EP3940098A1 - Alliages d'aluminium pour la fabrication de canettes d'aluminium par extrusion par percussion - Google Patents

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

Info

Publication number
EP3940098A1
EP3940098A1 EP20382638.3A EP20382638A EP3940098A1 EP 3940098 A1 EP3940098 A1 EP 3940098A1 EP 20382638 A EP20382638 A EP 20382638A EP 3940098 A1 EP3940098 A1 EP 3940098A1
Authority
EP
European Patent Office
Prior art keywords
aluminium
weight
alloy
alloys
content
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.)
Pending
Application number
EP20382638.3A
Other languages
German (de)
English (en)
Inventor
Ester Villanueva Viteri
Jon Mikel Sánchez Severino
Iban Vicario Gómez
Jorge Armentia Ortíz
María Begoña Bustinza Arriortua
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.)
Envases Metalurgicos de Alava SA
Original Assignee
Envases Metalurgicos de Alava SA
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Envases Metalurgicos de Alava SA filed Critical Envases Metalurgicos de Alava SA
Priority to EP20382638.3A priority Critical patent/EP3940098A1/fr
Publication of EP3940098A1 publication Critical patent/EP3940098A1/fr
Pending legal-status Critical Current

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
    • C22C21/08—Alloys based on aluminium with magnesium 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
    • 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
    • C22F1/05—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 of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions

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 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).
  • Si iron
  • Mg manganesium
  • Mn manganesium
  • Al aluminium
  • 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 an undesirable 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. %; and 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 ⁇ -Al 5 FeSi 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 % Fe, 0.05-0.2 % Si, ⁇ 0.01 % Mg, ⁇ 0.01 % Cu, ⁇ 0.02 % Zn, 0.0 - 0.03 % Ti, 0.01 - 0.06 % Mn, 0.05 - 0.2 % Zr.
  • the addition of Zr into the alloy in a range of 0.05 - 0.2 wt. % allows to maintain tensile test strength and improve deformable and burst pressure.
  • 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 processes 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.
  • WO2013061707A1 discloses an aluminium alloy, and its applications in the manufacture of lithium-ion battery housings to which certain mechanical properties are required, as well as the possibility of laser welding the plates of said alloy. Its composition is the following expressed in % by weight: 0.05 Mg, ⁇ 0.1 Ti, 0.05-0.3 Si, 0.05-0.7 Fe, 0.05-0.2 Cu, 0.8-1.5 Mn, 2-20 ppm B (or 2-10 or 2-30 ppm B) with the rest aluminium and unavoidable impurities.
  • this document refers to the presence of boron in the alloy in very low proportions, while this metal is understood to lend desirable characteristics to the alloy in the application of battery casing, and it also avoids the use of Ti-based grain refiners to increase the ductility of the alloy, wherein the latter may adversely affect grain refinement and fine grain hardening, thus also negatively impacting on strength and ductility of the resulting aluminium alloy. Also, an alloy for cans with a high Mn percentage (0.8-1.5 wt.%) promotes 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 high percentages of Mn (>0.3 wt.%), were added to avoid the needle-like ⁇ -Al 5 FeSi compounds, but the combination of both Mn and Fe elements increases the tooling wear, can reduce the ductility of the alloy and increase the risk of cracking.
  • Mg as alloying element is not described, but rather appears to be present as an impurity.
  • Mg is usually known in the art to provide better mechanical properties, metastable clusters and / or precipitates based on magnesium are formed (as Mg 2 Si), leading to an increase in strength and thus counteracting recrystallization, so a loss of strength is caused thereby.
  • the Ti content is limited to 0.01 wt.% to 0.04 wt.%, wherein said amounts of Ti are known to potentially affect grain refinement in an undesirable way. While the use of titanium in an aluminium alloy may typically result in advantageous grain refinement and fine grain hardening, which may eventually increase the strength and ductility of the aluminium alloy, for a correct grain refining, higher amounts thereof are known to be usually required, thus also increasing the cost of these alloys.
  • 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 higher temperatures, and a higher back annealing resistance is also obtained, resulting in improved container performance and mechanical properties.
  • tensile strength is maintained or improved and deformation resistance and burst pressure is increased.
  • 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 and other specific alloying elements can rise 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.%.
  • Cans made from aluminium alloys of the invention achieve 5-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 from 0.100 to 0.265 wt. %, from 0.150 to 0.265 wt. %, from 0.200 to 0.265 wt. %, or even from 0.200 to 0.260 wt.%. Alloys of the invention including this silicon content were 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 0.150-0.240 wt., 0.200-0.250 wt. %, or 0.210-0.230 wt. %. 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 0.010-0.090 wt.%, in the range of 0.010-0.080 wt.%, in the range of 0.010-0.070 wt.%, or in the range of 0.010-0.065 wt.%. They may also have a copper content in the range of from 0.065 to 0.100 wt.%. Alloys of the invention, which include this copper content, advantageously allow heat treating the alloy while only producing reduced amounts of Al 2 Cu precipitates. These copper contents were also found to guarantee a minimum elastic yield and ultimate tensile strength without reducing corrosion resistance of the alloy.
  • Aluminium alloys of the invention may also preferably have a magnesium content in the range of 0.080-0.180 wt.% or in the range of 0.080-0.160 wt.%. They may also have a magnesium content in the range of 0.100-0.200 wt.%, or in the range of 0.150-0.200 wt.%. With this magnesium content, aluminium alloys of the invention were surprisingly found to allow their heat treatment, while only producing reduced amounts of Mg 2 Si precipitates. Besides, this magnesium content also made it possible to avoid an increase of wearing of transformation tools, and balancing the increase of yield strength increase with the minimum percentage of copper and iron to avoid adversely affecting elongation.
  • Aluminium alloys of the invention may preferably have a chromium content which is equal to or less than 0.090 wt.%, equal to or less than 0.080 wt.%, equal to or less than 0.070 wt.%, equal to or less than 0.060 wt.%, or equal to or less than 0.055 wt.%. Aluminium alloys of the invention may also preferably have a chromium content which is less than 0.090 wt. %, less than 0.080 wt. %, less than 0.070 wt.%, less than 0.060 wt. %, or less than 0.055 wt. %.
  • titanium content of the aluminium alloys may preferably be in the range of 0.065-0.250 wt. %, in the range of 0.065-0.200 wt. %, or in the range of 0.065-0.150 wt. %.
  • the aluminium alloys of the invention may also preferably have 0.100-0.300% wt. % Ti, or 0.125-0.300% wt. % Ti.
  • Aluminium alloys of the invention may preferably have a manganese content in the range of 0.100-0.380 wt.% or in the range of 0.100-0.370 wt.%. Aluminium alloys may also have a manganese content in the range of from 0.100 to 0.200 wt.%, or from 0.150 to 0.200 wt.%.
  • 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.
  • boron content may preferably be in the range of 0.005-0.050 wt. %, in the range of 0.010-0.040 wt. %, or in the range of 0.010-0.030 wt. %. Boron content may also be between 0.005 to 0.015 wt. %, between 0.015 to 0.025 wt. %, between 0.025 to 0.040 wt. %, or between 0.040 to 0.060 wt. %. The presence of these boron amounts was found to lead to increased formation of TiB 2 particles and promote a better grain refinement of the alloy.
  • 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 obtain 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 5-bar higher deformable and burst pressures compared with the 99.5 wt. % Al alloy, in the case of Alloy 1 (see examples below), and about 2-3 bar in Alloy 2 and 3 (see examples below). These alloys advantageously avoided or at least reduced the presence and size of ⁇ -Al 5 FeSi due to the synergic combination of Fe and Mn in the selected amounts.
  • Figure 1 illustrates an exemplary aluminium alloy of the invention with the described microstructures with some porosity inherent to the slug manufacturing process (slugs were annealed at 500°C for 5 hours) at x50 augmentations.
  • 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 titanium as alloying element 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.
  • the majority of 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)) is normally added in the form of wire, which also serves to refine the microstructure of the alloy.
  • 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 discernable increase. In some embodiments, 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 discernable increase, though there might be an increase about 0.003-0.0055 wt.%. However, even without there being an apparent significant increase in the boron amount, a beneficial effect on grain refinement was observed, as discussed below.
  • the Ti-based grain refiners allow 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 aluminium 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 aluminium strip and may be used to produce impact extrusion slugs.
  • a block caster can be used.
  • the molten aluminium 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 multistep 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 3 bar.
  • 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 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 5 Bar in the case of alloy 1 in comparison with A5 alloy and higher values than alloys A3Mn and A3MnZr. Burst test also showed a 2-3 bar increase in the case of Alloy 2 and Alloy 3 in comparison with A5 alloy, similar in comparison with A3MnZr alloy and slightly smaller than A3Mn alloy.
  • the tensile strength of aluminium alloy of the invention and burst and deformation test values 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 increase of Ti in the alloy can reduce grain size, thus promoting that precipitates are smaller in size.
  • TiB 2 particles are very stable at high temperatures, improving mechanical properties of aluminium alloys at high temperatures.
  • 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.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Extrusion Of Metal (AREA)
EP20382638.3A 2020-07-16 2020-07-16 Alliages d'aluminium pour la fabrication de canettes d'aluminium par extrusion par percussion Pending EP3940098A1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
EP20382638.3A EP3940098A1 (fr) 2020-07-16 2020-07-16 Alliages d'aluminium pour la fabrication de canettes d'aluminium par extrusion par percussion

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP20382638.3A EP3940098A1 (fr) 2020-07-16 2020-07-16 Alliages d'aluminium pour la fabrication de canettes d'aluminium par extrusion par percussion

Publications (1)

Publication Number Publication Date
EP3940098A1 true EP3940098A1 (fr) 2022-01-19

Family

ID=71995913

Family Applications (1)

Application Number Title Priority Date Filing Date
EP20382638.3A Pending EP3940098A1 (fr) 2020-07-16 2020-07-16 Alliages d'aluminium pour la fabrication de canettes d'aluminium par extrusion par percussion

Country Status (1)

Country Link
EP (1) EP3940098A1 (fr)

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
WO1999018250A1 (fr) * 1997-10-03 1999-04-15 Reynolds Metal Company Alliage d'aluminium resistant a la corrosion et emboutissable, article constitue de celui-ci et son procede de production
FR2773819A1 (fr) 1998-01-22 1999-07-23 Cebal Alliage d'aluminium pour boitier d'aerosol
EP1624083A2 (fr) * 2004-07-27 2006-02-08 Boxal France Procédé de fabrication de boîtiers d'aérosols
WO2013040339A1 (fr) 2011-09-16 2013-03-21 Ball Aerospace & Technologies Corp. Contenants filés par choc à partir de déchets d'aluminium recyclés
WO2013061707A1 (fr) 2011-10-28 2013-05-02 株式会社神戸製鋼所 Conteneur en aluminium pour accumulateur secondaire, ainsi que son procédé de fabrication
EP3031941A1 (fr) * 2013-12-06 2016-06-15 Moravia Cans a.s. Alliage résistant à la chaleur pour la production de bombes aérosols
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
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
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

Patent Citations (15)

* 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
WO1999018250A1 (fr) * 1997-10-03 1999-04-15 Reynolds Metal Company Alliage d'aluminium resistant a la corrosion et emboutissable, article constitue de celui-ci et son procede de production
FR2773819A1 (fr) 1998-01-22 1999-07-23 Cebal Alliage d'aluminium pour boitier d'aerosol
EP1064413A1 (fr) * 1998-01-22 2001-01-03 Cebal S.A. Alliage d'aluminium pour boitier d'aerosol
EP1624083A2 (fr) * 2004-07-27 2006-02-08 Boxal France Procédé de fabrication de boîtiers d'aérosols
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
US20130068352A1 (en) * 2011-09-16 2013-03-21 Ball Corporation Impact extruded containers from recycled aluminum scrap
WO2013061707A1 (fr) 2011-10-28 2013-05-02 株式会社神戸製鋼所 Conteneur en aluminium pour accumulateur secondaire, ainsi que son procédé de fabrication
EP3031941A1 (fr) * 2013-12-06 2016-06-15 Moravia Cans a.s. Alliage résistant à la chaleur pour la production de bombes aérosols
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
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
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

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
"Aluminium and Aluminium Alloys, Alloy and Temper Designation Systems ED - Davis J R", 1 December 1993, ALUMINUM AND ALUMINUM ALLOYS; [ASM SPECIALTY HANDBOOK], ASM INTERNATIONAL, MATERIALS PARK, OHIO, PAGE(S) 21, ISBN: 978-0-87170-496-2, XP002728368 *

Similar Documents

Publication Publication Date Title
CN111032897A (zh) 形成铸造铝合金的方法
EP2664687B1 (fr) Produit d'alliage d'aluminium moulé à usinabilité améliorée et son procédé de fabrication
CN102796925A (zh) 一种压力铸造用的高强韧压铸铝合金
EP3842561B1 (fr) Procédé de fabrication d'un produit laminé en alliage d'aluminium
CN103205608B (zh) 用于铝蜂窝板芯的稀土铝锰合金箔的制备方法
JP2007092117A (ja) 高強度・低比重アルミニウム合金
US20120097297A1 (en) High hardness, high corrosion resistance and high wear resistance alloy
JP4542016B2 (ja) 成形用アルミニウム合金板の製造方法
AU2002302077B2 (en) Temperable Copper Alloy as Material for Producing Casting Moulds
JP2009144190A (ja) 高強度高延性アルミニウム合金板およびその製造方法
US4963322A (en) Process for the production of good fatigue strength aluminum alloy components
CN103946404A (zh) 冲压成形性与形状冻结性优良的铝合金板及其制造方法
EP0460234B1 (fr) Toles a base d'un compose intermetallique de titane-aluminium et procede de production d'une telle tole
JP5059353B2 (ja) 耐応力腐食割れ性に優れたアルミニウム合金板
JP5059505B2 (ja) 高強度で成形が可能なアルミニウム合金冷延板
JP3286982B2 (ja) 金型素材
EP3940098A1 (fr) Alliages d'aluminium pour la fabrication de canettes d'aluminium par extrusion par percussion
EP3940099A1 (fr) Alliages d'aluminium pour la fabrication de boîtes d'aluminium par extrusion par percussion
EP3940100A1 (fr) Alliages d'aluminium pour la fabrication de boîtes d'aluminium par extrusion par percussion
US20050158204A1 (en) Method of production of broadside plates for continuous casting molds
JP2007098407A (ja) 成形用アルミニウム合金板の製造方法
JP2006249481A (ja) 成形用アルミニウム合金板の製造方法および冷間圧延用アルミニウム合金板素材
EP1522600B1 (fr) Alliage d' Aluminium forgé à haute résistance en fatigue
JP7432352B2 (ja) キャップ材用アルミニウム合金板及びその製造方法
JP2007077485A (ja) 成形用アルミニウム合金板

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE APPLICATION HAS BEEN PUBLISHED

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: REQUEST FOR EXAMINATION WAS MADE

17P Request for examination filed

Effective date: 20220624

RBV Designated contracting states (corrected)

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR