CA2091355A1 - Aluminium alloy suitable for can making - Google Patents
Aluminium alloy suitable for can makingInfo
- Publication number
- CA2091355A1 CA2091355A1 CA002091355A CA2091355A CA2091355A1 CA 2091355 A1 CA2091355 A1 CA 2091355A1 CA 002091355 A CA002091355 A CA 002091355A CA 2091355 A CA2091355 A CA 2091355A CA 2091355 A1 CA2091355 A1 CA 2091355A1
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- CA
- Canada
- Prior art keywords
- accordance
- stock
- alloy
- less
- aluminium
- 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.)
- Abandoned
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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
- C22C21/10—Alloys based on aluminium with zinc as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/053—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 zinc as the next major constituent
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- 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)
- Metal Rolling (AREA)
- Containers Having Bodies Formed In One Piece (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Aluminium can stock which has strength, ductility and anisotropic properties in excess of conventional aluminium can stocks. The aluminium can stock is produced from an alloy with 3.0-8.0 wt%
zinc, 0.5-3.0 wt% magnesium, less than 0.7 wt% iron, 0.01-2.0 wt%
silicon, 0.05-0.9 wt% copper, 0.1-1.1 wt% manganese, less than 0.3 wt% chromium and incidental impurities less than 0.15 wt%. While zirconia is not generally an impurity in these aluminium alloys it is preferable that the amount present is less than 0.01 wt%.
The aluminium can stock is produced by a process comprising the steps of forming melt of the alloy metal suitable for casting, casting the melt into a form suitable for rolling, performing an intermediate rolling to an intermediate thickness, treating the alloy material with heat, performing finish rolling by a cold rolling reduction within the range of 2 to 85 % and temper heat treating the material to the desired ductility and strength properties.
zinc, 0.5-3.0 wt% magnesium, less than 0.7 wt% iron, 0.01-2.0 wt%
silicon, 0.05-0.9 wt% copper, 0.1-1.1 wt% manganese, less than 0.3 wt% chromium and incidental impurities less than 0.15 wt%. While zirconia is not generally an impurity in these aluminium alloys it is preferable that the amount present is less than 0.01 wt%.
The aluminium can stock is produced by a process comprising the steps of forming melt of the alloy metal suitable for casting, casting the melt into a form suitable for rolling, performing an intermediate rolling to an intermediate thickness, treating the alloy material with heat, performing finish rolling by a cold rolling reduction within the range of 2 to 85 % and temper heat treating the material to the desired ductility and strength properties.
Description
W092/03~86 2 ~ 913 S 5 PCT/AU91/00376 ~t,,.,. ,, -- 1 --.,.
TISLlS: a~W{I:2 IW aLI.OY SUITaBI~ FOR QN ~CING
~h~s invention relates to the use of aluminium based alloys for the manufacture of liquid containers and in particular to a high zinc content aluminium base alloy suitable for liquid container construction.
Conventional two-piece aluminium beverage containers are generally fabricated from two distinct alloys such as the Aluminium Association Specification 3004 and 5182 (See Table 1). 3004 alloy is generally used for body stock by deep drawing and wall ironing forming methods but lacks the necessary rigidity and strength properties to be a useful lid stock whereas 5182 alloy which ~s unsuitable for body stock has the properties desirable for can lid fabrication. Increased demand for this type of container and the need for stronger cans of thinner gauge materlal has spurred development of new alloys and in particular alloys which can be used for both body and lid stock.
To be suitable for can body stock an alloy must possess the required comb~nation of good formabil~ty and strength properties whilst also being economical to manufacture.
The AA3004 type alloy composition alloys are traditionally produced by casting the alloy using the 2~ direct chill casting method (DC-cast) into an ingot block of cross-section around 500 ~m thick x 700 mm , _~
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' ~ r ' , . ~ ' . , ' . ~ - ` ' ': ~' ~. .~ ' ' , ' ' W092~03586 - PCT/AU9l/00376 209~3S~ - 2 -wide. T~e ingots are then homogenised at temperatures between 500 and 620-C for 4-24 hours and hot rolled.
The hot rolling procedure red~ces the ingot thickness to a gauge ofiabout 2-3 mm by a series of breakdown passes.
The material is then usually annealed at temperatures of 300 - 400C for periods between O.S and 4 hrs to allow the metal to recrystallise. The annealed metal is then subjected to a cold rolling schedule to develop strength and other properties. This normally consists of 2 - 5 passes using 20 - 50% reductions to achieve a final gauge of about 0.3 - 0.33 , ,.
The final gauge sheet is then fabricated into alumini~m cans by use of a cupping machine and can body maker. Circular discs approximately 135 , diameter are cut or punched from the cold worked sheet on the cupping machine and drawn into shallow cups. The cup then enters the bodymaker and ig flrst redrawn into a cup close to that of its final diameter. The sidewalls are then reduced in thickness in one or more wall ironing operations to produce a can body around 65 diameter and 140 " high with a wall thickness of between 0.10 -0.18 mm.
The material from which the body is drawn has anisotropic properties (i.e. the properties d~ffer with direction) and so the top of the drawn body has a scalloped top, with approximately 4 peiaks oriented 90 apart the peaks of which are called ears. The degree of SUBSTITUTE SHEET
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2~91355 "earing" is determined simplistically by the following equation:
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where h. is the distance between the bottom of the cup and peak of the ears and ht is the distance between the bottom of the cup and valley of the ear.
For the body to be acceptable for further fabrlcation into a beverage container the formed body must have earing levels of no more than 3-5% and preferably less than 3%. The tops of the can bodies are trimmed off (fixed for a given process), during a slitting operation and the "eared" area is scrapped.
Another ma;or considerat~on of the quality of the finished body is its ability to form in the body maker without tearing and to have a s~ooth surface finish, free of drawing streaks and lines. Deep grooves caused by "galling" may appear on the finished can walls if the material is not of the correct microstructure.
Downgauging of conventional strain-hardened alloys to reduce the cost of body manufacture requires the use of increased alloying element concentrations (e.g.
copper, manganese and magnesium) to increase strength.
~owever, as these concentrations are increased, the formability of the resultant alloy decreases; in fact, SUBSTITUTE SHEET
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W092/03s86 2 0 913 5 ~ PCTtAU91/00376 the potential strength of the 3xxx series based alloys is ultimately limited by the amount of ralling strain which can be sustained during processing before surface finish and material properties deteriorate. Other aluminium alloy systems currently used for other applications are potentially capable of achieving much higher strength levels than 3xxx series alloy.
Although, ultimately, a container can be formed from a fabr~cated downgauged high strength 3004 type alloy of non-galling, low earing characteristics, unless the strength is great enough to offset the strength lost from reduced wall thickness the buckle resistance of the can will be reduced.
Buckle strength of resistance is determined by applying pressure with~n a drawn and wall ironed can and then gradually increasing the pressure until the bottom end of the can deforms and bulges out, ~.e. it buckles or the inverted dome reverses. The pressure at which the bottom buckles is then designated as the buckle strength or dome reversal pressure. To be acceptable as a can body a can formed from the alloy sheet must exhibit a buckle strength of at least 85 p.s.i. Cans drawn from high strength 3004 alloy produced using conventional direct chill (D.C.) cast methods exhibit a buckle strength of about 90 p.s.i.
Whilst the production of 3004 body stock by the ingot casting method is widely used, economic and energy SUBSTITUTE SHEET
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considerations would favour the manufacture of aluminium sheet by a continuous cast route. The prior art has addressed the continuous strip cast method where aluminium is cast into a thin alloy web about one inch thick~ She homogenisation process may be eliminated and the hot rolling reductions to intermediate gauge are minimised using this technique and the process of hot rolling can be eliminated entirely if the desired microstructure is achieved during continuous casting of very thin strip. The material is then annealed and processed in a manner similar to ingot cast materials. At this stage, can stock produced by this method has proven unsatisfactory for further processing and can body manufacture.
lS ~hus, it is an ob~ect of the present invent~on to provide an aluminium alloy suitable for can stock which has non-gall~ng, low earing and high strength characteristics with good formability at least comparable with existing AA3004 type alloys which will allow can bodies to be made from thinner sheet feed stock. It is also an object of the present invention to provide can stock which is also suitable for the manufacture of can lids thus, allowing manufacturing of a complete two-piece beverage can from one alloy 2~ composition. ~he alloy will be amenable to fabrication into can stock via both tbe direct chill cast and the continuous strip cast methods. Accordingly, the invention relates to a can stock and process for SlJBsTlTuTE SHEET
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; , . `~ - ~.................. . -.- . ; - . ' W092/03~ 913 ~ ~ PCT/AU9l/00-~76 producing a can stock from an aluminium alloy comprising 3.0 - 8.0 wt% zinc, 0.5 -3.0 wt% magnesium, less than 0.7 wt~ iron, 0:01 - 2:0 wt% silicon 0:05 -0.9 wt%
copper, 0.1 - 1.1 wt% manganese and 0.00.3 wt%
chromium. The incidental impurity level in the alloy is less than a total of 0.15 wt%.
In accordance with another aspect of the invention, the alloy is processed into feed for a can line by a process comprising, forming a melt of the alloy metal suitable for casting, casting the melt into a form suitable for rolling, performing an ~ntermediate rolling to an intermediate thickness, treating the alloy with heat, performing ~in~sh rolling by cold rolling within the range of 2 to 85%, temper heat treating the material to the desired ductility and strength.
The alloy preferably comprises constituents in ~ollowing weight percent ranges, zinc 4.0 - 6.5, magnesium 1.0 - 2.5, manganese 0.3 - 0.8, silicon 0.15 -O.3, iron up t~ 0.45, copper 0;10 - O.50, ~omium up to 0.20 total incidental impurities less than 0.1.
SUBSTITUTE SHEET
' , - ' ,, , 2~913~5 W092/03~86 PCT/AU9t/00376 While an alloy containing zirconium up to a maximum level of 0.25 wt% may be suitable for can stock, to produce a can body with low earing, it ~s preferable that the zirconium level is less than 0.08 wt% and most S preferable that it i~ not added to the melt and its level is below tbh standard level of impurity for that element of 0.01 wt%.
It has been found that an alloy which falls within the above compos~tion range achieves high tensile and yield strength properties as well as good formability and "non-galling" wall ironing quality. Thus the alloy is preferably used to produce both the body and the lid of the beverage container.
She alloy is capable of producing a can body which has a dome reverYal strength in excess of 9O p.s.i. and a wall ironed thickness of less than 0.16 mm. A 3004 alloy is generally only capable of achieving such a dome reversal strength with a wall thickness equal to or greater than 0.16 mm.
The above alloy may suitably be cast by the direct chill casting method, continuous roll casting or continuous strip casting. However, if the alloy is to be produced using roll or strip casting the compositional range of the alloy can be broadened.
2S The amount of Zn, Mg, Mn, Fe and Si may be increased which results in higher volume fraction of SUBSTITUTE SHEET
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W O 92/03586 2 0 913 5 5 PC~r/A U91/00376 alpha phase particles a~ter casting and a greater amount of precipitation during final processing.
The alloy sheet may be produced by a combination of rolling reduction and heat treatmant in the final stages of manufacture. Consequently, fabrication steps vary with end use requirements. ~owever, during the performance of the heat treatment processes, it has been found that the alloy thus formed was especially adaptable to solution heat treatment of very short duration, while more lengthy heat treatments can be used to simultaneously anneal the sheet using recrystallisat~on anneal or recovery anneal techniques.
For container construction or for other requirements where strength and Sormability are important the ingot or strip cast material may be heat treated to homogenise the cast material and preferably hot rolled ar.d then cold rolled. ~he material is then solution heat treatet and given a cold rolling reduction. Lastly to improve strength and ductility, the alloy is aged to a temper dependent on the end use requirements.
Preferably the cast material, if ingot cast, is subjected to an additional heat treatment step to homogenise the alloy and preferably followed by a hot rolling step.
~he intermediate rolling preferably is a cold SUBSTITUTE SHEET
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W092/03586 PCT/AU9l/00376 ~ rolling stage and may employ a full anneal or recovery intermediate anneal during the cold rolling practice.
The step of treating the alloy with heat is preferably a solution heat treatment which may be followed by a natural ageing stage.
~he fin~sh rolling step is essential to the invent~on to provide the necessary strength properties to the final product but still must maintain sufficient ductility and formability properties to be a su$table can stock. The finish rolling is thus a cold rolling reduction in the range 2-85% and preferably within the range of 10-80% and most preferably within the range of 30-80%. The final temper heat treatment is preferably artific~al ageing. --In accordance with a further aspect of the invention there is provided a can line feed produced from the alloy of the invention which preferably has yield and tensile strength of in excess of 400 MPa and a total elongation of 4% or more.
The alloy of the invent~on may also be used to produce can endstock which in a tempered state must have a miniumum yield stress of 31Q MPa, a minimum ultimate tensile stress of 355 MPa and MIN 6% elongation.
The strengths and elongations specified above for can end stock relate to the post bake strength of the material.
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WO 9~/035X6 2 0 91~ 5 ~ PCltAU91/00376 Generally endstock i~ manufactured in coil form and is -~ent to tbe end makers who then coat tb~ material and bake the coated sheet at modest temperatures of between 155C and 210C for 10 - 30 minutes. Usually a specified test for the metal is 205C bake for 20 minutes. The can end maker then produces the can ends by conventional metal farming processes which are well known to those skilled ~n the art.
As can endstock made in accordance with the invention has strength and ductility properties in the "post baked" state in excess of the above miniumum values, suitable can ends can be produced from the alloy in accordance with the invention.
A further aspect of the lnvention is a two piece beverage container produced from the alloy of the invention. The container preferably ha~ a wall th~ckness of less than 0.12 , and a dome reverasal strength of greater than 90 p.s.i.
The foregoing and other features ob~ects and advantages of the present invention will become more apparent from tbe following description of the preferred embodiments and accompanying drawings.
Table 1 contains details of the invention alloy range and preferred range.
Figure 1 is a flow diagram showing the overall processing details for the alloys;
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W092/03586 2 0 913 5 5 PCT/AU9l/00376 Figure 2 is a Differential Scanning Calorimetry Thermal Analysis curve for the invention alloy; F~}se Flgure 3(a) is a flow diagram representing the final stage fabrication of the alloy;
Figure 3(b) illustrates the effect of the final cold rolling reduction, and F~gure 3(c) represents the effects of cold working and artificial ageing on the alloy of Example l;
Figure 4 shows micrographs of alloy 2 of Example 2 at ~arious stages of processing in which 4(a) is the microstructure after the material is hot rolled, 4(b) is the microstructure after. the mater~al has been annealed 4(~) is the microstructure after the final cold rolling reduction Figure 5 shows the effect of natural ageing on Alloys 1, 2 and 3 (Example 2).
Figures 6 - 8 are graphs representing the response of the alloys of Example 2 to time at a given temperature in the final ageing treatment.
Figure 9 represents the effects of natural ageing . and ~oldwor~ on the alloy;
.
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W O 92/03586 2 0 913 5 5 PC~r/A U9l/00376 Figure 10 represents the effect of using a double heat ~reatment in the art~ficial ageing step and the effect of coldwork;
Fl~ure 11 represents tensile results for the alloys of the invention;
Figure 12 represents strength and ductility characteristics for the alloys of the in~ention compared to those of conventional 3004 body stock; and Figure 13 represents an overview of the benefits of the alloys of the invention.
An alloy in accordance with the invent~on comprises the following basic alloying elements (wt%): copper (O.05 - O.9), mangane~e (O.1 - 1.1), magne~ium (O.5 -3.0), and a relatively high concentrat~on of zinc (3.0 -8.0). Furthermore, the following add~tives are included ~n the melt: chromium (0.0 -0.30), silicon (0.1 - 2.0) and iron (0.0 - 0.5).
It has been found that, after solution heat treatment the majority of the magnesium and zinc are suspended in solid solution and precipitate during the tempering heat treatment adding the required strength to the alloy.
It is essential to the invention that the silicon, manganese and iron add~tives be within the ranges specified above as these elements are required to form SUBSTITUTE SHEET
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W092/03~86 PCT/AU91/00376 the desired dispersed second phase distribution (alpha phase) in the alloy which is critical for the production of a non-galling wall ironed can.
Zirconium and chromium are typically found in the melt at impurity levels of less than O.Cl wt%, but if already present or added to the melt for additional strength properties, it is preferable that they are present at levels less than 0.08 wt% and less than 0.05 wt% respectively.
~he effect of the very low levals of grain refining elements chromium and preferably zirconium, is that full recrystallisation of the product after, for example, hot rolling or low temperature annealing (345C for 0.5 - 2 hours) can take place.
~f the zirconium and chromium levels in the alloy exceed the specified levels in the present invention, then the wrought structure created by hot and cold rolling will be retained during solution heat treatment or anneal and the properties of the final gauge sheet will be more anisotropic. This is particularly disadvantageous if the sheet material is to go through deep drawing operations as the anisotropic properties result in material of high earing which is undesirable for the can body making process. High strengths can be obtained by increasing the concentration of these i ele~ents but formability and earing suffer as a result.
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Wos2/03~86 PCT/AU91/00376 The yield strength and tensile strength of the 10 alloy in accordance with the invention is far greater than that of a 3xxx series can body material. The 3004 alloy has yield and tensile strengths of around 285 and 330 MPa respect~vely with 4S elongation whereas the alloy of the invention exhibits yield and tensile strengths around 420 and 480 MPa respectively with a total elongation measured on a 50 mm gauge length of 4%
or more. When such a sheet is drawn and wall ironed into a body for a two-piece beverage container it possesses can buckle strengths in excess of 100 p.s.i.
with a wall thickness of 0.12mm. The véry high strength and improved duct~lity of this alloy over any type of 3004 or modified 3xxx series alloy allows the gauge of sheet used for the initial forming operatlon (can line feed) to be reduced by at least 10% while still retaining buckle strength and formability in the finished body.
The high strength of this alloy also allows it to be made into lid stock for cans. Alloy AA5182 which is currently used for beverage can lids has a tensile strength of 395 MPa and an elongation of 4%. The 3004 alloy is generally not used to produce lid stock as it does not have sufficient strength for the desired lid thickness. The invention alloy can match the properties of AA518Z, and thus a two-piece can may be made from one alloy composition instead of the conventional two.
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W092/03S86 PCT/AU9l/00376 When the alloy is cast by the DC-casting method to produce can bodies it i3 first homogenised. The cast is preferably homogenised as a block between 480- and 500oc for a period of 5 to 10 hours. ~he material is then hot rolled preferably from a temperature of up to 500C down to a thickness ~uitable for coiling (preferably less than 5 ). It is preferable that the hot rolling coil finishing temperature is above about 300C as the alloy will automatically anneal during the coiling operation.
The material is then cold rolled and preferably employs a full anneal or recovery intermediate anneal during the cold rolling practice. After this rolling stage the strip preferably has a thickness of between 0.8 and 0.4 mm. ~hese thicknèsses are required as a rolling reduction must be effected dur~ng the final processing to can sheet gauge to provide the necessary sheet flatness and final gauge strength. Next a solution heat treatment at temperatures preferably between 480C and 595C for duration times between 5 seconds and 1 hr is followed by a water quench to ambient temperature.
A solution heat treatment for duration times toward the upper end of the range will also anneal the material if it has been cold rolled prior to the solution heat treatment. Nevertheless, the composition of the alloy allows the material to be heat treated for much shorter times than would normally be performed in processing SuBsTlTuTE SHEET
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The alloy strip may then be allowed to naturally age at room temperature preferably for a period of zero to 48 hours prior to cold rolling of the strip.
To provide the necessary strength properties in the metal, lt is necessary that the finish rolling step, has a cold rolling reduction within the range 2 to 85 percent, the reduction preferably being lO and 80% and most preferably 30 and 70%. It has been found that even with a cold rolling reduction towards the upper limits of this range, the necessary ductility and formability properties for a viable can stock are present.
Finally the sheet material is aged to a temper between the underaged and over-aged states. The ageing w~ll depend on the equipment used and the can manufacturer's strength and ductility specifications and is preferably within the range 120 to 26-C for a time of between l minute and 4 hours.
Solution heat treatment of the material prior to the final processing recrystallises the material and reduces the anisotropic properties created by the cold rolling schedule. This means that when given a final rolling reduction a~d fully aged to the desired temper, a deep drawing material is created which has very low anisotropic properties and very low earing levels. A
cup formed from final gauge 3004 or ~odified alloy SUBSTITUTE SHEET
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W092/03SX6 2 0 913 5 ~ PCT/AU91/00376 typically has an earing level of 3%, whereas a cup formed from an alloy of the present invention has earing levels of less than 2%.
An alternative to the direct chlll cast method is that the alloy can be strip cast in a conventional strip caster and solidified into a web approximately an inch or less in thickness. The molten alloy feedstock for this, may be richer in composition than that used in the DC cast alloy but would be of the preferred invention alloy range (see Table 1). It is then preferred that the strip is given a hot or cold rolling reduction in sheet thickness of at least 25% and more preferable 50 to 85%.
The alloy composition o the present invention and processing techn~que allows llquid container bodies to be made from thinner gauge sheet stock and achieve cost reductions. Furthermore, one alloy can be used for body end stock and easy-open tab stock by varying the processing steps of the alloy. The use of a single alloy type for all of the component parts of liquid container results in production costs benefits and improvements in scrap recycling efficiency.
The alloy of the invention is now demonstrated in the following Examples.
An alloy with the following composition (wt%) was direct chill cast to an ingot size of 50 cm x 120 cm SUBSTITUTE SHEET
~" :'.'' . ', ' ' ' ' "' ', ' ' . ' ' . ' ' ' , , W092/0358~ PCT~AU9l/00376 zn Mg FE Si Cu Nn CrAl 4.83 1.53 0.35 0.16 0.019 0.47 0.01 balance The ingot was subjected to the following schedule to produce a coil of the sheet.
- homogenise 5 hrs 4800 - 595C
- hot roll to 3.175 " .
coil exit gauge temperature 295 - 315C
- standard edge trim applied - anneal 370C - 373 for 3 hours - cold roll 60% reduction to 1.22 - solut~on heat treatment at 1.22 flash solutionise at 585C for 10 seconds - cold roll~ng reductions 40% to 0.73 ., 37% to 0.454 - 35% to 0.303 mm - level and solvent wash - artificial ageing to T87 temper - age at 160C for 1 hr.
In the schedule, the coil, once heat treated, was rolled in back-to-back passes to final gauge with a SuBsTlTuTE SHEET
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maximum delay of 48 hours before commencing to roll.
Levelling was performed within 5 days of cold rolling to avoid eccessive natural ageing as the material age harden~ after cold rolling.
An average of 50 samples tested gave yield strength = 393 MPa ultimate tensile strength = 406 MPa elongation 4%
ductility = 4.34 mm Can bodies produced from the samples showed a dome reversal of 105 p.s.i. from 0.30 mm dome wall thickness.
Figure 3(b) illustrates the effect of the final cold rolling reduction on the strength and ductility of the alloy and F~gure 3(c) demonstrates the effect of artificial ageing time on strength and ductility of the above alloy after solution heat treatment (S.H.T.) and 70% cold rolling reduction. The ageing temperature is 250F (121C).
Three alloys iA accordance with the invention of compositions shown in Table 1 were direct chill cast into ingots 100 x 300 mm in cross-section of 1.2 m length. The ingots were then scalped into blocks 190 wide and 100 mm thick and lengths of 200 mm. Each of the ingots were then heomogenised at temperature between 500C and 585~C. A higher bomogenisation temperature was SUBSTITUTE SHEET
wo 92/o3s86 2 ~ 9 i3 S ~ - 20 - PCT/AV91/00376 used for the alloys of highest solute content to allow for more complete homogenisation. The thermal analysis curve of the precipitation reaction in the alloy during ~eomogenisation is shown in Figure 2. The following S letters represent the positions in Figure 2, where changes in the various phases occur. As is the dlssolution of GP zones; B is the precipitation of (MgZn2) phase, C, the disæolution of ~ ~ ~ phase: D, the precipitation of T phase, E, the dissolution of T
phase; and F the localized GB liquidation.
Homogenisation and hot rolling schedules for each of the sample alloys are shown in Table 2.
To hot roll the alloys the scalped blocks were cooled to a rolling temperature of between 500 and 485C
~n the ~urnace. The blocks were then removed from the furnace and ind~vidually rolled from a gauge of 100 mm to a finished gauge of approximately 2 - 3 . The microstructure of the hot rolled material is shown in Figure 4a.
~he finishing temperature of hot rolling was often above 200-C which was sufficient to allow some recovery of the rolled structure prior to cold rolllng to the solution heat treatment gauge. ~owever, in the case of some of the alloy 3 samples, the material was given a recrystallisation anneal at a temperature of 345C for 3 hours. This allowed the material to fully recover and recrystallise. The fully recrystallised grain size of SuBsTlTuTE SHEET
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W092/03586 2 ~ 9 ~ 3 5 S PCT/AU91/00376 the alloy had an average diameter of l9m (ASTM 8.S) (Flgure 4b).
In this softened condit~on the alloys were cold rolled to a number of different gauges as shown in Table 4. This was to allow for a number of different final cold rolling reductions to be made to the given final gauge material for body stock forming. A schematic of the Sinal material processing is included in Flgure 3a. `
Figure 4(c) shows the microstructure of alloy 2 in Example 2 after the final cold rolling reduction and as can be seen from the micrograph the material has an ;r alpha phase (a - Al(Fe,Mn)S~) totally dispersed within the matrix. This microstructure results in a wall ironed can body with excellent non-galling properties.
Solution heat treatment of the plate was conducted at a temperature of 500C to put elements into solution in preparation for the final ageing procedures. A study of the natural ageing behaviour of the three alloys after solution heat treatment of 2 hours at 500C is shown in Figure 5. The material was cold water quenched and then given a number of heat treat~ents. Ageing studies and hardness measurements were used to charactise the response of the alloys to various treatments. Tensie studies were then made o~ sheet in certain conditions to establish the yield strengths and elongations of the specific alloy treatments.
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w092/03586 PCT/AU91/00376 Final ageing treatment studies are show in Figures 6 - 8.
Figures 6(a), 6(~) and 6(c) show the respon~e of the alloys to ageing at 155C aSter a first ageing stage at 121C Sor 1, 2 and 3 hours respectively.
Figures 7(a), 7(~) and 7(c) represents the ageing response of the alloys at 111C with a preced~ng natural ageing stage of 0, 24 and 48 hours respectively.
Figures 8(a), 8(b) and 8(c) represent the ageing response of the alloys at 131C with a preceding natural ageing stage of 0, 24 and 48 hours respectively.
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HIGH STRENGTH CAN STOCK ¦ :
ALLOY COMPOSITION I I
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, CHEMICAL COMPOSITION (wt%) = A1 Zn Mg Mn Si Fe Cu Cr ¦
Alloy 1 Bal 3 8 1.1 0.460.2 0.3 0.12 ~.007 Alloy 2 Bal 4.6 1.3 0.42 0.2 0.4 0.10<.008 ¦
L Alloy 3 eal 6.0 1 8 0.560.2 0.350.10 OO
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¦ Alloy 1 500 500 100 2.5 ¦ Alloy 2 565 490 100 2.7 ¦ Alloy 3 585 480 100 2.8 .
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~9135~ -WO 92~03~86 PCI`/AU91/00376 -Gauge ShVAnn N.A. C.W. M11~ (2) YS urs EL Eanng Dùme Rev ID. Imm1 (C/hO Ihn) (%) ~hnl lhn) IMPa) lMpa) 1%~ l%) IPs8 ~1 0.320 500/1 48 lO 121/3 ~5513 - - - 0.0 62 ~1 0.320 500/t 48 lO ~21/3 15513 - - - 0.2 a1 ~1 0.320 500/1 48 10 121/3 ~55/3 - - - 0.1 ~1 0.320 500/1 48 10 121/3 ~55/3 - - - 0.2 a4 ~1 0.320 500/1 48 30 121t3 155/3 - - - 0.0 84 ~1 0.320 50011 48 30 121/3 15513 - - - 0.0 a8 ~1 0.320 soal1 48 30 121~3 155/3 - - - QS 90A1 0.320 500/1 4a 30 121/3 155/3 - - - 0.1 -~1 0.342 500/1 48 60 121/3 15513 318 335 3.1 0.9 A1 0.321 500/1 U 60 12113 155/3 304 324 5.1 1.7 ~106 ~1 0.320 500/1 48 60 121/3 155/3 - - - 1.9 A1 0.328 500/1 48 60 121/1 155/4 315 339 2.8 æ1 184 Al Q320 500/1 48 60 121/3 - - - - 2.6 9B
A1 0.329 500/1 4B 10 121/6 - 181 æ8 9.6 Q2 80 ~1 0.328 500/1 48 60 121/6 - 316 343 4.2 2.0 ~1 0.305 500t1 4a 60 121/24 - 332 351 5.1 1.9 A1 0.311 500/1 48 60 121124 - 324 349 4.8 2.2 A2 0.320 500/1 4B 60 121/3 - - - - 2.0 A2 0.326 500/1 U 60 121/6 - 372 391 4.9 1.8 ,108 A2 0.320 500/1 U 10 121/6 - - - - 1.9 - ;
A2 0.307 500/1 48 30 121/6 - 353 390 7.3 1.7 104 A2 0.296 500/1 48 30 121/24 - 383 483 6.3 1.3 A2 0.322 500t1 48 60 121/24 - 369 392 3.5 1.5 ~108 A2 0.325 500t1 48 60 121/24 - 375 395 4.6 1.9 ~110 A2 Q320 500/1 48 10 121t3 115/3 - - - 0.4 102A2 0.320 500t1 48 30 121/3 155/3 - - ~ 15 A2 0.320 50a~1 U 30 121/3 15513 - - - 2.0 >108 A2 0.320 500t1 48 30 121/3 155/3 - - - 2.4 >108 ~2 0320 500/1 48 30 121/3 155/3 - - - 1.5 ~112 A2 0 323 500/1 48 60 121/3 15513 373 395 3.9 2.1 ,109 -A2 0.320 500t1 48 80 121/3 155/3 - - - æo A2 0.326 500/1 48 60 121/3 15513 374 393 6 1.8 10B
A2 0.320 500/1 48 60 121/1 155/4 - - - - 1.5 ~3 0.325 500t1 48 60 121/24 - 400 501 3.2 2.2 ~3 0.3~,1 500t1 48 60 121/24 - 473 478 4.3 ~3 0.330 500t1 48 30 121/24 - 418 435 53 0.8 ~3 0.295 500/1 U 10 121/6 - 423 464 8 1.1 A3 0.315 500/1 48 30 121/6 - 439 471 7 1 1 A3 0.327 500t1 U 60 121/B - 263 492 3 A3 0.315 500/1 4B 10 121/3 155/3 386 473 10 0.6 ~3 0.326 500/1 48 30 121/3 155/3 424 4U 4.5 0.9 A3 0.331 500/1 48 30 121/3 15513 417 451 5.6 Q9 A3 0.348 500/1 48 60 121/3 155/3 467 468 1.2 2.0 A3 0.328 500/1 48 60 121/3 155/3 441 454 2.5 1.9 ~3 0.326 500/1 48 60 121/1 155/4 448 475 5 SUBSTITUTE SHEET
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W092/035~ 0 913 ~ ~ PCTtAU91/00376 Figure 9 demonstrates the effect of cold rolling -alloy 2:
Figures lO(a) and lO(b) demonstrate the effects of secondary artificial ageing on material of alloy 2 with prior cold word (cw) treatment from 0-60%. The alloy of Figure lO(a) has undergone a solution heat treatment of 500C for 2 hours, 0 hours natural ageing, cold working and united artificial ageing at 1210C
for 3 hours. In Figure lO(c), the alloy has undergone solution heat treatment at 500C for 2 hours, 48 hours of natural ageing, cold working and an initial artificial ageing at 121C for 3 hours.
Table 4 demonstrates the response of alloys 1,2 and 3 of Example 2 to varying effects of cold working and artif~cial ageing.
The column marked C .W. represents the ~
reduction during a cold working step. The columns AA(l) and AA(2) are expressed in the form T/t where T
is the temperature C of that step of heat treatment and t is the time in hours the material i9 held at that temperature.
The column mar~ed N. A. represents the natural ageing time. SHT/ANN is the solution heat treatment/annealing temperature and time expressed in the T/t format given for the artificial ageing step tAA(1) and AA(2)]. The remaining columns represent SUBSTITUTE SHEET
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the properties of yield strength, ultimate tensile strength, elongation, earing and dome reversal pressure respectively.
A number of sheet alloys were formed into cups for body making and the earing levels measured. The cups were then formed into bodies on a can body maker.
Each of the example results is from a successful can body free of holes or surface marking. The buckle resistance of selected cans was measured on a conventional buckle resistance testing machine.
From the results the alloys demonstrate a very high tensile strength with ductilities in excess of 4%. The earing levels of can bodies made from the alloy of the invention show earing levels between 0 -2.4~. These levels are on average 1% lower for a given condition than that of can bodies made from 3004 alloys.
., .
The dome reversal pressures for these cans made from alloys of the invention at the same thickness as cans made from 3004 are far in excess of 3004 values.
Dome reversal pressures for cans of 3004 alloy are typically about 9O p.s.i. maximum whereas the cans of the same thickness made from the invention alloys is between lOO and 115 p.s.i.
The graph of Figure 11 illustrates the effect ageing has on the tensile properties of alloys 2 and 3 SUBSTITUTE SHEET
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W092/03~86 PCT/AU91/00376 and Figure 12 shows a comparison between ~ensile properties for the invention alloys and that of 3004.
Figure 12 shows how the inven~ion alloys between lines A and B have tensile strengths about 20 - 40% higher than 3004 type alloys ~conventlonal can stock) with ductilities in excess of 4~ and are therefore superior in a number of properties.
A stronger can body material means that the wall thickness of a can body can be reduced whilst maintaining sændard 3004 rigidity and buckle resistant.
As discussed earlier for an alloy to be suitable as can end stock, minimum post bake strength and ductility properties are required.
An alloy with the composition of alloy 3 in Example 2 are subjected to the following processing steps.
1. Hot rolling to 3.0 mm.
2. Cold rolling from 3.0 to 0.8 mm.
3. Anneal at 345C for 1 hour.
4. The materlal was sectioned into 2 samples with one sample cold rolled to 0.43 - and the other to 0.355 mm.
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W092/03586 PCT/AU91/003~6 S. Both samples were sub;ected to a solution heat treatment at 500C for 1 hour before being water quenched.
6. 8Oth samples were then cold rolled to 0.315 mm representing a cold rolling reduction of 30% and ~;
10% respectively.
7. The samples were then sectioned to produce 8 samples and all samples were sub~ected to natural ageing for 24 hours.
8. The samples were sùb~ected to artificial ageing at 121C for 3 hours or 6 hours.
9. Half the samples were then baked at 205C for 20 minutes .
10. Tensile tests and cups were then ed for each sample and the results tabulated in Table 5.
Table 6 illustrates the % drop in strength and ductility properties as a result of a bake used by can end producers.
From the results of Example 3, it can be seen that a can end produced in accordance with the invention has post bake properties which exceed the minimum requirements of strength and ductility.
Present can end stock alloy AA5182 has a yield stress of 325 MPa, ultimate tensile stress of 370 MPa SuBsTlTuTE SHEET
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Wo92to3586 PCT/AU91/00376 and an elongation of 8%. It can be seen that post bak~ properties of can end stock in accordance with the alloy and process of the invention, has properties comparable with conventional can end stock.
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W092t03586 2 0 9 ~ 3 5 5 PCT/AU91/00376 Figure 13 basically illustrates the main adantages of the invention over conventional can xtock alloys. Cans with comparable strength mean lower cost of alloy from thinner material allowing less material to be consumed to make the same number of cans.
As demonstrated by the Examples, can body can be produced with strength, ductillty and anisotropic properties which far exceeds propertie~ obtainable from con~entional body stock alloys. As it is possible to also produce can end stock, using the alloy and produced in accordance with the invention, having the necessary properties to produce can ends, a two piece beverage container can be produced from the same alloy type with the same alloy composition.
~ he claims form part of the disclosure of this specification.
SuBsTlTuTE SHE~T
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TISLlS: a~W{I:2 IW aLI.OY SUITaBI~ FOR QN ~CING
~h~s invention relates to the use of aluminium based alloys for the manufacture of liquid containers and in particular to a high zinc content aluminium base alloy suitable for liquid container construction.
Conventional two-piece aluminium beverage containers are generally fabricated from two distinct alloys such as the Aluminium Association Specification 3004 and 5182 (See Table 1). 3004 alloy is generally used for body stock by deep drawing and wall ironing forming methods but lacks the necessary rigidity and strength properties to be a useful lid stock whereas 5182 alloy which ~s unsuitable for body stock has the properties desirable for can lid fabrication. Increased demand for this type of container and the need for stronger cans of thinner gauge materlal has spurred development of new alloys and in particular alloys which can be used for both body and lid stock.
To be suitable for can body stock an alloy must possess the required comb~nation of good formabil~ty and strength properties whilst also being economical to manufacture.
The AA3004 type alloy composition alloys are traditionally produced by casting the alloy using the 2~ direct chill casting method (DC-cast) into an ingot block of cross-section around 500 ~m thick x 700 mm , _~
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The hot rolling procedure red~ces the ingot thickness to a gauge ofiabout 2-3 mm by a series of breakdown passes.
The material is then usually annealed at temperatures of 300 - 400C for periods between O.S and 4 hrs to allow the metal to recrystallise. The annealed metal is then subjected to a cold rolling schedule to develop strength and other properties. This normally consists of 2 - 5 passes using 20 - 50% reductions to achieve a final gauge of about 0.3 - 0.33 , ,.
The final gauge sheet is then fabricated into alumini~m cans by use of a cupping machine and can body maker. Circular discs approximately 135 , diameter are cut or punched from the cold worked sheet on the cupping machine and drawn into shallow cups. The cup then enters the bodymaker and ig flrst redrawn into a cup close to that of its final diameter. The sidewalls are then reduced in thickness in one or more wall ironing operations to produce a can body around 65 diameter and 140 " high with a wall thickness of between 0.10 -0.18 mm.
The material from which the body is drawn has anisotropic properties (i.e. the properties d~ffer with direction) and so the top of the drawn body has a scalloped top, with approximately 4 peiaks oriented 90 apart the peaks of which are called ears. The degree of SUBSTITUTE SHEET
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where h. is the distance between the bottom of the cup and peak of the ears and ht is the distance between the bottom of the cup and valley of the ear.
For the body to be acceptable for further fabrlcation into a beverage container the formed body must have earing levels of no more than 3-5% and preferably less than 3%. The tops of the can bodies are trimmed off (fixed for a given process), during a slitting operation and the "eared" area is scrapped.
Another ma;or considerat~on of the quality of the finished body is its ability to form in the body maker without tearing and to have a s~ooth surface finish, free of drawing streaks and lines. Deep grooves caused by "galling" may appear on the finished can walls if the material is not of the correct microstructure.
Downgauging of conventional strain-hardened alloys to reduce the cost of body manufacture requires the use of increased alloying element concentrations (e.g.
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~owever, as these concentrations are increased, the formability of the resultant alloy decreases; in fact, SUBSTITUTE SHEET
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W092/03s86 2 0 913 5 ~ PCTtAU91/00376 the potential strength of the 3xxx series based alloys is ultimately limited by the amount of ralling strain which can be sustained during processing before surface finish and material properties deteriorate. Other aluminium alloy systems currently used for other applications are potentially capable of achieving much higher strength levels than 3xxx series alloy.
Although, ultimately, a container can be formed from a fabr~cated downgauged high strength 3004 type alloy of non-galling, low earing characteristics, unless the strength is great enough to offset the strength lost from reduced wall thickness the buckle resistance of the can will be reduced.
Buckle strength of resistance is determined by applying pressure with~n a drawn and wall ironed can and then gradually increasing the pressure until the bottom end of the can deforms and bulges out, ~.e. it buckles or the inverted dome reverses. The pressure at which the bottom buckles is then designated as the buckle strength or dome reversal pressure. To be acceptable as a can body a can formed from the alloy sheet must exhibit a buckle strength of at least 85 p.s.i. Cans drawn from high strength 3004 alloy produced using conventional direct chill (D.C.) cast methods exhibit a buckle strength of about 90 p.s.i.
Whilst the production of 3004 body stock by the ingot casting method is widely used, economic and energy SUBSTITUTE SHEET
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considerations would favour the manufacture of aluminium sheet by a continuous cast route. The prior art has addressed the continuous strip cast method where aluminium is cast into a thin alloy web about one inch thick~ She homogenisation process may be eliminated and the hot rolling reductions to intermediate gauge are minimised using this technique and the process of hot rolling can be eliminated entirely if the desired microstructure is achieved during continuous casting of very thin strip. The material is then annealed and processed in a manner similar to ingot cast materials. At this stage, can stock produced by this method has proven unsatisfactory for further processing and can body manufacture.
lS ~hus, it is an ob~ect of the present invent~on to provide an aluminium alloy suitable for can stock which has non-gall~ng, low earing and high strength characteristics with good formability at least comparable with existing AA3004 type alloys which will allow can bodies to be made from thinner sheet feed stock. It is also an object of the present invention to provide can stock which is also suitable for the manufacture of can lids thus, allowing manufacturing of a complete two-piece beverage can from one alloy 2~ composition. ~he alloy will be amenable to fabrication into can stock via both tbe direct chill cast and the continuous strip cast methods. Accordingly, the invention relates to a can stock and process for SlJBsTlTuTE SHEET
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; , . `~ - ~.................. . -.- . ; - . ' W092/03~ 913 ~ ~ PCT/AU9l/00-~76 producing a can stock from an aluminium alloy comprising 3.0 - 8.0 wt% zinc, 0.5 -3.0 wt% magnesium, less than 0.7 wt~ iron, 0:01 - 2:0 wt% silicon 0:05 -0.9 wt%
copper, 0.1 - 1.1 wt% manganese and 0.00.3 wt%
chromium. The incidental impurity level in the alloy is less than a total of 0.15 wt%.
In accordance with another aspect of the invention, the alloy is processed into feed for a can line by a process comprising, forming a melt of the alloy metal suitable for casting, casting the melt into a form suitable for rolling, performing an ~ntermediate rolling to an intermediate thickness, treating the alloy with heat, performing ~in~sh rolling by cold rolling within the range of 2 to 85%, temper heat treating the material to the desired ductility and strength.
The alloy preferably comprises constituents in ~ollowing weight percent ranges, zinc 4.0 - 6.5, magnesium 1.0 - 2.5, manganese 0.3 - 0.8, silicon 0.15 -O.3, iron up t~ 0.45, copper 0;10 - O.50, ~omium up to 0.20 total incidental impurities less than 0.1.
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' , - ' ,, , 2~913~5 W092/03~86 PCT/AU9t/00376 While an alloy containing zirconium up to a maximum level of 0.25 wt% may be suitable for can stock, to produce a can body with low earing, it ~s preferable that the zirconium level is less than 0.08 wt% and most S preferable that it i~ not added to the melt and its level is below tbh standard level of impurity for that element of 0.01 wt%.
It has been found that an alloy which falls within the above compos~tion range achieves high tensile and yield strength properties as well as good formability and "non-galling" wall ironing quality. Thus the alloy is preferably used to produce both the body and the lid of the beverage container.
She alloy is capable of producing a can body which has a dome reverYal strength in excess of 9O p.s.i. and a wall ironed thickness of less than 0.16 mm. A 3004 alloy is generally only capable of achieving such a dome reversal strength with a wall thickness equal to or greater than 0.16 mm.
The above alloy may suitably be cast by the direct chill casting method, continuous roll casting or continuous strip casting. However, if the alloy is to be produced using roll or strip casting the compositional range of the alloy can be broadened.
2S The amount of Zn, Mg, Mn, Fe and Si may be increased which results in higher volume fraction of SUBSTITUTE SHEET
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W O 92/03586 2 0 913 5 5 PC~r/A U91/00376 alpha phase particles a~ter casting and a greater amount of precipitation during final processing.
The alloy sheet may be produced by a combination of rolling reduction and heat treatmant in the final stages of manufacture. Consequently, fabrication steps vary with end use requirements. ~owever, during the performance of the heat treatment processes, it has been found that the alloy thus formed was especially adaptable to solution heat treatment of very short duration, while more lengthy heat treatments can be used to simultaneously anneal the sheet using recrystallisat~on anneal or recovery anneal techniques.
For container construction or for other requirements where strength and Sormability are important the ingot or strip cast material may be heat treated to homogenise the cast material and preferably hot rolled ar.d then cold rolled. ~he material is then solution heat treatet and given a cold rolling reduction. Lastly to improve strength and ductility, the alloy is aged to a temper dependent on the end use requirements.
Preferably the cast material, if ingot cast, is subjected to an additional heat treatment step to homogenise the alloy and preferably followed by a hot rolling step.
~he intermediate rolling preferably is a cold SUBSTITUTE SHEET
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W092/03586 PCT/AU9l/00376 ~ rolling stage and may employ a full anneal or recovery intermediate anneal during the cold rolling practice.
The step of treating the alloy with heat is preferably a solution heat treatment which may be followed by a natural ageing stage.
~he fin~sh rolling step is essential to the invent~on to provide the necessary strength properties to the final product but still must maintain sufficient ductility and formability properties to be a su$table can stock. The finish rolling is thus a cold rolling reduction in the range 2-85% and preferably within the range of 10-80% and most preferably within the range of 30-80%. The final temper heat treatment is preferably artific~al ageing. --In accordance with a further aspect of the invention there is provided a can line feed produced from the alloy of the invention which preferably has yield and tensile strength of in excess of 400 MPa and a total elongation of 4% or more.
The alloy of the invent~on may also be used to produce can endstock which in a tempered state must have a miniumum yield stress of 31Q MPa, a minimum ultimate tensile stress of 355 MPa and MIN 6% elongation.
The strengths and elongations specified above for can end stock relate to the post bake strength of the material.
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WO 9~/035X6 2 0 91~ 5 ~ PCltAU91/00376 Generally endstock i~ manufactured in coil form and is -~ent to tbe end makers who then coat tb~ material and bake the coated sheet at modest temperatures of between 155C and 210C for 10 - 30 minutes. Usually a specified test for the metal is 205C bake for 20 minutes. The can end maker then produces the can ends by conventional metal farming processes which are well known to those skilled ~n the art.
As can endstock made in accordance with the invention has strength and ductility properties in the "post baked" state in excess of the above miniumum values, suitable can ends can be produced from the alloy in accordance with the invention.
A further aspect of the lnvention is a two piece beverage container produced from the alloy of the invention. The container preferably ha~ a wall th~ckness of less than 0.12 , and a dome reverasal strength of greater than 90 p.s.i.
The foregoing and other features ob~ects and advantages of the present invention will become more apparent from tbe following description of the preferred embodiments and accompanying drawings.
Table 1 contains details of the invention alloy range and preferred range.
Figure 1 is a flow diagram showing the overall processing details for the alloys;
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W092/03586 2 0 913 5 5 PCT/AU9l/00376 Figure 2 is a Differential Scanning Calorimetry Thermal Analysis curve for the invention alloy; F~}se Flgure 3(a) is a flow diagram representing the final stage fabrication of the alloy;
Figure 3(b) illustrates the effect of the final cold rolling reduction, and F~gure 3(c) represents the effects of cold working and artificial ageing on the alloy of Example l;
Figure 4 shows micrographs of alloy 2 of Example 2 at ~arious stages of processing in which 4(a) is the microstructure after the material is hot rolled, 4(b) is the microstructure after. the mater~al has been annealed 4(~) is the microstructure after the final cold rolling reduction Figure 5 shows the effect of natural ageing on Alloys 1, 2 and 3 (Example 2).
Figures 6 - 8 are graphs representing the response of the alloys of Example 2 to time at a given temperature in the final ageing treatment.
Figure 9 represents the effects of natural ageing . and ~oldwor~ on the alloy;
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W O 92/03586 2 0 913 5 5 PC~r/A U9l/00376 Figure 10 represents the effect of using a double heat ~reatment in the art~ficial ageing step and the effect of coldwork;
Fl~ure 11 represents tensile results for the alloys of the invention;
Figure 12 represents strength and ductility characteristics for the alloys of the in~ention compared to those of conventional 3004 body stock; and Figure 13 represents an overview of the benefits of the alloys of the invention.
An alloy in accordance with the invent~on comprises the following basic alloying elements (wt%): copper (O.05 - O.9), mangane~e (O.1 - 1.1), magne~ium (O.5 -3.0), and a relatively high concentrat~on of zinc (3.0 -8.0). Furthermore, the following add~tives are included ~n the melt: chromium (0.0 -0.30), silicon (0.1 - 2.0) and iron (0.0 - 0.5).
It has been found that, after solution heat treatment the majority of the magnesium and zinc are suspended in solid solution and precipitate during the tempering heat treatment adding the required strength to the alloy.
It is essential to the invention that the silicon, manganese and iron add~tives be within the ranges specified above as these elements are required to form SUBSTITUTE SHEET
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W092/03~86 PCT/AU91/00376 the desired dispersed second phase distribution (alpha phase) in the alloy which is critical for the production of a non-galling wall ironed can.
Zirconium and chromium are typically found in the melt at impurity levels of less than O.Cl wt%, but if already present or added to the melt for additional strength properties, it is preferable that they are present at levels less than 0.08 wt% and less than 0.05 wt% respectively.
~he effect of the very low levals of grain refining elements chromium and preferably zirconium, is that full recrystallisation of the product after, for example, hot rolling or low temperature annealing (345C for 0.5 - 2 hours) can take place.
~f the zirconium and chromium levels in the alloy exceed the specified levels in the present invention, then the wrought structure created by hot and cold rolling will be retained during solution heat treatment or anneal and the properties of the final gauge sheet will be more anisotropic. This is particularly disadvantageous if the sheet material is to go through deep drawing operations as the anisotropic properties result in material of high earing which is undesirable for the can body making process. High strengths can be obtained by increasing the concentration of these i ele~ents but formability and earing suffer as a result.
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Wos2/03~86 PCT/AU91/00376 The yield strength and tensile strength of the 10 alloy in accordance with the invention is far greater than that of a 3xxx series can body material. The 3004 alloy has yield and tensile strengths of around 285 and 330 MPa respect~vely with 4S elongation whereas the alloy of the invention exhibits yield and tensile strengths around 420 and 480 MPa respectively with a total elongation measured on a 50 mm gauge length of 4%
or more. When such a sheet is drawn and wall ironed into a body for a two-piece beverage container it possesses can buckle strengths in excess of 100 p.s.i.
with a wall thickness of 0.12mm. The véry high strength and improved duct~lity of this alloy over any type of 3004 or modified 3xxx series alloy allows the gauge of sheet used for the initial forming operatlon (can line feed) to be reduced by at least 10% while still retaining buckle strength and formability in the finished body.
The high strength of this alloy also allows it to be made into lid stock for cans. Alloy AA5182 which is currently used for beverage can lids has a tensile strength of 395 MPa and an elongation of 4%. The 3004 alloy is generally not used to produce lid stock as it does not have sufficient strength for the desired lid thickness. The invention alloy can match the properties of AA518Z, and thus a two-piece can may be made from one alloy composition instead of the conventional two.
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W092/03S86 PCT/AU9l/00376 When the alloy is cast by the DC-casting method to produce can bodies it i3 first homogenised. The cast is preferably homogenised as a block between 480- and 500oc for a period of 5 to 10 hours. ~he material is then hot rolled preferably from a temperature of up to 500C down to a thickness ~uitable for coiling (preferably less than 5 ). It is preferable that the hot rolling coil finishing temperature is above about 300C as the alloy will automatically anneal during the coiling operation.
The material is then cold rolled and preferably employs a full anneal or recovery intermediate anneal during the cold rolling practice. After this rolling stage the strip preferably has a thickness of between 0.8 and 0.4 mm. ~hese thicknèsses are required as a rolling reduction must be effected dur~ng the final processing to can sheet gauge to provide the necessary sheet flatness and final gauge strength. Next a solution heat treatment at temperatures preferably between 480C and 595C for duration times between 5 seconds and 1 hr is followed by a water quench to ambient temperature.
A solution heat treatment for duration times toward the upper end of the range will also anneal the material if it has been cold rolled prior to the solution heat treatment. Nevertheless, the composition of the alloy allows the material to be heat treated for much shorter times than would normally be performed in processing SuBsTlTuTE SHEET
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The alloy strip may then be allowed to naturally age at room temperature preferably for a period of zero to 48 hours prior to cold rolling of the strip.
To provide the necessary strength properties in the metal, lt is necessary that the finish rolling step, has a cold rolling reduction within the range 2 to 85 percent, the reduction preferably being lO and 80% and most preferably 30 and 70%. It has been found that even with a cold rolling reduction towards the upper limits of this range, the necessary ductility and formability properties for a viable can stock are present.
Finally the sheet material is aged to a temper between the underaged and over-aged states. The ageing w~ll depend on the equipment used and the can manufacturer's strength and ductility specifications and is preferably within the range 120 to 26-C for a time of between l minute and 4 hours.
Solution heat treatment of the material prior to the final processing recrystallises the material and reduces the anisotropic properties created by the cold rolling schedule. This means that when given a final rolling reduction a~d fully aged to the desired temper, a deep drawing material is created which has very low anisotropic properties and very low earing levels. A
cup formed from final gauge 3004 or ~odified alloy SUBSTITUTE SHEET
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W092/03SX6 2 0 913 5 ~ PCT/AU91/00376 typically has an earing level of 3%, whereas a cup formed from an alloy of the present invention has earing levels of less than 2%.
An alternative to the direct chlll cast method is that the alloy can be strip cast in a conventional strip caster and solidified into a web approximately an inch or less in thickness. The molten alloy feedstock for this, may be richer in composition than that used in the DC cast alloy but would be of the preferred invention alloy range (see Table 1). It is then preferred that the strip is given a hot or cold rolling reduction in sheet thickness of at least 25% and more preferable 50 to 85%.
The alloy composition o the present invention and processing techn~que allows llquid container bodies to be made from thinner gauge sheet stock and achieve cost reductions. Furthermore, one alloy can be used for body end stock and easy-open tab stock by varying the processing steps of the alloy. The use of a single alloy type for all of the component parts of liquid container results in production costs benefits and improvements in scrap recycling efficiency.
The alloy of the invention is now demonstrated in the following Examples.
An alloy with the following composition (wt%) was direct chill cast to an ingot size of 50 cm x 120 cm SUBSTITUTE SHEET
~" :'.'' . ', ' ' ' ' "' ', ' ' . ' ' . ' ' ' , , W092/0358~ PCT~AU9l/00376 zn Mg FE Si Cu Nn CrAl 4.83 1.53 0.35 0.16 0.019 0.47 0.01 balance The ingot was subjected to the following schedule to produce a coil of the sheet.
- homogenise 5 hrs 4800 - 595C
- hot roll to 3.175 " .
coil exit gauge temperature 295 - 315C
- standard edge trim applied - anneal 370C - 373 for 3 hours - cold roll 60% reduction to 1.22 - solut~on heat treatment at 1.22 flash solutionise at 585C for 10 seconds - cold roll~ng reductions 40% to 0.73 ., 37% to 0.454 - 35% to 0.303 mm - level and solvent wash - artificial ageing to T87 temper - age at 160C for 1 hr.
In the schedule, the coil, once heat treated, was rolled in back-to-back passes to final gauge with a SuBsTlTuTE SHEET
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maximum delay of 48 hours before commencing to roll.
Levelling was performed within 5 days of cold rolling to avoid eccessive natural ageing as the material age harden~ after cold rolling.
An average of 50 samples tested gave yield strength = 393 MPa ultimate tensile strength = 406 MPa elongation 4%
ductility = 4.34 mm Can bodies produced from the samples showed a dome reversal of 105 p.s.i. from 0.30 mm dome wall thickness.
Figure 3(b) illustrates the effect of the final cold rolling reduction on the strength and ductility of the alloy and F~gure 3(c) demonstrates the effect of artificial ageing time on strength and ductility of the above alloy after solution heat treatment (S.H.T.) and 70% cold rolling reduction. The ageing temperature is 250F (121C).
Three alloys iA accordance with the invention of compositions shown in Table 1 were direct chill cast into ingots 100 x 300 mm in cross-section of 1.2 m length. The ingots were then scalped into blocks 190 wide and 100 mm thick and lengths of 200 mm. Each of the ingots were then heomogenised at temperature between 500C and 585~C. A higher bomogenisation temperature was SUBSTITUTE SHEET
wo 92/o3s86 2 ~ 9 i3 S ~ - 20 - PCT/AV91/00376 used for the alloys of highest solute content to allow for more complete homogenisation. The thermal analysis curve of the precipitation reaction in the alloy during ~eomogenisation is shown in Figure 2. The following S letters represent the positions in Figure 2, where changes in the various phases occur. As is the dlssolution of GP zones; B is the precipitation of (MgZn2) phase, C, the disæolution of ~ ~ ~ phase: D, the precipitation of T phase, E, the dissolution of T
phase; and F the localized GB liquidation.
Homogenisation and hot rolling schedules for each of the sample alloys are shown in Table 2.
To hot roll the alloys the scalped blocks were cooled to a rolling temperature of between 500 and 485C
~n the ~urnace. The blocks were then removed from the furnace and ind~vidually rolled from a gauge of 100 mm to a finished gauge of approximately 2 - 3 . The microstructure of the hot rolled material is shown in Figure 4a.
~he finishing temperature of hot rolling was often above 200-C which was sufficient to allow some recovery of the rolled structure prior to cold rolllng to the solution heat treatment gauge. ~owever, in the case of some of the alloy 3 samples, the material was given a recrystallisation anneal at a temperature of 345C for 3 hours. This allowed the material to fully recover and recrystallise. The fully recrystallised grain size of SuBsTlTuTE SHEET
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W092/03586 2 ~ 9 ~ 3 5 S PCT/AU91/00376 the alloy had an average diameter of l9m (ASTM 8.S) (Flgure 4b).
In this softened condit~on the alloys were cold rolled to a number of different gauges as shown in Table 4. This was to allow for a number of different final cold rolling reductions to be made to the given final gauge material for body stock forming. A schematic of the Sinal material processing is included in Flgure 3a. `
Figure 4(c) shows the microstructure of alloy 2 in Example 2 after the final cold rolling reduction and as can be seen from the micrograph the material has an ;r alpha phase (a - Al(Fe,Mn)S~) totally dispersed within the matrix. This microstructure results in a wall ironed can body with excellent non-galling properties.
Solution heat treatment of the plate was conducted at a temperature of 500C to put elements into solution in preparation for the final ageing procedures. A study of the natural ageing behaviour of the three alloys after solution heat treatment of 2 hours at 500C is shown in Figure 5. The material was cold water quenched and then given a number of heat treat~ents. Ageing studies and hardness measurements were used to charactise the response of the alloys to various treatments. Tensie studies were then made o~ sheet in certain conditions to establish the yield strengths and elongations of the specific alloy treatments.
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w092/03586 PCT/AU91/00376 Final ageing treatment studies are show in Figures 6 - 8.
Figures 6(a), 6(~) and 6(c) show the respon~e of the alloys to ageing at 155C aSter a first ageing stage at 121C Sor 1, 2 and 3 hours respectively.
Figures 7(a), 7(~) and 7(c) represents the ageing response of the alloys at 111C with a preced~ng natural ageing stage of 0, 24 and 48 hours respectively.
Figures 8(a), 8(b) and 8(c) represent the ageing response of the alloys at 131C with a preceding natural ageing stage of 0, 24 and 48 hours respectively.
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HIGH STRENGTH CAN STOCK ¦ :
ALLOY COMPOSITION I I
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, CHEMICAL COMPOSITION (wt%) = A1 Zn Mg Mn Si Fe Cu Cr ¦
Alloy 1 Bal 3 8 1.1 0.460.2 0.3 0.12 ~.007 Alloy 2 Bal 4.6 1.3 0.42 0.2 0.4 0.10<.008 ¦
L Alloy 3 eal 6.0 1 8 0.560.2 0.350.10 OO
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¦ Alloy 1 500 500 100 2.5 ¦ Alloy 2 565 490 100 2.7 ¦ Alloy 3 585 480 100 2.8 .
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~9135~ -WO 92~03~86 PCI`/AU91/00376 -Gauge ShVAnn N.A. C.W. M11~ (2) YS urs EL Eanng Dùme Rev ID. Imm1 (C/hO Ihn) (%) ~hnl lhn) IMPa) lMpa) 1%~ l%) IPs8 ~1 0.320 500/1 48 lO 121/3 ~5513 - - - 0.0 62 ~1 0.320 500/t 48 lO ~21/3 15513 - - - 0.2 a1 ~1 0.320 500/1 48 10 121/3 ~55/3 - - - 0.1 ~1 0.320 500/1 48 10 121/3 ~55/3 - - - 0.2 a4 ~1 0.320 500/1 48 30 121t3 155/3 - - - 0.0 84 ~1 0.320 50011 48 30 121/3 15513 - - - 0.0 a8 ~1 0.320 soal1 48 30 121~3 155/3 - - - QS 90A1 0.320 500/1 4a 30 121/3 155/3 - - - 0.1 -~1 0.342 500/1 48 60 121/3 15513 318 335 3.1 0.9 A1 0.321 500/1 U 60 12113 155/3 304 324 5.1 1.7 ~106 ~1 0.320 500/1 48 60 121/3 155/3 - - - 1.9 A1 0.328 500/1 48 60 121/1 155/4 315 339 2.8 æ1 184 Al Q320 500/1 48 60 121/3 - - - - 2.6 9B
A1 0.329 500/1 4B 10 121/6 - 181 æ8 9.6 Q2 80 ~1 0.328 500/1 48 60 121/6 - 316 343 4.2 2.0 ~1 0.305 500t1 4a 60 121/24 - 332 351 5.1 1.9 A1 0.311 500/1 48 60 121124 - 324 349 4.8 2.2 A2 0.320 500/1 4B 60 121/3 - - - - 2.0 A2 0.326 500/1 U 60 121/6 - 372 391 4.9 1.8 ,108 A2 0.320 500/1 U 10 121/6 - - - - 1.9 - ;
A2 0.307 500/1 48 30 121/6 - 353 390 7.3 1.7 104 A2 0.296 500/1 48 30 121/24 - 383 483 6.3 1.3 A2 0.322 500t1 48 60 121/24 - 369 392 3.5 1.5 ~108 A2 0.325 500t1 48 60 121/24 - 375 395 4.6 1.9 ~110 A2 Q320 500/1 48 10 121t3 115/3 - - - 0.4 102A2 0.320 500t1 48 30 121/3 155/3 - - ~ 15 A2 0.320 50a~1 U 30 121/3 15513 - - - 2.0 >108 A2 0.320 500t1 48 30 121/3 155/3 - - - 2.4 >108 ~2 0320 500/1 48 30 121/3 155/3 - - - 1.5 ~112 A2 0 323 500/1 48 60 121/3 15513 373 395 3.9 2.1 ,109 -A2 0.320 500t1 48 80 121/3 155/3 - - - æo A2 0.326 500/1 48 60 121/3 15513 374 393 6 1.8 10B
A2 0.320 500/1 48 60 121/1 155/4 - - - - 1.5 ~3 0.325 500t1 48 60 121/24 - 400 501 3.2 2.2 ~3 0.3~,1 500t1 48 60 121/24 - 473 478 4.3 ~3 0.330 500t1 48 30 121/24 - 418 435 53 0.8 ~3 0.295 500/1 U 10 121/6 - 423 464 8 1.1 A3 0.315 500/1 48 30 121/6 - 439 471 7 1 1 A3 0.327 500t1 U 60 121/B - 263 492 3 A3 0.315 500/1 4B 10 121/3 155/3 386 473 10 0.6 ~3 0.326 500/1 48 30 121/3 155/3 424 4U 4.5 0.9 A3 0.331 500/1 48 30 121/3 15513 417 451 5.6 Q9 A3 0.348 500/1 48 60 121/3 155/3 467 468 1.2 2.0 A3 0.328 500/1 48 60 121/3 155/3 441 454 2.5 1.9 ~3 0.326 500/1 48 60 121/1 155/4 448 475 5 SUBSTITUTE SHEET
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W092/035~ 0 913 ~ ~ PCTtAU91/00376 Figure 9 demonstrates the effect of cold rolling -alloy 2:
Figures lO(a) and lO(b) demonstrate the effects of secondary artificial ageing on material of alloy 2 with prior cold word (cw) treatment from 0-60%. The alloy of Figure lO(a) has undergone a solution heat treatment of 500C for 2 hours, 0 hours natural ageing, cold working and united artificial ageing at 1210C
for 3 hours. In Figure lO(c), the alloy has undergone solution heat treatment at 500C for 2 hours, 48 hours of natural ageing, cold working and an initial artificial ageing at 121C for 3 hours.
Table 4 demonstrates the response of alloys 1,2 and 3 of Example 2 to varying effects of cold working and artif~cial ageing.
The column marked C .W. represents the ~
reduction during a cold working step. The columns AA(l) and AA(2) are expressed in the form T/t where T
is the temperature C of that step of heat treatment and t is the time in hours the material i9 held at that temperature.
The column mar~ed N. A. represents the natural ageing time. SHT/ANN is the solution heat treatment/annealing temperature and time expressed in the T/t format given for the artificial ageing step tAA(1) and AA(2)]. The remaining columns represent SUBSTITUTE SHEET
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the properties of yield strength, ultimate tensile strength, elongation, earing and dome reversal pressure respectively.
A number of sheet alloys were formed into cups for body making and the earing levels measured. The cups were then formed into bodies on a can body maker.
Each of the example results is from a successful can body free of holes or surface marking. The buckle resistance of selected cans was measured on a conventional buckle resistance testing machine.
From the results the alloys demonstrate a very high tensile strength with ductilities in excess of 4%. The earing levels of can bodies made from the alloy of the invention show earing levels between 0 -2.4~. These levels are on average 1% lower for a given condition than that of can bodies made from 3004 alloys.
., .
The dome reversal pressures for these cans made from alloys of the invention at the same thickness as cans made from 3004 are far in excess of 3004 values.
Dome reversal pressures for cans of 3004 alloy are typically about 9O p.s.i. maximum whereas the cans of the same thickness made from the invention alloys is between lOO and 115 p.s.i.
The graph of Figure 11 illustrates the effect ageing has on the tensile properties of alloys 2 and 3 SUBSTITUTE SHEET
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W092/03~86 PCT/AU91/00376 and Figure 12 shows a comparison between ~ensile properties for the invention alloys and that of 3004.
Figure 12 shows how the inven~ion alloys between lines A and B have tensile strengths about 20 - 40% higher than 3004 type alloys ~conventlonal can stock) with ductilities in excess of 4~ and are therefore superior in a number of properties.
A stronger can body material means that the wall thickness of a can body can be reduced whilst maintaining sændard 3004 rigidity and buckle resistant.
As discussed earlier for an alloy to be suitable as can end stock, minimum post bake strength and ductility properties are required.
An alloy with the composition of alloy 3 in Example 2 are subjected to the following processing steps.
1. Hot rolling to 3.0 mm.
2. Cold rolling from 3.0 to 0.8 mm.
3. Anneal at 345C for 1 hour.
4. The materlal was sectioned into 2 samples with one sample cold rolled to 0.43 - and the other to 0.355 mm.
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W092/03586 PCT/AU91/003~6 S. Both samples were sub;ected to a solution heat treatment at 500C for 1 hour before being water quenched.
6. 8Oth samples were then cold rolled to 0.315 mm representing a cold rolling reduction of 30% and ~;
10% respectively.
7. The samples were then sectioned to produce 8 samples and all samples were sub~ected to natural ageing for 24 hours.
8. The samples were sùb~ected to artificial ageing at 121C for 3 hours or 6 hours.
9. Half the samples were then baked at 205C for 20 minutes .
10. Tensile tests and cups were then ed for each sample and the results tabulated in Table 5.
Table 6 illustrates the % drop in strength and ductility properties as a result of a bake used by can end producers.
From the results of Example 3, it can be seen that a can end produced in accordance with the invention has post bake properties which exceed the minimum requirements of strength and ductility.
Present can end stock alloy AA5182 has a yield stress of 325 MPa, ultimate tensile stress of 370 MPa SuBsTlTuTE SHEET
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W092t03586 2 0 9 ~ 3 5 5 PCT/AU91/00376 Figure 13 basically illustrates the main adantages of the invention over conventional can xtock alloys. Cans with comparable strength mean lower cost of alloy from thinner material allowing less material to be consumed to make the same number of cans.
As demonstrated by the Examples, can body can be produced with strength, ductillty and anisotropic properties which far exceeds propertie~ obtainable from con~entional body stock alloys. As it is possible to also produce can end stock, using the alloy and produced in accordance with the invention, having the necessary properties to produce can ends, a two piece beverage container can be produced from the same alloy type with the same alloy composition.
~ he claims form part of the disclosure of this specification.
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Claims (29)
1. A process for producing an aluminium can stock from aluminium alloy comprising 3.0 to 8.0 wt%
zinc, 0.5 - 3.0 wt% magnesium, less than 0.7 wt% iron, 0.01 - 2.0 wt% silicon, 0.05 - 0.9 wt% copper, 0.1 -1.1 wt% manganese, less then 0.3 wt% chromium and incidental impurities less than a total of 0.15 wt%, said process comprising the steps of forming melt of tbe alloy metal suitable for casting, casting the melt into a form suitable for rolling, performing an intermediate rolling to an intermediate thickness, treating the alloy material with heat, performing finish rolling by a cold rolling reduction within the range of 2 to 85% and temper heat treating the material to the desired ductility and strength properties.
zinc, 0.5 - 3.0 wt% magnesium, less than 0.7 wt% iron, 0.01 - 2.0 wt% silicon, 0.05 - 0.9 wt% copper, 0.1 -1.1 wt% manganese, less then 0.3 wt% chromium and incidental impurities less than a total of 0.15 wt%, said process comprising the steps of forming melt of tbe alloy metal suitable for casting, casting the melt into a form suitable for rolling, performing an intermediate rolling to an intermediate thickness, treating the alloy material with heat, performing finish rolling by a cold rolling reduction within the range of 2 to 85% and temper heat treating the material to the desired ductility and strength properties.
2. The process in accordance with claim 1 wherein the aluminium alloy has a zirconium level of less than 0.01 wt%.
3. The process in accordance with claim 1 or claim 2 whereby the alloy material has a metal matrix which has an alpha phase dispersed therethrough.
4. The process in accordance with claim 1 or claim 2 wherein the finish rolling step is a cold rolling reduction of between 10 - 80%.
5. The process in accordance with claim 1 or claim 2 wherein the finish rolling step is a cold rolling reduction of 30 - 70%.
6. The process in accordance with claim 1 or claim 2 wherein zinc is present in tbe range of 4 -6.5 wt%, magnesium 1.0 - 2.5 wt% manganese, 0.3 - 0.8 wt% silicon 0.15 - 0.3 wt%, iron up to 0.45 wt%, copper 0.10 - 0.50 wt% and chromium up to 0.05 wt%.
7. The process in accordance with claim 1 wherein a heat treatment step follows the casting step to homogenise the material.
8. The process in accordance with claim 5 wherein a hot rolling step follows the heat treatment step and precedes the intermediate rolling step.
9. The process in accordance with claim 8 wherein after the hot rolling step the material is hot coiled at a sufficiently high temperature to allow the coiled material to anneal while in the coiled state.
10. The process in accordance with any one of claims 1 - 8 wherein the intermediate rolling step is a cold rolling stage.
11. The process in accordance with claim 7 wherein the intermediate rolling step includes a full anneal or recovery intermediate anneal during the cold rolling stage.
12. The process in accordance with claim 1 where the step of treating the alloy with heat is a solution heat treatment.
13. An aluminium can stock produced from an alloy having 3.0 - 8.0 wt% zinc, 0.5 - 3.0 wt%
magnesium less then 0.7 wt% iron, 0.01 - 2.0 wt%
silicon, 0.05 - 0.9 wt% copper, 0.1 - 1.1 wt%
manganese, less then 0.3 wt% chromium and incidental impurities less then a total of 0.15 wt%.
magnesium less then 0.7 wt% iron, 0.01 - 2.0 wt%
silicon, 0.05 - 0.9 wt% copper, 0.1 - 1.1 wt%
manganese, less then 0.3 wt% chromium and incidental impurities less then a total of 0.15 wt%.
14. An aluminium can stock in accordance with claim 13 wherein the zinc composition is in the range of 4 - 6.5 wt%.
15. An aluminium can stock in accordance with claim 13 wherein the magnesium composition is in the range of 1.0 - 2.5 wt%.
16. An aluminum can stock in accordance with claim 13 wherein the manganese composition is in the range of 0.3 - 0.8 wt%.
17. An aluminium can stock in accordance with claim 13 wherein the silicon content is in the range of 0.15 - 0.3 wt%.
18. An aluminium can stock in accordance with claim 13 wherein iron content is less than 0.45 wt%.
19. An aluminum can stock in accordance with claim 13 wherein copper is in the range of 0.10 - 0.50 wt%
20. An aluminium can stock in accordance with claim 13 wherein chromium is in the range of less than 0.05 wt%.
21. An aluminium can stock in accordance with claim 13 wherein zirconium is present in an amount less than 0.01 wt% and zirconium is the range of less than 0.08 wt%.
22. The aluminium can stock in accordance with claim 13 wherein zinc is present in the range 4 - 6.5 wt%, magnesium 1.0 - 2.5 wt%, manganese 0.3 - 0.8 wt%, silicon 0.15 - 0.30 wt%, iron less than 0.45 wt%, copper 0.10 - 0.50 wt%, chromium less than 0.05 wt%
and zirconium less than 0.01 wt%.
and zirconium less than 0.01 wt%.
23. An aluminium can stock in accordance with any one of claims 13 - 21 wherein the alloy material is formed in a melt and cast into a form suitable for rolling, the material then undergoes intermediate rolling to an intermediate thickness before being treated with heat, a finish rolling is then performed on the material by a cold rolling reduction within the range of 2 to 85% and then the material is temper heat treated to the desired ductility and strength.
24. The aluminum can stock in accordance with claim 23 wherein the finish rolling reduction is in the range of 10 to 80%.
25. The aluminium can stock in accordance with claim 23 wherein the finish rolling reduction is in the range of 30 to 70%.
26. A two piece beverage container comprising a body portion and an end portion, said body portion and said end portion being produced from the can stock in accordance with any one of claims 23 - 25.
27. A two piece beverage container, comprising a body portion and an end portion wherein the can stock for both said body portion and said portion wherein the can stock for both said body portion and said end portion is produced by the process in accordance with any one of claims 1 to 12.
28. A two piece beverage container in accordance with claim 26 wherein said container has a dome reversal of above about 100 psi.
29. A can body produced by deep drawing the can stock of any one of the claims 23 - 25 having an average earing level of less than 2%.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| AUPK189490 | 1990-08-22 | ||
| AUPK1894 | 1990-08-22 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CA2091355A1 true CA2091355A1 (en) | 1992-02-23 |
Family
ID=3774908
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA002091355A Abandoned CA2091355A1 (en) | 1990-08-22 | 1991-08-21 | Aluminium alloy suitable for can making |
Country Status (7)
| Country | Link |
|---|---|
| EP (1) | EP0544758A1 (en) |
| JP (1) | JPH06503854A (en) |
| CN (1) | CN1060115A (en) |
| BR (1) | BR9106787A (en) |
| CA (1) | CA2091355A1 (en) |
| WO (1) | WO1992003586A1 (en) |
| ZA (1) | ZA916651B (en) |
Families Citing this family (23)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6045632A (en) * | 1995-10-02 | 2000-04-04 | Alcoa, Inc. | Method for making can end and tab stock |
| AU4699497A (en) * | 1996-10-25 | 1998-05-22 | Lars Frederiksen | A method of working hard aluminium of standard type (us) aa 7075 t6 |
| CA2352333C (en) | 1998-12-18 | 2004-08-17 | Corus Aluminium Walzprodukte Gmbh | Method for the manufacturing of an aluminium-magnesium-lithium alloy product |
| IL156386A0 (en) * | 2000-12-21 | 2004-01-04 | Alcoa Inc | Aluminum alloy products and artificial aging method |
| FR2846669B1 (en) * | 2002-11-06 | 2005-07-22 | Pechiney Rhenalu | PROCESS FOR THE SIMPLIFIED MANUFACTURE OF LAMINATED PRODUCTS OF A1-Zn-Mg ALLOYS AND PRODUCTS OBTAINED THEREBY |
| WO2004090185A1 (en) | 2003-04-10 | 2004-10-21 | Corus Aluminium Walzprodukte Gmbh | An al-zn-mg-cu alloy |
| US20050238528A1 (en) * | 2004-04-22 | 2005-10-27 | Lin Jen C | Heat treatable Al-Zn-Mg-Cu alloy for aerospace and automotive castings |
| US8002913B2 (en) * | 2006-07-07 | 2011-08-23 | Aleris Aluminum Koblenz Gmbh | AA7000-series aluminum alloy products and a method of manufacturing thereof |
| MX2013002636A (en) | 2010-09-08 | 2013-05-09 | Alcoa Inc | Improved aluminum-lithium alloys, and methods for producing the same. |
| WO2013172910A2 (en) | 2012-03-07 | 2013-11-21 | Alcoa Inc. | Improved 2xxx aluminum alloys, and methods for producing the same |
| KR20150038678A (en) * | 2012-09-20 | 2015-04-08 | 가부시키가이샤 고베 세이코쇼 | Aluminum alloy plate for automobile part |
| CN102994829A (en) * | 2012-09-29 | 2013-03-27 | 吴雅萍 | High-strength aluminium alloy |
| JP5848694B2 (en) * | 2012-12-27 | 2016-01-27 | 株式会社神戸製鋼所 | Aluminum alloy plate for DI can body |
| US9587298B2 (en) | 2013-02-19 | 2017-03-07 | Arconic Inc. | Heat treatable aluminum alloys having magnesium and zinc and methods for producing the same |
| JP5710675B2 (en) * | 2013-03-29 | 2015-04-30 | 株式会社神戸製鋼所 | Aluminum alloy plate for packaging container and method for producing the same |
| CN103567704A (en) * | 2013-10-28 | 2014-02-12 | 任静儿 | Manufacturing method for aluminum alloy composite material for cooler used for air conditioner |
| JP6657116B2 (en) * | 2014-04-30 | 2020-03-04 | アルコア ユーエスエイ コーポレイション | Method for producing aluminum container from aluminum sheet with improved formability |
| WO2016192040A1 (en) * | 2015-06-02 | 2016-12-08 | GM Global Technology Operations LLC | Aluminum alloy for forming an axisymmetric article |
| TWI601836B (en) * | 2016-06-02 | 2017-10-11 | 中國鋼鐵股份有限公司 | Method for manufacturing aluminum sheet |
| CN106544560B (en) * | 2016-10-31 | 2018-06-05 | 宁波市佳利来机械制造有限公司 | A kind of automobile air conditioner compressor housing |
| US11932928B2 (en) | 2018-05-15 | 2024-03-19 | Novelis Inc. | High strength 6xxx and 7xxx aluminum alloys and methods of making the same |
| CA3151478C (en) * | 2019-10-02 | 2024-05-28 | Novelis Inc. | Aluminum flat rolled products with high recycled content for light gauge packaging solutions and related methods |
| JP2021188102A (en) * | 2020-06-02 | 2021-12-13 | 国立大学法人九州大学 | Aluminum alloy material and hydrogen embrittlement inhibitor for aluminum alloy material |
Family Cites Families (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3187428A (en) * | 1960-10-19 | 1965-06-08 | Reynolds Metals Co | Method of treating aluminum and aluminum alloys preparatory to bright finishing |
| CH480883A (en) * | 1964-08-27 | 1969-11-15 | Alusuisse | Process for the production of hardenable strips and sheets from hardenable aluminum alloys with copper contents below 1% |
| DE1483324C2 (en) * | 1965-12-02 | 1975-04-24 | Vereinigte Aluminium-Werke Ag, 5300 Bonn | Use of AIZnMg alloys with low notch sensitivity |
| GB1186161A (en) * | 1966-04-07 | 1970-04-02 | High Duty Alloys Ltd | Improvements in or relating to the Heat Treatment of Aluminium Alloys |
| FR1543955A (en) * | 1967-05-19 | 1968-10-31 | Cegedur | Aluminum alloy road crash barriers |
-
1991
- 1991-08-21 CA CA002091355A patent/CA2091355A1/en not_active Abandoned
- 1991-08-21 WO PCT/AU1991/000376 patent/WO1992003586A1/en not_active Application Discontinuation
- 1991-08-21 EP EP91915278A patent/EP0544758A1/en not_active Withdrawn
- 1991-08-21 JP JP3513794A patent/JPH06503854A/en active Pending
- 1991-08-21 BR BR919106787A patent/BR9106787A/en unknown
- 1991-08-22 CN CN91108893A patent/CN1060115A/en active Pending
- 1991-08-22 ZA ZA916651A patent/ZA916651B/en unknown
Also Published As
| Publication number | Publication date |
|---|---|
| CN1060115A (en) | 1992-04-08 |
| JPH06503854A (en) | 1994-04-28 |
| BR9106787A (en) | 1993-06-29 |
| ZA916651B (en) | 1992-07-29 |
| WO1992003586A1 (en) | 1992-03-05 |
| EP0544758A1 (en) | 1993-06-09 |
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