ZA200600425B - Thin strips or foils of alfesi alloy - Google Patents
Thin strips or foils of alfesi alloy Download PDFInfo
- Publication number
- ZA200600425B ZA200600425B ZA200600425A ZA200600425A ZA200600425B ZA 200600425 B ZA200600425 B ZA 200600425B ZA 200600425 A ZA200600425 A ZA 200600425A ZA 200600425 A ZA200600425 A ZA 200600425A ZA 200600425 B ZA200600425 B ZA 200600425B
- Authority
- ZA
- South Africa
- Prior art keywords
- alloy
- strip
- foil
- mpa
- thin strip
- Prior art date
Links
- 229910045601 alloy Inorganic materials 0.000 title claims description 47
- 239000000956 alloy Substances 0.000 title claims description 47
- 239000011888 foil Substances 0.000 title claims description 21
- 238000000137 annealing Methods 0.000 claims description 35
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 33
- 239000000203 mixture Substances 0.000 claims description 17
- 229910052742 iron Inorganic materials 0.000 claims description 12
- 238000000034 method Methods 0.000 claims description 11
- 229910052710 silicon Inorganic materials 0.000 claims description 10
- 238000009749 continuous casting Methods 0.000 claims description 9
- 238000005266 casting Methods 0.000 claims description 8
- 238000004519 manufacturing process Methods 0.000 claims description 7
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 6
- 238000000265 homogenisation Methods 0.000 claims description 6
- 239000010703 silicon Substances 0.000 claims description 6
- 238000005098 hot rolling Methods 0.000 claims description 5
- 238000005097 cold rolling Methods 0.000 claims description 4
- 238000002360 preparation method Methods 0.000 claims description 2
- 229910017082 Fe-Si Inorganic materials 0.000 claims 1
- 229910017133 Fe—Si Inorganic materials 0.000 claims 1
- 239000011572 manganese Substances 0.000 description 16
- 229910052748 manganese Inorganic materials 0.000 description 11
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 9
- 238000010438 heat treatment Methods 0.000 description 7
- 230000009466 transformation Effects 0.000 description 6
- 230000009172 bursting Effects 0.000 description 5
- 238000005204 segregation Methods 0.000 description 5
- 229910052782 aluminium Inorganic materials 0.000 description 4
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 4
- 229910052751 metal Inorganic materials 0.000 description 4
- 239000002184 metal Substances 0.000 description 4
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 3
- 238000001953 recrystallisation Methods 0.000 description 3
- 239000004411 aluminium Substances 0.000 description 2
- 229910052802 copper Inorganic materials 0.000 description 2
- 238000010191 image analysis Methods 0.000 description 2
- 150000002739 metals Chemical class 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 229910018191 Al—Fe—Si Inorganic materials 0.000 description 1
- 229910000914 Mn alloy Inorganic materials 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000005238 degreasing Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000004806 packaging method and process Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
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
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
-
- 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
-
- 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
- C22F1/043—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 of alloys with silicon as the next major constituent
Description
Therefore, there is a need to develop new alloys and/or to optimise transformation procedures to satisfy market demand.
Manganese is normally added to increase the mechanical strength. for example as in the 8006 alloy for which the composition (% by weight) registered with the
Aluminum Association is as follows:
Si<0.40; Fe:1.2-20; Cu<0.30; Mn :030-1.0; Mg<0.10
The result of adding manganese is to harden the material. The mechanical properties obtained with patent US 6 517 646 belonging to the applicant for an alloy with composition Si = 0.23%; Fe =1.26%; Cu = 0.017%; Mn = 0.37%; Mg = 0.0032%;
Ti=0.008%, in combination with a favourable transformation procedure, gives a value
R., equal to 103 MPa for a thickness of 6.6 um.
The mechanical properties can also be improved by adding a small quantity of manganese in alloys in the 8000 series containing iron. Patent application WO 02/64848 (Alcan International) describes the fabrication of thin strips made of AlFeSi alloy containing from 1.2% to 1.7% Fe and 0.35% to 0.8% of Si, by continuous casting. A high mechanical strength is obtained by adding 0.07% to 0.20% of manganese to the alloy. This addition of manganese is recognised as being necessary to obtain a small grain size after final annealing.
Therefore, manganese appears to be an element capable of improving the mechanical properties of 8000 alloys. However, manganese in solid solution or in the form of fine precipitates can block or delay recrystaliisation during final annealing.
Therefore, the precipitation of phases containing manganese needs to be controlled precisely during each step in the procedure, which is often difficult. Any drift in the transformation procedure has non-negligible consequences on the effectiveness of the final annealing. Therefore, it would be very useful to develop an alloy that does not contain any manganese, but that does have high mechanical properties.
US Patent 5 503 689 (Reynolds Metals) describes a process for manufacturing a thin strip made of an alloy containing 0.30% to 1.1% Si and 0.40% to 1.0% Fe, less than 0.25% Cu and less than 0.1% Mn, by continuous casting and cold rolling without intermediate annealing. The preferred contents of iron and silicon are between 0.6% and 0.75%.
US Patent 5 725 695 (Reynolds Metals) describes a procedure for the same composition, with intermediate annealing between 400°C and 440°C (750°F — 825°F) and a final recrystallisation annealing at 288°C (550°F). The ratio of the Si and Fe contents is greater than or equal to 1. In the examples, the maximum ultimate tensile strength obtained is 90 MPa (13.13 ksi), the maximum yield stress is 39.1 MPa (5.68 ksi), and the elongation is 11.37% for thicknesses of 46 um (0.00185'). These mechanical properties are still low for some applications.
For alloys obtained by continuous casting, it is often necessary to perform a high temperature heat treatment to reduce the noxiousness of segregations, by resorbing precipitation Jumps and homogenising the structure through the thickness. The effect of a homogenisation at 600°C for the 8011 alloy (composition 0.71% Fe; 0.77% Si; 0.038% Cu; 0.006% Mn; 98.45% Al) obtained by twin-roll casting is described in the article by Y. Birol “Centerline Segregation in a Twin-Roll Cast AA801] Alloy”,
Aluminium, 74, 1998, pp 318-321. The precipitated phases are modified and heterogeneities are reduced. The reduction in central segregation subsequently limits the porosity of very thin foils and improves their formability.
It is economically attractive to limit the heat treatment temperature. For an 8111 alloy with composition 0.7% Fe; 0.7% Si; Mn < 0.02, Zn < 0.02; Cu < 0.02, a beginning of a transformation of the phases is observed with total recrystallisation at 460°C, although annealing at 550°C - 580°C is necessary to obtain a more complete transformation (see M. Slamova et al. “Response of AA8006 and AA8111 Strip-Cast
Rolled Alloys to High Temperature Annealing”, ICAA-6. 1998). Therefore low temperature homogenisation could be considered for alloys without manganese.
Moreover, in the transformation to low thicknesses subsequent to homogenisation, it is standard practice to add an intermediate annealing step in order to soften the metal. For manganese alloys, the intermediate annealing control usually requires a high temperature heat treatment (at above 400°C) so as to obtain recrystallisation.
For manganese-free 8000 type alloys, it is possible to envisage a heat treatment at a lower temperature than for 8006 type alloys.
Patent application WO 99/23269 (Nippon Light Metal and Alcan International) describes a process applicable to AlFeSi alloys containing 0.2% to 1% of Si and 0.3% to 1.2% of Fe, with a Si/Fe ratio of between 0.4 and 1.2, in which intermediate annealing is done in two steps, the first between 350°C and 450°C, and the second between 200°C and 330°C. The purpose of this process is to reduce surface defects in the foil.
Mechanical properties are not mentioned.
The purpose of the invention is to obtain thin strips or foils made of an AlFeS: alloy with no added manganese, with a high mechanical strength while maintaining good formability, with the most economic industrial manufacturing procedure possible.
Subject matter of the invention
The subject matter of the invention is a thin foil between 6 pm and 200 pm thick, and preferably between 6 um and 50 um thick, of an alloy with the following composition (% by weight):
Si:1.0-1.5; Fe:1.0-1.5 Cu<0.2; Mn<Q0.1; other elements < 0.05 each and < 0.15 total, remainder Al, preferably with the condition Si/Fe > 0.95, with an ultimate tensile strength in the annealed temper Ry, > 110 MPa for thicknesses > 9 um and > 100 MPa for thicknesses between 6 um and 9 pm. The yield stress Ro of the thin foil (measured on sheared test pieces) is preferably > 70 MPa. The ultimate clongation is greater than the following values, as a function of the thickness of the foil: 9-15 5 7
The silicon content of the alloy is preferably between 1.1% and 1.3% and its iron content is between 1.0% and 1.2%.
Another subject matter of the invention is a manufacturing process for thin strips thinner than 200 um made of an Al-Fe-Si alloy with composition (% by weight):
Si: 1.0-1.5; Fe: 10-15; Cu<02; Mn<0.l; other elements <0.05 each and < 0.15 total, remainder Al, preferably with the condition Si/Fe > 0.95, including the preparation of a first strip either by vertical semi-continuous casting of a plate and hot rolling, or by continuous casting possibly followed by hot rolling, cold rolling of this first strip down to the final thickness, possibly with intermediate annealing for between 2 h and 20 h at a temperature between 250°C and 350°C, and preferably between 280°C and 340°C, and final annealing at a temperature between 200°C and 370°C.
The thin strips or foils according to the invention are made from 8000 AlSiFe alloys with almost no manganese, typically less than 0.1%. Iron and silicon contents are significantly higher than 8011 and 8111 alloys that are the most frequently used manganese-free AlSiFe alloys for thin foil. One preferred composition range is an alloy containing 1.1% to 1.3% of silicon and 1.0% to 1.2% of iron.
Alloys according to the invention preferably have a composition such that the
Si/Fe ratio of silicon and iron contents is > 0.95. Their mechanical strength in the annealed temper (O temper) is exceptional for alloys with this composition, with an ultimate tensile strength R,, > 110 MPa or even 115 MPa for thicknesses > 9 pm, and > 100 MPa for thicknesses from 6 pm to 9 pm, and a conventional yield stress at 0.2%,
Rg, > 70 MPa. This high mechanical strength is not obtained at the expense of formability, since elongations are at least as high as for 8011 and 8111 alloys, and bursting pressures are higher.
These high mechanical properties are obtained equally well for strips produced from plates obtained by conventional vertical semi-continuous casting and hot rolled. and for strips derived from continuous casting, either by belt casting or twin-rol} casting.
Continuous belt casting is also following by hot rolling. 5 Hot rolled strips, or as-cast strips obtained by continuous twin-roll casting, may be homogenised at low temperature (between 450°C and 500°C) to reduce the central segregation that may reduce formability to the final thickness. This low temperature heat treatment is sufficient to resorb any central segregations in these manganese-free alloys.
The strips are then cold rolled, either down to the final thickness or to an intermediate thickness between 0.5 mm and 5 mm, at which an intermediate annealing is performed.
Unlike alloys containing manganese, this intermediate annealing can be done at a relatively low temperature between 250°C and 350°C, and preferably between 280°C and 340°C, for longer than 2 hours. Although this temperature range is described in the literature, particularly in patent application WO 02/064848 mentioned above, it is below the normal range that remains above 400°C.
The applicant has observed that the application of low temperature heat treatments to an AlFeSi alloy, more particularly with a composition such that Si/Fe > 0.95, possibly eliminating the intermediate annealing when technically possible, results in significantly higher mechanical strength than is possible with normal intermediate annealing, at least 15% better. This higher mechanical strength is obtained while improving the formability measured by the bursting pressure or the dome height according to standard 1SO 2758.
Final annealing is done at a temperature between 200°C and 370°C for between h and 72 h. Annealing durations depend on the degreasing quality of the foil. A fine grain structure is obtained after annealing, with an average grain size measured by image analysis with a scanning electron microscope equal to less than 3 pm.
The combination of low temperature homogenisation or no homogenisation at all with an intermediate annealing at low temperature or no intermediate annealing at all, is economically advantageous but also helps to obtain a fine grain size. The grain size is
€ about 30% lower than is possible with heat treatments at a higher temperature. consequently increasing the mechanical properties Rpa and R,. which for small thicknesses are related to the number of grain joints. This gain is not achieved at the detriment of elongation. since the increase in the number of grains in the thickness also & limits the risk of local damage in one or two single grains in the thickness of the foil.
Thin foils according to the invention are particularly suitable for applications requiring good mechanical strength and high formability, for example such as fabrication of multi-layer composites, particularly for lids for packaging of fresh products, overcaps or aluminium wrapping.
Example 1
Two 6.1 mm thick strips made of alloy A according to the invention and alloy B type 8111 with the composition (% by weight) indicated in table 1 were made by continuous twin-rol! casting, in order to demonstrate the influence of the composition of the alloy:
Table 1
B 197 0.7 0.001 0.003 0.0005 [0.001 {0.007 [0.0005 26 The strips were cold rolled to a thickness of 2 mm and an intermediate annealing was then carried out on them for 5 hours at 320°C. The strips were then cold rolled in several passes to the final thickness of 38 pm. A final annealing was then carried out on them for 40 hours at 270°C.
The mechanical properties were measured in each case. The measured values were the ultimate tensile strength R.,, (in MPa), the conventional yield stress at 0.2% Rg» and the ultimate elongation A (in %) according to standard NF-EN 546-2, the bursting pressure in air Pe (in kPa) measured according to standard ISO 2738 and the dome height Hd (in mm). The results are given in table 2:
Table 2
Alloy | Rw (MPa) | Roz (MPa) 1A (%) Pe er
IA 1123 | 76 : 30 394 9.2
It is found that. unlike the 8111 type alloy B, the ultimate strength of the alloy A strip is much higher than 110 MPa, and the yield stress is higher than 70 MPa. The bursting pressure and the elongation are also higher, such that this alloy is both stronger and more formable.
Example 2
A 6.1 mm thick strip made of alloy A described in example 1 was made by continuous twin-roll casting. The strip was then cold rolled to a thickness of 2 mm. A normal intermediate annealing for an alloy of this type was then carried out on part of the strip, for 5 hours at 500°C. An intermediate annealing was carried out on the other part of the strip, for 5 hours at 320°C according to the invention. The two parts of the strip were then cold rolled in several passes to the final thickness of 10.5 um. A final annealing was then carried out on them for 40 hours at 270°C.
The properties were the same as in example 1, and the values are shown in table 3:
Table 3
Inter. ‘Rn (MPa) | Rg; (MPa) | A (%) Pe (kPa) Hd (mm) re wT
[tis found that the lower temperature of the intermediate annealing increases the mechanical strength, the elongation, the bursting strength and the formability.
The average grain size measured by image analysis with an SEM. 1s 3.6 um for = annealing at 470°C, and 2.3 um for annealing at 320°C. Therefore the increase in mechanical properties for low temperature annealing is related to the reduction in grain size obtained after final annealing.
Claims (13)
1. Thin strip or foil between 6 pm and 200 pm thick, of an alloy with the following composition (% by weight): Si :1.0-1.5; Fe:1.0-1.5; Cu < 0.2; Mn <0.1; other elements < 0.05 each and
< 0.15 total, remainder Al, with an ultimate tensile strength Rp, in the annealed temper > 110MPa for thicknesses > 9 pm and > 100 MPa for thicknesses between 6 um and 9 pum.
2. Thin strip or foil according to claim 1, characterised in that the thickness of the strip or foil is between 6 pm and 50 pm.
3. Thin strip or foil according to either of claims 1 or 2, characterised in that it has an ultimate tensile strength Ry, in the annealed temper > 115 MPa for thicknesses >9 um.
4. Thin strip or foil according to any one of claims 1 to 3, characterised in that it has a yield stress Rg >> 70 MPa.
5. Thin strip or foil according to any one of claims 1 to 4, characterised in that its ultimate elongation A is a function of the thickness, as follows: A CE EL LE
6. Thin strip or foil according to claim 5, characterised in that its ultimate elongation A is a function of the thickness, as follows: EE Amended sheet 09/03/2007
. ,
7. Thin strip or foil according to any one of claims 1 to 6, characterised in that the alloy has a composition such that Si/Fe > 0.95.
8. Thin strip or foil according to any one of claims 1 to 7, characterised in that the silicon content of the alloy is between 1.1% and 1.3% and its iron content is between 1.0% and 1.2%.
9. Manufacturing process for thin strips thinner than 200 um made of an Al- Fe-Si alloy with composition (% by weight): Si:1.0-1.5;Fe:1.0-1.5; Cu<0.2; Mn<0.1; other elements < 0.05 each and <0.15 total, remainder Al, including the preparation of a first strip either by vertical semi-continuous casting of a plate and hot rolling, or by continuous casting possibly followed by hot rolling, cold rolling of this first strip down to the final thickness, possibly with intermediate annealing at a temperature between 250°C and 350°C, and final annealing at a temperature between 200°C and 370°C.
10. Manufacturing process according to claim 9, characterised in that the intermediate annealing temperature is between 280°C and 340°C.
11. Process according to either of claims 9 or 10, characterised in that the alloy has a composition such that Si/Fe > 0.95.
12. Process according to any one of claims 9 to 11, characterised in that the first strip is subjected to an homogenisation at a temperature between 450°C and 500°C before cold rolling.
13. Process according to any one of claims 9 to 12, characterised in that the strip is prepared by continuous twin-roll casting. Amended sheet 09/03/2007
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
FR0308864A FR2857981A1 (en) | 2003-07-21 | 2003-07-21 | Thin sheet or strip of aluminum alloy for bottle caps and wrapping foil has a thickness of less than 200 microns, is essentially free of manganese, and has increased mechanical strength |
Publications (1)
Publication Number | Publication Date |
---|---|
ZA200600425B true ZA200600425B (en) | 2007-03-28 |
Family
ID=33560962
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
ZA200600425A ZA200600425B (en) | 2003-07-21 | 2004-07-19 | Thin strips or foils of alfesi alloy |
Country Status (21)
Country | Link |
---|---|
US (1) | US20060213590A1 (en) |
EP (1) | EP1644545B1 (en) |
JP (1) | JP4989221B2 (en) |
CN (1) | CN100445405C (en) |
AR (1) | AR044882A1 (en) |
AT (1) | ATE355392T1 (en) |
AU (1) | AU2004259877A1 (en) |
BR (1) | BRPI0412775A (en) |
CA (1) | CA2532585A1 (en) |
DE (1) | DE602004005045T2 (en) |
DK (1) | DK1644545T3 (en) |
EA (1) | EA009227B1 (en) |
ES (1) | ES2281831T3 (en) |
FR (1) | FR2857981A1 (en) |
NO (1) | NO338970B1 (en) |
PL (1) | PL1644545T3 (en) |
PT (1) | PT1644545E (en) |
SA (1) | SA04250245B1 (en) |
UA (1) | UA80778C2 (en) |
WO (1) | WO2005010222A2 (en) |
ZA (1) | ZA200600425B (en) |
Families Citing this family (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US8403027B2 (en) * | 2007-04-11 | 2013-03-26 | Alcoa Inc. | Strip casting of immiscible metals |
US7846554B2 (en) * | 2007-04-11 | 2010-12-07 | Alcoa Inc. | Functionally graded metal matrix composite sheet |
US20100084053A1 (en) * | 2008-10-07 | 2010-04-08 | David Tomes | Feedstock for metal foil product and method of making thereof |
US8956472B2 (en) * | 2008-11-07 | 2015-02-17 | Alcoa Inc. | Corrosion resistant aluminum alloys having high amounts of magnesium and methods of making the same |
JP5275446B2 (en) * | 2009-03-05 | 2013-08-28 | 東洋アルミニウム株式会社 | Aluminum alloy foil for current collector and method for producing the same |
KR101308963B1 (en) | 2011-07-22 | 2013-09-25 | 한국생산기술연구원 | Diecasting aluminum alloy for radiator grille |
US10160580B2 (en) * | 2013-01-09 | 2018-12-25 | Albea Americas, Inc. | Layered materials comprising aluminum foil and tubes made therefrom |
EP3235916B1 (en) | 2016-04-19 | 2018-08-15 | Rheinfelden Alloys GmbH & Co. KG | Cast alloy |
CN117568667B (en) * | 2024-01-15 | 2024-04-19 | 中铝材料应用研究院有限公司 | Aluminum foil material and preparation method thereof |
Family Cites Families (10)
Publication number | Priority date | Publication date | Assignee | Title |
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JPH0762223B2 (en) * | 1985-04-11 | 1995-07-05 | 古河電気工業株式会社 | Method of manufacturing deep drawing closure |
US5503689A (en) * | 1994-04-08 | 1996-04-02 | Reynolds Metals Company | General purpose aluminum alloy sheet composition, method of making and products therefrom |
JP3107191B2 (en) * | 1994-11-16 | 2000-11-06 | 古河電気工業株式会社 | Method for producing aluminum alloy support for lithographic printing plate |
US5714019A (en) * | 1995-06-26 | 1998-02-03 | Aluminum Company Of America | Method of making aluminum can body stock and end stock from roll cast stock |
US5725695A (en) * | 1996-03-26 | 1998-03-10 | Reynolds Metals Company | Method of making aluminum alloy foil and product therefrom |
JP4058536B2 (en) * | 1997-10-31 | 2008-03-12 | 日本軽金属株式会社 | Method for producing aluminum alloy foil |
EP1058743B1 (en) * | 1998-02-18 | 2002-09-25 | Alcan International Limited | Process of manufacturing high strength aluminum foil |
US6531006B2 (en) * | 2001-02-13 | 2003-03-11 | Alcan International Limited | Production of high strength aluminum alloy foils |
FR2832497B1 (en) * | 2001-11-19 | 2004-05-07 | Pechiney Rhenalu | ALUMINUM ALLOY STRIPS FOR HEAT EXCHANGERS |
FR2836154B1 (en) * | 2002-02-15 | 2004-10-22 | Pechiney Rhenalu | THIN STRIPS IN ALUMINUM-IRON ALLOY |
-
2003
- 2003-07-21 FR FR0308864A patent/FR2857981A1/en active Pending
-
2004
- 2004-06-23 AR ARP040102197A patent/AR044882A1/en not_active Application Discontinuation
- 2004-07-19 DE DE602004005045T patent/DE602004005045T2/en active Active
- 2004-07-19 DK DK04767726T patent/DK1644545T3/en active
- 2004-07-19 AU AU2004259877A patent/AU2004259877A1/en not_active Abandoned
- 2004-07-19 BR BRPI0412775-7A patent/BRPI0412775A/en not_active IP Right Cessation
- 2004-07-19 CA CA002532585A patent/CA2532585A1/en not_active Abandoned
- 2004-07-19 CN CNB2004800210038A patent/CN100445405C/en not_active Expired - Fee Related
- 2004-07-19 EA EA200600276A patent/EA009227B1/en not_active IP Right Cessation
- 2004-07-19 ZA ZA200600425A patent/ZA200600425B/en unknown
- 2004-07-19 UA UAA200601770A patent/UA80778C2/en unknown
- 2004-07-19 AT AT04767726T patent/ATE355392T1/en not_active IP Right Cessation
- 2004-07-19 PL PL04767726T patent/PL1644545T3/en unknown
- 2004-07-19 WO PCT/FR2004/001902 patent/WO2005010222A2/en active IP Right Grant
- 2004-07-19 EP EP04767726A patent/EP1644545B1/en active Active
- 2004-07-19 ES ES04767726T patent/ES2281831T3/en active Active
- 2004-07-19 US US10/565,219 patent/US20060213590A1/en not_active Abandoned
- 2004-07-19 PT PT04767726T patent/PT1644545E/en unknown
- 2004-07-19 JP JP2006520859A patent/JP4989221B2/en active Active
- 2004-08-11 SA SA04250245A patent/SA04250245B1/en unknown
-
2006
- 2006-01-31 NO NO20060508A patent/NO338970B1/en unknown
Also Published As
Publication number | Publication date |
---|---|
BRPI0412775A (en) | 2006-09-26 |
AU2004259877A1 (en) | 2005-02-03 |
NO338970B1 (en) | 2016-11-07 |
PL1644545T3 (en) | 2007-07-31 |
CN100445405C (en) | 2008-12-24 |
DE602004005045D1 (en) | 2007-04-12 |
WO2005010222A2 (en) | 2005-02-03 |
JP2007502360A (en) | 2007-02-08 |
NO20060508L (en) | 2006-01-31 |
AR044882A1 (en) | 2005-10-05 |
DE602004005045T2 (en) | 2007-11-15 |
EP1644545B1 (en) | 2007-02-28 |
CN1997763A (en) | 2007-07-11 |
CA2532585A1 (en) | 2005-02-03 |
SA04250245B1 (en) | 2007-10-29 |
EA009227B1 (en) | 2007-12-28 |
JP4989221B2 (en) | 2012-08-01 |
US20060213590A1 (en) | 2006-09-28 |
EA200600276A1 (en) | 2006-10-27 |
ATE355392T1 (en) | 2006-03-15 |
DK1644545T3 (en) | 2007-06-18 |
ES2281831T3 (en) | 2007-10-01 |
PT1644545E (en) | 2007-04-30 |
FR2857981A1 (en) | 2005-01-28 |
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UA80778C2 (en) | 2007-10-25 |
EP1644545A2 (en) | 2006-04-12 |
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