JPS5964758A - Method of producing strip material of aluminum alloy - Google Patents

Abstract

(57) [Summary] This bulletin contains application data before electronic filing, so abstract data is not recorded.

Description

DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a process for preparing continuous strip cast aluminum alloys suitable for use in the manufacture of deep drawn, wall ironed products such as cans.

In recent years, for example, the Aluminum Association standard (Alum
inum As5ocation 5pecif
) Aluminum alloys such as Ro004 can be made into two-piece YiV by deep drawing and ironing.
It has been successfully produced in cans for refreshing drinks. The widespread use of two-piece aluminization has created a demand for aluminum alloy sheets to form can bodies that not only provide the necessary formability and strength, but are also economical to manufacture. I've been doing it.

Typically, deep drawn and ironed aluminum alloy sheets useful in the manufacture of soft drink cans have a thickness of about 20 inches to about 66.5 centimeters.
25 inch) ingots are cast by direct quench casting. Ingot is 510℃-607 for 4-24 hours,
Homogenized at a temperature of 2°C (950-1125°F) and then hot rolled, where the ingot is
4.4°C-482,2°C (400-900'Ii'
) is passed through a series of blooming rolls held at approximately 0.33
Roll down to millimeter (0,0130 inch) reroll gauge.

The re-rolled material is then subjected to an annealing process, where the material is heated to 315.6°C-4 to recrystallize the metallographic structure.
The skin is heated at 600-900'F for 5-3 hours. The annealed re-rolled gauge is subjected to a final finish hardening process, and the monthly charge is approximately 0.33 mm IJ (0,01
The material is cold rolled (room temperature rolled) to a final size of 3 inches) or about 90 inches of its original size to produce a temper material of near full hardness (HI3) required for two-piece can shells.

Although directly cooled, pit-cast aluminum alloys can be used successfully to build cans, economic and energy considerations favor stripping aluminum sheets by continuous strip casting.

In this method, molten aluminum is cast and hardened into a thin web with a thickness of 1 inch or less, thereby minimizing subsequent rolling;
And expensive (hot rolling should be eliminated).

In the production of continuous slit 0 cast aluminum alloys for can production, for example, 5.08-25.4 mm IJ (0,
2-1,0") thin cured cast webs are typically
°F) with intermediate recrystallization annealing and cold rolling at approx.
It is rolled down to a size of 6 mm (0,160 inches). Thereafter, as in the production of direct cooled ingot cast pellets, the thinned and annealed pellets are approximately 0.66 mm (0.0
It is subjected to a final finish hardening process by cold rolling to a final size of 13 inches (13 inches) to obtain the H19 number required for can manufacturing.

Continuous strip cast aluminum alloys have been advantageously used in many fabricated products;
It has not been widely used to make can bodies with ironed walls.

In the production of two-piece deep-drawn, iron-walled soft drink cans, a circular disc or blank is cold-rolled (H1) in order to be deep-drawn into the desired shape.
9) Punched out from the sheet month.

Deep drawing is a method in which a metal sheet 7 is formed between a punch and a guide to hold the shell-like part.If you want a deep-drawn shell with a thick bottom and thin walls, - If deep drawing and overnight wall ironing are used in succession, the blank is first drawn to a tap of approximately the final surface diameter.The side walls are then reduced in area by one or more ironing operations. .

Due to the nature of the working stresses that occur during wall ironing of deep-drawn shells, continuous steels such as 3004
When wall ironing is applied to cast aluminum alloy, it may cause scratches on the surface of the die, or alternatively, it may cause deep grooves in the can, which is a problem in this technical field. Well then (-
(It is called "Kajiri"). Galling has a negative impact on the acceptability of the can product and the efficiency of the can manufacturing process. Generally, galling is not observed during wall ironing of aluminum sheets of the same alloy composition made from direct cooled ingot castings.

Although the strip casting method has economical advantages, it has the disadvantage that it does not suffer from galling when it is subjected to several machining operations, such as wall ironing when a two-piece aluminum can is assembled. Therefore, the utility and applicability of continuous strip cast aluminum alloys in can manufacturing has been extremely limited.

The art has been directed to the problem of providing a continuous lip cast aluminum alloy 'x 4M that does not exhibit galling even when subjected to several machining operations in the manufacture of cans. For example, U.S. Pat. No. 4,111,721 discloses a method for testing continuous strip cast aluminum alloys for anti-galling properties, in which the aluminum strip is subjected to a final cold reduction pass. At least 482.2°0 (90
D'F'), advantageously about 621.1°C (1150'F'
) for about 16 to 24 hours.

In a technique prior to U.S. Pat. No. 4,111,721, namely U.S. Pat. No. 3,930,895, fishing line strips are cooled in a continuous strip cast aluminum alloy suitable for can manufacturing. Monthly] Ladle 510 in front of Nobu
It discloses homogenizing at a temperature of -565.6°C (950-1050°F) for about 8 to about 16 hours.

That technology! 11+-e has reported that non-galling continuous strip cast aluminum alloy 1 has been manufactured, but the strip has one earring.
±sL, which is generally unacceptable as a ladle for making cans. r-1-1: "Wave" is a deep drawing process in which an aluminum sheet is drawn and wall ironed. It has a scallop-like appearance.

Scarotzu, that is, ears, is a tip of the tongue that is not liked worldwide because it is necessary to remove the ear in order to have a smooth or flat upper lip. Of course! 1iii - This requires trimming the wall before or after the wall ironing = 1 trimming, but this involves an increase in manufacturing costs and a waste of monthly fees.

The degree of selvage in a deep-drawn tip is determined by the following equation.

he is the distance between the bottom of the tip and the top of the moon,
ht is the bottom of the tip and J4. is the distance between the valley and the valley.

To be acceptable for "4+J" cans, the aluminum base metal sheet when processed into chips must exhibit an ear wave generation level of about 3.5% or less, preferably 6% or less. Ear wave generation levels experienced with commercially available continuously cast strips of 004 aluminum alloy are typically in the range of 5 or higher.

Therefore, if the degree of selvage during continuous casting aluminum strip deep drawing is reduced to a level of about 6.5 or less, it will greatly contribute to the continuous casting aluminum strip manufacturing technology. That is clear.

Another problem experienced with 6004 continuous strip cast aluminum base metal Q'11. - When the aluminum alloy is processed into two-piece deep-drawn and wall-ironed cans, it exhibits a high level of buckling strength, i.e., without flipping over the bottom (demonstrating the ability to withstand high internal pressures).

Buckling strength is measured by applying pressure to the interior of a deep-drawn, wall-ironed can, gradually applying pressure until the bottom end of the can deforms and bulges or warps. The pressure when the bottom Th1S warps is called buckling strength. Cans made from aluminum alloys are too small (both 6.3 k!7/cm” (90 p.
si), preferably 6.65 kg/cTL” (95
psi) and 7 kg/crn2 (100 psi). 565.5°C-595.5°C (1050-1100°F) to remove galling
) A hard tempered sheet of continuous strip cast aluminum alloy 6004 homogenized at a temperature of approximately 5.95 kg
/crrL2 (85Tlei) -1-
0 The present invention is made of melted clay; the aluminum material has an overall thickness of 25 mm.
．． Cast by continuous strip casting into webs of 4 mm (1 inch) or less! 1Th4. A method for preparing can materials from continuous cast aluminum strips with a non-galling property and less burr formation when deep drawn into hollow products by deep drawing and wall ironing with characteristic features and wall ironing. l-1-ro. S1-IJ Tsubu material ni”
was heated at 510°C (950°C) for a sufficient time to homogenize the alloy.
F) to a temperature of 621.1°C (115 [J', Ei'). The equalized IJ roll is cold rolled to at least 25 parts of the sheet thickness during the first rolling process. The cold rolled sheet is approximately 2
It is heated to a temperature of up to 87.8°C (550°F) and subjected to a second cold rolling to reduce the thickness by at least 10%.

Cold-rolled products have a grain structure that is 11) crystallized''3-
The original thickness of the Mukuro sheet is reduced by 75% in order to apply heat to the sheet.
Final pressure is applied to a thickness of .

In order to most advantageously reduce ear development, the sheet should be placed in the second
In the middle between the cold rolling and the recrystallization heating process of 287.
A second recovery heat is applied to 8°C (550°F).

As will be discussed below, strip cast aluminum sheets suitable for producing deep drawn and wall ironed soft drink containers can be produced by controlling the homogenization process within the parameters mentioned above. It has been found that the sheet fire resists galling even when subjected to aperture and wall ironing action. By using the cold rolling and recuperation heating parameters described above before the heating process for crystallization, a 87/'minium sheet exhibiting low generation and non-galling properties is produced.

Generally, to prepare aluminum alloy sheet according to the present invention, the homogenizing process is continued for up to about 50 hours, preferably from about 10 to about 25 hours, at about 510°C (9
50°F) to about 621.1°C (1150”F), preferably about 537.8°C (1000°F) to about 593°F.
Heated at 3°0 (1100°F).

Homogeneous treatment is less (approximately 10 hours at approximately 593.3°C (11
Advantageously, it is carried out at a temperature of 00'li').

It has been observed that several hours of partial heating of the metal may be required to reach the temperature at which homogenization takes place.

When a cast aluminum web is heated in coil form to a homogeneous temperature, there is an initial melting process that would otherwise cause the coal layers to melt and weld together, ruining the coil'4+! product for further use. It has been found to be possible to heat the coil slowly and with a pre-programmed arrangement for a range of 2 to 10 hours σ) at increasing temperatures in order to reduce the temperature. ; IS Ml; The block diagram heating sequence that has been found to be effective for uniformity of cast aluminum coils is as follows.

Change the web temperature for 5 hours to the ambient temperature (25.9℃=75uF)
) to 537.8°C (1000'li')4).

Web temperature to 537.8°C (1000'F) for 6 hours
Temperature 1 from 565.6°C (1050'Ii')
-ru.

The web temperature was increased to 565.6"C (1050'l) for 5 hours.
i') to 593.5°C (1100°F), ++1-1. □ Web "20 hours 5930.') ± 5.5
Homogenize at ! (1100 ± 10'F).

The homogenization step of the method according to the invention results in extremely important changes in the microstructure of the alloy, primarily with regard to the shape, shape and distribution of the intervening metal inner rotors in the IJ flux. It was found that the change in the arrangement of the intrametallic particles was influenced by the temperature and time of the homogenization treatment, and that the degree of galling was inversely proportional to the size of the intrametallic particles.

Microscopic observation of the aluminum alloy 3004 that has undergone the homogenization process according to the present invention shows that the second component of the aluminum alloy, for example (MnFθ5i)Al, changes its shape significantly by agglomeration and increases in size. It shows that. The net effect of this is that the intrametallic particles develop into spherical shapes with particle sizes of 1 to 3 microns.

° These relatively large, spherical granules act as anti-galling bearings on the strip cast sides during the severe machine processing experienced in two-piece can wall ironing operations (1). It is believed that.

For example, it is cold-rolled by a normal method to 0.64 mm! J
(0,0135 inch) H-19
Tempered, continuously cast aluminum alloy strips are typically about 0.3-0.7 microns thick, and this strip exhibits severe galling when ignited during ironing operations. However, when the aluminum web is subjected to a homogenization process before cold rolling, the size of the inner metal particles increases with the increase of the homogenization temperature, and the galling decreases proportionally when the IJ tube is subjected to a wall ironing condition. let

The relationship between homogenization temperature, intrametal particle size and galling is summarized in the table below.

Table 482.2-510 (900-95 [J) 0
．． 5-1.0 Normal 537.8-565.6 (10
00-1050) 0.7-1.2
1M Small 587.8-615.6 (1090-1140
) 1.0-3.0 no yield Aluminum web for 20 hours at this temperature is 510 °C'-621,1 °C (9
When homogenized at 50-11500F), cans formed from the web do not produce cracks during ironing, or exhibit unacceptable cylindrical undulations after being hand-twisted. .

According to the present invention, a) after the cold rolling/recycle-recrystallization heating process, the wave is reduced to the level required to make the deep-drawn, wall-ironed container commercially acceptable.

5 aluminum alloy material is manufactured by continuous strip casting and, after homogenization according to the aforementioned parameters, has a thickness of 25.4 millimeters (1 inch) -1, and typically approx. A cooled rolled web having a thickness of 6.35 mm ([J, 25 in.) to 12.7 mm (0.50 in.) is subjected to a first cold rolling process, resulting in an overall dimension of approx. 25% or more, preferably about 5%
The pressure is reduced from 0 to about 75%. Thereafter, the cold rolling tunnel is heated to the recovery temperature level.

As used in the art, the term "temperature" refers to the temperature at which the rolled metal is heated without forming a new grain structure (softening temperature).600
For 4 types of aluminum alloys, the recovery temperature is 148.9
℃ (JO'F) to approximately 287.8°C (550°F)
) is the Xi1Σ enclosure. After the first cold rolling, the cold rolled web recovery temperature ranges from 176.7°C (50'F') to about 260°C (50'F') in about 2 to 6 hours.
00°F), preferably about 21°C in about 2 to 4 hours.
8.3°C (425°F) to 246, V'0 (475'
F)-1: So.

After being heated at the recovery temperature, the heated web is cooled to ambient temperature and subjected to a second cold rolling process, which reduces the overall thickness of the web by at least 10%, preferably about 10 rolls). Press down to

As will be shown hereinafter, heating to the Webke temperature halfway between the 12 cold rolling cycles is important in reducing the selvage properties of the aluminum sheet.

After the second cold rolling process, the temperature of the cold rolled web is raised to the "ladder temperature" level.

The term "1 recrystallization temperature" as used in the art means the temperature at which a rolled metal web completely forms a new grain structure and simultaneously softens. In the case of the 6004 alloy, the grain structure changes to a generally elongated or even-axis structure when the alloy is heated to the crystallization temperature.

In the practice of the present invention, the recrystallization temperature is about 615.6°
C (600,'F') to approximately 482.2°C (900°
F) the temperature is heated for about 1 to 4 hours, preferably from about 700'F to about 426
．． Heat at a temperature between 7°C (800'F) for about 2 to about 6 hours.

After being heated at the recrystallization temperature for a predetermined period of time, the crystallized round glass is cooled to atmospheric temperature and then cold rolled, for example, by at least about 50%, preferably from about 60 to about 90%. and the dimensions dictated by the performance requirements of the can, e.g.
．． It is said to be 30 mm IJ (0,012 inch) and 67 mm (I3.0145 inch) and H19 temper.

To reduce the ear wave occurrence defect to a certain degree, the aluminum web is heated to a second recovery temperature, or the second recovery heating is performed between the second cold rolling process and the recrystallization heating process.

The second recovery heating is approximately 232.2°C (450'F').
) and 21:l 7. from about 0.5 to about 6 hours at a temperature between 550'F' and preferably about 246.1
°0 (475°F) to 273.9°C (525°F)
for about 0.75 to about 1.25 hours.

When performing the second recuperation heating, the web may be cooled to room temperature between the second recuperation heating step and the recrystallization step. Recrystallization heating is preferably performed by directly heating from the second recovery temperature to the recrystallization temperature without cooling to room temperature.

Furthermore, to consistently reduce ears, it is advantageous to cool after the homogenization process according to the invention in web-controlled stages, i.e., at a cooling rate of 41.7°C (75°F) per hour. It turned out that. Preferred cooling 11] Oral sequence is summarized as follows.

Cooling temperature range Time to reach low temperature Average cooling rate °C
('F') (hour) °C/hour (°
F/hour) 593.3-482.2 (110[J-';'
00) , 4.0 27.8 (50) 4
82.2-398.9 (900-750) 2
．． 0 41.7 (75) 398.9-191J
, 6 (750-375) 12.5 16.
7 (O) In the practice of the present invention, a preferred aluminum alloy is a 6004 aluminum alloy containing chromium with a weight ratio of +J, 1, -0.4. When processed into two-piece deep-drawn and wall-ironed cans, the sheets formed from the chromium-containing aluminum alloy 3004 exhibit an increased level of buckling strength, i.e., the ability of the can to withstand high internal pressures without bottom bowing. shows.

The preferred chromium-proprietary aluminum alloy 6004 in the practice of this invention has the following range of components by weight: about 0.5 to about 1.5 parts magnesium, about (1
, 5kr) about 1.5% 0)-qkang, about 0.1 to about 1.0% iron, about 0.1 to about 0.5% silicon,
0 to about 0.25% zinc, 0 to about 0.25% copper,
About 0.1 to about 0.4% chromium, the balance being aluminum and female elements and impurities.

For the desired processing of a sheet formed from chromium-proprietary aluminum alloy 6004, it is essential that the material be rolled for at least 50% in the recrystallized state. The seat in this state is -2,80CJkg/Cr
rL2 (40,000pei) to 3+150k
S//cmt" (45, (100psi) 0) range tensile N yield % degree, 50.8 mm IJ length sample 1j11.l The total elongation is 1.5% or more. Sheet 2,8ooku 2 (40,000
psi ) to 3.150! $/c+? (45,
000 psi) is the tensile yield strength when the Hamura is squeezed,
When made into a two-piece soft drink container with wall ironing, it was found to correspond to a can crimp strength of less than 6.86 kg/crn2.

The improved physical properties imparted to Alloy 6004, particularly the high tensile yield strength achieved by containing about 0.1 to about 0.4% chromium by weight, are completely unparalleled based on the prior art. This was not expected.

Thus, U.S. 11 permit No. 4,111,721,
It is taught that additives of 3004 metallurgy, such as chromium, have a profound effect on the size of the internal particles of the metal in the alloy, and therefore should be limited to a very small amount, about 1/several hundred thousandths of a percent by weight. U.S. Pat. No. 3,834,900 states that the presence of chromium in strip cast aluminum alloys should be minimized, and should be limited to less than 0.001% by weight in order to prevent defects in tin construction. I teach.

The composition and processing limits according to the present invention were determined by the composition and processing limits of sheets prepared from continuous strip cast alloys modified according to the present invention.
f: Must be followed in detail to achieve the high tensile yield strength physical properties required for characterization. Strict adherence to the chromium content in the alloy is important to the practice of this invention. For example, the highest levels of chromium content in earthworks can cause problems such as breakage during can formation. If less than about 0.1% chromium, by weight, is included in the alloy, the tensile yield strength of sheets drawn from continuous strip cast alloys will be lower than the minimum requirements for soft drink performance of the chromium-containing alloys of the present invention. When converting the components into sheet I by strip gearing, the aluminum and alloy components are charged into a molten 9.r furnace, from which the alloy flows to conventional s) IJ casters, which The length is 25.4 mm (1 inch) or less, preferably, the size is less than 6
．． 65 mm (0.25 inch) to 12.7 mm (0
, 50 inches). The strip cast web is formed into a sheet with non-galling, low earing, and high strength properties by employing the homogenization and cold rolling/annealing process of the present invention.

For a more complete understanding of the invention, reference may be made to the following examples of the invention.

Example ■ Aluminum Association standard (Alum: lnum As5o
Specification ) 30
A series of strip cast aluminum alloys containing various aluminum components within the range of No. 04 aluminum alloys were deep drawn and evaluated for use in the manufacture of can bodies by wall ironing. The composition of the alloy is summarized in Table 1.

Table 1 Alloy 1 1.07 0.94 0.32 0.22
0. IJ6 - Alloy 1 [1,141,120,230,
280, U2 0.11 alloy 11 1.10 1.
08 0.22 0.30 0.02 -Alloy IV
1.03 1. Ofj O,410,210,05
- Pieces of cast aluminum strip 12.2 mm (0.48 in.) thick, 0.3 m (1 ft.) wide and 0.9 m (3 ft.) long, are placed in a furnace in a nitrogen atmosphere. 590°C (10°C) and rapidly raise it to the desired temperature
94°i? ) and 610° C. (1130 uFI) for 10 to 40 hours. The strip was then removed from the oven and cooled to ambient temperature by blowing compressed cold air onto the strip. The homogeneous conditions used in the series of tests are summarized below in Table H.

Table II Homogeneous conditions Temperature Holding time A 6
10 (1130) 30B 600
(1112) 350 590 (10
94) 40D 596.3 (11
00) 10 The cooled strip is 66 to 75% (4,06 mm - 6,05 mm = 0.
160-[3,12[] It was rolled through a series of buses using commercial rolling equipment until a reduction in the range of 4 inches was achieved.

A first recovery temperature is applied to the rolled-down stub IJ tube, and the strip is preheated to 232.2°C (450'l?).
The sample was placed in a heated oven for 6 hours, then removed from the oven and cooled to room temperature.

After the first cold rolling and recovery temperature treatment, the strip has a thickness of 10-25% (3.05 mm = 0.12
A second cold rolling was performed by successively passing through a pair of reduction rolls until the material was rolled down to 0 inches).

After the second cold rolling, the strip was rolled at 260 °C (50
0'F) for 1 hour, then 426
．． Annealed for 2 hours at a recrystallization temperature of 7°C (800'F).

The series of cold rolling/recovery-recrystallization (annealing) conditions applied to the IJ tube are summarized below as shown in Table 3.

For control purposes, the cold rolling/annealing conditions of Example I were repeated except that no recovery temperature heating was performed between the cold rolling and recrystallization steps. These contrasting conditions are marked r CI J
and "C2" and summarized as shown in Table 3.

The recrystallized strip is cooled to ambient temperature and then S) l) The horn is reduced to a thickness of approximately 88% (H19 temper) from 0.34 mm (0, [ ] 1134 inches to 0
．． The strip was hardened by successively passing it through a commercial rolling mill until it was 5-8 mm (0.0148 inches) thick.

The H19 tenba strip, when examined by backscatter scanning electron microscopy, has an intrametallic particle size in the range of 1 to 3 microns and exhibits no galling when the strip is subjected to wall icing conditions for can manufacturing. It was found that this shows that.

In order to investigate the degree of ring-shaped ears that occur when strips are subjected to drawing operations for can manufacturing, a diameter of 55 mm.
Cut from a 9 mm (2.2 inch) round blank H19 cured strip and reduce the diameter by 69 inches to 53.
5 mm) (1.32 inches) It was deep drawn into a shallow cup shape in diameter. The tool used to deep draw a 0.64 mm (0.0155 inch) sheet had a 6.5 inch positive air gap of 0.013 mm (0.00 mm) between the punch and die walls.
05 inches). This standard test, which serves as the deep drawing step of the can manufacturing process, typically requires a die gap of less than 5% and a diameter reduction of 39%. For each test, the drawing speed and the drawing pressure of the blank were adjusted to obtain a chip without breakage or wrinkles.

Tables ■ and V below summarize the results of ear development tests using strips with the alloy composition shown in Table I subjected to the homogenization and cold rolling/burning conditions described in Tables ■ and ■. It is. The results for each ear development test represent the average of 6 tests.

The results of earing tests on aluminum strips subjected to contrasting cold rolling/annealing cycles C1 and C2 are summarized in Table v1 below.

Referring to the selvage data summarized in Tables ■ and V and comparing these data with the selvage data of comparable Table Vl, it is found that the aluminum strips processed by cold rolling/annealing cycles 1 and 2 It is immediately apparent that the ear occurrence rate is lower when compared to comparable cold rolling/annealing cycles C1 and 02. These data indicate that cold rolling/annealing cycles 1 and 2, which include one or more recovery heating steps before recrystallization heating, are different from cold rolling/annealing cycles 1 and 2, which include one or more recrystallization steps, but without recovery heating steps. It has been shown to be more effective than C1 and C2 in otogenetic scarcity. Cold rolling/annealing cycle 1 showed superior ear reduction compared to cold rolling/annealing cycle 2, with cycle C1 having a lower second rolling reduction (10%) than cycle 2 (25%). )
, it has been shown that a lower pressure (1095) in the second round is better for reducing ear formation.

Example ■ The thickness after applying the heating process according to the present invention is 12.7 mm (0.
The method of Example I was repeated, except that the heating and cooling conditions were carried out as would be expected in a commercially produced 10-15) inch coil of continuous strip cast aluminum alloy of 0.50 inch). The programmed heating and cooling sequence outlined in the preferred embodiment section was used to achieve strip homogenization in the coil demonstration test. The times and temperatures used in the heating and cooling sequences are summarized in Table 1.

The homogenized S) IJ tube was then cooled in the following order according to Table Vll.

610 to 593.3 (1130 to 1100) 0
．． 6596-3 to 482.2 (1100 to 900
to) 4.0482, 2 to 398.9 (900 to 7
50) 2.0398, 9 to 190.6 (750 to 675) 12.5190, the furnace was closed at 6°O (375°F) and allowed the strip to cool to room temperature.

The cooled strip was then cold rolled/annealed as in Example I using the cold rolling/annealing conditions summarized in the table below.

For control purposes, the cold rolling/annealing conditions shown in Example 1 were repeated except that no sympathy temperature heating was performed between the cold rolling reduction and recrystallization steps.

This control condition is designated by the symbol C3 and is summarized in Table ■ below.

Heating and cooling conditions expected to occur in commercial coil processing were used in the valley recovery and recrystallization process. These conditions are set out in the table (■) below.

The cooled, recrystallized strips listed in Table 1 are cured to ki 19 tenths and have a thickness of 0.64 (0.
,0134 inch) to 0.376 mm ([J,014 inch)
8 inches).

) 119 tenba strips were inspected with a scanning electronics 12i mirror using the backscatter method and found that the size of the particles within the metal was in the range of 1 to 6 microns, and the strips were subjected to wall ironing for can manufacturing. It was shown that no edge galling occurred.

The results of ear development tests using strips treated with the homogenization and cold-pressing/annealing conditions described in Tables V111 and 1 and containing the alloying components listed in Table 1 are summarized in Tables X-XIIIK below.
We have a friendship agreement. Each otogenetic test represents the average of 6 tests.

Can it be compared? The results of the selvage test on aluminum strips subjected to 8-hour pressure treatment/annealing cycle C3 are shown in Table XI below.
VK summarizes.

Table X Otogenetic Test I G O, 351 (oral, (
J138) 3.12II G
O,36ro (0,0143)
3.12I C+ 0.356 (0
,0140) 2.67 Table M Ear development test results I F 0.3S8
(0,0163) 4.811f
F O,353([,1,[j1
39) 4.3ro11t Tj'
[J,,15bl (0,L1138)
4.65 I G O, 356 ([J
, LIMU) 4.28If G
0.361 (0, (J142) 3.36
Ill G O, 358 ([J, 01
41) Table 4.24 Ears generation test results I P 0.356 (0,0140
) 4.36If F 0.353
(0,0139) 4.20m h″
0.325 (0,0128) 5.74
1 GO, 345 (0,0136)
4.28II G O, 351 (L
l, 0138) 3,761, G
O,353 (0,0139) Table 4.14 Xi Ear development test results I E 0.353 (0,013
9) 3.98 II k O, 35
3 (0,0139) 3.98111 K
O, Ro 56 (hada old 40) 4.4 (J table
XIV Ear development test results I F O, 332 (0,0131)
4.66II F 0.345
(0,0136) 3.77111, F
D, 338 ([h0133) 5.9
91 (+0.348
(0,0137) Ro, 86II G
O,353' (0,0139) 4. b
9III G O, 34Ll ([J
, 0134) 4.87 & cold 1iJJ pressure treatment/g13
It is readily apparent that ear development is most reduced when using Blunt Cycle 5.

Cold EI rolling/annealing cycle 6, which is the same as cycle 5 but using a 25% second generation pressure iris instead of 10%, also reduces ear formation or A second cold compaction of 10 buns is shown to be more beneficial in reducing ear development than that achieved using cycle 5.

Cold rolling/annealing cycle 7, which utilizes one recovery heating and one recrystallization heating, does not achieve the same level of ear reduction as cycle 5, but cold rolling/annealing cycle C3, which uses one recrystallization Compared to chemical heating, it is superior in reducing ear formation.

The dual recovery heat/recrystallization heat of cycle 8 reduced ear development when compared to control cycle C3, which is not advantageous over cycle 5 with only one recrystallization heat.

EXAMPLE A strip cast aluminum alloy was prepared having an alloy composition according to the invention, designated by the symbol "I", and an alloy composition designated by the symbol rAJ and having alloy constituents varying within the range of the 3004 standard. These alloys were then evaluated for use in making deep drawn and wall ironed can bodies. The ingredients of the alloy are summarized in Table XVK below.

Table XV Alloy 1 1.14 1.12 0.23 0.28
0.02 0.11 Alloy A11.07 (J, 94
0,32 0.22 0.06 -Alloy A2 1.
10 1.08 (J, 22 0.30 0.02
- Bank length 12.2 mm (0.48 inches) and width 6
A cast aluminum strip 0 cm (1 ft) long or 90 cm (6 ft) long is placed in a furnace with an atmospheric atmosphere.
590°C (1L 194°F) to 600"C (111
The mixture was heated at homogenization temperatures ranging from 2'F) for 10 to 40 hours. Thickness: approx. 12.7 mm (0,0 inch)
A commercially produced 10-15 ton coil of continuously produced aluminum alloy strip is suitable for homogenization and when treated with the programmed heating and cooling procedure outlined in the preferred embodiment of this patent application. Homogenization of the strips was performed using possible heating and cooling conditions. The rt1 and temperatures used in this heating and cooling procedure are summarized in Table X■.

Table XVI A 600 (111,2) 35
35B 590 (1094) 40
400 590 (1094) 10
The homogenized strip according to the conditions listed in Table XVI was then cooled in the following order:

610 maybe 593.3 (1130 to 1100)
0.6596.5 to 482.2 (1100 maybe 900) 4.0482.2 to 398.
9 (900-750) 2.0398.9-190.
6 (750 to 375 > 12.5190
．． The furnace was closed at 6°C (375'FI) and the strip was allowed to cool to room temperature.

The cooled strip is reduced using a commercial sander until it is reduced to a thickness ranging from 66 to 75% (4.06 mm = 0.160 inch to 3.05 mm = 0.120 inch). Rolled through successive passes.

In the first series of cold rolling/recovery-recrystallization heats, a first recovery temperature is applied to the reduced strip (C66-72%), and the strip is heated to 232.2°C (4
50°F) and held there for 6 hours. After the first cold rolling/recovery temperature treatment, the strip is then reduced in thickness by 10-25% (3.05 mm = 0.5 mm).
The strip was cold rolled a second time through a pair of rolls successively to a reduction of 1211 inches (1211 inches).

The outer strip subjected to the second cold rolling was rolled at 260°C for 1 hour.
A second recuperation heat of 500"F was performed, followed by heating to a recrystallization temperature of 800'F for 2 hours.

In the first change, the second cold rolling was eliminated, and the first
The first series of cold rolling/recovery-P+ □crystallization heating was changed by performing recrystallization immediately after the second recovery heating. In the second change, post-heating was eliminated,
Immediately after cold rolling, crystallization was performed.

The cold rolling/annealing conditions applied to the series of strips are summarized in Table XVII below.

Heating and cooling conditions that would be expected in commercial coil processing were used during each of the recovery and recrystallization processes. These conditions are summarized in Table XVIll below.
It is summarized in.

Table ■■ 1 4 6
- -24 6
- -3'
5 4104
5 4
55-
7 10 Second Recovery Second (B) Recrystallization 190. ,! S°C 411 411 5-- 411 The recrystallized strip is cooled to room temperature and then the strip has a thickness of about 88% ()119 temper);
0.338 mm (0.0133 inch) to 0.67.
The strip was cured by successively passing it through a commercial rolling mill until it was rolled down to 6 mm (J, 0148 inches).

) i19 Tenvers) When the IJ tube was examined using a backscattering scanning electron microscope, the size of the internal metal particles was in the range of 1 to 6 microns, and no galling occurred even when the walls were ironed for can production. It turns out that this is an indication that it will not.

In order to investigate the level of ear formation that is expected to occur when added to IJ tubes (pulling work for can manufacturing)
Diameter 50.8 mm (2,
20 inches) circular blank, resulting in a 69% reduction in diameter to create a 33.53 mm 6.5% positive void (0,0127 mm = 0.0005 inch). Met.

A die void of 5% and a diameter reduction of 39% are typically required for standard testing for ear development testing, which simulates the deep drawing process during the can manufacturing process. The speed of making the tip and the pressure of squeezing the blank were adjusted for each test to obtain a tip that was free of breakage and wrinkles.

Table XIX-
XXI K summarizes. Each result of the ear development test is 6
Shows the average of batch tests.

The tensile strength mechanical properties of the H19 geometalized strip, namely yield strength, ultimate strength and total tensile elongation, are as low as 50.
ASTM Test Method No. E-8 (ASTM Te5t Pro-ce) using 8 mm (2 inch) specimens
Determination was made by dure Number E-, 8). The results of each physical property test are as follows:
The average of a total of six tests, three times in the horizontal direction and three times in the horizontal direction, is shown. The results of these tests are also recorded in Tables X-E below.

Before that, :i,'ll:+i6 strip cast aluminum alloy 3U [J4 also formed can wall JHJ strength is H
The tensile force of l・9 tempered sheet σ1 (It is recognized that there is a close relationship -f with the strength of the gods and Buddhas. n'J ML wall/IIf
The relationship between strength and tensile yield strength is shown in Table XXn K below.
summarized.

Together with the overall elongation, the tensile yield strength is a measure of the formability of the sheet. For can body production: I%l, the sheet must have an ultimate tensile strength of at least 2940 Ry/cm2.

The overall tensile elongation, previously determined as a+1+, is a measure of malleability.

To be suitable for can manufacturing, the sheet must have a total tensile elongation of at least 1.5%.

Table W Relationship between tensile yield strength/J buckling strength (Tensile yield strength KkgAL2 (es i , i Q ” ) Buckling strength kin” T'f5 s i ) 2541 (36
,3) 5.86(83,7)2576(3
6,8) 5.96(85,2)2618(
37,4) 6.20 (88,5) 2646
(37,8) 6.36 (90,9)267
4 (38,2) 6.27 (89,5) 27
09(38,7) 6.48(92,5)2
772C59,6) 6.58C94,0)
27B6 (39,8) 6.79C97,0
)2835(40,5) 6.90(98,
5) 28,! 12 (40,6) 6.95C
99,0) 2891 (41,3) 7.00
(100,0)2989(42,7) 7.
07 (101,0) 2975 (42,5)
7.14 (102,0) Average 2 of 6 tests in total, 6 times in the longitudinal direction and 6 times in the transverse direction with respect to the main rolling direction.

For a sheet 10.343 mm (0.0135 inch) thick, 0.343 mm (0.0135 inch) thick sheet. [] 0.07 kg/G7A2 for a thickness change of 0.025 mm (0,0001 inch)
Table XIX of buckling strength measured by adjusting at a rate of (1 psi) For reference, by incorporating 0.11% chromium into aluminum alloy 3004, the tensile yield strength is increased by 1, and therefore there is no adverse effect on the can formability of the sheet formed from the alloy. It is immediately obvious that the buckling strength should be increased accordingly without affecting the shadow #.Thus, the tensile yield strength of Alloy I is 2800 kP.
/12 (40,0,00psi) tx overall upper circumference, buckling strength 'Y6.86kg/am2 (98psi
). Similarly, the ultimate tensile strength of alloy 1 is above the minimum requirement of 1.5%'Y.

By comparing the data listed in Tables XX and XXI with that listed in Table
It can be readily seen that the conventional 6004 alloy, such as No. 2, has a significantly higher strength than Alloy I when processed under the same conditions as Alloy I.

Example 1 ■ A second series of strip cast aluminum alloys was evaluated for use in the manufacture of drawn and wall ironed can bodies. The ingredients of the alloy are summarized in Table XX■ below G1.

Table XX■ Alloy composition (weight) Mg Mn Fe Si Zn Cr C
u alloy A 1.131.150,460,170.
070.260.15 alloy O,900,960
,350,130,060,250,15 alloy
1.051.030.49 o, 15) 0.070.
The alloy was impregnated with copper to simulate aluminum can scrap containing 0.1 to 0.2 inches of copper at a heavy discharge ratio of 200.15.

The aluminum alloy Hunter type (Hunter t,
6.6 mm (
0.26 inch) thick sheet,
It was wound into a coil of 2.25 mm (5000 volts). The coil was allowed to reach room temperature for 48 hours.

Next, the cooled coil was placed in a furnace and homogenized in a nitrogen atmosphere. The coil heats up to 580″C (107°C) in 12 hours.
The coil was then heated in the furnace to 200"F' (96.3°C) for 62 hours. cooled down.

The cooled coil was removed from the furnace and allowed to cool to room temperature for an additional 48 hours.

Once cooled to room temperature, the coils are subjected to a first cold rolling/recovery temperature treatment, and the cooled coils are each coated with a thickness ranging from 86% to 85 mm. 0.052 to 0.059 inch)
It was rolled in a series of passes using a commercial rolling mill until it was rolled.

The thinner coil is then subjected to the first recovery temperature treatment,
The coil was put back into the furnace and heated up to 232.20 (450
'F) ± 1.67°C (3'F), held at that temperature for 4 hours, then heated to 1.48'C for 9 hours.
The coil was then cooled in the furnace to 600"F. The coil was removed from the furnace and cooled to room temperature over the next 48 hours.

After the first rolling/recovery temperature treatment, each coil has a thickness of 25% (0.991mm = 0.0mm).
It was subjected to a second cold rolling by passing successively through a pair of rolling rolls until it was rolled down (from 39 in. to I, IIA mm-U., 044 in.).

After the second cold rolling, the coil is returned to the furnace and 3
A second recovery heat treatment is performed by raising the furnace temperature to 260°C (500°F) in an hour, and at that temperature 1.5
Time held. The coil heats up to 426.7℃ (80℃) in 6 hours.
It was annealed at the recrystallization temperature by raising the furnace temperature to 0° F. and held at this temperature for a period of time. The coil was cooled in the oven to 148.9°C (300'l?) for 14 hours, then removed from the oven and cooled to room temperature for the next 48 hours.

The recrystallized coil is then rolled through a commercial rolling mill until the coil thickness is reduced by approximately 65% to 67%, or 0.343 mm (0.0135 inch). Roll hardening was performed.

The roll-hardened coils were then run on a commercial drawing and wall ironing line to form two-piece aluminum soft drink cans, with approximately 5,000 cans produced from each coil. No galling was observed. It wasn't. Ear occurrence was 2.0.
It was 2.6%.

The cans were rated H' for buckling strength, ie, the ability to withstand high internal pressures without buckling.

1. The buckling strength is reduced by applying pressure 1" in the wall ironed can and then gradually increasing the pressure until the bottom of the can deforms and bulges, i.e. buckles.
1 determined. Next, the pressure when the bottom part buckles is the actual force I (
It is called intensity -f'. To be accepted as can body material,
The canister is made of alloy sheet and has a capacity of at least 6.5 kl.
? / Cm2 (90 psi).

The average buckling strengths of cans made from Alloys A, B and C in the manner described above are recorded in Table XXIV below.

Table XX■ Alloy Buckling strength 9/Cm2 (p B i ) A 6.72 (96) B
6.16 (88) C6, 58 (94) Agent Asamura Akira 376

Claims (1)

Claims: (1) In a method of making an aluminum alloy strip system suitable for the manufacture of deep-drawn and wall-ironed products, the aluminum The alloy is continuously cast; the strip is heated to about 510°C (950°C) for up to 50 hours.
'F) to a temperature of about 621.1°C (1150°F); the homogenized strip is cold rolled to a reduced thickness (by 25%); vinegar)
The IJ tube was heated to approximately 176.7°C (350°F) and 287°C.
Heat to a recovery temperature of between 8°C (550°F);
Perform cold rolling for 3 times; cold rolled strip approximately 3 times
15.6°C (600°F) and approximately 482.2°C (900'
F ) (')lfJJ O) heating to a recrystallization temperature; then cold rolling said recrystallized strip to a final dimension with a total thickness reduced by at least about 50%; A method for producing an aluminum alloy strip material having the following characteristics. .7 millimeters (0.50 inches). (3) The method of claim 1, wherein the strip has a thickness of between about . 537.8°0 (1000'F') and approx.
At temperatures between 96.3°C (1100°F') approximately 10
(4) A method according to claim 1, characterized in that the first cold rolling is homogenized for about 25 hours. 5. The method of claim 1, wherein the strip is heated to about 400'F' ) and about 246
．． A method of making an aluminum alloy strip characterized by heating at a recovery temperature of between about 1°C (475'F') for about 2 to about 6 hours. (6) The method of claim 1m, wherein the strip is heated to about 218.3°C (425°F) and about 246°C.
A method of making a strip of aluminum alloy, characterized in that it is heated at a recovery temperature of between 1°C (475°F). (7)% In the method of claim 1, the cold rolled strip is heated to about 700°C.
(8) A method of forming an IJ tube in an aluminum alloy, characterized in that the aluminum alloy is heated to a recrystallization temperature between Ei') and about 454.4°C (850°F). A method according to claim 1, characterized in that the second cold rolling reduces the thickness by about 10 to 25 mm. In the method according to scope 1, after the second cold rolling and up to the recrystallization temperature.
Before heating the IJ tube, it is heated to a second recovery temperature,
The second recovery temperature is in the range of about 232.2°C (450°F) to about 287.8'C (550uF'0), and the heating is for about 0.5 to 6 hours. How to make aluminum alloy strips. (+, 0) Scope of Interest In the method described in paragraph 1, the recrystallized strip is cold rolled to a total thickness reduction of about 85% to about 90% of its final dimension. A method of making an aluminum alloy strip characterized by.圓 In the method according to claim 1, the aluminum alloy conforms to the Aluminum Association standard (Aluminum Association standard).
m As5ocation 5specificati
A method of making a strip of aluminum alloy, characterized in that it is a 6004 aluminum alloy. (12j%) In the method of claim 1, the aluminum alloy has a weight ratio of about 0.5 to about 1.5%.
% magnesium, about 0.5% to about 1.5% manganese by weight, about 0.1% to about 1.0% iron by weight, about 0.1% to about 0.5% by weight Silicon, k, about [ ] in weight ratio, 0 or about 0.25% Zinc, about 0.0 in weight ratio
03) Claims In the method of scope 1, the cold-rolled S) IJ tube has a diameter of about 176 mm prior to recrystallization.
．． 7℃ (350'F') and approximately 287.8℃ (55Ll''
F) aluminum alloy steel strips characterized in that they are heated for at least 2 hours to the recovery temperature of Q4) The method of claim 1, wherein the first cold rolling reduces the thickness by about 50 to about 85 degrees. Method. (I5) In the method according to claim 1,
06) Process according to claim 1, wherein the second cold rolling reduces the thickness by about 10 to 5 [[[l/l''j]. In this case, the recrystallized IJ tube has a total thickness of about 5 mm.
A strip of aluminum alloy, characterized in that it is cold rolled to a final dimension reduced by about 90% from 0 to about 90%. A method of making an aluminum alloy strip, the chromium content being in the range of about 0.11 to about 0.25. (18) In an aluminum alloy sheet made from continuous strip cast aluminum alloy up to 25.4 mm (1; 1 inch) thick, with a thickness of 0.206 mm (0,008 inch) to 0.46 mm IJ (0,0
1 inch), the thickness of which is reduced by at least 50% by cold rolling to provide high temper, about 0.5 to about 1.5 parts magnesium by weight and about 0.5 to 1 part M by weight. .5% manganese, about 0.1 to about 1.0% iron by weight, ■ (about 0.1 to about 0.5% by weight)
of silicon, from about 0.0 to about 0.25% zinc, from about 0.0 to about 0.25% zinc, from about 0.1% to about 0.25% copper, and from about 0.1% to about 0.25% i-. An aluminum alloy sheet characterized by containing chromium 4. (1!++ Claim 18) In the aluminum alloy sheet according to J8+, the hard tempered core has a hardness of at least 2800 kVcm2 (40,000p
si) and a tensile yield strength of at least 2940 kg
An aluminum alloy sheet having an ultimate tensile strength of /C1rL2 (42,000 psi) and an overall tensile elongation of at least a factor of 1.5. (20+ An aluminum alloy sheet having at least 50% cold rolled defects in the sheet according to claim 18. (21) A sheet prepared by the method according to claim 1. 22) In an aluminum alloy suitable for the production of can material, about [1.5 to about 1.5% by weight of magnesium, about 0.5 to 1.5% by weight of manganese, about 0.1 to about 1.0% iron, about 0.1 to about 0.5% silicon by weight, about 0.0 to about 0.0% by weight silicon.
25% Zinc, from about 0.0 to about 0.25918 by weight
of copper and about 0.1 to about 0.4% chromium by weight.