EP0227001B1 - Procédé de fabrication d'outils - Google Patents

Procédé de fabrication d'outils Download PDF

Info

Publication number
EP0227001B1
EP0227001B1 EP86117455A EP86117455A EP0227001B1 EP 0227001 B1 EP0227001 B1 EP 0227001B1 EP 86117455 A EP86117455 A EP 86117455A EP 86117455 A EP86117455 A EP 86117455A EP 0227001 B1 EP0227001 B1 EP 0227001B1
Authority
EP
European Patent Office
Prior art keywords
process according
phase
grain size
grain
deformation
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
EP86117455A
Other languages
German (de)
English (en)
Other versions
EP0227001A3 (en
EP0227001A2 (fr
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.)
Frommeyer Georg Dr
Robert Zapp Werkstofftechnik & Co KG GmbH
Original Assignee
Frommeyer Georg Dr
Robert Zapp Werkstofftechnik & Co KG GmbH
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 Frommeyer Georg Dr, Robert Zapp Werkstofftechnik & Co KG GmbH filed Critical Frommeyer Georg Dr
Priority to AT86117455T priority Critical patent/ATE90899T1/de
Publication of EP0227001A2 publication Critical patent/EP0227001A2/fr
Publication of EP0227001A3 publication Critical patent/EP0227001A3/de
Application granted granted Critical
Publication of EP0227001B1 publication Critical patent/EP0227001B1/fr
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/12—Both compacting and sintering
    • B22F3/16—Both compacting and sintering in successive or repeated steps
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/10—Alloys containing non-metals

Definitions

  • the invention relates to a method for producing tools from alloyed steels or stellites by thermoforming.
  • Tool steels and stellites or hard metals are generally characterized by high levels of carbon, chromium, cobalt, molybdenum, vanadium and tungsten. Together with the corresponding carbides, these elements give the material the necessary strength, in particular wear resistance and hardness. However, this is usually at the expense of toughness and is associated with a corresponding increase in the resistance to deformation.
  • a method is known from US Pat. No. 3,951,697 is known in which steels with a very high carbon content are set after a heat treatment at at least 500 ° C by deformation on an equiaxed basic structure with a finely dispersed spherulitic cementite.
  • This process is also suitable for the use of powders as the starting material. This is done in such a way that a starting powder with a carbon content of more than 1%, the carbon of which is predominantly in the form of spherulitic cementite, is mixed with an iron powder with a grain size of less than 10 ⁇ m, then compacted and then sintered at 600 to 700 ° C.
  • the structure of the sintered compact mainly consists of a coaxial grain with an average grain size of less than 10 ⁇ m and an evenly distributed, mainly spherulitic cementite in the temperature range from 723 to 900 ° C. Apart from powder compaction, no deformation takes place in the known method. In addition, the process only affects iron-carbon materials with a carbon content of over 1.0% and otherwise only impurities such as 0.4 to 0.5% manganese and 0.1 to 0.2% silicon.
  • the invention has for its object to provide a method which avoids the aforementioned disadvantages and allows the production of finished parts from alloys, which due to their high deformation resistance normally cannot be deformed or at most can be deformed into a blank which requires machining.
  • a stellitic preform with an equiaxial structure and over 30 vol.% Carbidic and / or boridic precipitation phase is thermoformed at 700 to 1000.degree. C., thereby forming a matrix with a grain size of 1 to 3 ⁇ m and one Elimination phase set with a grain size of 0.2 to 1.0 ⁇ m and finally superplastically shaped.
  • the small grain size set in the process according to the invention ensures a low yield stress due to grain boundary sliding and thus reduces the required forming force and tool wear.
  • the method according to the invention therefore runs in two stages;
  • the first stage of the process is to use the powder-metallurgically produced, due to the high cooling rate of, for example, 104 to 105 SchmelzK / s during melt atomization, already fine crystalline, preferably already equiaxial, multi-phase structure of the alloy powder both with regard to the matrix and also with regard to the carbidic and / or boridic precipitation phase to further refine the consolidated state and thereby a thermally stable microstructure during the subsequent thermomechanical processing as a result of hot forming in the second process stage, with a grain size of 1 to 3 ⁇ m or 0.2 to 1.0, which is preferably fine both for the matrix and for the precipitation phase ⁇ m.
  • the material structure in the first process stage can be conditioned by thermomechanical processing, which is the case with steel alloys in austenitic Condition, for example, begins at about 900 o C and the ⁇ / ⁇ phase conversion in the range from 750 to 820 o C to a final rolling temperature of 650 o C goes through.
  • thermomechanical processing which is the case with steel alloys in austenitic Condition, for example, begins at about 900 o C and the ⁇ / ⁇ phase conversion in the range from 750 to 820 o C to a final rolling temperature of 650 o C goes through.
  • the material to be deformed cools down continuously and, in addition to the phase change, the carbides and / or borides are eliminated.
  • the carbides and / or borides are eliminated in the hot forming of stellites in the temperature range from 1000 to 700 ° C. during the shaping and the associated continuous cooling.
  • thermomechanical conditioning there is a refinement of the matrix grain, which is then equiaxial at the latest, as well as a finer dispersion of the carbide and boride particles as a result of the favorable conditions for nucleation during the phase change. Both have an impact in the direction of higher material strength.
  • the conditioning of the starting material produced by powder metallurgy can also be carried out by isothermal shaping with the aim of recrystallizing the structure and setting a fine-grained structure as a prerequisite for the superplastic state.
  • the isothermal deformation takes place at temperatures below the transformation temperature, for example at 450 ° C., preferably with a low degree of deformation, for example with a cross-sectional decrease of about 10%, and should include a cyclic ⁇ / ⁇ phase transformation which, owing to the different volumes of the ⁇ and ⁇ phase to internal tensions and thus to internal internal tensions induced deformation of the matrix grain.
  • This can be followed by a short primary recrystallization annealing, for example 20 to 60 seconds, to refine the matrix grain size of the hot isostatically pressed blank, which leads to a further grain refinement.
  • the aim of the conditioning of the starting material is to establish a structure which is equiaxial for superplastic shaping in the second process stage and which is characterized by a fine structure grain which favors the forming behavior.
  • the resistance to deformation is reduced and, at the same time, the rate of deformation can be increased.
  • the formed material which is adjusted to a specific multiphase structure, is shaped at a temperature in the order of 50 to 70% of the melting temperature of, for example, 650 to 780 o C, which allows high degrees of deformation at low flow stresses and therefore also manufacture Complicated finished parts made of alloys, the composition of which does not allow shaping by forming without the special pretreatment of the first stage of the method according to the invention.
  • the forming speed is preferably 10 ⁇ 3 to 5.10 ⁇ 1 s ⁇ 1.
  • the forming temperature is below the temperature of the beginning secondary crystallization or grain coarsening, since each grain growth increases the resistance to deformation and therefore requires higher deformation forces.
  • the method according to the invention is particularly suitable for high-carbon cold work steels such as X 178 Cr V 5 2 9 X 155 Cr VW Co 4 5 12 5 X 135 Cr VW Mo 4 4 6 4 X 220 Cr V 17 6 X 245 Cr V 5 10 These have carbon contents from 1.0 to 2.5% and high alloy contents of chromium, vanadium, tungsten, molybdenum and cobalt from 4 to 17%.
  • the following alloys are also suitable: X 375 Cr Mo Fe 25 10 60 X 220 Cr W Co 30 12 56 X 120 Cr Mo Co 27 4 60 X 100 Cr W Co NB 15 15 52 3.
  • the Stellite are iron and cobalt-based stellite with high boron and carbon contents of 1 to 4%, and contents of the alloying elements chromium, molybdenum, tungsten, 15 to 30%, which can be transformed at a relatively low temperature of 650-720 o C.
  • the superplastic shape can be followed by coarse grain annealing in order to increase the creep resistance or heat resistance.
  • the round blank 1 shown in FIG. 1 consists of the high-strength cold work steel X 245 Cr V 5 10, which was produced by powder metallurgy by hot isostatic pressing and was set to a structure with a matrix grain size of 1 to 3 ⁇ m. It serves to manufacture the disk-shaped rotary knife shown in FIG. 2 with a cone angle ⁇ of 150 to 160 ° , a thickness of 1.0 to 1.5 mm and an inner diameter of 50 mm and an outer diameter of 100 mm.
  • the circular blank 1 was produced by punching from a powder metallurgy and then rolled out at a temperature of 1150 to 1250 ° C. to a thickness of 2.5 mm and measuring 100 ⁇ 200 ⁇ 8 mm. In order to create a sufficient material reserve for the formation of the cutting edges 2 of the rotary knife, the thickness of the board exceeded the finished thickness of the rotary knife by 1 mm.
  • the low forming temperature saves energy, ensures minimal scaling and prevents harmful grain growth.
  • superplastic forming results in a higher density because pores and cracks weld, as well as higher strength and toughness. Because there is no machining, there are no fatigue cracks in the machining grooves, which increases the tool life by 25 to 30%.
  • the method according to the invention is suitable for producing cut bells and tools, shape cutting tools, knives, for example disc, filter and tobacco knives with a thickness of less than 3 mm, embossing dies, jam and pressure rings for extruders, sintering compression tools, extrusion tools and dies, molding tools for the wobble extrusion and multi-hole plates each made of cold work steels, for the production of profile milling cutters, form turning steels and profile countersunk heads from high speed steels as well as for the production of glass blow molding tools, profile rods, nozzles, impellers, turbine disks and valve seats made of stellites. It is characterized by low forming temperatures and a low power requirement.
  • the finely dispersed, equiaxial and texture-free microstructure guarantees constant and reproducible mechanical properties, in particular high strength with excellent ductility and good fatigue behavior.
  • the dimensional accuracy and surface quality are so good that reworking is not necessary.
  • the surface roughness is usually less than 1 ⁇ m.

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)
  • Manufacturing & Machinery (AREA)
  • Forging (AREA)
  • Powder Metallurgy (AREA)
  • Turning (AREA)
  • Treatment Of Steel In Its Molten State (AREA)

Claims (16)

  1. Procédé de fabrication d'outils en acier, dans lequel on comprime à chaud une ébauche préparée par métallurgie des poudres, caractérisé en ce qu'on déforme à chaud une ébauche en acier hautement allié à structure cristalline équiaxiale et comprenant plus de 30 % en volume d'une phase précipitée de carbure et/ou de borure au-dessous de A1 avec une conversion de phase alpha/gamma cyclique ou à l'état austénitique et on établit ainsi une matrice avec une taille de grain de 1 à 3 µm et une phase précipitéc avec une taille de grain de 0,2 à 1,0 µm, et en ce qu'on termine cette ébauche par déformation superplastique.
  2. Procédé de fabrication d'outils en acier, dans lequel on comprime à chaud une ébauche préparée par métallurgie des poudres, caractérisé en ce qu'on déforme à chaud une ébauche stellitique à structure cristalline équiaxiale et comprenant plus de 30 % en volume d'une phase précipitée de carbure et/ou de borure à 700 à 1000°C et on établit ainsi une matrice avec une taille de grain de 1 à 3 µm et une phase préclpitée de 0,2 à 1,0 µm, et en ce qu'on termine cette ébauchc par déformation superplastique.
  3. Procédé selon l'une ou l'autre des revendications 1 et 2, caractérisé en ce qu'on déforme un matériau de départ présentant une structure cristalline équiaxiale de manière superplastique jusqu'à la taille finale.
  4. Procédé selon l'une ou plusieurs des revendications 1 à 3, caractérisée en ce que l'on déforme de manière superplastique des aciers à outils préparés par métallurgie des poudres et des stellites à des températures d'environ 0,5 à 0,7 Tm, puis qu'on les refroidit de manière continue.
  5. Procédé selon la revendication 4, caractérisé par une température de déformation de 900 à 650 °C.
  6. Procédé selon l'une quelconque des revendications 1 à 3, caractérisé en ce qu'on déforme à chaud un matériau de départ stellitique pendant un refroidissement continu de 1000 °C jusqu'à 760 °C.
  7. Procédé selon l'une quelconque des revendications 4 à 6, caractérisé en ce que le taux de déformation est supérieur à 30 % et l'allongement s'élève à quelques centaines de pourcent.
  8. Procédé selon l'une quelconque des revendications 1 à 3, caractérisé en ce qu'on déforme de manière isotherme et superplastique des aciers a outils, préparés par métallurgie des poudres, au-dessous de leur température de transition.
  9. Procédé selon la revendication 8, caractérisé en ce que le taux de déformation s'élève jusqu'à 800 %.
  10. Procédé selon l'une ou l'autre des revendications 8 et 9, caractérisé par un glissement des joints intergranulaires et une recristallisation dynamique à 600 à 700 °C.
  11. Procédé selon l'une quelconque des revendications 1 à 10, caractérisé par un formage superplastique à une température au-dessous de la température de recristallisation secondaire et de croissance des grains.
  12. Procédé selon l'une quelconque des revendications 8 à 11, caractérisé par un formage superplastique d'alliages d'acier à 650 à 780 °C.
  13. Procédé selon l'une ou l'autre des revendications 11 et 12, caractérisé en ce que la vitesse de déformation ε est de 10⁻³ à 10⁻¹s⁻¹.
  14. Procédé selon l'une ou plusieurs des revendications 11 à 13, caractérisé en ce que l'exposant m de la vitesse d'allongement est de 0,4 à 0,5.
  15. Procédé selon l'une ou plusieurs des revendications 11 à 13, caractérisé en ce que l'exposant m de la vitesse d'allongement pour de la stellite est de 0,35 à 0,4.
  16. Procédé selon l'une ou plusieurs des revendications 11 à 15, caractérisé en ce que les articles formés sont soumis à un recuit pour grossissement des grains.
EP86117455A 1985-12-18 1986-12-16 Procédé de fabrication d'outils Expired - Lifetime EP0227001B1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
AT86117455T ATE90899T1 (de) 1985-12-18 1986-12-16 Verfahren zum herstellen von werkzeugen.

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE19853544759 DE3544759A1 (de) 1985-12-18 1985-12-18 Verfahren zum herstellen von werkzeugen
DE3544759 1985-12-18

Publications (3)

Publication Number Publication Date
EP0227001A2 EP0227001A2 (fr) 1987-07-01
EP0227001A3 EP0227001A3 (en) 1988-05-04
EP0227001B1 true EP0227001B1 (fr) 1993-06-23

Family

ID=6288747

Family Applications (1)

Application Number Title Priority Date Filing Date
EP86117455A Expired - Lifetime EP0227001B1 (fr) 1985-12-18 1986-12-16 Procédé de fabrication d'outils

Country Status (6)

Country Link
US (1) US5028386A (fr)
EP (1) EP0227001B1 (fr)
JP (1) JPS62156203A (fr)
AT (1) ATE90899T1 (fr)
DE (1) DE3544759A1 (fr)
ES (1) ES2041242T3 (fr)

Families Citing this family (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4969099A (en) * 1986-03-11 1990-11-06 Toyota Jidosha Kabushiki Kaisha Double-detecting, trouble-judging and failsafe devices in system for integrally controlling automatic transmission and engine
US4945481A (en) * 1986-05-08 1990-07-31 Toyota Jidosha Kabushiki Kaisha System for integrally controlling automatic transmission and engine
US4838124A (en) * 1986-06-30 1989-06-13 Toyota Jidosha Kabushiki Kaisha System for integrally controlling automatic transmission and engine
JPH0712809B2 (ja) * 1986-07-07 1995-02-15 トヨタ自動車株式会社 自動変速機及びエンジンの一体制御装置
WO2005094274A2 (fr) * 2004-03-24 2005-10-13 Smith International, Inc. Traitement a l'etat solide de lames de couteaux manuels pour en ameliorer l'efficacite

Family Cites Families (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2127082A5 (fr) * 1971-02-22 1972-10-13 Charbonnages De France
JPS5510642B2 (fr) * 1973-10-31 1980-03-18
US4073648A (en) * 1974-06-10 1978-02-14 The International Nickel Company, Inc. Thermoplastic prealloyed powder
US3976482A (en) * 1975-01-31 1976-08-24 The International Nickel Company, Inc. Method of making prealloyed thermoplastic powder and consolidated article
US3951697A (en) * 1975-02-24 1976-04-20 The Board Of Trustees Of Leland Stanford Junior University Superplastic ultra high carbon steel
JPS5485106A (en) * 1977-12-20 1979-07-06 Seiko Epson Corp Magnet made from inter-rare-earth-metallic compound
JPS5887204A (ja) * 1981-11-17 1983-05-25 Kobe Steel Ltd 急冷凝固粉末を用いた超合金の恒温鍛造方法
JPS5893802A (ja) * 1981-11-30 1983-06-03 Sumitomo Electric Ind Ltd 難加工性合金線材の製造方法
US4533390A (en) * 1983-09-30 1985-08-06 Board Of Trustees Of The Leland Stanford Junior University Ultra high carbon steel alloy and processing thereof
DE3346089A1 (de) * 1983-12-21 1985-07-18 Dr. Weusthoff GmbH, 4000 Düsseldorf Verfahren zum herstellen hochfester, duktiler koerper aus kohlenstoffreichen eisenbasislegierungen
US4582536A (en) * 1984-12-07 1986-04-15 Allied Corporation Production of increased ductility in articles consolidated from rapidly solidified alloy
JPS62134130A (ja) * 1985-12-05 1987-06-17 Agency Of Ind Science & Technol 高強度・難加工材の超塑性ウオ−ムダイ・パツク鍛造法

Also Published As

Publication number Publication date
DE3544759C2 (fr) 1989-08-03
US5028386A (en) 1991-07-02
EP0227001A3 (en) 1988-05-04
ES2041242T3 (es) 1993-11-16
EP0227001A2 (fr) 1987-07-01
DE3544759A1 (de) 1987-06-19
JPS62156203A (ja) 1987-07-11
ATE90899T1 (de) 1993-07-15

Similar Documents

Publication Publication Date Title
EP3228724B1 (fr) Acier à outil, en particulier pour travail à chaud et objet en acier
DE2937724C2 (de) Pulvermetallurgisch hergestelltes Stahlerzeugnis mit hohem Vanadiumcarbid- Anteil
DE2621472C2 (de) Verwendung einer Hartlegierung für Schneid-,Scher-oder Verformungswerkzeuge
DE69814896T2 (de) Stahl und wärmebehandeltes werkzeug, hergestellt in einem integrierten pulvermetallurgischem prozess und die nutzung eines solchen stahles für werkzeuge
EP2359951A1 (fr) Outils dotés d'une région de travail thermo-mécaniquement modifiée et procédés pour la formation de tels outils
EP3409801B1 (fr) Matière composite contenant des particules dures, fabriquée par métallurgie des poudres, utilisation d'une matière composite et procédé de fabrication d'un composant en matière composite
DE1533275B1 (de) Verfahren zur pulvermetallurgischen Herstellung von Hartlegierungen
CH664976A5 (de) Verbundkoerper und verfahren zu seiner herstellung.
DE1298293B (de) Hochverschleissfeste, bearbeitbare und haertbare Sinterstahllegierung und Verfahren zu deren Herstellung
DE69906782T2 (de) Stahl, verwendung des stahls, daraus hergestelltes produkt und verfahren zu dessen herstellung
Kasak et al. Powder-metallurgy tool steels
DE2060605C3 (de) Pulvermetallurgisch durch Sintern hergestellte, ausscheidungshärtbare, korrosions- und hochwarmfeste Nickel-Chrom-Legierung
DE60019758T2 (de) Pulvermetallurgisch hergestellter schnellarbeitsstahl
EP4018006A1 (fr) Acier à outils pour applications de travail à froid et à grande vitesse
EP0322397B1 (fr) Acier à coupe rapide préparé par la métallurgie des poudres, objet résistant à l'usure et procédé de préparation de cet acier
EP1647606B1 (fr) Alliage de nickel résistant à l'usure et a dureté élevée, et son utilisation comme un outil à haute température
WO2003000457A1 (fr) Outil de coupe en forme de bande
EP0227001B1 (fr) Procédé de fabrication d'outils
DE2362650C3 (de) Verfahren zur Verbesserung der Wannverformbarkeit von Zerstäubungspulvern
Pinnow et al. P/M tool steels
EP1985390B1 (fr) Outils dotés d'une région de travail thermo-mécaniquement modifiée et procédés pour la formation de tels outils
EP0149210B1 (fr) Procédé de fabrication d'ébauches résistantes ductiles à partir d'alliages, à base de fer, riches en carbone
DE4436670C2 (de) Gegenstände aus Superlegierungen auf Nickelbasis mit verbesserter Zerspanbarkeit sowie Verfahren zur Herstellung eines spanend bearbeiteten Werkstücks aus einer derartigen Superlegierung
DE2840935C2 (de) Verfahren zur Herstellung eines Hartmetalls
EP1129803B1 (fr) Matériau préparé par métallurgie des poudres avec isotropie améliorée des propriétés mécaniques

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: A2

Designated state(s): AT BE CH ES FR GB GR IT LI LU NL SE

PUAL Search report despatched

Free format text: ORIGINAL CODE: 0009013

AK Designated contracting states

Kind code of ref document: A3

Designated state(s): AT BE CH ES FR GB GR IT LI LU NL SE

17P Request for examination filed

Effective date: 19881010

17Q First examination report despatched

Effective date: 19900323

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 ES FR GB GR IT LI LU NL SE

REF Corresponds to:

Ref document number: 90899

Country of ref document: AT

Date of ref document: 19930715

Kind code of ref document: T

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

Effective date: 19930630

ET Fr: translation filed
ITF It: translation for a ep patent filed
REG Reference to a national code

Ref country code: GR

Ref legal event code: FG4A

Free format text: 3008898

REG Reference to a national code

Ref country code: ES

Ref legal event code: FG2A

Ref document number: 2041242

Country of ref document: ES

Kind code of ref document: T3

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

Ref country code: GB

Payment date: 19931125

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: 19931216

Year of fee payment: 8

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

Ref country code: FR

Payment date: 19931217

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: 19931221

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: 19931222

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: 19931227

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: 19931231

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: 19940104

Year of fee payment: 8

EPTA Lu: last paid annual fee
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
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: 19941216

Ref country code: GB

Effective date: 19941216

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

Ref country code: SE

Effective date: 19941217

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

Ref country code: BE

Effective date: 19941231

EAL Se: european patent in force in sweden

Ref document number: 86117455.5

BERE Be: lapsed

Owner name: FROMMEYER GEORG

Effective date: 19941231

Owner name: ROBERT ZAPP WERKSTOFFTECHNIK G.M.B.H. & CO K.G.

Effective date: 19941231

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

Ref country code: GR

Free format text: THE PATENT HAS BEEN ANNULLED BY A DECISION OF A NATIONAL AUTHORITY

Effective date: 19950630

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

Ref country code: NL

Effective date: 19950701

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

Effective date: 19941216

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

Ref country code: FR

Effective date: 19950831

REG Reference to a national code

Ref country code: GR

Ref legal event code: MM2A

Free format text: 3008898

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

Effective date: 19950701

EUG Se: european patent has lapsed

Ref document number: 86117455.5

REG Reference to a national code

Ref country code: FR

Ref legal event code: ST

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: 19951217

REG Reference to a national code

Ref country code: ES

Ref legal event code: FD2A

Effective date: 19960113

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

Ref country code: AT

Payment date: 20041227

Year of fee payment: 19

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

Ref country code: CH

Payment date: 20041229

Year of fee payment: 19

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: 20051216

Ref country code: AT

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

Effective date: 20051216

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: 20051231

Ref country code: CH

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

Effective date: 20051231

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL