EP0996757B1 - Karbonnitridlegierung auf titanbasis mit nitrierter oberflächenzone - Google Patents
Karbonnitridlegierung auf titanbasis mit nitrierter oberflächenzone Download PDFInfo
- Publication number
- EP0996757B1 EP0996757B1 EP98923278A EP98923278A EP0996757B1 EP 0996757 B1 EP0996757 B1 EP 0996757B1 EP 98923278 A EP98923278 A EP 98923278A EP 98923278 A EP98923278 A EP 98923278A EP 0996757 B1 EP0996757 B1 EP 0996757B1
- Authority
- EP
- European Patent Office
- Prior art keywords
- atomic
- binder phase
- titanium
- phase
- cutting tool
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Lifetime
Links
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
- C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
- C22C29/04—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbonitrides
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C30/00—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process
- C23C30/005—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process on hard metal substrates
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
- C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
- C23C8/20—Carburising
-
- 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
- B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
-
- 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
- B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
- B22F2998/10—Processes characterised by the sequence of their steps
-
- 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
- B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy
Definitions
- the present invention relates to a liquid phase sintered body of a carbonitride alloy with titanium as main component which has improved properties particularly when used as cutting tool material in cutting operations requiring sharp edges in combination with high wear resistance and plastic deformation resistance. This has been achieved by heat treating the material in a nitrogen atmosphere.
- Titanium based carbonitride alloys so called cermets
- cermets are today well established as insert material in the metal cutting industry and are especially used for finishing. They consist of carbonitride hard constituents embedded in a metallic binder phase.
- the hard constituent grains generally have a complex structure with a core surrounded by a rim of other composition.
- group VIa elements In addition to titanium, group VIa elements, normally both molybdenum and tungsten and sometimes chromium, are added to facilitate wetting between binder and hard constituents and to strengthen the binder by means of solution hardening.
- Group IVa and/or Va elements i.e. Zr, Hf, V, Nb and Ta, are also added in all commercial alloys available today. All these additional elements are usually added as carbides, nitrides and/or carbonitrides.
- the grain size of the hard constituents is usually ⁇ 2 ⁇ m.
- the binder phase is normally a solid solution of mainly both cobalt and nickel.
- the amount of binder phase is generally 3 - 25 wt%.
- Other elements are sometimes added as well, e.g. aluminium, which are said to harden the binder phase and/or improve the wetting between hard constituents and binder phase.
- cermets compared to WC-Co based material are relatively high wear resistance and chemical inertness can be obtained without applying surface coatings. This property is utilized mainly in extreme finishing operations requiring sharp edges and chemical inertness to cut at low feed and high speed. However, these desirable properties are generally obtained at the expense of toughness and edge security as well as ease of production.
- the most successful materials have large nitrogen content (N/(C+N) often exceeding 50%) which makes sintering in conventional processes difficult due to porosity caused by denitrification. High nitrogen content also makes the material difficult to grind. Grinding may be necessary to obtain sharp defect free edges and close tolerances.
- US 4,447,263 discloses inserts of a titanium based carbonitride alloy provided with a wear resistant surface layer of carbonitride or oxycarbonitride alone or in combination where the surface layer is completely free from binder phase.
- the layer is obtained by a heat treatment at 1100 - 1350°C in an atmosphere of N 2 , CO and/or CO 2 at subpressure.
- US 5,336,292 where the surface layer contains a low amount of binder phase but is separated from the interior of the material by a sharp interface to a binder phase enriched zone.
- the layer is obtained by heat treatment in an atmosphere of N 2 and/or NH 3 possibly in combination with at least one of CH 4 , CO and CO 2 at 1100 - 1350°C for 1-25 hours at atmospheric pressure or higher.
- the heat treatment is performed as a process step included in the cooling part of the sintering cycle or as a separate process e.g. as last production step, after any optional grinding operation has been performed.
- Fig 1 is a photomicrograph in 2000X showing a portion of an insert of the present invention.
- Fig 2 is an EMPA (electron Microprobe Analysis) line scan of Co, N, W, Ti and C in a portion of an insert of the present invention.
- Fig 3 is an X-ray diffractogram of the heat treated surface of an insert of the present invention.
- the sintered titanium-based carbonitride alloy of teh present invention contains 2-15 atomic %, preferably 2-6 atomic %, tungsten and/or molybdenum. Apart from titanium, the alloy contains 0-15 atomic % of group IVa and/or group Va elements, preferably 0-5 atomic % tantalum and/or niobium. As binder phase forming element 5-25 atomic %, preferably 9-16 atomic %, cobalt is added. The alloy has a N/(C+N) ratio in the range 10-60 atomic %, preferably 10-40 atomic %. Most preferably no elements apart from C, N, Ti, W, Ta and Co are intentionally added.
- the nitrogen content increases towards the surface.
- This enrichment is mainly due to the presence of TiN grains formed during heat treatment and can be identified by X-ray diffraction. These TiN grains may grow separately but can also grow epitaxially, forming an outer shell at least partly surrounding carbonitride grains.
- the nitrogen enriched zone has a binder phase content being approximately the same as in the bulk and being distributed all the way out to the surface.
- the Co content at the surface is 50-150 %, preferably 75-130%, most preferably 90-125%, of the bulk value depending on whether any Co gradient towards the surface was present in the material prior to heat treatment.
- the enriched zone is not a coating and not an essentially binder phase free hard phase layer.
- the Co-content in the surface zone is essentially the same as in the inner part of the body.
- Ti containing hard phase is seen as two distinct peaks, one peak originating from TiN, the other peak originating from mixed cubic carbonitride phase.
- the intensity ratio TiN(200)/TiCN(200) shall be >0.5, preferably >1, most preferably >1.5.
- a distinct peak originating from Co based binder phase is also seen.
- the alloy must not contain nickel and/or iron apart from inevitable impurities. For higher levels of these binder forming elements the desired microstructure cannot be produced. Instead an essentially binder phase free hard phase surface layer is formed. Such layers have been presented by previous inventors as an alternative to expensive coating operations but have inferior properties compared to CVD- and PVD coatings.
- the sintered carbonitride alloys according to the present invention are made by a method in which powders of carbides, carbonitrides and/or nitrides are mixed with Co to a prescribed composition and pressed into green bodies of desired shape.
- the green bodies are liquid phase sintered in vacuum or a controlled gas atmosphere at a temperature in the range 1370-1500 °C, preferably using the technique described in Swedish patent application 9701858-4.
- the inserts are heat treated at a temperature of 1150-1250 °C in an atmosphere comprising 500-1500 mbar, preferably 1000-1500 mbar, nitrogen gas for 1-40 hours, preferably 10-25 hours.
- nitrification can be used to enhance chemical inertness, wear resistance and plastic deformation resistance of cermets without obtaining a hard phase surface layer.
- the reason for this has turned out to be that in a Co based binder phase and at relatively high nitrogen pressures in the furnace, nitrogen diffusion from the surface is distinctly faster than titanium diffusion.
- TiN is nucleated inside the material rather than at the surface. The rate of TiN formation at a given depth from the surface is determined by the nitrogen activity at that depth. Ti is most probably taken predominantly from the rims of the hard phase grains. Thus, the rims are dissolved at least to some extent, leading to decreased grain size.
- a powder mixture with a chemical composition of (at%) 40.7% Ti, 3.6% W, 30.4% C 13.9% N and 11.4% Co was manufactured from Ti(C,N), WC and Co raw material powders.
- the mean grain size of the Ti(C,N) and WC powders were 1.4 ⁇ m.
- the powder mixture was wet milled, dried and pressed into green bodies of the insert type TNMG 160408-PF. The bodies were liquid phase sintered at 1430 °C for 90 minutes in a 10 mbar Ar atmosphere.
- Fig 1 shows polished cross sections of the inserts prepared by standard metallographic techniques and characterised using optical microscopy and electron microprobe analysis (EMPA). Optical microscopy showed that the inserts had a golden to bronze coloured approximately 40 ⁇ m thick surface zone, Fig 1.
- Fig 2 shows an EMPA line scan analysis of Co, N, W, Ti and C ranging from the surface and 500 ⁇ m into the material.
- Fig 3 shows an X-ray diffractogram of the heat treated surface.
- the Ti-based hard phase gives rise to two distinct series of peaks, one originating from TiN with an intensity being approximately twice that of the other, which originates from a carbonitride phase. Co peaks are also present in the diffractogram.
- TNMG160408-PF inserts were manufactured of a powder mixture consisting of (in atomic-%) Co 8.3, Ni 4.2, Ti 34.8, Ta 2.5, Nb 0.8, W 4.2, Mo 2, C 26.6 and N 16.6 and liquid phase sintered in a conventional process. These inserts were coated with an about 4 ⁇ m thick Ti(C,N)-layer and a less than 1 ⁇ m thick TiN-layer using the physical vapour deposition technique (PVD). This is a well established PVD-coated cermet grade within the P25-range for turning.
- PVD physical vapour deposition technique
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
- Powder Metallurgy (AREA)
- Cutting Tools, Boring Holders, And Turrets (AREA)
- Ceramic Products (AREA)
- Carbon And Carbon Compounds (AREA)
Claims (3)
- Schneidwerkzeugeinsatz aus gesinterter Carbonitridlegierung auf Titanbasis mit einem Gehalt an harten Bestandteilen auf der Basis von Ti, Zr, Hf, V, Nb, Ta, Cr, Mo und/oder W in einer Kobaltbindephase, wobei diese Legierung kein Ni und/oder Fe enthält und eine 50 bis 60 µm, vorzugsweise 15 bis 50 µm, am meisten bevorzugt 20 bis 40 µm dicke, an Stickstoff angereicherte Oberflächenzone mit einem Bindephasengehalt aufweist, der etwa der gleiche wie in der Masse ist und vollständig bis zur Oberfläche hin verteilt ist, und einem Co-Gehalt an der Oberfläche im Bereich von 50 bis 150 %, vorzugsweise 75 bis 130 %, am meisten bevorzugt 90 bis 125 % des Massenwertes.
- Schneidwerkzeugeinsatz nach Anspruch 1, dadurch gekennzeichnet, dass ein Röntgenstrahlendiffraktogramm der Oberfläche zwei Gruppen von Peaks enthält, die von harter Phase auf Ti-Basis stammen, und eine Gruppe von Peaks enthält, die von einer Bindephase auf Co-Basis stammen, wobei das Intensitätsverhältnis TiN(200)/TiCN(200) >0,5, vorzugsweise >1, am meisten bevorzugt >1,5 ist.
- Schneidwerkzeugeinsatz nach einem der vorausgehenden Ansprüche, dadurch gekennzeichnet, dass er außer unvermeidbaren Verunreinigungen zusätzlich zu Titan 2 bis 15, vorzugsweise 2 bis 7 Atom-% Wolfram und/oder Molybdän, 0 bsi 15 Atom-% Elemente der Gruppe IVa and/oder Va außer Titan, Wolfram und/oder Molybdän, vorzugsweise 0 bis 5 Atom-% Tantal und/oder Niob, 5 bis 25, vorzugsweise 9 bis 16 Atom-% Kobalt und mit einem mittleren N/(C+N)-Verhältnis im Bereich von 10 bis 60, vorzugsweise 10 bis 40 Atom-% enthält.
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
SE9701859A SE9701859D0 (sv) | 1997-05-15 | 1997-05-15 | Titanium based carbonitride alloy with nitrogen enriched surface zone |
SE9701859 | 1997-05-15 | ||
PCT/SE1998/000910 WO1998051831A1 (en) | 1997-05-15 | 1998-05-15 | Titanium based carbonitride alloy with nitrided surface zone |
Publications (2)
Publication Number | Publication Date |
---|---|
EP0996757A1 EP0996757A1 (de) | 2000-05-03 |
EP0996757B1 true EP0996757B1 (de) | 2002-11-20 |
Family
ID=20406993
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP98923278A Expired - Lifetime EP0996757B1 (de) | 1997-05-15 | 1998-05-15 | Karbonnitridlegierung auf titanbasis mit nitrierter oberflächenzone |
Country Status (7)
Country | Link |
---|---|
EP (1) | EP0996757B1 (de) |
JP (1) | JP4170402B2 (de) |
AT (1) | ATE228175T1 (de) |
DE (1) | DE69809555T2 (de) |
IL (1) | IL132346A (de) |
SE (1) | SE9701859D0 (de) |
WO (1) | WO1998051831A1 (de) |
Families Citing this family (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
SE519830C2 (sv) * | 1999-05-03 | 2003-04-15 | Sandvik Ab | Titanbaserad karbonitridlegering med bindefas av kobolt för finbearbetning |
SE519832C2 (sv) * | 1999-05-03 | 2003-04-15 | Sandvik Ab | Titanbaserad karbonitridlegering med bindefas av kobolt för lätt finbearbetning |
SE519834C2 (sv) * | 1999-05-03 | 2003-04-15 | Sandvik Ab | Titanbaserad karbonitridlegering med bindefas av kobolt för seghetskrävande finbearbetning |
SE0103970L (sv) * | 2001-11-27 | 2003-05-28 | Seco Tools Ab | Hårdmetall med bindefasanrikad ytzon |
US7175687B2 (en) * | 2003-05-20 | 2007-02-13 | Exxonmobil Research And Engineering Company | Advanced erosion-corrosion resistant boride cermets |
US7316724B2 (en) * | 2003-05-20 | 2008-01-08 | Exxonmobil Research And Engineering Company | Multi-scale cermets for high temperature erosion-corrosion service |
JP4703122B2 (ja) * | 2004-03-23 | 2011-06-15 | 京セラ株式会社 | TiCN基サーメットの製造方法 |
JP4703123B2 (ja) * | 2004-03-23 | 2011-06-15 | 京セラ株式会社 | 表面被覆TiCN基サーメットの製造方法 |
EP2058070B1 (de) * | 2006-08-31 | 2014-02-26 | Kyocera Corporation | Schneidwerkzeug, herstellungsverfahren dafür und schneidverfahren |
Family Cites Families (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4447263A (en) * | 1981-12-22 | 1984-05-08 | Mitsubishi Kinzoku Kabushiki Kaisha | Blade member of cermet having surface reaction layer and process for producing same |
SE9101865D0 (sv) * | 1991-06-17 | 1991-06-17 | Sandvik Ab | Titanbaserad karbonitridlegering med slitstarkt ytskikt |
ES2112053T3 (es) * | 1994-05-03 | 1998-03-16 | Widia Gmbh | Ceramel y procedimiento para su fabricacion. |
-
1997
- 1997-05-15 SE SE9701859A patent/SE9701859D0/xx unknown
-
1998
- 1998-05-15 JP JP54915998A patent/JP4170402B2/ja not_active Expired - Fee Related
- 1998-05-15 AT AT98923278T patent/ATE228175T1/de not_active IP Right Cessation
- 1998-05-15 EP EP98923278A patent/EP0996757B1/de not_active Expired - Lifetime
- 1998-05-15 DE DE69809555T patent/DE69809555T2/de not_active Expired - Fee Related
- 1998-05-15 IL IL13234698A patent/IL132346A/xx not_active IP Right Cessation
- 1998-05-15 WO PCT/SE1998/000910 patent/WO1998051831A1/en active IP Right Grant
Also Published As
Publication number | Publication date |
---|---|
EP0996757A1 (de) | 2000-05-03 |
IL132346A (en) | 2003-04-10 |
ATE228175T1 (de) | 2002-12-15 |
JP4170402B2 (ja) | 2008-10-22 |
JP2001524886A (ja) | 2001-12-04 |
DE69809555T2 (de) | 2003-03-27 |
WO1998051831A1 (en) | 1998-11-19 |
DE69809555D1 (de) | 2003-01-02 |
IL132346A0 (en) | 2001-03-19 |
SE9701859D0 (sv) | 1997-05-15 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
US4843039A (en) | Sintered body for chip forming machining | |
EP0600115B1 (de) | Mehrlagig beschichtetes Schneidwerkzeug aus Hartmetallegierung | |
EP1348779B1 (de) | Beschichtetes Schneidwerkzeug zur Drehbearbeitung von Stahl | |
EP0594875B1 (de) | Mehrfach plattiertes Hartlegierungsschneidwerkzeug | |
US5296016A (en) | Surface coated cermet blade member | |
US7794830B2 (en) | Sintered cemented carbides using vanadium as gradient former | |
US5694639A (en) | Titanium based carbonitride alloy with binder phase enrichment | |
USRE35538E (en) | Sintered body for chip forming machine | |
JP3934160B2 (ja) | 結合相富化した表面領域を有する超硬合金の製造方法 | |
US5336292A (en) | Titanium-based carbonitride alloy with wear resistant surface layer | |
US5589223A (en) | Process for producing cermet cutting tools having both longitudinal and granular crystal structures | |
US7544410B2 (en) | Hard metal or cermet body and method for producing the same | |
US5681651A (en) | Multilayer coated hard alloy cutting tool | |
EP1997938A2 (de) | Beschichtetes Schneidewerkzeug | |
KR20170103626A (ko) | 서멧, 절삭 공구, 및 서멧의 제조 방법 | |
US6193777B1 (en) | Titanium-based carbonitride alloy with nitrided surface zone | |
JP2008290239A (ja) | 耐熱衝撃性チタニウム基炭窒化物及びそれを製造するための焼結方法 | |
EP0812367B1 (de) | Karbonitridlegierung auf titanbasis mit kontrollierbarem verschleisswiderstand und zähigkeit | |
EP0996757B1 (de) | Karbonnitridlegierung auf titanbasis mit nitrierter oberflächenzone | |
EP1052297B1 (de) | Verfahren zur Herstellung von Ti(C,N)-(Ti,Ta,W)(C,N)-Co Legierungen für Schneidwerkzeug | |
US5856032A (en) | Cermet and process for producing it | |
EP1422304B1 (de) | TI(C,N)-(TI,NB,W)(C,N)-CO Legierung für Frässchneideinsätze | |
KR20040044156A (ko) | 다듬질 및 반다듬질 선삭 절삭 공구용Ti(C,N)-(Ti,Nb,W)(C,N)-Co 합금 | |
KR100334709B1 (ko) | 티탄탄화질화물계서멧절삭날및코팅된서멧절삭날 | |
JPH04231469A (ja) | 被覆TiCN基サーメット |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
PUAI | Public reference made under article 153(3) epc to a published international application that has entered the european phase |
Free format text: ORIGINAL CODE: 0009012 |
|
17P | Request for examination filed |
Effective date: 19991008 |
|
AK | Designated contracting states |
Kind code of ref document: A1 Designated state(s): AT CH DE FR GB IT LI SE |
|
17Q | First examination report despatched |
Effective date: 20011024 |
|
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 CH DE FR GB IT LI SE |
|
REF | Corresponds to: |
Ref document number: 228175 Country of ref document: AT Date of ref document: 20021215 Kind code of ref document: T |
|
REG | Reference to a national code |
Ref country code: GB Ref legal event code: FG4D |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: EP |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: NV Representative=s name: BOVARD AG PATENTANWAELTE |
|
REF | Corresponds to: |
Ref document number: 69809555 Country of ref document: DE Date of ref document: 20030102 |
|
ET | Fr: translation filed | ||
PLBE | No opposition filed within time limit |
Free format text: ORIGINAL CODE: 0009261 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT |
|
26N | No opposition filed |
Effective date: 20030821 |
|
REG | Reference to a national code |
Ref country code: GB Ref legal event code: 732E |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: PUE Owner name: SANDVIK INTELLECTUAL PROPERTY HB Free format text: SANDVIK AKTIEBOLAG##811 81 SANDVIKEN (SE) -TRANSFER TO- SANDVIK INTELLECTUAL PROPERTY HB##811 81 SANDVIKEN (SE) |
|
REG | Reference to a national code |
Ref country code: GB Ref legal event code: 732E |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: PUE Owner name: SANDVIK INTELLECTUAL PROPERTY AB Free format text: SANDVIK INTELLECTUAL PROPERTY HB##811 81 SANDVIKEN (SE) -TRANSFER TO- SANDVIK INTELLECTUAL PROPERTY AB##811 81 SANDVIKEN (SE) |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: TP |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: TP |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: SE Payment date: 20090512 Year of fee payment: 12 Ref country code: IT Payment date: 20090519 Year of fee payment: 12 Ref country code: FR Payment date: 20090515 Year of fee payment: 12 Ref country code: DE Payment date: 20090511 Year of fee payment: 12 Ref country code: AT Payment date: 20090514 Year of fee payment: 12 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: CH Payment date: 20090513 Year of fee payment: 12 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: GB Payment date: 20090513 Year of fee payment: 12 |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: PL |
|
GBPC | Gb: european patent ceased through non-payment of renewal fee |
Effective date: 20100515 |
|
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: 20100515 |
|
EUG | Se: european patent has lapsed | ||
REG | Reference to a national code |
Ref country code: FR Ref legal event code: ST Effective date: 20110131 |
|
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: 20100531 Ref country code: CH Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20100531 |
|
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: 20100516 Ref country code: IT Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20100515 |
|
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: 20101201 |
|
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: 20100531 |
|
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: 20100515 |