EP0750685B1 - Aluminium foil - Google Patents

Aluminium foil Download PDF

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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
Application number
EP95911439A
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German (de)
English (en)
French (fr)
Other versions
EP0750685A1 (en
Inventor
Gary John Mahon
Graeme John Marshall
Ricky Arthur Ricks
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.)
Rio Tinto Alcan International Ltd
Original Assignee
Alcan International Ltd Canada
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Filing date
Publication date
Application filed by Alcan International Ltd Canada filed Critical Alcan International Ltd Canada
Publication of EP0750685A1 publication Critical patent/EP0750685A1/en
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    • 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

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Physics & Mathematics (AREA)
  • Metal Rolling (AREA)
  • Laminated Bodies (AREA)
  • Cookers (AREA)
  • Polishing Bodies And Polishing Tools (AREA)
  • Conductive Materials (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Cell Electrode Carriers And Collectors (AREA)
EP95911439A 1994-03-18 1995-03-17 Aluminium foil Expired - Lifetime EP0750685B1 (en)

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 (ja)
JP (1) JPH09510504A (ja)
AT (1) ATE173301T1 (ja)
AU (1) AU683361B2 (ja)
CA (1) CA2185216A1 (ja)
DE (1) DE69505957T2 (ja)
DK (1) DK0750685T3 (ja)
ES (1) ES2124536T3 (ja)
GB (1) GB9405415D0 (ja)
WO (1) WO1995025825A1 (ja)

Families Citing this family (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0972089B1 (en) * 1997-04-04 2004-12-08 Alcan International Limited Aluminum alloy composition and method of manufacture
EP1058743B1 (en) * 1998-02-18 2002-09-25 Alcan International Limited Process of manufacturing high strength aluminum foil
FR2813316B1 (fr) 2000-08-29 2002-10-18 Pechiney Rhenalu Procede de fabrication de bandes tres minces en alliage aluminium-fer
FR2836154B1 (fr) * 2002-02-15 2004-10-22 Pechiney Rhenalu Bandes minces en alliage aluminium-fer
KR100898470B1 (ko) * 2004-12-03 2009-05-21 샤프 가부시키가이샤 반사 방지재, 광학 소자, 및 표시 장치 및 스탬퍼의 제조 방법 및 스탬퍼를 이용한 반사 방지재의 제조 방법
US10161020B2 (en) * 2007-10-01 2018-12-25 Arconic Inc. Recrystallized aluminum alloys with brass texture and methods of making the same
CN104060132A (zh) * 2014-07-23 2014-09-24 卢德强 一种新型铝合金及连续铸轧制造高深冲性铝箔的方法
CN107099702B (zh) * 2017-05-10 2019-08-23 山东远瑞金属材料有限公司 8021a合金高延伸锂离子电池用铝箔生产工艺
CN111349825A (zh) * 2020-04-26 2020-06-30 江苏鼎胜新能源材料股份有限公司 一种利用短流程铸轧坯生产高韧性电池铝箔的制备方法
CN111549261A (zh) * 2020-05-13 2020-08-18 江苏鼎胜新能源材料股份有限公司 一种短流程铸轧坯生产深冲冷成型药用铝箔的制备方法
EP4015658A1 (de) * 2020-12-18 2022-06-22 Speira GmbH Aluminiumfolie mit verbesserter barriereeigenschaft
CN113981338B (zh) * 2021-09-16 2022-10-28 江苏大学 一种富铁铝合金的组织控制方法
CN114345936A (zh) * 2021-12-23 2022-04-15 江苏鼎胜新能源材料股份有限公司 一种高韧性的药用高延展性的铝箔生产工艺
CN116179897A (zh) * 2022-12-02 2023-05-30 乳源东阳光优艾希杰精箔有限公司 一种高强度高延伸率铝箔及其应用

Family Cites Families (6)

* Cited by examiner, † Cited by third party
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 (ja) * 1986-07-18 1988-02-03 Kobe Steel Ltd 方向性の優れたアルミニウム合金の製造法
JPS6434548A (en) * 1987-07-30 1989-02-06 Furukawa Aluminium Production of high strength aluminum foil
DE3914020A1 (de) * 1989-04-28 1990-10-31 Vaw Ver Aluminium Werke Ag Aluminiumwalzprodukt und verfahren zu seiner herstellung
JPH03153836A (ja) * 1989-11-10 1991-07-01 Mitsubishi Alum Co Ltd Ａｌ熱交換器用高強度Ａｌ合金製フィン材

Also Published As

Publication number Publication date
WO1995025825A1 (en) 1995-09-28
DK0750685T3 (da) 1999-07-26
ATE173301T1 (de) 1998-11-15
GB9405415D0 (en) 1994-05-04
ES2124536T3 (es) 1999-02-01
EP0750685A1 (en) 1997-01-02
DE69505957T2 (de) 1999-05-27
DE69505957D1 (de) 1998-12-17
CA2185216A1 (en) 1995-09-28
AU1901095A (en) 1995-10-09
JPH09510504A (ja) 1997-10-21
AU683361B2 (en) 1997-11-06

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