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.
• 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. During this annealing treatment, 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.
• this invention provides aluminium foil composed of an alloy of composition by weight %:
• 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 n 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) .
• 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_ 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 Fe Alg and/or (FeMn)Alg 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. Eventually these boundaries will attain high misorientations with their neighbours, i.e.
• 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) .
• Figure 1 shows the effect of annealing temperature on tensile strength of laboratory processed alloys rolled to 140 ⁇ m
• Figure 2 shows the effect of annealing temperature on tensile yield stress of laboratory processed alloys rolled to 140 ⁇ m
• Figure 3 shows the effect of annealing temperature on tensile elongation of laboratory processed alloys rolled to 140 ⁇ m; and Figures 4a and 4b are pole diagrams of a foil sample before and after annealing.
• the 140 ⁇ m foil has been annealed for 2 hours t 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,
• FIG. 4a and 4b show the pole figures generated from the ⁇ ill ⁇ 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 1mm has been examined and the mean linear intercept grain size determined to.be 3.1 ⁇ m.
• TEM Transmission Electron Microscope

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• Chemical & Material Sciences (AREA)
• Organic Chemistry (AREA)
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• Engineering & Computer Science (AREA)
• Materials Engineering (AREA)
• Mechanical Engineering (AREA)
• Crystallography & Structural Chemistry (AREA)
• Thermal Sciences (AREA)
• Physics & Mathematics (AREA)
• Laminated Bodies (AREA)
• Metal Rolling (AREA)
• Cookers (AREA)
• Polishing Bodies And Polishing Tools (AREA)
• Conductive Materials (AREA)
• Cell Electrode Carriers And Collectors (AREA)
• Heat Treatment Of Sheet Steel (AREA)

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• 1994
  • 1994-03-18 GB GB9405415A patent/GB9405415D0/en active Pending
• 1995
  • 1995-03-17 DK DK95911439T patent/DK0750685T3/da active
  • 1995-03-17 AU AU19010/95A patent/AU683361B2/en not_active Ceased
  • 1995-03-17 AT AT95911439T patent/ATE173301T1/de not_active IP Right Cessation
  • 1995-03-17 CA CA002185216A patent/CA2185216A1/en not_active Abandoned
  • 1995-03-17 ES ES95911439T patent/ES2124536T3/es not_active Expired - Lifetime
  • 1995-03-17 WO PCT/GB1995/000608 patent/WO1995025825A1/en active IP Right Grant
  • 1995-03-17 DE DE69505957T patent/DE69505957T2/de not_active Expired - Lifetime
  • 1995-03-17 EP EP95911439A patent/EP0750685B1/de not_active Expired - Lifetime
  • 1995-03-17 JP JP7524474A patent/JPH09510504A/ja not_active Ceased

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