EP3940100A1 - Alliages d'aluminium pour la fabrication de boîtes d'aluminium par extrusion par percussion - Google Patents

Alliages d'aluminium pour la fabrication de boîtes d'aluminium par extrusion par percussion Download PDF

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EP3940100A1
EP3940100A1 EP20382640.9A EP20382640A EP3940100A1 EP 3940100 A1 EP3940100 A1 EP 3940100A1 EP 20382640 A EP20382640 A EP 20382640A EP 3940100 A1 EP3940100 A1 EP 3940100A1
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Prior art keywords
weight
aluminium
range
alloy
alloys
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German (de)
English (en)
Inventor
Ester Villanueva Viteri
Jon Mikel Sánchez Severino
Iban Vicario Gómez
Jorge Armentia Ortíz
María Begoña Bustinza Arriortua
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Envases Metalurgicos de Alava SA
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Envases Metalurgicos de Alava SA
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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
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • 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
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • C22C21/14—Alloys based on aluminium with copper as the next major constituent with silicon
    • 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
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • C22C21/16—Alloys based on aluminium with copper as the next major constituent with magnesium
    • 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
    • C22F1/057—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 copper as the next major constituent

Definitions

  • the field of the invention is related to aluminium alloys.
  • the present invention relates to aluminium alloys for manufacturing of aluminium cans by impact extrusion.
  • Aluminium cans for example aerosol cans, are typically manufactured from aluminium slugs by impact extrusion from alloys of series 1XXX and from the series 3XXX, which are previously stamped from an aluminium narrow strip.
  • the first digit (Xxxx) indicates the main alloying element, which has been added to the aluminium alloy
  • the second digit (xXxx) indicates a modification of the specific alloy
  • the third and fourth digits are numbers given to identify a specific alloy in the series and can refer, for example, to the purity of the aluminium or to the specific combination of alloying elements.
  • the body of the can may be formed by impact extrusion from slug.
  • the cans are internally coated and dried (polymerization) at around 250 °C.
  • the external coating, printing and lacquering follow. Drying of the external colour, printing and lacquering usually takes place at around 150 - 190 °C.
  • the neck of the can may be formed, for example, on a multi-die necking machine.
  • Aluminium alloys from 1XXX series are used for production of cans because they have good manufacturability at impact extrusion, being the most common aluminium grades EN AW 1050A having a minimum Al (aluminium) content of 99.5% by weight, and EN AW 1070 having an Al minimum content of 99.7% by weight. These two aluminium alloys are very ductile, but have reduced mechanical strength after lacquering, so the can weight cannot be lightened.
  • US7520044B2 discloses an alloy for can production based on system Al-Mg-Si system that comprises 0.12 to 0.20 weight % Fe (iron), 0.35 to 0.45 weight % Si (silicon), 0.25 to 0.40 weight % Mg (magnesium), 0.05 to 0.15 weight % Mn (manganese), and the rest is Al (aluminium).
  • a high percentage of Si > 0.35 wt.% promotes a quick wear of transformation tools, and also a higher tonnage press is needed to deform the slug to obtain the cans.
  • the presence of a high percentage of Mg also promotes a quicker degradation of the tooling and requires higher deformation forces.
  • FR2773819A1 proposes a can alloy with Cu (copper) and Mn, where the composition of Cu and Mn is inside a polygon defined by a system of axis with Mn (wt.%) in abscissa and Cu (wt.%) in ordinates.
  • a percentage of Mn between 0.2 and 0.4 wt.% promotes the maintenance of mechanical properties after lacquering.
  • Cu is limited between 0.4 and 0.65 wt.% in order to obtain a high corrosion resistance and high mechanical characteristics.
  • Ti should be within a percentage between 0.005 and 0.05 wt.% to obtain small as-cast grain size.
  • the high percentage of Cu also promotes a reduced corrosion resistance of the alloy.
  • FR2457328A1 discloses an alloy for can production with good cold deformation and resistant to the lacquering process.
  • This document discloses an alloy having ⁇ 0.4 wt % Fe, 0.15-0.35 wt. % Si, 0.15-0.35 wt. % Mg, ⁇ 0.01 wt. % Cu, ⁇ 0.2 wt. % Cr, ⁇ 0.2 wt. % Mn, ⁇ 0.15 wt. % Zr and ⁇ 0.05 wt. % of any other alloying element.
  • the described alloy has low Ti amounts ( ⁇ 0.05 wt. %), thus significantly reducing the beneficial effects typically associated with higher Ti relative amounts.
  • Cu weight percentage is very limited, which negatively impacts on the mechanical properties of the alloy, compared to alloys with higher Cu amounts, and promotes the formation of Al 2 Cu precipitates. Also, since low Mn amounts are present in these alloys, they are not in enough quantity to compensate for the presence of Fe, and acicular ⁇ -Al 5 FeSi phase formation occurs.
  • EP2881477B1 discloses a heat resistant alloy for can production with good cold deformation and resistant to the lacquering process.
  • This document discloses an alloy according to EN AW 1050A with Si ⁇ 0.25 wt. %; Fe ⁇ 0.4 wt. %; Cu ⁇ 0.05 wt. %; Mn ⁇ 0.05 wt. %; Zn ⁇ 0.07 wt. %; Ti ⁇ 0.05 wt. %, characterized in that each composition contains added Zr in an amount ranging between 0.10 and 0.15% by weight. Again, since low Mn amounts are present in these alloys, they are not in enough quantity to compensate for the presence of Fe, and acicular ⁇ -Al5FeSi phase formation therefore inevitably occurs.
  • EP3075875A1 discloses an aluminium alloy for cans manufactured by the impact extrusion method with constant mechanical properties before and after polymerization.
  • This document discloses an alloy that contains alloying elements in mass percent: 0.1-0.55 wt. % Fe, 0.05-0.2 wt. % Si, ⁇ 0.01 wt. % Mg, ⁇ 0.01 wt. % Cu, ⁇ 0.02 wt. % Zn, 0.0 - 0.03 wt. % Ti, 0.01 - 0.06 wt. % Mn, 0.05 - 0.2 wt. % Zr. The addition of Zr into the alloy in the range of 0.05 - 0.2 wt.
  • % allows to maintain tensile test strength and improve deformable and burst pressure.
  • the addition of Zr increase the recrystallization threshold above 300°C and other elements like Fe, Mn, Ti and Si in the form of intermetallic phases strengthen the aluminium matrix and provide higher mechanical properties, reflected on higher deformable and burst pressures.
  • these alloys are more expensive because they contain zirconium.
  • the use of such low amounts of copper and magnesium necessarily requires using high-purity raw materials produced by electrolysis, sometimes even by several consecutive electrolytic steps, to ensure that low amounts of any undesired specific metal, which may be a contaminant, are obtained. Due to this, the cost of these aluminium alloys becomes undesirably more expensive.
  • JPS6333185A discloses an aluminium alloy brazing sheet with excellent corrosion resistance and drooping resistance, composed by 0.2-1.5 wt.% Mn and 0.03-0.15 wt.% Zr.
  • Zr promotes coarsening of the crystal grain at core material brazing time and crystal grain formation, thus preventing the restraining action of Fe, which is present as impurity.
  • an amount of Zr is needed which corresponds to at least 20 wt.% of the Fe content.
  • Zr is an expensive alloying element, in contrast with Fe.
  • a higher percentage of Zr promotes an increase in the price of the alloy, and Fe is always present as an alloying element, but it can also be considered a contaminant depending on its wt.%. Reducing the Fe wt.% to low values in an alloy also supposes an increase in the price of the alloy, due to the need of working with high purity alloys.
  • WO2013040339A1 discloses aluminium alloys for impact extrusion manufacturing process employing recycled aluminium scraps with relatively pure aluminium.
  • Disclosed alloys are composed at least about 97 wt.% Al, at least about 0.1 wt.% Si, at least about 0.25 wt.% Fe, at least about 0.05 wt.% Cu, at least about 0.07 wt.% Mn and at least about 0.05 wt.% Mg.
  • These alloying elements in the disclosed amounts negatively modify metallurgical and mechanical characteristics, and also increase solidification temperature range, increase yield strength values and decrease ductility.
  • WO2018125199A1 discloses aluminium alloys for impact extrusion manufacturing processes employing recycled aluminium scraps with relatively pure aluminium. Alloy is composed by at least about 97.56 wt.% Al, at least about 0.07 wt.% Si, at least about 0.22 wt.% Fe, at least about 0.04 wt.% Mn, at least about 0.02 wt.% Mg and at most about 0.15 wt.% impurities and a balance comprising one of Cu, Zn, Cr, and Ti elements. Nevertheless, these alloys with low-alloying elements content are normally more expensive than the alloys with alloy compositions that can be obtained with less pure materials.
  • WO9937826A1 discloses aluminium alloys for the manufacture of containers. However, these alloys involve high Mg percentages (0.8-1.5 wt.%), which promote a quick degradation of tooling, and increase the tonnage loads when punching slugs.
  • WO2020048988A1 discloses an aluminium alloy consisting of: 0.07 wt.% to 0.17 wt.% silicon, 0.25 wt.% to 0.45 wt.% iron, 0.02 wt.% to 0.15 wt.% copper, 0.30 wt.% to 0.50 wt.% manganese, 0.05 wt.% to 0.20 wt.% chromium, 0.01 wt.% to 0.04 wt.% titanium, and the remainder aluminium and optionally additional admixtures.
  • a content in Fe over 0.25 wt.% implies a reduction on the ductility of the alloy, more tool wearing and also it could lead to the need of higher pressing forces.
  • Mn >0.3 wt.%
  • Mg is known in the art to potentially provide better mechanical properties
  • its use in aluminium alloys is responsible for the formation of intermetallics with an effect of precipitation hardening at the temperatures used for baking an inner lacquer.
  • metastable clusters and / or precipitates based on magnesium are formed (as Mg 2 Si), leading to an increase in strength and counteracting recrystallization, so a loss of strength is caused thereby.
  • the Cu content is limited to 0.02 wt.% to 0.15 wt.%, wherein such low amounts have been found to adversely affect strength and heat resistance of the aluminium alloy due to the reduced formation of Al 2 Cu precipitates.
  • WO2020048994A1 discloses an aluminium alloy consisting of: 0.07 wt.% to 0.17 wt.% silicon, 0.25 wt.% to 0.45 wt.% iron, 0.05 wt.% to 0.20 wt.% copper, 0.30 wt.% to 0.50 wt.% manganese, 0.05 wt.% to 0.25 wt.% magnesium, 0.01 wt.% to 0.04 wt.% titanium, and the remainder aluminium and optionally additional admixtures.
  • the content in Fe over 0.25 wt. % implies a reduction on the ductility of the alloy, more tool wearing and also it could lead to the need of higher pressing forces.
  • the present invention provides aluminium alloys for manufacturing of aluminium cans by impact extrusion, which solves the technical problems known in the art of:
  • the present invention provides an aluminium alloy by impact extrusion, wherein said alloy consists of:
  • Chemical composition of the alloy of the present invention allows to increase the recrystallization threshold to the higher temperatures and a higher back annealing resistance is obtained, resulting in improved container performance and mechanical properties.
  • elements like Fe, Mn, Ti, Cr and Si which typically are in the form of intermetallic phases, strengthen the aluminium matrix and enable the achievement of higher mechanical properties. Higher mechanical properties are reflected in high deformable and burst pressures.
  • the addition of Mn, Zr, V and other specific alloying elements can rise the recrystallization threshold of the material up above 300°C.
  • Aluminium alloys according to the invention enable the manufacturing of cans with the minimal decrease in mechanical properties or with the same mechanical properties as the starting material, i.e. alloy with minimal aluminium mass fraction of 99.5 wt. % Al.
  • Cans made from aluminium alloys of the invention achieve 2-3 bar higher deformation resistance and burst pressure compared with an alloy containing 99.5 wt. % aluminium.
  • the present invention provides an aluminium alloy by impact extrusion, wherein said alloy consists of:
  • Aluminium alloys of the invention may preferably have a silicon content in the range of 0.050-0.175wt. %, in the range of 0.050-0.150wt. %, in the range of 0.050-0.100wt. %, in the range of 0.075-0.200wt. % or in the range of 0.100-0.200wt. %.
  • This silicon content in the aluminium alloys of the invention was found to surprisingly avoid an increase of wearing of transformation tools.
  • Aluminium alloys of the invention may also preferably have an iron content in the range of 0.150-0.240wt. %, in the range of 0.175-0.240wt. %, in the range of 0.175-0.230wt. %, in the range of 0.190-0.230wt. %, in the range of 0.200-0.250wt. %, or in the range of 0.210-0.250wt. %. Alloys of the invention including this iron content were found to significantly avoid an increase of wearing of transformation tools and a decrease on the ductility of the alloy.
  • aluminium alloys of the invention may preferably have a copper content in the range of 0.300-0.650wt. %, in the range of 0.300-0.600wt. %, or in the range of 0.300-0.500wt. %. These aluminium alloys may also have a copper content in the range of 0.400-0.800wt. %, in the range of 0.500-0.800wt. %, in the range of 0.650-0.800wt. %, or in the range of 0.650-0.750 wt. % to allow heat treating the alloy, by creating small Al 2 Cu precipitates. Alloys of the invention, which include this copper content, advantageously guarantee achievable manufacturing forces. Furthermore, the presence of such high amounts of copper increases the mechanical properties of the alloys, as evidenced in the examples provided below.
  • Aluminium alloys of the invention may also preferably have a magnesium content in the range of 0.050-0.150wt. %, in the range of 0.050 to 0.100wt. %, in the range of 0.100 to 0.150wt. %, or in the range of 0.150-0.200wt. %.
  • a magnesium content in the range of 0.050-0.150wt. %, in the range of 0.050 to 0.100wt. %, in the range of 0.100 to 0.150wt. %, or in the range of 0.150-0.200wt. %.
  • this magnesium content also made it possible to avoid an increase of wearing of transformation tools, and balance the yield strength increase with the minimum percentage of iron to avoid adversely affecting elongation.
  • Aluminium alloys of the invention may preferably have a chromium content which is in the range of 0.003-0.040wt.
  • Titanium content of the aluminium alloys may preferably be in the range of 0.010-0.075wt. %, in the range of 0.010-0.050wt. %, in the range of 0.050 to 0.100wt. %, or in the range of 0.050 to 0.075wt. %.
  • This titanium content creates very fine TiB 2 particles and promote a very intensive grain refinement of the alloy which is difficult to achieve using other titanium ranges, thus increasing its mechanical properties.
  • the precipitation of such very fine intermetallics with Ti that are stable to thermal treatments counteracts the recrystallization effect. With the Ti amounts used in the aluminium alloys of the invention, wearing on transformation tools was mitigated.
  • boron content may preferably be in the range of 0.001-0.030wt. %, in the range of 0.001 to 0.010wt. %, in the range of 0.010% to 0.050wt. %, in the range of 0.010% to 0.030wt. %, or in the range of 0.030-0.050wt. %.
  • the presence of this boron amount was found to lead to increased formation of TiB 2 particles and promote a better grain refinement of the alloy.
  • Aluminium alloys of the invention may preferably have a manganese content in the range of 0.010 to 0.100wt. %, in the range of 0.010 to 0.080wt. %, in the range of 0.100 to 0.250wt. %, in the range of 0.200 to 0.400wt. %, in the range of 0.200 to 0.300wt. %, or in the range of 0.250 to 0.400wt. %.
  • the presence of Mn in such amounts was found to advantageously reduce the presence of ⁇ -Al 5 SiFe intermetallic needles, by transforming them into ⁇ -Al 12 (Mn,Fe)Si 2 , and also resulted in an increased deformability of the obtained alloys and reduced tool wearing.
  • This manganese content in the aluminium alloys of the invention was also found to avoid the necessity of much higher pressures of the machinery employed to make the deformation of the cans, thus making conformation easier. It also solved the sludge problem that occurs with high percentages of manganese in combination with iron, chromium and other alloying elements.
  • secondary alloying elements can be any other alloying element or impurity in the alloy with the proviso that secondary alloying elements are always present in a weight percentage less than 0.15%, more preferably in a weight percentage less than 0.150%.
  • secondary alloying elements can be any other alloying element or impurity in the alloy with the proviso that each individual secondary alloying element is always present in a weight percentage less than 0.05%, more preferably in a weight percentage less than 0.050%.
  • Aluminium alloys of the invention made it possible to provide enhanced mechanical properties. Specifically, they were found to better maintain the mechanical properties after polymerization, at the level of the starting material. This is reflected in achieving 2-3 bars higher deformable and burst pressures compared with the 99.5 wt. % Al alloy, in the case of Alloy 1 (see example below).
  • Figure 1 illustrates an exemplary aluminium alloy of the invention with the described microstructures at x50 augmentations obtained from slugs annealed at 500°C for 5 hours.
  • Cans made from the alloys of the present invention meet the burst requirements set forth by jurisdictional regulations, while being pliable enough to be formed using impact extrusion without an additional machine tonnage or a superior impact extrusion tooling, because mechanical properties at high temperature are advantageously improved. It is particularly surprising that, according to the invention, a defined percentage of Cu and Mg as alloying elements in combination with the rest of alloy components in the defined ranges of composition can bring about advantageous changes in the strength properties or the drop in strength in a can, preferably an aerosol can.
  • the containers of the present invention can be light weighted ( i.e. walls and bottom thickness can be thinned) and still meet the burst requirements, where cans made from conventional materials ( i.e. EN AW 1070 or EN AW 1050) cannot. Light weighting the containers is both environmentally and financially beneficial.
  • Aluminium alloy melt is produced in a melting furnace which is fed with the T-form blocks of electrolytic aluminium or with the electrolytic aluminium and with the process scrap obtained from stamping.
  • a melting furnace which is fed with the T-form blocks of electrolytic aluminium or with the electrolytic aluminium and with the process scrap obtained from stamping.
  • dross is removed from the melt and melt is poured into the holding furnace, where alloying of aluminium melt is performed.
  • alloying elements such as titanium (Ti), chromium (Cr), manganese (Mn), iron (Fe), silicon (Si), magnesium (Mg), copper (Cu) and others are added at this point.
  • alloying elements are added into the aluminium melt in the form of tablets, small blocks or wire, as master alloys or near pure elements, including high quality scraps as for the Cu.
  • Master alloy AlTi5B1 5% titanium; 1% boron (B)
  • B boron
  • Other master alloy compositions can be added to the melt to refine the microstructure, such as AlTi3B1, AITiC, or AITi10B1. If titanium boride is added to a composition comprising EN AW 1070 and EN AW 3104, then the amount of boron in the composition may not show a discernible increase.
  • the amount of boron in the composition can typically increase by less than about 0.0006 wt. %.
  • the amount of titanium in the composition may also not show a discernible increase, though there might be an increase by about 0.003-0.0055 wt.%.
  • a beneficial effect on grain refinement was observed, as discussed below.
  • the Ti based grain refiners allows the aluminium alloy to be grain refined during nucleation and solidification of the aluminium alloy.
  • metals solidify, the metal requires a surface on which to nucleate. Once the solid is nucleated, it will begin to grow. If there are very few nuclei in the melt, the resulting grains can be large because the grains grow unimpeded by their neighboring grains.
  • a melt with few nucleants can begin to solidify from the mold walls and impurities floating in the liquid metal, which results in a coarse as-cast grain structure lacking in ductility.
  • Lower ductility can negatively affect the ability to roll (hot or cold) the aluminium alloy.
  • large as-cast grains result in large second phase particles, which also reduce metal ductility.
  • solute elements can segregate to intergranular liquid pools, which become rich in the solute to form these particles or intermetallic compounds.
  • a Ti-based grain refiner can be added to a melt in order to form fine TiB 2 particles therein.
  • these particles can act as nuclei on which solidification can begin and from which grains can grow.
  • the grains can impinge on each other limiting their growth.
  • the size of the intermetallic compounds can decrease, and they will be more finely distributed in the metal matrix.
  • a main objective of grain refinement using a Ti base grain refiner can be to reduce the as-cast grain size.
  • the as-cast grain size the smaller size of intermetallics. If the as-cast grain size is very fine (less than about 10 microns) and well dispersed, then the grain growth during hot rolling and annealing can be reduced.
  • gases must be removed from the melt. Gases are removed from the melt already in the melting and casting/holding furnace with the so - called porous plugs, with rotatory degassers or by specific equipment. Degassing of the melt with the inert gas argon or nitrogen allows to reduce the total amount of dissolved gases into the alloy and also reduce the presence of oxides. After degassing, filters (ceramic foam, blankets...) are used to remove metal and non-metal inclusions from the molten metal.
  • Different casting methods may be used and may be chosen from a wheel belt caster, a Hazelett caster and/or a block caster.
  • a wheel belt caster When a wheel belt caster is used, the molten aluminium can be held between a flanged wheel and a thick metal belt during solidification. The belt wraps around the wheel at about 180°. Both the wheel and the belt are chilled with water on the back side to optimize and control heat extraction.
  • This wheel belt caster process is commonly used in the process to make EN AW 1070 and EN AW 1050 slugs.
  • the thick steel belt is inflexible and unable to deflect and maintain contact with the slab that is shrinking due to solidification.
  • the effect is magnified by the using more alloyed alloys because it solidifies over a larger temperature range (between about 480°C and about 685°C) than the EN AW 1050 and EN AW 1070 (typically between about 645°C and about 655°C) purer alloys.
  • the aluminium strip may reach a temperature of 530 °C at the casting wheel outlet. The aluminium strip travels to the hot rolling mill and then to the cold rolling mill through a roller track.
  • a Hazelett caster may be used.
  • the molten aluminium can be held between two flexible steel belts during solidification.
  • Steel dam blocks can be chain mounted and form the sides of the mold.
  • the parallel belts can slope slightly downward to allow gravity to feed molten aluminum into the system.
  • High pressure water is sprayed on the back side of both belts to optimize and control heat extraction. This highpressure water also deflects the belt to keep it in contact with the solidifying, contracting slab. This belt deflection enables the Hazelett caster to produce a wide range of aluminium (and other) alloys.
  • the Hazelett caster process is commonly used to produce architectural aluminum strip and may be used to produce impact extrusion slugs.
  • a block caster can be used.
  • the molten aluminum is held between a series of chain mounted steel blocks during solidification and form the sides of the mold.
  • the blocks are water cooled to optimize and control heat extraction.
  • a lubricating powder may be applied to the caster components that contact the slab. More specifically, a graphite or silica powder may be applied as necessary. Temperature control is important during and following the casting process. During casting, regardless of the casting process used, the cooling rate and temperature profile of the slab must be carefully controlled during solidification. The wheel belt caster reduces the cooling water flow rate to achieve this. If the Hazelett caster is used, the water flow for general control and gas flow over the slab may be used to closely modify the temperature. Ambient conditions, especially air flow must be controlled near the caster. This air flow control is especially critical when gas flow is used to modify the slab temperature.
  • the temperature of the slab at the exit of the caster must also be carefully controlled.
  • the exit temperature of the slab through the Hazelett caster can be above about 520°C, however the maximum temperature of any part of the slab exiting the caster can be less than about 582°C.
  • the exit temperature of the slab can be between about 430°C and about 490°C, which can depend on the composition of the aluminium alloy.
  • the process of strip rolling is performed by the reduction of the input narrow strip with minimal transverse deformation.
  • Longitudinal rolling is a continuous forming operation that reduces the cross-section of the material between the counter rotating rollers.
  • Reduction in the hot rolling mill is 40-70% of the strip thickness, while in the cold rolling mill it reaches 30-50%. Aluminium narrow strip is casted with the casting speed up to 10 m/min.
  • Stamping machines usually have from 60 to 625 strokes per minute.
  • Stamped slugs fall on the conveyor belt below the stamping machine. From here, they are led into the annealing containers and into the annealing furnaces, where the slugs are softened and the oil, which remained from stamping, is burned off.
  • the slugs are surface treated by sandblasting, vibrating or tumbling, since a certain degree of roughness is required for impact extrusion in order to homogeneously distribute lubricant on the surface of slugs before the impact extrusion process.
  • the manufacturing process of aluminium cans is composed of several stages, such as formation of the can body, lacquering, polymerization, printing, drying at high temperatures and formation of the neck of the can.
  • First the body of the cans is formed from the slug by the impact extrusion.
  • lacquering of the internal surface of can and polymerization of the coating at around 250 °C follows.
  • the coating of the external surface follows and drying at around 150 °C follows in the next step.
  • printing and drying of the print at around 150 °C follows and after that, lacquering of the external surface and drying at around 170-190 °C.
  • lacquering of the external surface and drying at around 170-190 °C In the last stage formation of the can opening, neck and the dome in the multi-step necking machine takes place.
  • Aluminium narrow strip is casted from aluminium alloy of the invention using a "rotary strip caster / wheel belt caster”, “Hazelett caster” and/or a “block caster” method(s), and advantageously enables the casting of narrow strip also without defects on the surface of the strip.
  • Example 1 Exemplary aluminium can alloys according to the invention (Preparation, composition and mechanical properties)
  • Aluminium slugs with different compositions have been prepared by melting a standard EN-AW 1050 base alloy in a 60-kg electric furnace, alloying elements at 720°C, homogenizing and de-gassing with hydrogen for 2 minutes and later pouring of 8 cylindrical bars in a die casting probe die.
  • the obtained cylindrical bars where preheated at 450°C for 1 hour 15 minutes and forged, with a 22% of section reduction in the forging operation.
  • Slugs where machined from bars and annealing thermal treatment was held at 500°C for 5 hours. After the slugs where shot blasted with white corundum f36 at 3bar.
  • Tables 1, 2 and 3 present the changes in the Brinell hardness (HB), Yield strength (Rp0.2), Ultimate tensile strength (Rm) and Elongation (A) values during different steps of the manufacturing process of cans in relation to the composition of Al alloy.
  • Table 1 Alloy 1 A5 A3Mn A3MnZr Si (% by weight) 0.107 0.088 0.080 0.090 Fe (% by weight) 0.217 0.205 0.300 0.200 Cu (% by weight) 0.464 0.001 0 0 Mn (% by weight) 0.022 0 0.320 0.240 Mg (% by weight) 0.052 0.003 0 0.130 Cr (% by weight) 0.004 0 0.030 0 Ni (% by weight) 0 0 0.010 0 Ti (% by weight) 0.015 0.014 0.020 0.020 Ag (% by weight) 0 0 0 0 V (% by weight) 0.013 0.011 0.010 0.010 Zr (% by weight) 0.0
  • Industrial cans were manufactured with standard equipment. ⁇ 44.5x6.8 mm slugs were employed to obtain ⁇ 45x190 cans with 0.28 mm wall thickness and 0.8 mm bottom thickness, for a pressurized can of 15bar. Test bars were obtained from manufactured cans before and after lacquering. The obtained results for cans before the lacquering process are specified in Table 2 and after lacquering in Table 3.
  • Table 4 presents the obtained results by performing the 15-bar test procedure over manufactured cans from the different alloys. Burst test results showed an increase of more than 2-3 Bar in the case of alloy 1 in comparison with A5 alloy and higher values than alloys A3Mn and A3MnZr. In the case of deformation test, Alloy 1 also showed about 2 bar increase in the case of Alloy 1 in comparison with A5 alloy, and slightly higher than A3MnZr alloy and A3Mn alloy. Table 4 Alloy 1 A5 A3Mn A3MnZr Deformation test (Bar) 20.4 17.77 22.74 19.12 Burst test (Bar) 24.34 22.93 25.40 26.51
  • the tensile strength of aluminium alloy of the invention and burst and deformation test were found to be higher at the end of the process compared to the tensile strength of A5 after extrusion, and similar or better than A3Mn and A3MnZr alloys.
  • the samples were cut from the slugs and prepared according to standard metallographic procedures, by hot mounting in conductive resin, grinding, and polishing.
  • the microstructure, the different regions and the averaged overall chemical composition of each sample were investigated by an optic microscope model DMI5000 M (LEICA Microsystems,Wetzlar, Germany).
  • Vickers microhardness FM-700 model (FUTURE-TECH, Kawasaki, Japan) was employed on the slugs and on obtained cans. At least 10 random individual measurements were made, and the obtained values were transformed to HB units.

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  • Extrusion Of Metal (AREA)
EP20382640.9A 2020-07-16 2020-07-16 Alliages d'aluminium pour la fabrication de boîtes d'aluminium par extrusion par percussion Withdrawn EP3940100A1 (fr)

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Citations (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2457328A1 (fr) 1979-05-25 1980-12-19 Cebal Alliage d'aluminium de type a-gs
FR2773819A1 (fr) 1998-01-22 1999-07-23 Cebal Alliage d'aluminium pour boitier d'aerosol
US7520044B2 (en) 2004-07-27 2009-04-21 Boxal France Aerosol can fabrication process
WO2013040339A1 (fr) 2011-09-16 2013-03-21 Ball Aerospace & Technologies Corp. Contenants filés par choc à partir de déchets d'aluminium recyclés
EP3075875A1 (fr) 2015-04-03 2016-10-05 Talum d.d. Kidricevo Alliage d'aluminium pour bombes aérosol fabriqué par l'extrusion par percurssion et procédé de préparation de celui-ci
EP2881477B1 (fr) 2013-12-06 2017-03-29 Moravia Cans a.s. Alliage résistant à la chaleur pour la production de boîtiers d'aérosol
US20180078982A1 (en) * 2013-04-09 2018-03-22 Ball Corporation Aluminum impact extruded bottle with threaded neck made from recycled aluminum and enhanced alloys
WO2018125199A1 (fr) 2016-12-30 2018-07-05 Ball Corporation Alliage d'aluminium pour récipients extrudés par choc et procédé pour le fabriquer
WO2020048994A1 (fr) 2018-09-07 2020-03-12 Neuman Aluminium Austria Gmbh Alliage d'aluminium, produit semi-fini, procédé pour fabriquer une pastille, procédé pour fabriquer une boîte et utilisation d'un alliage d'aluminium
WO2020048988A1 (fr) 2018-09-07 2020-03-12 Neuman Aluminium Austria Gmbh Alliage d'aluminium, produit semi-fini, procédé pour fabriquer une pastille, procédé pour fabriquer une boîte et utilisation d'un alliage d'aluminium
RU2718370C1 (ru) * 2019-11-18 2020-04-06 Акционерное общество "Арнест" Сплав на основе алюминия и аэрозольный баллон из этого сплава

Patent Citations (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2457328A1 (fr) 1979-05-25 1980-12-19 Cebal Alliage d'aluminium de type a-gs
FR2773819A1 (fr) 1998-01-22 1999-07-23 Cebal Alliage d'aluminium pour boitier d'aerosol
WO1999037826A1 (fr) 1998-01-22 1999-07-29 Cebal S.A. Alliage d'aluminium pour boitier d'aerosol
US7520044B2 (en) 2004-07-27 2009-04-21 Boxal France Aerosol can fabrication process
WO2013040339A1 (fr) 2011-09-16 2013-03-21 Ball Aerospace & Technologies Corp. Contenants filés par choc à partir de déchets d'aluminium recyclés
US20180078982A1 (en) * 2013-04-09 2018-03-22 Ball Corporation Aluminum impact extruded bottle with threaded neck made from recycled aluminum and enhanced alloys
EP2881477B1 (fr) 2013-12-06 2017-03-29 Moravia Cans a.s. Alliage résistant à la chaleur pour la production de boîtiers d'aérosol
EP3075875A1 (fr) 2015-04-03 2016-10-05 Talum d.d. Kidricevo Alliage d'aluminium pour bombes aérosol fabriqué par l'extrusion par percurssion et procédé de préparation de celui-ci
WO2018125199A1 (fr) 2016-12-30 2018-07-05 Ball Corporation Alliage d'aluminium pour récipients extrudés par choc et procédé pour le fabriquer
WO2020048994A1 (fr) 2018-09-07 2020-03-12 Neuman Aluminium Austria Gmbh Alliage d'aluminium, produit semi-fini, procédé pour fabriquer une pastille, procédé pour fabriquer une boîte et utilisation d'un alliage d'aluminium
WO2020048988A1 (fr) 2018-09-07 2020-03-12 Neuman Aluminium Austria Gmbh Alliage d'aluminium, produit semi-fini, procédé pour fabriquer une pastille, procédé pour fabriquer une boîte et utilisation d'un alliage d'aluminium
RU2718370C1 (ru) * 2019-11-18 2020-04-06 Акционерное общество "Арнест" Сплав на основе алюминия и аэрозольный баллон из этого сплава

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