EP0750685B1 - Aluminium foil - Google Patents
Aluminium foil Download PDFInfo
- Publication number
- EP0750685B1 EP0750685B1 EP95911439A EP95911439A EP0750685B1 EP 0750685 B1 EP0750685 B1 EP 0750685B1 EP 95911439 A EP95911439 A EP 95911439A EP 95911439 A EP95911439 A EP 95911439A EP 0750685 B1 EP0750685 B1 EP 0750685B1
- Authority
- EP
- European Patent Office
- Prior art keywords
- foil
- aluminium foil
- rolled
- composition
- 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
Links
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
Definitions
- This invention is concerned with aluminium foil having improved strength.
- the good balance of strength and formability of thin gauge foil is obtained by achieving a combination of fine grain size after final annealing and dispersion strengthening.
- This invention describes the use of an additional strengthening mechanism to achieve increased strength; namely solid solution strengthening, and specifies the range within which the solute level must be controlled in order to avoid loss of other beneficial properties associated with the solute-free versions of these alloys.
- British Patent Specification 1 479 429 described dispersion-strengthened aluminium alloys based on the Al-Fe-Mn system, such as AA 8006 and AA 8014. (from Registration record of international alloy designations and chemical composition limits for wrought Al and wrought Al alloys, AA Inc. May 1987).
- the as-cast ingot comprised unaligned intermetallic rods. These were broken up during working to provide a wrought aluminium alloy product containing dispersed intermetallic particles.
- the invention was applicable to the production of rolled sheet, which was to some extent anisotropic. It was possible to reduce the relative proportions of the anisotropy by introducing small proportions of Cu and/or Mg which remained in solid solution in the Al phase and had known strength providing properties.
- the loss of anisotropy implies discontinuous recrystallisation and loss of grain size control, which changes would have been acceptable in the sheet products mainly envisaged and exemplified.
- JP-A- 1 034 548 described the production of high strength aluminium foil by twin-roller casting and having the composition 0.8-2wt% Fe, 0.1-1% Si, 0.01-0.5% Cu, 0.01-0.5% Mg, 0.01-1% Mu, one or more among ⁇ 0.1% Ti and ⁇ 0.05% B and the balance Aluminium. Final annealing is performed at 400°C.
- the successful production of aluminium foil having useful properties depends on several critical parameters.
- the metal to be rolled must not be too hard, otherwise rolling down to the very low thicknesses below 100 ⁇ m required is not commercially viable.
- the foil After rolling, the foil has to be heated, to a temperature sufficient to remove rolling lubricant but not so high that adjacent sheets of foil stick together.
- This temperature window is quite narrow, generally 220 - 300°C, and results in a final annealing treatment of the foil.
- recrystallisation takes place, and it is necessary that this be continuous recrystallisation, which retains a desired small grain size, rather than discontinuous recrystallisation, which results in grain growth. If large grains are present, the foil has reduced mechanical properties. While these critical parameters have long been achieved using Al-Fe-Mn alloys, it was not apparent that they could be achieved in combination with solid solution hardening. And indeed, as the inventors have discovered, the nature and amount of solute that can be added is critically circumscribed.
- this invention provides aluminium foil composed of an alloy of composition by weight %: Fe 1.2 - 2.0% Mn 0.2 - 1.0% Mg and/or Cu 0.1 - 0.5% Si up to 0.4% Zn up to 0.1% Ti up to 0.1% balance Al of at least commercial purity which foil has an average grain size below 5 ⁇ m after final annealing.
- the invention provides aluminium foil of the stated composition, wherein at least 50% by volume of the as-rolled texture is retained after final anneal.
- the invention provides aluminium foil of the stated composition, wherein the crystallographic texture of the final annealed product is a retained rolling texture.
- the aluminium foil preferably has a thickness below 100 ⁇ m, particularly in the range 5 - 40 ⁇ m e.g. 10 - 20 ⁇ m.
- the improved strength of foil according to this invention should enable thinner gauges to be marketed.
- Fe and Mn are present to provide dispersion strengthening properties, as described in the aforesaid GB 1 479 429.
- the Fe content is 1.4 - 1.8%; the Mn content is 0.3 - 0.6%; and the Fe + Mn content is 1.8 - 2.15%.
- Mg and/or Cu is added to provide solution strengthening, in a concentration of 0.1 - 0.5% preferably 0.15 - 0.35%. At the lower end of these ranges, little strengthening is observed. At the upper end of these ranges, there is a risk that the solute will encourage discontinuous recrystallisation and will result in undesired grain growth. This risk is particularly apparent at relatively high annealing temperatures. As shown in the examples, Mg provides a better solution strengthening effect than Cu at equivalent concentrations and is accordingly preferred.
- Mg and Cu are the only two usable solution strengthening additives.
- Si and Zn are included in the AA specifications of AA 8006 and AA 8014. But they are preferably not deliberately included here. It is an advantage of the invention that recycled scrap metal can be used to make the foil.
- the foil is specified as having an average (or mean) grain size below 5 ⁇ m, preferably below 3 ⁇ m.
- the grain size is preferably substantially uniform, and is achieved as a result of continuous recrystallisation during final anneal. Alternatively a non-uniform grain size may be acceptable provided that gross discontinuous recrystallisation during final anneal is avoided.
- the majority of grains may have a size of 2-3 ⁇ m with a minor proportion of grains of 10-30 ⁇ m. This duplex grain size structure may reduce the ductility of the foil, but the overall properties may nevertheless be satisfactory.
- Grain size may be determined by the mean linear intercept method. On a micrograph of a section of the alloy under test, a line (e.g. a straight line or a circle) of known length is drawn, and a count is made of the number of intercepts of that line with grain boundaries.
- the mean linear intercept grain size (mean grain size) is the length of the line divided by the number of intercepts.
- the foil is generally anisotropic. Cold-rolling develops an as-rolled texture typical of dilute Al alloys. Texture is conventionally measured from an orientation distribution function in terms of six parameters (cube, goss, copper, S, brass and random). Conventionally, these are measured as a volume fraction of crystals orientated over a ⁇ 15° spread about the appropriate Miller indices which are ⁇ 001 ⁇ 100>, ⁇ 110 ⁇ 001>, ⁇ 112 ⁇ 111>, ⁇ 123 ⁇ 634>, ⁇ 011 ⁇ 211> respectively, the random component being the remaining volume fraction.
- the copper, S and brass components are generated by cold rolling. Discontinuous recrystallisation would tend to destroy the as-rolled texture and favour the formation of cube and/or goss and/or random.
- the foil of this invention at least 50% by volume, preferably 75% of this as-rolled texture as represented by the copper, S and brass components is retained after final anneal.
- the crystallographic texture of the final annealed product is substantially the same as the as-rolled product with no significant levels of recrystallisation texture components.
- the foil of this invention may have a surface roughness greater than that of its solute-free counterpart. This increase in roughness was confirmed by optical profilometry (Perthometer) measurements, giving an R a of 0.38 for foil of this invention (Example 2) compared with an R a of 0.24 for a commercial foil of corresponding composition without Mg. The rougher surface improves the matt appearance of the foil.
- a molten aluminium alloy of desired composition is cast, e.g. by direct chill (D.C.) casting, or alternatively by roll casting or belt casting or other known casting techniques.
- the cast metal is rolled by successive rolling steps in conventional manner down to the required foil thickness. These steps typically involve hot rolling followed by cold rolling, possibly with one or more interannealing steps.
- the foil is heated to a temperature sufficient to remove the rolling lubricant.
- the heating rate is preferably 1°C - 100°C per hour. As noted above, this temperature is typically in the range 220 - 300°C, preferably 230 - 280°C, more preferably 230 - 250°C, and also effects continuous recrystallisation of the foil.
- the aluminium foil of this invention is preferably substantially free of surface contamination by rolling lubricant.
- a range of aluminium alloys are known to achieve a fine grain size after final annealing by a gradual coarsening of the cold-rolled substructure, sometimes called continuous recrystallisation, which allows a good combination of strength and formability to be achieved.
- continuous recrystallisation a range of aluminium alloys are known to achieve a fine grain size after final annealing by a gradual coarsening of the cold-rolled substructure, sometimes called continuous recrystallisation, which allows a good combination of strength and formability to be achieved.
- continuous recrystallisation which allows a good combination of strength and formability to be achieved.
- non-deformable intermetallic particles such as the FeAl 6 and/or (FeMn)Al 6 eutectic rods formed during solidification of Al-Fe-Mn alloys such as AA 8006 and AA 8014
- these particles must have increased dislocation activity associated with them in order to maintain continuity across the aluminium/particle interface.
- these dislocations are capable of rearranging themselves into dislocation walls, or sub-grain boundaries.
- the geometrically necessary dislocations generated during the rolling process continue to migrate to, and recover into, the sub-grain boundaries, increasing their misorientation.
- the conventional (solute-free) AA 8006 achieves a fine grain size after anneal, which imparts the good balance of strength and ductility associated with these alloys.
- the strength is inversely proportional to the grain (or sub-grain) size, and follows a d -1 relationship.
- This invention still maintains this strengthening mechanism whilst using the additional strengthening mechanism of solid solution strengthening. If the amount of solute added is too high then the ability to control the grain size during the final anneal is lost, giving rise to a decrease in grain size strengthening and formability. This presumably is because dynamic recovery is prevented during rolling, and so the driving force for discontinuous recrystallisation is increased. This also makes it increasingly difficult to roll the foil to the required thin gauge because of the increased rolled strength, giving a loss of the roll softening normally found in solute-free alloys of this type.
- Another aspect of the rearrangement of dislocations into high angle grain boundaries during the rolling process is that the strength of the foil decreases as the rolling strain is increased (roll softening), instead of the usual roll hardening associated with most aluminium alloys. Adding solute to the alloy will hinder the ability of the dislocations to rearrange themselves into low energy configuration in the sub-grain boundaries, and will prevent roll softening from occurring. Thus, if too much solute is added the cold rolled strength of the foil will be significantly increased, losing the ability to roll the material to the thin gauges needed for household foil and packaging applications (within the range 40 ⁇ m to 5 ⁇ m).
- the 140 ⁇ m foil has been annealed for 2 hours at a range of temperatures using a simulation of batch annealing, involving heating to temperature at 25°C/hour and longitudinal tensile properties measured.
- the variation of UTS, 0.2% proof stress, and elongation-to-failure are shown in Figures 1, 2 and 3, respectively, for the five alloys.
- All alloys containing the solute additions show an improvement in UTS over the solute-free AA 8006, with the improvement being of the order of 20 to 40 MPa after the commercially usable anneal at temperatures in the region of 220 - 260°C.
- the more concentrated alloys have lower strengths than the 0.2% additions.
- FIG. 4a and 4b show the pole figures generated from the ⁇ 111 ⁇ aluminium planes orientated relative to the rolling direction (vertical), transverse direction (horizontal) and the foil plane normal (into the page).
- Figure 4a is the as-rolled foil.
- Figure 4b is the annealed foil.
- the contour levels are 1.00 1.60 2.20 2.80 3.40 4.00 4.60. This shows that the crystallographic texture is essentially unaltered by the anneal, i.e. the texture is a retained rolling texture.
- the grain size of the 14 ⁇ m foil has been determined after commercial annealing using the mean linear intercept technique. This has been performed on micrographs obtained in the Transmission Electron Microscope (TEM). A total line length of lmm has been examined and the mean linear intercept grain size determined to be 3.1 ⁇ m. Effect of solute additions on the as-rolled strength of laboratory processed alloys rolled to give the equivalent strain as commercially rolled housefoil.
- TEM Transmission Electron Microscope
Abstract
Description
Fe | 1.2 - 2.0% |
Mn | 0.2 - 1.0% |
Mg and/or Cu | 0.1 - 0.5% |
Si | up to 0.4% |
Zn | up to 0.1% |
Ti | up to 0.1% |
balance Al of at least commercial purity |
Effect of solute additions on the as-rolled strength of laboratory processed alloys rolled to give the equivalent strain as commercially rolled housefoil. | |||
Alloy | 0.2% Proof Stress (MPa) | UTS (MPa) | Elongation (%) |
8006 | 159 | 210 | 6.1 |
8006 + 0.2% Cu | 217 | 268 | 5.9 |
8006 + 0.4% Cu | 249 | 309 | 3.3 |
8006 + 0.2% Mg | 259 | 311 | 2.2 |
8006 + 0.4% Cu | 274 | 331 | 2.4 |
Tensile properties of commercially produced 14 µm foil. | ||||
Alloy | condition | 0.2% Proof Stress (MPa) | UTS (MPa) | Elongation (%) |
AA8006 | As-rolled | 165 | 190 | 1.0 |
AA8006 | Plant annealed | 98 | 115 | 2.7 |
8006 + 0.2 Mg | As-rolled | 231 | 255 | 0.6 |
8006 + 0.2 Mg | Plant annealed | 102 | 123 | 1.9 |
14 µm Foil | ||
Compound | Volume % ± 15% | |
As-rolled | Annealed | |
Cube {001}<100> | 2.2 | 2.8 |
Goss (110)<001> | 3.2 | 2.4 |
Copper {112}<111> | 20.2) | 25.3) |
S {123}<634> | 35.2) 72.5 | 39.5) 79.2 |
Brass {011}<211> | 17.1) | 14.4) |
Random | 22.1 | 15.6 |
Claims (6)
- Aluminium foil composed of an alloy of composition in wt %:
Fe 1.2-2.0% Mn 0.2 - 1.0% Mg and/or Cu 0.1 - 0.5% Si up to 0.4% Zn up to 0.1% Ti up to 0.1% balance Al of at least commercial purity - Aluminium foil composed of an alloy of composition in wt %:
Fe 1.2-2.0% Mn 0.2 - 1.0% Mg and/or Cu 0.1 - 0.5% Si up to 0.4% Zn up to 0.1% Ti up to 0.1% balance Al of at least commercial purity, - Aluminium foil composed of an alloy of composition in wt %:
Fe 1.2-2.0% Mn 0.2 - 1.0% Mg and/or Cu 0.1 - 0.5% Si up to 0.4% Zn up to 0.1% Ti up to 0.1% balance Al of at least commercial purity, - Aluminium foil as claimed in any one of claims 1 to 3, wherein the foil thickness is 40 µm or less.
- Aluminium foil as claimed in any one of claims 1 to 4, wherein the alloy composition is
Fe 1.4-1.8% Mn 0.3 - 0.6% Fe+Mn 1.8-2.15% Mg 0.15-0.35% Si up to 0.4% balance Al of at least commercial purity. - A method of making the aluminium foil of any one of claims 1 to 5, which method comprises providing a billet of required composition, converting the billet to foil, and final annealing at a temperature of 220°C-300°C.
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
GB9405415A GB9405415D0 (en) | 1994-03-18 | 1994-03-18 | Aluminium foil |
GB9405415 | 1994-03-18 | ||
PCT/GB1995/000608 WO1995025825A1 (en) | 1994-03-18 | 1995-03-17 | Aluminium foil |
Publications (2)
Publication Number | Publication Date |
---|---|
EP0750685A1 EP0750685A1 (en) | 1997-01-02 |
EP0750685B1 true EP0750685B1 (en) | 1998-11-11 |
Family
ID=10752141
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP95911439A Expired - Lifetime EP0750685B1 (en) | 1994-03-18 | 1995-03-17 | Aluminium foil |
Country Status (10)
Country | Link |
---|---|
EP (1) | EP0750685B1 (en) |
JP (1) | JPH09510504A (en) |
AT (1) | ATE173301T1 (en) |
AU (1) | AU683361B2 (en) |
CA (1) | CA2185216A1 (en) |
DE (1) | DE69505957T2 (en) |
DK (1) | DK0750685T3 (en) |
ES (1) | ES2124536T3 (en) |
GB (1) | GB9405415D0 (en) |
WO (1) | WO1995025825A1 (en) |
Families Citing this family (13)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
AU6491898A (en) * | 1997-04-04 | 1998-10-30 | Alcan International Limited | Aluminum alloy composition and method of manufacture |
BR9908089A (en) | 1998-02-18 | 2000-10-31 | Alcan Int Ltd | Production process of high-strength aluminum sheets |
FR2813316B1 (en) * | 2000-08-29 | 2002-10-18 | Pechiney Rhenalu | PROCESS FOR PRODUCING VERY THIN STRIPS OF ALUMINUM-IRON ALLOY |
FR2836154B1 (en) * | 2002-02-15 | 2004-10-22 | Pechiney Rhenalu | THIN STRIPS IN ALUMINUM-IRON ALLOY |
KR100893251B1 (en) * | 2004-12-03 | 2009-04-17 | 샤프 가부시키가이샤 | Reflection preventing material, optical element, display device, stamper manufacturing method, and reflection preventing material manufacturing method using the stamper |
US10161020B2 (en) | 2007-10-01 | 2018-12-25 | Arconic Inc. | Recrystallized aluminum alloys with brass texture and methods of making the same |
CN104060132A (en) * | 2014-07-23 | 2014-09-24 | 卢德强 | Novel aluminum alloy and method for manufacturing aluminum foil with high deep-drawing performance by continuous cast-rolling |
CN107099702B (en) * | 2017-05-10 | 2019-08-23 | 山东远瑞金属材料有限公司 | 8021A alloy height extends lithium ion battery aluminium foil production technology |
CN111349825A (en) * | 2020-04-26 | 2020-06-30 | 江苏鼎胜新能源材料股份有限公司 | Preparation method for producing high-toughness battery aluminum foil by using short-process casting and rolling blank |
CN111549261A (en) * | 2020-05-13 | 2020-08-18 | 江苏鼎胜新能源材料股份有限公司 | Preparation method for producing deep-drawing cold-forming medicinal aluminum foil by short-process casting and rolling blank |
EP4015658A1 (en) * | 2020-12-18 | 2022-06-22 | Speira GmbH | Aluminium foil with improved barrier property |
CN113981338B (en) * | 2021-09-16 | 2022-10-28 | 江苏大学 | Structure control method of iron-rich aluminum alloy |
CN114345936A (en) * | 2021-12-23 | 2022-04-15 | 江苏鼎胜新能源材料股份有限公司 | Production process of high-toughness medicinal high-ductility aluminum foil |
Family Cites Families (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
GB1479429A (en) * | 1973-05-17 | 1977-07-13 | Alcan Res & Dev | Aluminium alloy products and method for making same |
US4737198A (en) * | 1986-03-12 | 1988-04-12 | Aluminum Company Of America | Method of making aluminum foil or fin shock alloy product |
JPS6326340A (en) * | 1986-07-18 | 1988-02-03 | Kobe Steel Ltd | Manufacture of aluminum alloy having superior directional property |
JPS6434548A (en) * | 1987-07-30 | 1989-02-06 | Furukawa Aluminium | Production of high strength aluminum foil |
DE3914020A1 (en) * | 1989-04-28 | 1990-10-31 | Vaw Ver Aluminium Werke Ag | ALUMINUM ROLLING PRODUCT AND METHOD FOR THE PRODUCTION THEREOF |
JPH03153836A (en) * | 1989-11-10 | 1991-07-01 | Mitsubishi Alum Co Ltd | Fin material made of high strength al alloy for al heat exchanger |
-
1994
- 1994-03-18 GB GB9405415A patent/GB9405415D0/en active Pending
-
1995
- 1995-03-17 ES ES95911439T patent/ES2124536T3/en not_active Expired - Lifetime
- 1995-03-17 JP JP7524474A patent/JPH09510504A/en not_active Ceased
- 1995-03-17 DE DE69505957T patent/DE69505957T2/en not_active Expired - Lifetime
- 1995-03-17 EP EP95911439A patent/EP0750685B1/en not_active Expired - Lifetime
- 1995-03-17 DK DK95911439T patent/DK0750685T3/en active
- 1995-03-17 AU AU19010/95A patent/AU683361B2/en not_active Ceased
- 1995-03-17 AT AT95911439T patent/ATE173301T1/en not_active IP Right Cessation
- 1995-03-17 WO PCT/GB1995/000608 patent/WO1995025825A1/en active IP Right Grant
- 1995-03-17 CA CA002185216A patent/CA2185216A1/en not_active Abandoned
Also Published As
Publication number | Publication date |
---|---|
DK0750685T3 (en) | 1999-07-26 |
ATE173301T1 (en) | 1998-11-15 |
CA2185216A1 (en) | 1995-09-28 |
AU683361B2 (en) | 1997-11-06 |
DE69505957D1 (en) | 1998-12-17 |
GB9405415D0 (en) | 1994-05-04 |
EP0750685A1 (en) | 1997-01-02 |
AU1901095A (en) | 1995-10-09 |
DE69505957T2 (en) | 1999-05-27 |
JPH09510504A (en) | 1997-10-21 |
ES2124536T3 (en) | 1999-02-01 |
WO1995025825A1 (en) | 1995-09-28 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
US3989548A (en) | Aluminum alloy products and methods of preparation | |
US4874440A (en) | Superplastic aluminum products and alloys | |
US4689090A (en) | Superplastic aluminum alloys containing scandium | |
JP3194742B2 (en) | Improved lithium aluminum alloy system | |
EP0610006B1 (en) | Superplastic aluminum alloy and process for producing same | |
US5055257A (en) | Superplastic aluminum products and alloys | |
EP0750685B1 (en) | Aluminium foil | |
US4126486A (en) | Producing improved metal alloy products | |
US20080299001A1 (en) | Aluminum alloy formulations for reduced hot tear susceptibility | |
EP1737995A1 (en) | Al-mg alloy sheet with excellent formability at high temperatures and high speeds and method of production of same | |
WO2018102328A1 (en) | Ecae materials for high strength aluminum alloys | |
WO2008120237A1 (en) | Alloy composition and preparation thereof | |
EP0104774B2 (en) | Light metal alloys | |
JPH07252573A (en) | Al-zn-mg-cu alloy excellent in toughness and its production | |
JP3022922B2 (en) | Method for producing plate or strip material with improved cold rolling characteristics | |
JP7318274B2 (en) | Al-Mg-Si-based aluminum alloy cold-rolled sheet and its manufacturing method, and Al-Mg-Si-based aluminum alloy cold-rolled sheet for forming and its manufacturing method | |
US20020153068A1 (en) | Production of aluminum alloy foils having high strength and good rollability | |
US20200354818A1 (en) | High Strength Microalloyed Magnesium Alloy | |
KR20220078525A (en) | aluminum alloy | |
Basori et al. | Effects of deformation and annealing temperature on the microstructures and hardness of Cu-29Zn-0.6 Bi brass | |
EP0846781B1 (en) | Process of forming an aluminium sheet with excellent high speed superplastic formability | |
JPH07116567B2 (en) | Method for producing A1-Cu-Li-Zr superplastic plate | |
JP7318275B2 (en) | Al-Mg-Si-based aluminum alloy cold-rolled sheet and its manufacturing method, and Al-Mg-Si-based aluminum alloy cold-rolled sheet for forming and its manufacturing method | |
JPH0978168A (en) | Aluminum alloy sheet | |
CN115652158B (en) | Creep-resistant Mg-Al deformed magnesium alloy and preparation method thereof |
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: 19960831 |
|
AK | Designated contracting states |
Kind code of ref document: A1 Designated state(s): AT BE CH DE DK ES FR GB GR IE IT LI LU NL PT SE |
|
17Q | First examination report despatched |
Effective date: 19970611 |
|
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 FR GB GR IE IT LI LU NL PT SE |
|
REF | Corresponds to: |
Ref document number: 173301 Country of ref document: AT Date of ref document: 19981115 Kind code of ref document: T |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: NV Representative=s name: E. BLUM & CO. PATENTANWAELTE Ref country code: CH Ref legal event code: EP |
|
REF | Corresponds to: |
Ref document number: 69505957 Country of ref document: DE Date of ref document: 19981217 |
|
REG | Reference to a national code |
Ref country code: IE Ref legal event code: FG4D |
|
REG | Reference to a national code |
Ref country code: ES Ref legal event code: FG2A Ref document number: 2124536 Country of ref document: ES Kind code of ref document: T3 |
|
ET | Fr: translation filed | ||
REG | Reference to a national code |
Ref country code: PT Ref legal event code: SC4A Free format text: AVAILABILITY OF NATIONAL TRANSLATION Effective date: 19990128 |
|
REG | Reference to a national code |
Ref country code: DK Ref legal event code: T3 |
|
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 | ||
REG | Reference to a national code |
Ref country code: GB Ref legal event code: IF02 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: SE Payment date: 20030305 Year of fee payment: 9 Ref country code: NL Payment date: 20030305 Year of fee payment: 9 Ref country code: AT Payment date: 20030305 Year of fee payment: 9 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: DK Payment date: 20030306 Year of fee payment: 9 Ref country code: CH Payment date: 20030306 Year of fee payment: 9 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: IE Payment date: 20030312 Year of fee payment: 9 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: PT Payment date: 20030317 Year of fee payment: 9 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: LU Payment date: 20030321 Year of fee payment: 9 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: GR Payment date: 20030327 Year of fee payment: 9 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: BE Payment date: 20030401 Year of fee payment: 9 |
|
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: 20040317 Ref country code: IE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20040317 Ref country code: AT Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20040317 |
|
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: 20040318 |
|
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: 20040331 Ref country code: DK Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20040331 Ref country code: CH Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20040331 Ref country code: BE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20040331 |
|
BERE | Be: lapsed |
Owner name: *ALCAN INTERNATIONAL LTD Effective date: 20040331 |
|
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: 20041001 |
|
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 NON-PAYMENT OF DUE FEES Effective date: 20041006 |
|
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: 20041015 |
|
EUG | Se: european patent has lapsed | ||
REG | Reference to a national code |
Ref country code: CH Ref legal event code: PL |
|
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: 20040930 |
|
NLV4 | Nl: lapsed or anulled due to non-payment of the annual fee |
Effective date: 20041001 |
|
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: 20050317 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: FR Payment date: 20050321 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: 20050407 Year of fee payment: 11 |
|
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: 20060318 |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: ST Effective date: 20061130 |
|
REG | Reference to a national code |
Ref country code: ES Ref legal event code: FD2A Effective date: 20060318 |
|
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: 20060331 |
|
REG | Reference to a national code |
Ref country code: GB Ref legal event code: 732E Free format text: REGISTERED BETWEEN 20110609 AND 20110615 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: GB Payment date: 20130215 Year of fee payment: 19 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R082 Ref document number: 69505957 Country of ref document: DE Representative=s name: PATENTANWAELTE WEICKMANN & WEICKMANN, DE Ref country code: DE Ref legal event code: R082 Ref document number: 69505957 Country of ref document: DE Representative=s name: WEICKMANN & WEICKMANN, DE |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: DE Payment date: 20140115 Year of fee payment: 20 |
|
GBPC | Gb: european patent ceased through non-payment of renewal fee |
Effective date: 20140317 |
|
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: 20140317 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R071 Ref document number: 69505957 Country of ref document: DE |