EP0754770B1 - Verfahren zum Herstellen eines dünnen Blechbandes mit verbesserter Tiefziehbarkeit - Google Patents

Verfahren zum Herstellen eines dünnen Blechbandes mit verbesserter Tiefziehbarkeit Download PDF

Info

Publication number
EP0754770B1
EP0754770B1 EP96401347A EP96401347A EP0754770B1 EP 0754770 B1 EP0754770 B1 EP 0754770B1 EP 96401347 A EP96401347 A EP 96401347A EP 96401347 A EP96401347 A EP 96401347A EP 0754770 B1 EP0754770 B1 EP 0754770B1
Authority
EP
European Patent Office
Prior art keywords
content
less
steel
strip
cold rolling
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
EP96401347A
Other languages
English (en)
French (fr)
Other versions
EP0754770A1 (de
Inventor
José Manuel Rubianes
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.)
Sollac SA
Original Assignee
Sollac SA
Lorraine de Laminage Continu SA SOLLAC
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 Sollac SA, Lorraine de Laminage Continu SA SOLLAC filed Critical Sollac SA
Publication of EP0754770A1 publication Critical patent/EP0754770A1/de
Application granted granted Critical
Publication of EP0754770B1 publication Critical patent/EP0754770B1/de
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

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
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0436—Cold rolling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0468—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment between cold rolling steps
    • 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
    • C22C38/02—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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • B21B2001/221—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length by cold-rolling

Definitions

  • the present invention relates to a method for manufacturing a thin sheet strip with improved drawability having good ability to expanding deformation and shrinking deformation, as well as a sheet thin with improved drawability obtained by this process.
  • Steels for stamping, or shrinking as part of steels for packaging, or expanding within the framework of steels by example for automobile, must have a number of special characteristics to allow them to be shaped.
  • the work hardening coefficient n must be as high as possible. Indeed this coefficient of work hardening defines the aptitude of the material to be deform in expansion and, the higher this coefficient, the better the material expanding deformation.
  • the significant cold work hardening which the sheet metal strip undergoes during rolling results, after annealing, in the formation of crystallographic textures leading to an anisotropy of the mechanical properties.
  • Its influence on the elastic limit Re, the tensile strength Rm and the elongation percent at break A% is relatively weak, but it is not the same for the thinning of the sheet during stresses suffered by the sheet during shaping.
  • This coefficient r represents the thinning capacity of the sheet and to guarantee the best stamping conditions, i.e. good flow of the metal in all directions, a Lankford coefficient is required r as high as possible.
  • anisotropy coefficient r ⁇ in the direction where it is the lowest r mini is as high as possible, which ensures that in all directions of stress, the metal does not go too thin.
  • Young's modulus must also be the highest possible, and a steel is all the more stampable as it develops these properties.
  • This type of steel has good characteristics stamping.
  • the steel thus produced is hot rolled, cold rolled with a reduction rate of 50%, then annealing at 750 ° C for 20 seconds, cold rolled with a reduction rate of 77% and annealed a second time at 870 ° C for 20 seconds.
  • This type of steel sheet has a Lankford coefficient r high but does not necessarily have the other properties necessary for good stamping, and it is extremely expensive to carry out essentially because of the low carbon content necessary to obtain this Lankford coefficient, as well as the high temperatures of the annealing
  • the object of the present invention is to propose a method of manufacture of a strip of sheet metal with improved drawability having a good suitability for expanding deformation as well as deformation shrinking, as well as an improved elongation at break, and which is economical to achieve.
  • the present invention relates more particularly to a process for manufacturing a strip of thin sheet metal with stampability improved having good suitability for expanding deformation and shrinkage deformation, process comprising the steps indicated in claim 1.
  • the present invention also relates to a sheet metal strip thin having good drawing ability obtained by the process according to the above characteristics.
  • the invention relates to a strip of thin sheet steel of improved stampability, that is to say having a low yield strength, a high Lankford coefficient greater than 2, preferably 2.4 in all directions of the sheet, significant consolidation, significant ductility and a high Young's modulus greater than 23,000 kg / mm 2 .
  • a steel is first produced, in a known manner, for example using a steelworks converter, the composition of which in thousandths of a percent is as follows: carbon ⁇ 20 silicon ⁇ 500 manganese ⁇ 1000 phosphorus ⁇ 100 sulfur ⁇ 50 aluminum ⁇ 100 nitrogen ⁇ 10 and none, one or more of the following: titanium ⁇ 150 niobium ⁇ 150 boron ⁇ 5 the rest being iron and residuals from the production process.
  • the steel has the following composition, in thousandths of a percent: carbon from 2 to 20 silicon from 100 to 500 manganese from 0 to 1000 phosphorus from 50 to 100 sulfur from 0 to 50 aluminum from 0 to 100 nitrogen from 2 to 8 and none, one or more of the following: titanium from 0 to 150 niobium from 10 to 50 boron from 0 to 2 the rest being iron and residuals from the production process.
  • the steel thus produced is then poured into slabs and then rolled to hot.
  • the hot rolled strip is then cold rolled with a reduction rate greater than 20%.
  • the strip thus cold rolled is then subjected to annealing at a temperature between the restoration temperature of the steel and 920 ° C, preferably between the steel restoration temperature and its recrystallization temperature.
  • Annealing can be either basic annealing or annealing continued.
  • a second cold rolling is then carried out with a rate of reduction greater than 20% by imparting roughness to the sheet metal strip determined.
  • a second annealing is carried out at a higher temperature. at the recrystallization temperature of the steel.
  • the Applicant has found that it is possible to increase the value of the Lankford coefficient r of the sheet so that it is greater than 2, preferably 2.4 when the temperature of the first annealing takes place at a temperature between the temperature for restoring the steel and its recrystallization temperature, preferably at a temperature equal to the steel restoration temperature plus 40 to 60 ° C.
  • the first scenario in which the rate of reduction of first cold rolling is low, while being greater than 20%, preferably in the range of 35 to 50%, and the reduction rate of the second rolling is important, preferably of the order of 65 to 75%.
  • the second scenario in which the rate of reduction of first cold rolling is important, preferably around 65 to 75% and the reduction rate of the second cold rolling is low, while being greater than 20%, preferably of the order of 35 to 50%.
  • the printed roughness is such that the roughness average Ra is between 0.9 and 1.7 microns.
  • the average roughness Ra is between 1.2 and 1.7 to favor stamping. But if you want to get a more shiny on the sheet, while retaining good stampability, we print the sheet has an average roughness Ra of between 0.9 and 1.4 microns.
  • This operation makes it possible, by eliminating the skin-pass operation, to guarantee a high Lankford coefficient greater than 2, preferably 2.4 and a low elastic limit because the skin-pass operation has the consequence of increasing the yield strength of the metal, and degrading the work hardening coefficient not .
  • the fact of being free from the skin-pass operation makes it possible to omit a step in the manufacture of the sheet metal strip and consequently reduces the cost thereof.
  • steels A and B are steels in accordance with the invention and the steel C corresponds to a composition according to the state of technique.
  • the restoration temperature of steel A which has been produced with a first basic annealing, is equal to 450 ° C. and its temperature of recrystallization is equal to 680 ° C.
  • the restoration temperature of steel B which has been produced with a first continuous annealing, is equal to 450 ° C. and its temperature of recrystallization is equal to 630 ° C.
  • Each of the three types of steel was then treated with different rolling and annealing and thus several sheet metal strips were produced thickness less than 1 mm.
  • the steel of the invention allows to obtain a significant gain in comparison with steel C of the prior art in terms of ductility and in terms of drawability.
  • the advantage of printing a controlled roughness during the second cold rolling allows a substantially more elastic limit Re weak than if one refrained from printing this roughness.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Organic Chemistry (AREA)
  • Metallurgy (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Continuous Casting (AREA)
  • Laminated Bodies (AREA)
  • Heat Treatment Of Steel (AREA)
  • Metal Rolling (AREA)
  • Glass Compositions (AREA)
  • Transition And Organic Metals Composition Catalysts For Addition Polymerization (AREA)
  • Compositions Of Macromolecular Compounds (AREA)
  • Coating With Molten Metal (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)

Claims (3)

  1. Verfahren zur Herstellung eines Feinblechbands mit verbesserter Tiefziehbarkeit, das eine gute Verformbarkeit bezüglich Streckung und eine gute Verformbarkeit bezüglich Querschnittsverminderung sowie eine verbesserte Bruchdehnung aufweist, umfassend:
    die Erzeugung eines Stahls mit jeweils in Tausendstel Gewichtsprozent einem Kohlenstoffgehalt von unter 20, einem Siliziumgehalt von unter 500, einem Mangangehalt von unter 1000, einem Phosphorgehalt von unter 100, einem Schwefelgehalt von unter 50, einem Aluminiumgehalt von unter 100, einem Stickstoffgehalt von unter 10 und mit keinem, einem oder mehreren der folgenden Elemente, nämlich Titan mit einem Gehalt von unter 150, Niobium mit einem Gehalt von unter 150 und Bor mit einem Gehalt von unter 5, wobei der Rest Eisen und Rückstände sind,
    die Durchführung eines Warmwalzvorgangs,
    die Durchführung eines Kaltwalzvorgangs mit einem Reduktionsgrad zwischen 35 und 50% oder zwischen 65 und 75%,
    die Durchführung eines Glühvorgangs bei einer Temperatur zwischen der Erholungstemperatur des Stahls und seiner Rekristallisationstemperatur,
    die Durchführung eines zweiten Kaltwalzvorgangs mit einem Reduktionsgrad zwischen 65 und 75%, wenn der erste Kaltwalzvorgang mit einem Reduktionsgrad zwischen 35 und 50% durchgeführt wurde, oder zwischen 35 und 50%, wenn der erste Kaltwalzvorgang mit einem Reduktionsgrad zwischen 65 und 75% durchgeführt wurde, wobei dem Blechband eine mittlere Rauhtiefe Ra zwischen 0,9 und 1,7 Mikron verliehen wird,
    die Durchführung eines zweiten Glühvorgangs bei einer Temperatur über der Rekristallisationstemperatur des Stahls.
  2. Verfahren zur Herstellung eines Feinblechbands mit verbesserter Tiefziehbarkeit nach Anspruch 1, dadurch gekennzeichnet, dass der im ersten Schritt erzeugte Stahl in Tausendstel Gewichtsprozent einen Kohlenstoffgehalt zwischen 2 und 20, einen Siliziumgehalt zwischen 100 und 500, einen Mangangehalt zwischen 0 und 1000, einen Phosphorgehalt zwischen 50 und 100, einen Schwefelgehalt zwischen 0 und 50, einen Aluminiumgehalt zwischen 0 und 100, einen Stickstoffgehalt zwischen 2 und 8 und eines oder mehrere der folgenden Elemente, nämlich Titan mit einem Gehalt zwischen 0 und 150, Niobium mit einem Gehalt zwischen 10 und 150 und Bor mit einem Gehalt zwischen 0 und 2 aufweist, wobei der Rest Eisen und Rückstände sind.
  3. Feinblechband mit verbesserter Tiefziehbarkeit, das eine gute Verformbarkeit bezüglich Streckung und eine gute Verformbarkeit bezüglich Querschnittsverminderung aufweist, dadurch gekennzeichnet, dass es durch das Verfahren nach den Ansprüchen 1 und 2 hergestellt wird.
EP96401347A 1995-07-18 1996-06-20 Verfahren zum Herstellen eines dünnen Blechbandes mit verbesserter Tiefziehbarkeit Expired - Lifetime EP0754770B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR9508643 1995-07-18
FR9508643A FR2736933B1 (fr) 1995-07-18 1995-07-18 Procede de fabrication d'une bande de tole mince a emboutissabilite amelioree

Publications (2)

Publication Number Publication Date
EP0754770A1 EP0754770A1 (de) 1997-01-22
EP0754770B1 true EP0754770B1 (de) 2001-11-14

Family

ID=9481066

Family Applications (1)

Application Number Title Priority Date Filing Date
EP96401347A Expired - Lifetime EP0754770B1 (de) 1995-07-18 1996-06-20 Verfahren zum Herstellen eines dünnen Blechbandes mit verbesserter Tiefziehbarkeit

Country Status (9)

Country Link
EP (1) EP0754770B1 (de)
JP (1) JPH0931539A (de)
KR (1) KR970005422A (de)
AT (1) ATE208831T1 (de)
DE (1) DE69616887T2 (de)
DK (1) DK0754770T3 (de)
ES (1) ES2164222T3 (de)
FR (1) FR2736933B1 (de)
PT (1) PT754770E (de)

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2767078B1 (fr) * 1997-08-07 1999-10-22 Lorraine Laminage Procede d'elaboration d'une tole mince en acier a ultra bas carbone pour la realisation de produits emboutis pour emballage et tole mince obtenue

Family Cites Families (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE1247251B (de) * 1964-04-25 1967-08-17 Opel Adam Ag Ziehblech fuer Ziehteile
JPS5832218B2 (ja) * 1978-08-22 1983-07-12 川崎製鉄株式会社 プレス性とくに形状凍結性の優れた高張力鋼板の製造方法
JPS61291924A (ja) * 1985-06-17 1986-12-22 Nippon Steel Corp 加工性の優れたプレス成形用鋼板の製造方法
DE3603691A1 (de) * 1986-02-06 1987-08-20 Hoesch Stahl Ag Alterungsfreier bandstahl
US5041166A (en) * 1989-09-11 1991-08-20 Kawasaki Steel Corporation Cold-rolled steel sheet for deep drawing and method of producing the same
ATE135414T1 (de) * 1990-11-09 1996-03-15 Nippon Steel Corp Kaltgewalztes stahlband mit hervorragender pressverformbarkeit und verfahren zur herstellung

Also Published As

Publication number Publication date
DE69616887T2 (de) 2002-05-29
FR2736933B1 (fr) 1997-08-22
FR2736933A1 (fr) 1997-01-24
ATE208831T1 (de) 2001-11-15
DE69616887D1 (de) 2001-12-20
JPH0931539A (ja) 1997-02-04
EP0754770A1 (de) 1997-01-22
KR970005422A (ko) 1997-02-19
ES2164222T3 (es) 2002-02-16
DK0754770T3 (da) 2002-02-25
PT754770E (pt) 2002-05-31

Similar Documents

Publication Publication Date Title
EP2155916B2 (de) Stahl von geringer dichte mit guten prägeeigenschaften
EP1592816B1 (de) Herstellungsverfahren eines mit ferritisch-martensitischem gefüge zweiphasigen kaltgewaltzten stahlbandes, sowie derart hergestelltes stahlband
EP2630269B1 (de) Warm- oder kaltgewaltes stahlblech, dessen hestellungsvefahren und dessen verwendung in der automobilindustrie
EP1427866B1 (de) Verfahren zur herstellung von geschweissten röhren und dadurch hergestelltes rohr
EP0524162A2 (de) Verfahren zur Herstellung eines dünnen Bandes aus Weichstahl
EP0896069B1 (de) Verfahren zum Herstellen eines dünnes Bandes aus Stahl mit sehr niedriger Kohlenstoffgehalt zur Herstellung von tiefgezogene Produkten für Verpackungen und also hergestelltes dünnes Band
EP1099769B1 (de) Verfahren zur Herstellung von warmgewalztem, hochfestem Stahlblech zur Umformung und insbesondere zum Tiefziehen
EP0754770B1 (de) Verfahren zum Herstellen eines dünnen Blechbandes mit verbesserter Tiefziehbarkeit
EP1065286B1 (de) Stahlband mit geringem Aluminiumgehalt für Behälter
EP0811081B1 (de) Verfahren zum herstellen von stahlblechern oder bandern fur die herstellung von dosen und also hergestelltes stahlband oder stahlblech
EP0521808B1 (de) Verfahren zum Herstellen von Tiefziehblechen
EP0718411B1 (de) Verfahren zum Herstellen von Stahlband zum Tiefziehen von Stahldosen
EP1065283B1 (de) Aluminiumberuhigtes Stahlband mit mittelhohem Kohlenstoffgehalt für Behälter
EP1065282B1 (de) Stahlband mit geringem Aluminiumgehalt für Behälter
EP1065284B2 (de) Aluminiumberuhigtes, niedriggekohltes Stahlband für Behälter
EP1065285B2 (de) Aluminiumberuhigtes, niedriggekohltes Stahlband für Behälter
FR2769251A1 (fr) Procede de fabrication d'une bande de tole d'acier pour la realisation d'emballages metalliques par emboutissage et tole d'acier obtenue
EP0699769B1 (de) Verfahren zur Herstellung eines tiefziehfähigen Verpackungsstahlen und nach diesem Verfahren hergestellter Stahl
JPH0759734B2 (ja) 加工性、肌荒れ性及びイヤリング性に優れた低炭素アルミニウムキルド冷延鋼板及びその製造方法
BE1005147A6 (fr) Procede de fabrication d'une bande ultra-mince en acier laminee a froid.

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 CH DE DK ES FI FR GB GR IE IT LI LU NL PT SE

17P Request for examination filed

Effective date: 19970205

17Q First examination report despatched

Effective date: 19990607

GRAG Despatch of communication of intention to grant

Free format text: ORIGINAL CODE: EPIDOS AGRA

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): AT BE CH DE DK ES FI FR GB GR IE IT LI LU NL PT SE

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: 20011114

REF Corresponds to:

Ref document number: 208831

Country of ref document: AT

Date of ref document: 20011115

Kind code of ref document: T

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

Free format text: FRENCH

REF Corresponds to:

Ref document number: 69616887

Country of ref document: DE

Date of ref document: 20011220

REG Reference to a national code

Ref country code: GB

Ref legal event code: IF02

REG Reference to a national code

Ref country code: ES

Ref legal event code: FG2A

Ref document number: 2164222

Country of ref document: ES

Kind code of ref document: T3

REG Reference to a national code

Ref country code: DK

Ref legal event code: T3

GBT Gb: translation of ep patent filed (gb section 77(6)(a)/1977)

Effective date: 20020220

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

Ref country code: CH

Payment date: 20020517

Year of fee payment: 7

REG Reference to a national code

Ref country code: GR

Ref legal event code: EP

Ref document number: 20010402557

Country of ref document: GR

REG Reference to a national code

Ref country code: PT

Ref legal event code: SC4A

Free format text: AVAILABILITY OF NATIONAL TRANSLATION

Effective date: 20020211

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

Ref country code: DE

Payment date: 20020603

Year of fee payment: 7

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

Ref country code: FR

Payment date: 20020611

Year of fee payment: 7

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

Ref country code: PT

Payment date: 20030523

Year of fee payment: 8

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

Ref country code: GR

Payment date: 20030529

Year of fee payment: 8

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

Ref country code: NL

Payment date: 20030530

Year of fee payment: 8

Ref country code: GB

Payment date: 20030530

Year of fee payment: 8

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

Ref country code: IE

Payment date: 20030603

Year of fee payment: 8

Ref country code: AT

Payment date: 20030603

Year of fee payment: 8

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

Ref country code: SE

Payment date: 20030604

Year of fee payment: 8

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

Ref country code: LU

Payment date: 20030605

Year of fee payment: 8

Ref country code: FI

Payment date: 20030605

Year of fee payment: 8

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

Ref country code: DK

Payment date: 20030610

Year of fee payment: 8

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

Ref country code: BE

Payment date: 20030612

Year of fee payment: 8

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

Ref country code: ES

Payment date: 20030617

Year of fee payment: 8

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 NON-PAYMENT OF DUE FEES

Effective date: 20030630

Ref country code: CH

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

Effective date: 20030630

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: 20040101

Ref country code: DE

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

Effective date: 20040101

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: 20040227

NLV4 Nl: lapsed or anulled due to non-payment of the annual fee

Effective date: 20040101

REG Reference to a national code

Ref country code: FR

Ref legal event code: ST

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: LU

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

Effective date: 20040620

Ref country code: GB

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

Effective date: 20040620

Ref country code: FI

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

Effective date: 20040620

Ref country code: AT

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

Effective date: 20040620

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 NON-PAYMENT OF DUE FEES

Effective date: 20040621

Ref country code: IE

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

Effective date: 20040621

Ref country code: ES

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

Effective date: 20040621

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 NON-PAYMENT OF DUE FEES

Effective date: 20040630

Ref country code: BE

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

Effective date: 20040630

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 NON-PAYMENT OF DUE FEES

Effective date: 20041220

BERE Be: lapsed

Owner name: S.A. *SOLLAC

Effective date: 20040630

REG Reference to a national code

Ref country code: DK

Ref legal event code: EBP

EUG Se: european patent has lapsed
EUG Se: european patent has lapsed
GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20040620

REG Reference to a national code

Ref country code: PT

Ref legal event code: MM4A

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

Effective date: 20041220

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: IT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES;WARNING: LAPSES OF ITALIAN PATENTS WITH EFFECTIVE DATE BEFORE 2007 MAY HAVE OCCURRED AT ANY TIME BEFORE 2007. THE CORRECT EFFECTIVE DATE MAY BE DIFFERENT FROM THE ONE RECORDED.

Effective date: 20050620

REG Reference to a national code

Ref country code: ES

Ref legal event code: FD2A

Effective date: 20040621