B1 (pl)
ES (1) ES2391312T3 (pl)
PL (1) PL2103704T3 (pl)
SI (1) SI2103704T1 (pl)

Families Citing this family (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2453026A1 (de) * 2010-11-10 2012-05-16 Swiss Steel AG Warmumgeformtes Stahlprodukt und Verfahren zu dessen Herstellung
EP2489748B1 (de) * 2011-02-18 2017-12-13 ThyssenKrupp Steel Europe AG Aus einem Komplexphasenstahl hergestelltes warmgewalztes Stahlflachprodukt und Verfahren zu dessen Herstellung
EP3061837A1 (de) 2015-02-27 2016-08-31 Swiss Steel AG Blankes bainitisches Langprodukt und Verfahren zu dessen Herstellung
MX2019010378A (es) 2017-03-01 2019-10-22 Ak Steel Properties Inc Acero endurecido por prensado con fuerza extremadamente alta y metodo para su produccion.
AT519669B1 (de) * 2017-06-07 2018-09-15 Voestalpine Schienen Gmbh Gleisteil und Verfahren zur Herstellung eines Gleisteils
WO2019180492A1 (en) 2018-03-23 2019-09-26 Arcelormittal Forged part of bainitic steel and a method of manufacturing thereof

Family Cites Families (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB2297094B (en) 1995-01-20 1998-09-23 British Steel Plc Improvements in and relating to Carbide-Free Bainitic Steels
US5922145A (en) * 1996-11-25 1999-07-13 Sumitomo Metal Industries, Ltd. Steel products excellent in machinability and machined steel parts
WO1998023784A1 (fr) * 1996-11-25 1998-06-04 Sumitomo Metal Industries, Ltd. Acier d'excellente usinabilite et composant usine
FR2756298B1 (fr) 1996-11-26 1998-12-24 Ascometal Sa Acier et procede pour la fabrication d'une piece de mecanique ayant une structure bainitique
JP3468239B2 (ja) * 2001-10-01 2003-11-17 住友金属工業株式会社 機械構造用鋼及びその製造方法
FR2847271B1 (fr) * 2002-11-19 2004-12-24 Usinor Procede pour fabriquer une tole en acier resistant a l'abrasion et tole obtenue
FR2847273B1 (fr) * 2002-11-19 2005-08-19 Usinor Piece d'acier de construction soudable et procede de fabrication
CN1210430C (zh) 2003-08-01 2005-07-13 清华大学 中低碳锰系空冷贝氏体钢
DE102005052069B4 (de) 2005-10-28 2015-07-09 Saarstahl Ag Verfahren zum Herstellen von Vormaterial aus Stahl durch Warmverformen

Also Published As

Publication number Publication date
SI2103704T1 (sl) 2012-11-30
PL2103704T3 (pl) 2012-12-31
EP2103704A1 (de) 2009-09-23
ES2391312T3 (es) 2012-11-23

Similar Documents

Publication Publication Date Title
DE69617002T4 (de) Verfahren zur herstellung von hochfesten nahtlosen stahlrohren mit hervorragender schwefel induzierter spannungsrisskorossionsbeständigkeit
DE69811200T2 (de) Einsatzstahl mit hervorragender verhinderung der sekundärrekristallisation während der aufkohlung, verfahren zu dessen herstellung, halbzeug für aufzukohlende teile
DE69429610T2 (de) Hochfester martensitischer rostfreier Stahl und Verfahren zu seiner Herstellung
EP3504349B1 (de) Verfahren zur herstellung eines höchstfesten stahlbandes mit verbesserten eigenschaften bei der weiterverarbeitung und ein derartiges stahlband
EP3976838B1 (de) Bauteil, hergestellt durch umformen einer stahlblechplatine und verfahren zu seiner herstellung
EP3535431B1 (de) Mittelmanganstahlprodukt zum tieftemperatureinsatz und verfahren zu seiner herstellung
EP2905348B1 (de) Hochfestes Stahlflachprodukt mit bainitisch-martensitischem Gefüge und Verfahren zur Herstellung eines solchen Stahlflachprodukts
DE4040355C2 (de) Verfahren zur Herstellung eines dünnen Stahlblechs aus Stahl mit hohem Kohlenstoffgehalt
DE69426341T2 (de) Graphit-Baustahl mit guter Zerspanbarkeit und guten Kaltverformungseigenschaften und Verfahren zu seiner Herstellung
DE69418565T2 (de) Wärmeunbehandelter stahl zum warmschmieden, verfahren zur herstellung eines daraus hergestellten schmiedestückes und schmiedestück
EP2103704B1 (de) Warmgewalztes Langprodukt und Verfahren zu dessen Herstellung
DE112016005223T5 (de) Nicht vergüteter Walzdraht mit ausgezeichneter Kaltverformbarkeit und Herstellungsverfahren davon
EP1274872B1 (de) Verfahren zur herstellung eines stickstofflegierten, sprühkompaktierten stahls, verfahren zu seiner herstellung
EP2009120B1 (de) Verwendung einer hochfesten Stahllegierung zur Herstellung von Stahlrohren mit hoher Festigkeit und guter Umformbarkeit
DE1483218C3 (de) Verfahren zum Herstellen eines warmfesten, ferritischen Cr-Mo-V-Stahles mit hoher Zeitstandfestigkeit und verbesserter Zeitbruchdehnung
DE102016115618A1 (de) Verfahren zur Herstellung eines höchstfesten Stahlbandes mit verbesserten Eigenschaften bei der Weiterverarbeitung und ein derartiges Stahlband
DE112015005347T5 (de) Lagerkomponente gebildet aus einer Stahllegierung
DE3113844A1 (de) "ferritfreier, ausscheidungshaertbarer rostfreier stahl"
EP1780293A2 (de) Verfahren zum Herstellen von Vormaterial aus Stahl durch Warmverformen
DE112008001181B4 (de) Verwendung einer Stahllegierung für Achsrohre sowie Achsrohr
DE60126646T2 (de) Stahllegierung, halter und haltereinzelteile für kunststoff-formwerkzeuge und vergütete rohlinge für halter und haltereinzelteile
DE3201204A1 (de) "verwendung eines kohlenstoff-mangan-stahles fuer bauteile mit hoher festigkeit und zaehigkeit bei einfacher waermebehandlung"
EP3061838B1 (de) Blankes bainitisches langprodukt und verfahren zu dessen herstellung
EP3225702B1 (de) Stahl mit reduzierter dichte und verfahren zur herstellung eines stahlflach- oder -langprodukts aus einem solchen stahl
WO2020038883A1 (de) Warmgewalztes unvergütetes und warmgewalztes vergütetes stahlflachprodukt sowie verfahren zu deren herstellung

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

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MT NL NO PL PT RO SE SI SK TR

AX Request for extension of the european patent

Extension state: AL BA MK RS

17P Request for examination filed

Effective date: 20091229

AKX Designation fees paid

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MT NL NO PL PT RO SE SI SK TR

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 BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MT NL NO PL PT RO SE SI SK TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

Free format text: NOT ENGLISH

REG Reference to a national code

Ref country code: CH

Ref legal event code: NV

Representative=s name: SCHMAUDER & PARTNER AG PATENT- UND MARKENANWAELTE

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 566189

Country of ref document: AT

Kind code of ref document: T

Effective date: 20120715

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

Free format text: LANGUAGE OF EP DOCUMENT: GERMAN

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 502008007670

Country of ref document: DE

Effective date: 20120906

REG Reference to a national code

Ref country code: SE

Ref legal event code: TRGR

REG Reference to a national code

Ref country code: ES

Ref legal event code: FG2A

Ref document number: 2391312

Country of ref document: ES

Kind code of ref document: T3

Effective date: 20121123

REG Reference to a national code

Ref country code: NL

Ref legal event code: VDEP

Effective date: 20120711

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG4D

Effective date: 20120711

REG Reference to a national code

Ref country code: PL

Ref legal event code: T3

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

Ref country code: LT

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: 20120711

Ref country code: NO

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: 20121011

Ref country code: HR

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: 20120711

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: 20120711

Ref country code: IS

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: 20121111

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: 20120711

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: 20121112

Ref country code: LV

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: 20120711

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: 20121012

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 FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20120711

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: 20120711

Ref country code: RO

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: 20120711

Ref country code: EE

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: 20120711

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

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

Ref country code: SK

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: 20120711

26N No opposition filed

Effective date: 20130412

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

Ref country code: BG

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: 20121011

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 502008007670

Country of ref document: DE

Effective date: 20130412

BERE Be: lapsed

Owner name: SWISS STEEL A.G.

Effective date: 20130331

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: 20130331

REG Reference to a national code

Ref country code: IE

Ref legal event code: MM4A

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: 20130331

Ref country code: IE

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

Effective date: 20130310

REG Reference to a national code

Ref country code: AT

Ref legal event code: MM01

Ref document number: 566189

Country of ref document: AT

Kind code of ref document: T

Effective date: 20130310

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

Ref country code: MT

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: 20120711

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: 20130310

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

Ref country code: TR

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: 20120711

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

Ref country code: HU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO

Effective date: 20080310

Ref country code: LU

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

Effective date: 20130310

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 9

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 10

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 11

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

Ref country code: CZ

Payment date: 20180308

Year of fee payment: 11

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

Ref country code: PL

Payment date: 20180308

Year of fee payment: 11

Ref country code: SE

Payment date: 20180321

Year of fee payment: 11

Ref country code: FR

Payment date: 20180330

Year of fee payment: 11

Ref country code: SI

Payment date: 20180305

Year of fee payment: 11

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

Ref country code: ES

Payment date: 20180430

Year of fee payment: 11

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

Ref country code: IT

Payment date: 20180327

Year of fee payment: 11

REG Reference to a national code

Ref country code: SE

Ref legal event code: EUG

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

Ref country code: CZ

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

Effective date: 20190310

Ref country code: SE

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

Effective date: 20190311

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

Effective date: 20190310

REG Reference to a national code

Ref country code: SI

Ref legal event code: KO00

Effective date: 20191111

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 NON-PAYMENT OF DUE FEES

Effective date: 20190310

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

Ref country code: FR

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

Effective date: 20190331

Ref country code: SI

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

Effective date: 20190311

Ref country code: IT

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

Effective date: 20190310

REG Reference to a national code

Ref country code: ES

Ref legal event code: FD2A

Effective date: 20200724

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 NON-PAYMENT OF DUE FEES

Effective date: 20190311

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

Ref country code: PL

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

Effective date: 20190310

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

Ref country code: DE

Payment date: 20230321

Year of fee payment: 16

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

Ref country code: CH

Payment date: 20230402

Year of fee payment: 16

REG Reference to a national code

Ref country code: DE

Ref legal event code: R119

Ref document number: 502008007670

Country of ref document: DE

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

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: 20241001

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: 20241001

Ref country code: CH

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

Effective date: 20240331