EP0099739B1

EP0099739B1 - Aluminum alloy and process for manufacture

Info

Publication number: EP0099739B1
Application number: EP19830304131
Authority: EP
Inventors: Harish D. Merchant; James G. Morris; Edgar Dr. Lossack; Gunther Dr. Scharf
Original assignee: Vereinigte Aluminium Werke AG; Continental Can Company USA Inc
Current assignee: Crown Beverage Packaging LLC
Priority date: 1982-07-15
Filing date: 1983-07-15
Publication date: 1988-12-07
Also published as: EP0099739A3; NO832560L; AU1687583A; DK324383D0; NO165349B; ES8501003A1; AR231408A1; ES524111A0; GB2172303A; NO165349C; GB2172303B; EP0099739A2; BR8303778A; GB2123319B; PT77030A; GB8319199D0; AU557719B2; DE3378640D1; PT77030B; DK324383A

Description

The present invention is directed to a process for making aluminium alloy strip stock and in particular to a process for preparing continuous strip cast aluminium alloy suitable for use in the manufacture of deep drawn and wall-ironed articles such as cans and the like.
In recent years, aluminium alloys such as the Aluminium Association Specification 3004 have been successfully fabricated into two piece beverage cans by deep drawing and ironing. The expanding use of two piece aluminium cans has created a need for aluminium alloy sheet for forming the can body that not only possesses the required combination of formability and strength properties but is also economical to manufacture.
Typically the aluminium alloy sheet useful in the production of deep drawn and ironed beverage cans is cast by direct chill casting an ingot having a thickness of 50.8-63.5 cm (20-25 inches). The ingot is homogenized at 510-607°C (950-1125°F) for 4-24 hours and then subjected to hot rolling wherein the ingot is passed through a series of breakdown rolls maintained at a temperature of 204-482°C (400-900°F) to reduce the ingot in thickness to a reroll gauge of about 0.033 cm (0.0130 inch).
Thereafter, the reroll stock is subjected to an annealing step wherein the stock is heated at 316-482°C (600-900°F) for 0.5―3 hours to effect recrystallization of the metal structure. The annealed reroll stock is subjected to a final work hardening step wherein the reroll stock is cold rolled (room temperature rolling) to a final gauge of about 0.033 cm (0.013 inch) or about 90% of its original thickness to produce the substantially full hard (H19) temper required for two-piece can body stock.
In spite of the successful use in can-making of direct chill ingot cast aluminium alloy, economic and energy considerations would favour the manufacture of the aluminium sheet by continuous strip casting. In this process the molten aluminium is cast and solidified into a thin web of 2.54 cm (one inch) or less in thickness so that subsequent rolling is reduced to a minimum and the costly step of hot rolling is eliminated.
In the manufacture of continuous strip cast aluminium alloy for can manufacture, the thin, e.g. 0.51-2.54 cm (0.2-1.0 inch) solidified cast web is typically reduced in thickness to a gauge of about 0.033 cm (0.130 inch) by cold rolling with an intermediate recrystallization anneal at 316―482°C (600-900°F). Thereafter, as in the manufacture of direct chill ingot cast stock, the thinned, annealed stock is subjected to a final work hardening step by cold rolling to a final gauge of about 0.033 cm (0.013 inch) to produce the H19 temper required for can body manufacture.
Although the continuous strip cast aluminium alloy is advantageously utilized for many fabricated products, such stock has not been used extensively for the manufacture of drawn and wall-ironed can bodies.
In the production of two-piece drawn and wall-ironed beverage cans, circular discs or blanks are cut or punched from the cold worked (H19) sheet for deep drawing into the desired shape. Deep drawing is a process for forming sheet metal between punch and die to produce a cup or shell-like part. When a deep drawn shell with a heavy bottom and thin sidewalls is desired, wall-ironing is used in conjunction with deep drawing. The blank is first drawn to approximately the final diameter cup. The sidewalls are then reduced in thickness in one or more ironing operations.
Because of the nature of the working stresses incurred during wall-ironing of the deep drawn shell, when continuous strip cast aluminium alloy such as 3004 is subjected to wall-ironing, scoring may occur on the die surface; alternately, deep grooves may appear on the finished can which is referred to in the art as "galling". Galling adversely affects the acceptability of the can product and the effectiveness of the can manufacturing process. Galling is not normally observed during wall-ironing aluminium sheets of the same alloy composition produced from direct chill ingot casting.
In spite of the economic advantage of the strip casting process, due to the drawback of not being gall-free when subjected to severe mechanical operations such as wall-ironing operations in two-piece aluminium can making, the utility and applicability of continuous strip cast aluminium alloy for can making has been extremely limited.
It is known to fabricate aluminium alloy strip stock by continuously casting an aluminium alloy in strip form; homogenizing the alloy strip; and then cold rolling the homogenized strip, as defined in the pre-characterizing portion of Claim 1.
The art has addressed the problem of providing continuous strip cast aluminium alloys which have the capability to be gall-free when subjected to the severe mechanical working conditions of can making. For example, U.S. 4,111,721 discloses a process for imparting an anti-galling character to a continuous strip cast aluminium alloy wherein the aluminium strip is heat treated at a temperature of at least 482°C (900°F) and advantageously at about 621°C (1150°F) for a period of time between 16 to 24 hours prior to its final cold reduction pass.
The art prior to U.S. 4,111,721, namely U.S. 3,930,895 disclosed that in the process of making continuous strip cast aluminium alloy suitable for can making, the cast strip, before cold rolling, is homogenized at a temperature of 510 to 566°C (950 to 1050°F) for 8 to 16 hours.
Although the art reported that gall-free continuous strip cast aluminium alloy had been produced, the strip has remained substantially unacceptable for can making stock because of the problem of "earing" which manifests itself as a scalloped appearance around the top edge of the cup during the deep drawing cup formation step of the drawn and wall-iron processing of the aluminium sheet.
The scallops, or ears, represent an almost universally undesirable feature of the cup as the ears must be removed in order to present a smooth or flat upper lip on the cup. This of course necessitates cup trimming prior or subsequent to wall-ironing with an attendant increase in production costs and material waste.
The level of earing in a drawn cup is determined by the following equation:
where he is the distance between the bottom of the cup and the peak of the ear and ht is the distance between the bottom of the cup and the valley of the ear.
To be acceptable for can making, the aluminium alloy sheet when processed into a cup must exhibit a low level of earing. The level of earing experienced with commercially available continuously cast strip of 3004 aluminium alloy is generally in the range of 5% or more. The present invention aims to provide lower levels of earing than the range of 5% or more. Advantageously, for optimum commercial use the level of earing should be reduced to no more than about 3.5% and preferably less than about 3% earing.
It is evident, therefore, that the reduction of the degree of earing during deep drawing of continuous cast aluminium strip to a level of about 3.5% or less represents a major contribution to the art of manufacture of continuous cast aluminium strip can stock.
Another problem encountered with continuous strip cast aluminium alloy 3004 is that the alloy sheet when fabricated into a two piece drawn and wall-ironed can exhibits a marginal level of buckle strength, that is, the ability of the can to withstand high internal pressure without bottom inversion.
Buckle strength is determined by applying pressure within a drawn and wall-ironed can and then gradually increasing the pressure until the bottom end of the can deforms and bulges out, i.e., it buckles. The pressure at which the bottom buckles is then designated as the buckle strength. To be acceptable as can body stock a can formed from the alloy sheet must exhibit a buckle strength of at least 620_X10³ N/m² (90 pounds per square inch (psi)), and preferably between 655x10³ and 689x10³ N/m² (95 and 100 psi). Cans drawn and wall ironed from a hard temper sheet of the continuous strip cast aluminium alloy 3004 homogenized at 566―593°C(1050―1100°F) to eliminate galling exhibit a buckle strength of about 586x 1 03 N/m² (85 psi).
The present invention relates to a process for the preparation of non-galling, low earing can stock from continuously cast aluminium strip suitable for deep drawing and wall-ironing into hollow articles.
The present invention provides a process for fabricating aluminium alloy strip stock suitable for the manufacture of drawn and wall-ironed articles, the process comprising the steps of: continuously casting an aluminium alloy in strip form; homogenizing the alloy strip; and then cold rolling the homogenized strip; characterised in that: the continuous cast strip has a thickness of up to 2.54 cm (one inch); said homogenizing step is carried out at a temperature of 510 to 621°C (950 to 1150°F) for up to 50 hours; said cold rolling step is carried out to yield at least a 25% reduction in thickness; and thereafter heating the cold rolled strip to a recovery temperature of from 177 to 288°C (350 to 550°F); cold rolling the strip to a second reduction in thickness of at least 10%; heating the cold rolled strip to a recrystallization temperature of from 316 to 428°C (600 to 900°F); and then cold rolling the recrystallized strip to a final gauge having a total reduction in thickness of at least about 50%.
In accordance with the present invention, the molten aluminium material is cast by continuous strip casting into a web generally of 2.54 cm (one inch) or less in thickness. The strip material is heated to a temperature of from 510 to 621°C (950 to 1150°F) for a time sufficient to homogenize the alloy. The homogenized strip material is cold rolled to effect a first reduction in sheet thickness of at least 25%. The cold rolled sheet is heated to a recovery temperature of from 177°C (350°F) to 288°C (550°F), and subjected to a second cold rolling to effect a reduction in thickness of at least 10%. The cold rolled sheet product is heated to effect recrystallization of the grain structure and then subjected to effect a final reduction in thickness which is at least about 50% and is preferably at least 75% of the original thickness of the sheet to impart an H19 temper to the sheet.
To effect the most advantageous reduction in earing, the sheet is subjected to a second recovery heating of from 177°C (350°F) to 288°C (550°F) intermediate between the second cold reduction and the recrystallization heating step.
As will hereinafter be illustrated, it has been determined that in the fabrication of strip cast aluminium sheet suitable for the production of drawn and wall-ironed beverage containers, control of the homogenization step within the parameters set forth above will render the sheet resistant to galling when subjected to drawing and ironing operations. Control of the cold roll and recovery heating parameters set forth above prior to the recrystallization heating step, will result in the fabrication of an aluminium sheet exhibiting low earing properties as well as non-galling characteristics.
Generally in affecting homogenization to prepare an aluminium alloy sheet product in accordance with the present invention, the continuous cast web is heated at 510 to 621°C (950 to 1150°F) and preferably 537 to 593°C (1000 to 1100°F) for a period of time up to about 50 hours and preferably 10 to 25 hours. Advantageously, the homogenization treatment is conducted at a temperature of about 593°C (1100°F) for at least about 10 hours. It is recognized that several hours are required to heat the metal to reach the temperature at which homogenization is effected.
In the event that the cast aluminium web is subjected to homogenization temperatures while in coil form, it has been determined that the coil be heated in a slow, pre-programmed manner for time periods ranging from 2 to 10 hours at increasing temperatures to avoid incipient melting of the alloy which will otherwise cause the coil layers to fuse and weld together and render the coiled product unsuitable for subsequent use. A programmed heating sequence which has been found advantageous for the homogenization of the continuous cast aluminium coil is as follows: Temperature of the web is raised from ambient 24°C (75°F) to 537°C (1000°F) over a 5 hour period.
Temperature of the web is raised from 537 to 566°C (1000 to 1050°F) over a 3 hour period.
Temperature of the web is raised from 566 to 593°C (1050 to 1100°F) over a 5 hour period.
Web is homogenized at 593±5.5°C (1100±10°F) for 20 hours.
The homogenization step of the process of the present invention imparts a very critical change in the microstructure of the alloy primarily in the size, shape and distribution of the intermetallic particles present in the alloy matrix. It has been determined that the change in intermetallic particle disposition is dependent upon the temperature as well as the time of the homogenization treatment and that the degree of galling is inversely dependent upon the intermetallic particle size.
Examination of photomicrographs of 3004 aluminium alloy subjected to the homogenization sequence of the present invention indicates that the secondary constituents in the aluminium alloy, e.g. (MnFeSi) Al, are caused to agglomerate whereby they change their shape substantially and increase in size. The net effect of this is the development of intermetallic particles approaching a globular shape having a particle size of 1 to 3 microns. These relatively large, globular shaped particles are believed to act as galling-resistant bearings for the strip cast stock during the severe mechanical working encountered in the wall-ironing operations of two piece can manufacture.
For example, continuous cast 3004 aluminium alloy strip cold rolled and size-reduced to 0.034 cm (0.0135 inch) gauge to H-19 temper by conventional practice typically has an intermetallic particle size in the order of 0.3-0.7 microns. As already indicated, this strip when subjected to ironing operations encounters severe galling. However, if the aluminium web is subjected to the homogenization step, as previously described, prior to cold rolling, the inter-metallic particle size increases with increasing homogenization temperature which results in a proportionate decrease in galling when the homogenized strip is subjected to wall-ironing conditions.
The relationship between homogenization temperature, intermetallic particle size and galling is summarized in the Table below:
Although the aluminium web when homogenized at 510-621°C (950-1150°F) will encounter no galling during wall-ironing a cup formed from the web, it will after being subjected to drawing operations, exhibit unacceptably high earing.
By following the cold roll/recovery-recrystallization heating sequence described herein there is attained a reduction in earing to levels required for commercial acceptance of the drawn and wall-ironed container.
Thus, after the aluminium alloy stock has been produced by continuous strip casting and homogenized in accordance with the parameters disclosed above, the cooled web which has a thickness of up to one inch and typically 0.64 to 1.27 cm (0.25 to 0.50 inch) in thickness is subjected to a first cold rolling step to effect a total gauge reduction in excess of about 25% and preferably 50 to 75%. Thereafter, the cold rolled sheet is heated to a recovery temperature level.
The term "recovery temperature" as it is used in the art means the temperature at which the rolled metal is heated whereby it is softened without forming a new grain structure. For aluminium alloys of the 3004 type the recovery temperature is in the range of 177 to 288°C (350 to 550°F). In accordance with the present invention, the cold rolled strip is heated to a recovery temperature of from 177 to 288°C (350 to 550°F). Preferably, the recovery temperature to which the cold rolled web is heated after the first cold roll reduction is 204 to 246°C (400 to 475°F) for 2 to 6 hours, and more preferably from 218 to 246°C (425 to 475°F) for 2 to 4 hours.
After being heated at the recovery temperature the heated web is cooled to ambient temperature and subjected to a second cold rolling step to effect a total reduction in thickness of the web of at least 10% and preferably from 10 to 25%.
As will hereinafter be illustrated, heating the web to a recovery temperature intermediate between the two cold rolling steps is critical to imparting a low earing characteristic to the aluminium sheet.
After the second cold roll step, the temperature of the cold rolled web is raised to the "recrystallization temperature" level.
The term "recrystallization temperature", as it is used in the art, means the temperature at which the rolled metal web softens simultaneously with the formation of a completely new grain structure. In the case of 3004 alloy, the grain structure changes from a substantially elongated structure to an equiaxed structure when the alloy is heated at the recrystallization temperature.
In the practice of the present invention, the recrystallization temperature is in the range of 316 to 482°C (600 to 900°F), the heating being effected for 1 to 4 hours and preferably at a temperature from 371 to 427°C (700 to 800°F) for 2 to 3 hours.
After heating at the recrystallization temperature for the prescribed time period, the recrystallized web is cooled to ambient temperature and then cold rolled, e.g., to at least about 50% and preferably 60 to 90%, to the final gauge dictated by can performance requirements, e.g., 0.030 to 0.037 cm (0.012 to 0.0145 inch) and H19 temper.
To achieve an optimum reduction in earing the aluminium web is heated a second time to a recovery temperature, the second recovery heating occurring between the second cold rolling step and the recrystallization heating step. The second recovery heating is effected at a temperature from 232 to 288°C (450 to 550°F) for 0.5 to 3 hours and preferably from 246 to 274°C (475 to 525°F) for 0.75 to 1.25 hours.
In effecting the second recovery heating, the web may be cooled to room temperature between the second recovery heating step and the recrystallization step. Preferably the recrystallization heating is carried out without prior cooling to room temperature by direct heating from the second recovery temperature to the recrystallization temperature.
It has been further determined that to achieve a consistency in earing reduction results it is advantageous that, after the homogenization step of the process of the present invention the web is cooled in a controlled stepped manner, i.e., at a cooling rate of no more than 42°C/hr (75°F/hr). A preferred sequence of cooling is summarized as follows:
An aluminium alloy preferred in the practice of the present invention is a 3004 aluminium alloy having incorporated therein 0.1-0.4% by weight chromium. Sheet formed from the chromium modified alloy 3004 when fabricated into a two piece drawn and wall-ironed can exhibits an improved level of buckle strength, that is, the ability of the can to withstand high internal pressure without bottom inversion.
The chromium modified aluminium alloy 3004 preferred in the practice of the present invention has the following range of constituents expressed in percent by weight: 0.5 to 1.5% magnesium, 0.5 to 1.5% manganese, 0.1 to 1.0% iron, 0.1 to 0.5% silicon, 0.0 to 0.25% zinc, 0.0 to 0.25% copper, 0.1 to 0.4% chromium, the balance being aluminium and incidental elements and impurities.
For sheet formed from the chromium modified alloy 3004 to perform as desired, it is essential that it be in the state resulting from a cold roll reduction of at least 50% of the material in the recrystallized state. The sheet in this state can exhibit tensile yield strengths in the range of 275.6x 10⁶ to 310.1 × 10° N/m² (40,000 to 45,000 psi) and total elongation, measured in 5.1 cm (2 inches) gauge length samples, of 1.5% or more. A tensile yield strength of 275.6x 10⁶ to 310.1 x 1 0⁶ N/m² (40,000 to 45,000 psi) in the sheet material has been found, when such sheet is drawn and wall ironed into a two piece beverage container, to correlate with a can buckle strength of at least 675x10³ N/_M ² (98 psi).
The improved properties imparted to alloy 3004, and particularly the high tensile yield strengths, by the incorporation therein of 0.1 to 0.4% by weight chromium is totally unexpected when viewed against the teachings of the prior art.
Thus, U.S. 4,111,721 teaches that additaments to alloy 3004 such as chromium should be limited to trace amounts in the order of several hundred thousands of a weight percent or less as such additaments tend to have profound effects on the intermetallic particle sizes in the alloy. U.S. 3,834,900 teaches that the presence of chromium in the strip cast aluminium alloy should be minimized, i.e., limited to a concentration of less than 0.001% by weight, to avoid casting defects.
The processing limitations of the present invention, and preferably the compositions of the preferred embodiments, should be closely followed in order to achieve the required high tensile yield strength properties which characterise the sheet prepared from continuous strip cast modified alloy of the present invention. Improved results may be obtained by the preferred process of the present invention when the chromium concentration in the Aluminium 3004 alloy is from 0.1 to 0.4 wt%. For example, if the maximum chromium concentration levels are exceeded, problems such as fracturing during can forming may result. If chromium levels of less than about 0.1 % by weight are incorporated in the alloy, the tensile yield strength of sheet fabricated from the continuous strip case alloy can fall below the minimum requirements for beverage can performance.
In converting the chromium modified alloy composition of the present invention into sheet material by strip casting, the aluminium and alloying elements are charged into a melting furnace from which a stream of alloy is fed to a conventional strip caster which solidifies a web of 2.54 cm (an inch) or less in thickness preferably 0.64 to 1.27 cm (0.25 to 0.50 inch) in thickness. The strip cast web is fabricated into sheet having non-galling, low earing and high strength characteristics by employing the homogenization and cold roll/anneal process conditions of the process of the present invention.
A more thorough understanding of the present invention may be attained by reference to the following specific examples of the practice of the invention.

Example I

A series of strip-cast aluminium alloys having varying alloy constituents including those within the Aluminium Association Specification 3004 aluminium alloy range were evaluated for use in the fabrication of drawn and wall-ironed can bodies. The composition of the alloys is summarized in Table I below:
30.5 cm (one foot) wide by 91.4 cm (three feet) long sections of the cast aluminium strip having a thickness of 1.22 cm (0.48 inch) were placed in a furnace in a nitrogen atmosphere, brought up rapidly to the desired temperature, and held for 10 to 40 hours at homogenization temperatures varying from 590°C to 610°C (1094 to 1130°F). Thereafter, the strips were removed from the furnace and cooled to ambient temperature by blowing cold compressed air on the strips. The homogenization conditions used in the series of runs are summarized in Table II as follows:
The cooled strips were rolled in successive passes using a commercial rolling mill until the strip was reduced to varying degrees of thickness ranging from 66 to 75% (0.41 to 0.30 cm) (0.160 to 0.120 inch).
The reduced thickness strips were subjdcted to a first recovery temperature wherein the strips were placed in a furnace previously heated to 232°C (450°F) and held for 3 hours after which time the strips were removed from the furnace and allowed to cool to room temperature.
After being subjected to the first cold roll/recovery temperature treatment, the strips were subjected to a second cold roll reduction by being passed successively through a pair of reduction rolls until the strip was reduced 10-25% in thickness to 0.30 cm (0.120 inch).
After the second cold roll reduction the strips were subjected to a second recovery heating at 260°C (500°F) for one hour and then annealed at a recrystallization temperature of 427°C (800°F) for 2 hours.
The cold roll/recovery-recrystallization (anneal) conditions to which the series of strips were subjected are summarized in Table III below.
For purposes of contrast, the cold roll/anneal conditions of Example I were repeated with the exception that no recovery temperature heating was effected between the cold roll reduction step and the recrystallization step. These contrasting conditions are summarized in Table III below designated by the symbols "C₁" and "C₂".
The recrystallized strips were cooled to ambient temperature and then work hardened by passing the strips successively in a commercial rolling mill until the strip was reduced about 88% in thickness (H19 temper) to 0.0340 to 0.0376 cm (0.0134 to 0.0148 inch).
The H19 temper strips were examined under a scanning electron microscope in the back scattering mode and found to have an intermetallic particle size in the 1 to 3 microns range indicating that no galling would occur when the strips were subjected to the wall-ironing conditions of can making.
To determine the extent of earing which would occur when the strips were subjected to the drawing operations of can making, circular blanks 5.59 cm (2.20 inch) diameter were cut from the H19 hardened strips and deep drawn into shallow cups of 3.35 cm (1.32 inch) diameter with a resultant 39% reduction in diameter. The tooling used for deep drawing 0.0343 cm (0.0135 inch) sheet was designed to yield about a 3.5% positive clearance (0.00127 cm) (0.0005 inch) between the walls of the punch and die. A die clearance of 5% or less and a reduction in diameter of 39% is typically required in this standard test for canstock earing which simulates the drawing step of the can making process. Cupping speed and blank clamping pressure were adjusted for each test to obtain a fracture and wrinkle-free cup.
The results of the earing tests using strips of the alloy compositions of Table I which had been subjected to the homogenization and cold roll/anneal conditions disclosed in Tables II and III are summarized in Tables IV and V below. Each earing test result represents an average of three tests.
The results of earing tests on aluminium strips subjected to comparative cold roll/anneal cycles C, and C₂ are summarized in Table VI below.
By reference to the earing data summarized in Tables IV and V, and comparing such data to the comparative earing data in Table VI, it is readily apparent that aluminium strip treated in accordance with cold roll/anneal cycles 1 and 2 produce lower earing when compared to comparative cold roll/anneal cycles C₁ and C₂. The data indicates that cold roll/anneal cycles 1 and 2 which involve one or more recovery heating steps prior to recrystallization heating can be more effective in reducing earing than anneal cycles C₁ and C₂ in which there are one or more recrystallization heating steps but no recovery heating step. Cold roll/anneal cycle 1 produces superior earing results when compared to cold roll/anneal cycle 2; cycle 1 having a lower second rolling reduction (10%) than cycle 2 (25%), indicating that a low (10%) second rolling reduction is desirable in reducing earing. However, the use of a second recovery treatment in which the strip is heated to a second recovery temperature after the second cold roll and prior to heating the strip to the recrystallization temperature is not essential to the present invention but is merely preferred in order to give reduced earing.

Example II

The procedure of Example I was repeated with the exception that there was simulated the heating and cooling conditions that would be expected to occur in a commercially produced 1.02x 104 to 1.53x 10⁴ kg (10-15 ton) coil of continuous strip cast aluminium alloy 3004 of about 1.27cm (0.50 inch) thickness which had been subjected to the heating sequence described above.
The programmed heating and cooling sequences outlined herein were used to achieve strip homogenization in these coil simulation tests. The time and temperature used in the heating and cooling sequences are summarized in Table VII below:
The strips homogenized in accordance with Table VII were then cooled in accordance with the following schedule:
At 191°C (375°F) the furnace was shut off and the strips allowed to cool to room temperature.
The cooled strips were then cold rolled/annealed in the manner of Example I using the cold roll/anneal conditions summaried in Table VIII below.
For purposes of contrast, the cold roll/anneal conditions of Example II were repeated with the exception that no recovery temperature heating was effected between the cold roll reduction step and the recrystallization step. This contrasting condition is summarized in Table VIII below designated by the symbol C₃.
The heating and cooling conditions that would be expected to occur in processing a commercial coil were used in each recovery and recrystallization step. These conditions are summarized in Table IX below:
The cooled recrystallized strips of Table IX were work hardened to H19 temper and reduced in thickness to 0.0340 to 0.0376 cm (0.0134 to 0.0148 inch).
The H19 temper strips were examined under a scanning electron microscope in the back scattering mode and found to have an intermetallic particle size in the 1 to 3 microns range, indicating that no galling would occur when the strips were subjected to the wall-ironing conditions of can making.
The results of earing tests using strips of the alloy compositions of Table I which had been subjected to the homogenization and cold roll/anneal conditions as disclosed in Tables VIII and IX are summarised in Tables X-XIII below. Each earing test result represents an average of 3 tests.
The results of earing tests on aluminium strips subjected to comparative cold roll/anneal cycle C₃ are summarised in Table XIV below.
By reference to the data summarized in Tables X-XIII and comparing such data to that in Table XIV, it is readily apparent that the largest reduction in earing occurs when cold roll/anneal cycle 5, which employs two recovery heatings prior to recrystallization is used.
Cold roll/anneal cycle 6 which is identical to cycle 5, except that a second cold roll reduction of 25% is used instead of 10%, produces a reduction in earing, but the reduction achieved is less than that achieved using cycle 5, indicating that a second cold roll reduction of 10% is more advantageous in effecting a reduction in earing.
Cold roil/anneal cycle 7 which utilizes a single recovery heating/single recrystallization heating sequence does not achieve the earing reduction level of cycle 5 but does produce a superior reduction in earing when compared to the single recrystallization heating of cold roll/anneal cycle C₃.
The double recovery heating/recrystallization heating of cycle 8 produces a reduction in earing when compared to control cycle C₃, but does not provide an advantage over cycle 5 which utilizes only one recrystallization heating.

Example III

A strip-cast aluminium alloy having the alloy composition of the present invention designated by the symbol "I" was prepared as well as alloy compositions having varying alloy constituents within the 3004 specification range designated by the symbol "A". These alloys were then evaluated for use in the fabrication of drawn and wall-ironed can bodies. The composition of the alloys is summarized in Table XV below:
30.5 cm (one foot) wide by 91.4 cm (three feet) long sections of the cast aluminium strip having a thickness of 1.22 cm (0.48 inch) were placed in a furnace in a nitrogen atmosphere and heated for 10 to 40 hours at homogenization temperatures varying from 590°C to 600°C (1094°F to 1112°F). The heating and cooling conditions that would be expected to occur in a commercially produced 1.02x 10⁴ to 1.5x10⁴ kg (10-15 ton) coil of a strip of continuous cast aluminium alloy of about 1.27 cm (0.50 inch) thickness when subjected to the programmed heating and cooling sequences preferred for homogenization and outlined in the Preferred Embodiments of this application were simulated to achieve strip homogenization. The time and temperature used in the heat and cooling sequences are summarized in Table XVI below:
The strips homogenized in accordance with the conditions in Table XVI were then cooled in accordance with the following schedule:
At 191°C (375°F) the furnace was shut off and the strips allowed to cool to room temperature.
The cooled strips were rolled in successive passes using a commercial rolling mill until the strip was reduced to varying degrees of thickness ranging from 66 to 75% (0.040 cm to 0.030 cm) (0.160 to 0.120 inch).
In a first series of cold roll/recovery-recrystallization heatings the reduced (66-72%) thickness strips were subjected to a first recovery temperature wherein the strips were heated in a furnace to 232°C (450°F) and held for 3 hours. After being subjected to the first cold roll/recovery temperature treatment, the strips were then subjected to a second cold roll reduction by being passed successively through a pair of reduction rolls until the strip was reduced 10-25% in thickness to 0.030 cm (0.120 inch).
After the second cold roll reduction the strips were subjected to a second recovery heating at 260°C (500°?) for one hour and then heated to recrystallization temperature of 427°C (800°F) for 2 hours.
The first series of cold roll recovery-recrystallization heatings was varied whereby in a first variation the second cold reduction was eliminated and recrystallization carried out immediately after the first recovery heating. In a second variation, the recovery heating was eliminated and recrystallization was carried out immediately after the cold reduction.
The cold roll/anneal conditions to which the series of strips were subjected are summarized in Table XVII below.
The heating and cooling conditions that would be expected to occur in processing a commercial coil were used in each recovery and recrystallization step. These conditions are summarized in Table XVIII below.
The recrystallized strips were cooled to room temperature and then were hardened by passing the strips successively in a commercial rolling mill until the strip was reduced about 88% in thickness (H19 temper) to 0.0338 to 0.0376 cm (0.0133 to 0.0148 inch).
The H19 tempered strips were examined under a scanning electron microscope in the back scattering mode and found to have an intermetallic particle size in the 1 to 3 microns range, indicating that no galling would occur when the strips were subjected to the wall-ironing conditions of can making.
To determine the level of earing that would occur when the strips were subjected to the drawing operations of can making, circular blanks 5.59 cm (2.20 inch) diameter were cut from the H19 hardened strips and deep drawn into shallow cups of 3.35 cm (1.32 inch) diameter with a resultant 39% reduction in diameter. The tooling used for deep drawing was designed to yield about a 3.5% positive clearance (0.00127 cm) (0.005 inch) between the walls of the punch and die. A die clearance of 5% or less and reduction in diameter of 39% is typically required in this standard test for earing which simulates the drawing step of the can making process. Cupping speed and blank clamping pressure were adjusted for each test to obtain a fracture and wrinkle-free cup.
The results of the earing tests using strips of the alloy compositions of the Table XV which had been subjected to the homogenization and cold roll/anneal conditions disclosed in Tables XVI and XVII are summarised in Tables XIX-XXI below. Each earing test result represents an average of three tests.
The mechanical properties of the H19 hardened strips in tension, i.e. yield strength, ultimate strength and tensile total elongation were determined in accordance with the ASTM Test Procedure Number E-8 using 5.1 cm (2 inches) gauge length test specimens. Each mechanical test result represents an average of six tests, three measured in the direction longitudinal and three in transverse to the rolling direction. The results of these tests are also recorded in Tables XIX-XXI below.
It had been previously determined that the buckle strength of cans formed from continuous strip cast aluminium alloy 3004 correlates closely with the tensile yield strength of the H19 temper sheet. The correlation between buckle strength and tensile yield strength is summarized in Table XXII below.
The tensile ultimate strength, along with the tensile total elongation, is a measure of sheet formability. To be suitable for can body manufacture, the sheet must have a tensile ultimate strength of at least 289x10⁶ N/m² (42,000 psi).
Tensile total elongation measured in percent is a measure of ductility. To be suitable for can body manufacture the sheet must have a tensile total elongation of at least 1.5%.
By reference to Table XIX it is immediately apparent that the incorporation of 0.11% by weight chromium in aluminium alloy 3004 improves the tensile yield strength and thereby the corresponding buckle strength without any deleterious effect on the can formability of sheet formed from the alloy. Thus the tensile yield strength of Alloy I generally exceeds 275.6x10⁶ N/m² (40,000 psi) reflecting a buckle strength in excess of 675.2x10³ N/m² (98 psi). Similarly, the total elongation of Alloy I is in excess of the minimum requirement of 1.5%.
By comparing the data recorded in Tables XX and XXI with that of Table XIX it is immediately apparent that conventional 3004 alloy, such as alloys A, and A₂, when processed in accordance with the same conditions of Alloy I have buckle strength substantially lower than that of Alloy I.

Example IV

A second series of strip cast aluminium alloys were evaluated for use in the fabrication of drawn and wall ironed can bodies. The composition of the alloys is summarized in Table XXIII below:
Copper was incorporated in the alloys to simulate aluminium can scrap which has been found to contain 0.1 to 0.2 percent by weight copper.
The aluminium alloys were continuously cast, using a Hunter type twin roll caster into sheet 0.66 cm (0.26 inches) thick which were wound into 2270 kg (5000 pound) coils. The coils were allowed to reach room temperature over a 48 hour period. The cooled coils were then placed in a furnace and homogenized in a nitrogen atmosphere. The coil was brought up to 580± 3.9°C (1076°F±7°F) over a 12 hour period and held at that temperature for 16 hours. Thereafter, the coils were allowed to cool in the furnace to 93°C (200°F) over a 32 hour period. The cooled coils were removed from the furnace and further allowed to cool to room temperature over the next 48 hours.
The room temperature cooled coils were subjected to a first cold roll/recovery temperature treatment wherein the cooled coils were rolled in successive passes using commercial rolling equipment until each of the coils was reduced to varying degrees of thickness varying from 83 to 85% (0.132 to 0.15 cm) (0.052 to 0.059 inches).
The reduced thickness coils were subjected to a first recovery temperature wherein the coils were placed in a furnace and heated to 232±1.7°C (450°F±3°F) over a 4 hour period and held at this temperature for 4 hours whereupon the coils were allowed to cool in the furnace to 149°C (300°F) over a period of nine hours. The coils were removed from the furnace and allowed to cool to room temperature over the next 48 hours.
After being subjected to the first cold roll/recovery temperature treatment, the coils were subjected to a second cold roll reduction by being passed successively through a pair of reduction rolls until each of the coils was reduced 25% in thickness 0.099 to 0.112 cm (0.039 to 0.044 inches).
After the second cold roll reduction, the coils were placed back in the furnace and subjected to a second recovery heating by raising the temperature of the furnace to 260°C (500°F) over a 3.5 hour period, and holding at that temperature for 1.5 hours. The coils were annealed at a recrystallization temperature by raising the temperature of the furnace to 427°C (800°F) over a 6 hour period and held at this temperature for 3 hours. The coils were allowed to cool in the furnace to 149°C (300°F) over a 14 hour period and then removed from the furnace and allowed to cool to room temperature over the next 48 hours.
The recrystallized coils were then work hardened by passing the coils successively in a commercial rolling mill until the coil was reduced 65 to 67% in thickness to 0.0343 cm (0.0135 inches).
The work hardened coils were then fabricated into two-piece aluminium beverage cans on a commercial drawn and wall ironing manufacturing line, about 5000 cans being fabricated from each coil. No galling was encountered. Earing ranged from 2.0 to 2.6%.
The cans were also evaluated for buckle strength, i.e., ability of the can to withstand high internal pressure without buckling.
Buckle strength is determined by applying pressure within a drawn and wall-ironed can and then gradually increasing the pressure until the bottom end of the can deforms and bulges out, i.e. it buckles. The pressure at which the bottom buckles is then designated as the buckle strength. To be acceptable as can body stock, a can formed from the alloy sheet must exhibit a buckle strength of at least 620.1 x 1 03 N/m² (90 pounds per square inch (psi)).
The average buckle strength for cans fabricated from alloys A, B and C in the above manner are recorded in the Table XXIV below:

Claims

1. A process for fabricating aluminium alloy strip stock suitable for the manufacture of drawn and wall-ironed articles, the process comprising the steps of: continuously casting an aluminium alloy in strip form; homogenizing the alloy strip; and then cold rolling the homogenized strip; characterized in that: the continuous cast strip has a thickness of up to 2.54 cm (one inch); said homogenizing step is carried out at a temperature of 510 to 621°C (950 to 1150°F) for up to 50 hours; said cold rolling step is carried out to yield at least a 25% reduction in thickness; and thereafter heating the cold rolled strip to a recovery temperature of from 177 to 288°C (350 to 550°F); cold rolling the strip to a second reduction in thickness of at least 10%; heating the cold rolled strip to a recrystallization temperature of from 316 to 482°C (600 to 900°F); and then cold rolling the recrystallized strip to a final gauge having a total reduction in thickness of at least about 50%.

2. A process according to claim 1, characterized in that the continuous cast aluminium strip has a thickness of from 0.635 to 1.27 cm (0.25 to 0.50 inch).

3. A process according to claim 1, characterized in that the strip is homogenized at a temperature from 537 to 593°C (1000 to 1100°F) for from 10 to 25 hours.

4. A process according to claim 1, characterized in that the first cold roll reduction effects a reduction in thickness of from 50 to 75%.

5. A process according to claim 1, characterized in that the strip is heated at a recovery temperature from 204 to 246°C (400 to 475°F) for from 2 to 6 hours.

6. A process according to claim 1, characterized in that the strip is heated at a recovery temperature of from 218 to 246°C (425 to 475°F) for from 2 to 4 hours.

7. A process according to claim 1, characterized in that the cold rolled strip is heated to a recrystallization temperature of from 371 to 454°C (700 to 850°F) for from 2 to 3 hours.

8. A process according to claim 1, characterized in that the second cold roll reduction effects a reduction in thickness of from 10 to 25%.

9. A process according to claim 1, characterized in that the strip is heated to a second recovery temperature after the second cold roll and prior to heating the strip to the recrystallization temperature, the second recovery temperature being in the range of from 232 to 288°C (450 to 550°F), the heating being effected for from 0.5 to 3 hours.

10. A process according to claim 1, characterized in that the recrystallized strip is cold rolled to a final gauge having a total reduction in thickness of from 85 to 90%.

11. A process according to claim 1, characterized in that the aluminium alloy is Aluminium Association Specification 3004 aluminium alloy.

12. A process according to claim 1, characterized in that the aluminium alloy includes from 0.5 to 1.5% by weight magnesium, from 0.5 to 1.5% by weight manganese, from 0.1 to 1.0% by weight iron, from 0.1 to 0.5% by weight silicon, from 0.0 to 0.25% by weight zinc, from 0.0 to 0.25% by weight copper and from 0.10 to 0.4% by weight chromium.

13. A process according to claim 1, characterized in that the cold rolled strip is heated prior to recrystallization to a recovery temperature of from 177 to 288°C (350 to 550°F) for at least 2 hours and then cold rolled to a second reduction in thickness of at least 10%.

14. A process according to claim 1, characterized in that the first cold roll reduction effects a reduction in thickness of from 50 to 85%.

15. A process according to claim 1, characterized in that the second cold roll reduction effects a reduction in thickness of from 10 to 50%.

16. A process according to claim 1, characterized in that the recrystallized strip is cold rolled to a final gauge having a total reduction in thickness of from 50 to 90%.

17. A process according to claim 12, characterized in that the chromium incorporated in the alloy 3004 is in the range of from 0.11 to from 0.25% by weight.