WO2007052416A1 - Tole en alliage d’aluminium laminee a froid pour bouteille canette ayant une excellente capacite de formation de col et procede de production de la tole en alliage d’aluminium laminee a froid - Google Patents

Tole en alliage d’aluminium laminee a froid pour bouteille canette ayant une excellente capacite de formation de col et procede de production de la tole en alliage d’aluminium laminee a froid Download PDF

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Publication number
WO2007052416A1
WO2007052416A1 PCT/JP2006/318241 JP2006318241W WO2007052416A1 WO 2007052416 A1 WO2007052416 A1 WO 2007052416A1 JP 2006318241 W JP2006318241 W JP 2006318241W WO 2007052416 A1 WO2007052416 A1 WO 2007052416A1
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Prior art keywords
cold
dispersed particles
aluminum alloy
rolling
rolled sheet
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PCT/JP2006/318241
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English (en)
Japanese (ja)
Inventor
Katsura Kajihara
Kiyohito Tsuruda
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Kabushiki Kaisha Kobe Seiko Sho
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Application filed by Kabushiki Kaisha Kobe Seiko Sho filed Critical Kabushiki Kaisha Kobe Seiko Sho
Priority to EP06797959A priority Critical patent/EP1944384A4/fr
Priority to US12/090,879 priority patent/US20080302454A1/en
Priority to CA002625098A priority patent/CA2625098A1/fr
Publication of WO2007052416A1 publication Critical patent/WO2007052416A1/fr

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
    • C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/047—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with magnesium as the next major constituent

Definitions

  • the present invention relates to an aluminum alloy cold-rolled plate (bottle can material plate) having excellent neck formability of a bottle can as a can body material for a bottle can (beverage can).
  • the aluminum alloy cold rolled sheet referred to in the present invention is a rolled sheet (cold rolled sheet) rolled through hot rolling and cold rolling.
  • the aluminum alloy is also referred to as an A1 alloy.
  • a two-piece aluminum can obtained by seaming a can body and a can lid (can end) is widely used.
  • the body is formed by subjecting a predetermined aluminum plate to can body forming such as cutting and DI forming (drawing and ironing), and then necking the body.
  • the mainstream is one with a smaller end diameter than the body diameter (hereinafter referred to as a two-piece aluminum can).
  • JIS3004 alloy and 3104 alloy which are A1-Mg-Mn alloys, have been widely used!
  • This JIS3004 alloy and 3104 alloy are excellent in ironing workability, and show relatively good formability even when cold rolled at a high rolling rate to increase strength. It is considered preferable.
  • bottle cans! that have a body, a mouth, and a screw cap!
  • the drawing ratio of the diameter of the mouth portion to the diameter of the body portion is larger than that of the two-piece aluminum can, wrinkles (cracks) and cracks are more likely to occur during neck processing.
  • a three-piece bottle can (including a screw cap; hereinafter referred to as a three-piece bottle can) and a two-piece bottle can (including a screw cap). 2 piece bottle cans).
  • the three-piece bottle can is generally manufactured by applying a part of the conventional two-piece aluminum can manufacturing method. That is, as disclosed in Patent Document 1 and Patent Document 2 described later, first, cutting and DI molding, baking, trimming, printing, baking, and necking (top molding: neck force) are performed on a predetermined aluminum plate. Sequentially applied. In the neck processing, a neck portion is formed on the bottom side portion of the body portion, and then an end portion of the neck portion is opened to provide a mouth portion. The outer periphery in the vicinity of the mouth portion is threaded for screw cap attachment to form a screw portion. After that, the flange portion is formed on one of the opening portions of the body portion facing the mouth portion as a bottom portion, and then the bottom portion is tightened to form the bottom portion.
  • the manufacturing method of the two-piece bottle can first includes a cutting on a predetermined aluminum plate A to form a body portion of the bottle can. DI molding is performed to form the body and bottom. Next, a neck neck or spin neck force check is applied in the vicinity of the opening of the body to form a neck, and the opening is used as a mouth. Thereafter, a screw cutting portion for attaching a screw cap is provided on the outer periphery in the vicinity of the mouth portion, whereby a two-piece bottle can is manufactured.
  • this two-piece bottle can, when the neck portion is formed, the neck portion is formed by performing die neck processing or spin neck processing in the vicinity of the opening portion of the body portion. It is difficult to configure with a large aperture ratio of mouth diameter to part diameter.
  • the mouth portion with respect to the diameter of the body portion is formed by the relatively hard rigidity of the aluminum plate.
  • wrinkles and cracks were likely to occur. Therefore, it has been difficult to form the drawing ratio of the conventional two-piece bottle can with the drawing ratio of the three-piece bottle can.
  • the Mn solid solution amount and crystal grain size of the hot-rolled sheet are controlled within a predetermined range, and the ear ratio of the hot-rolled sheet is stabilized to ⁇ 3 to ⁇ 6%, which is then subjected to intermediate annealing. It has also been proposed that the cold-rolled sheet obtained by cold rolling is made to have an ear rate of 0 to 2% stably (Patent Document 3).
  • Patent Document 1 Japanese Patent Laid-Open No. 2002-256366
  • Patent Document 2 JP 2004-250790 A
  • Patent Document 3 Japanese Patent Laid-Open No. 2003-342657
  • these two-piece bottle cans tend to be smaller and smaller in diameter in recent years, such as mini bottle cans.
  • 2-piece bottle cans such as mini bottle cans, in particular, retort processing
  • the force that increases the tightening load of the cap tends to require strength of the can body that can withstand the increase of the tightening load. For this reason, higher strength is also required on the can material side.
  • the gist of the aluminum alloy cold-rolled sheet for bottle cans excellent in neck formability is as follows: Mn: 0.7 to 1.5% (mass 0 / 0 , the same shall apply hereinafter), Mg: 0.8 to 1.7%, Fe: 0.1 to 0.7%, Si: 0.05 to 0.5%, Cu: 0.1 to 0.6% contains, has with balance of forces Alpha 1 and unavoidable impurities, and, the dispersed particles mosquito ⁇ 300 111 2 per Saizu of 0.05 to 1 111 observed by from 5,000 to 15,000 times the ⁇ tissue Among these dispersed particles, the number ratio of dispersed particles having a size of 0.3 m or more is within a range of 15 to 70% with respect to the total number of dispersed particles. It is assumed that
  • the gist of the manufacturing method of the aluminum alloy cold-rolled sheet for bottle cans excellent in neck part moldability of the present invention is the above gist or a preferred embodiment of an aluminum alloy described later.
  • the ingot is homogenized at a temperature of 550 ° C or higher and then gradually cooled to a temperature range of 450 to 550 ° C at a cooling rate of 25 ° C Zhr or less.
  • 50 to 400 dispersed particles having a size of 0.05 to 1 ⁇ m are observed per 300 / zm 2 as observed by TEM 5000 to 15000 times the plate structure after cold rolling.
  • the number ratio of the dispersed particles having a size of 0.3 m or more in the dispersed particles is to be in the range of 15 to 70% with respect to the total number of dispersed particles.
  • the DI can body of the bottle can is required to be further thinned mainly for the purpose of reducing the manufacturing cost and reducing the weight.
  • it is also strongly required that the ear rate during DI molding is low. If the ear rate during DI molding is lowered, the yield during DI molding can be increased, and furthermore, the can body can be prevented from being broken due to the cutting out of the can body.
  • dispersed particles such as Mg Si present in the aluminum alloy cold-rolled sheet structure are used.
  • the dispersed particles are coarsened to some extent, and then the sizes are made uniform. , Make a certain amount (a certain number).
  • the dispersed particles are coarsened to a certain extent, and the size is made uniform, and a certain amount is present, and is uniform and isotropic in the state of the hot-rolled sheet (direction or anisotropic). Without crystallinity), obtain crystal grains and improve the ear rate of the subsequent cold-rolled sheet.
  • FIG. 1 is a drawing-substituting photograph showing the presence of dispersed particles of an aluminum alloy of the present invention (Invention Example 1).
  • FIG. 2 is a drawing-substituting photograph showing the presence of dispersed particles of the aluminum alloy of the present invention (Invention Example 2).
  • FIG. 3 is a development view of a cup obtained by DI molding a plate material.
  • composition of the aluminum alloy cold-rolled sheet for bottle cans excellent in high-temperature characteristics of the present invention is Mn: 0
  • the composition contains ⁇ 0.6%, the balance being A1 and inevitable impurity power.
  • Mn 0.7 to 1.5%.
  • Mn is an effective element that contributes to improvement in strength and further contributes to improvement in formability.
  • Mn is extremely important because the ironing, neck force, threading, and the like described above are performed during DI molding. It becomes.
  • Mn forms various Mn-based intermetallic compounds such as A1-Fe-Mn-Si-based intermetallic phase.
  • the formability or strength workability during each of the above processes can be improved.
  • the power that emulsion type lubricants are usually used If the amount of ⁇ phase is small, the lubricity is insufficient even when emulsion type lubricants are used. There is a risk of appearance defects such as scuffing and seizure. Therefore, Mn is an indispensable element for generating ⁇ phase and preventing surface flaws during ironing.
  • the Mn content is 0.7% or more, preferably 0.8% or more, preferably 0.85% or more, and more preferably 0.9% or more.
  • the upper limit of the Mn content is 1.5%, preferably 1.3%, more preferably 1.1%, and even more preferably 1.0%.
  • Mg 0.8 to 1.7%.
  • Mg is effective in that the strength can be improved. Furthermore, by including it together with Cu, which will be described later, the cold rolled sheet of the present invention is finally annealed (also called finish annealing. For example, temperature: about 100 to 150 ° C, time: annealing for about 1 to 2 hours), Subsequent canning and soft baking can be suppressed when force baking (baking printing). That is, when both Mg and Cu are contained, Al—Cu—Mg precipitates during baking (baking printing), and thus softness during baking can be suppressed.
  • the Mg content is 0.8% or more, preferably 0.9% or more, and more preferably 1.0% or more.
  • Mg is excessive, work hardening is likely to occur, and formability is reduced. Therefore, the upper limit of the Mg content is 1.7%, preferably 1.6%, and more preferably 1.35%.
  • Mg also affects the amount of Mn deposited and dissolved. In other words, as the amount of Mg increases, the amount of precipitation of the A1-Fe-Mn-Si intermetallic compound phase) is suppressed, and the amount of Mn solid solution tends to increase. For this reason, it is preferable to determine the Mg content in relation to the Mn solid solution amount.
  • Fe has the effect of refining crystal grains, and further generates the above-mentioned A1-Fe-Mn-Si intermetallic compound ( ⁇ phase), which contributes to the improvement of moldability. Fe is also useful in that it promotes Mn crystallization and precipitation and controls the amount of Mn solid solution in the aluminum matrix and the dispersion state of Mn-based intermetallic compounds. On the other hand, if Fe is excessive in the presence of Mn, a large primary intermetallic compound is likely to be generated, which may impair the moldability.
  • the Fe content can be set according to the Mn content, and the preferred mass ratio (FeZMn) of Fe and Mn is, for example, in the range of 0.1 to 0.7, preferably It is in the range of 0.2 to 0.6, and more preferably in the range of 0.3 to 0.5.
  • the lower limit Fe content is 0.1% or more, preferably 0.2% or more, and more preferably 0.3% or more. Further, the upper limit content of Fe is 0.7% or less, preferably 0.6% or less, and more preferably 0.5% or less.
  • Si 0.05-0.5%.
  • Si consists of Mg Si intermetallic compounds and A1-Fe-Mn-Si intermetallic compounds (hyperphase).
  • the Si content is 0.05% or more, preferably 0.1% or more, and more preferably 0.
  • the upper limit of the Si content is 0.5%, preferably 0.45%, more preferably 0.4%.
  • the lower limit of Cu content is 0.1% or more, preferably 0.15% or more, more preferably 0.2%. That's it.
  • the upper limit of Cu content is 0.6%, preferably 0.5%, more preferably 0.35%.
  • examples of the strength improving element having the same effect include Cr and Zn.
  • one or two of Cr and Zn can be selectively contained.
  • the Cr content is 0.001% or more, preferably 0.002% or more, in order to exert the strength improvement effect.
  • the upper limit of the Cr content is 0.3%, preferably 0.25%.
  • the strength can be improved by aging precipitation of Al—Mg—Zn-based particles.
  • the Zn content is 0.05% or more, preferably 0.06% or more.
  • the upper limit for the Zn content is 0.5%, preferably 0.45%.
  • Ti is a grain refinement element. This effect was demonstrated! / Sometimes it is contained selectively. In this case, the Ti content is 0.005% or more, preferably 0.01% or more, and more preferably 0.015% or more. If Ti is excessive, a huge A1-Ti intermetallic compound crystallizes and hinders formability. Therefore, the upper limit of Ti content is 0.2%, preferably 0.1%, more preferably 0.05%.
  • the Ti may be contained alone, but may be contained together with a small amount of B.
  • the B content when selectively contained is 0.0001% or more, preferably 0.0005% or more, and more preferably 0.0008% or more.
  • the upper limit of the B content is 0.05%, preferably 0.01%, and more preferably 0.005%.
  • the elements other than those described above are unavoidable impurities, and in order not to inhibit the above-mentioned plate characteristics, the content should be basically low.
  • the inclusion of up to the upper limit of each element of 3000 series aluminum alloy is permitted.
  • dispersed particles such as Mg Si, Al—Fe—Mn—Si (hyperphase), precipitates
  • Mg Si, Al—Fe—Mn—Si (hyperphase) precipitates present in the aluminum alloy cold rolled sheet structure are roughened to some extent.
  • the size is made uniform and a certain amount (a certain number) is present.
  • a certain amount a certain number
  • the pinning effect of the dispersed particles is alleviated, and uniform and isotropic crystal grains (not having directionality or anisotropy) are obtained in the hot-rolled sheet state, and the ear ratio is improved.
  • the ratio of the number of dispersed particles having a size of 0.3 m or more is set to a range of 15 to 70% with respect to the total number of dispersed particles.
  • the lower limit of the number ratio of the dispersed particles having the above size is preferably 20% or more, more preferably 25% or more, and the range is 20 to 70%, and further 25 to 70%. And is preferred.
  • Figs. 1 and 2 show 10000-fold TEM photographs of the cold rolled sheet structure of the aluminum alloy of the present invention.
  • the dispersed black particles compounds such as Mg Si and precipitates
  • Figure 1 shows the results of Table 3 in the examples described later.
  • Example 1 and FIG. 2 are Example 2.
  • the dispersed particles of the structure of the present invention in FIG. 1 have a larger number ratio of relatively coarse dispersed particles having a size of 0.3 m to 1 ⁇ m with respect to the total number of the dispersed particles. It has been. That is, the number ratio of the relatively coarse dispersed particles is 48% with respect to the total number of dispersed particles. That is, dispersed particles having a relatively large size and uniform size Can be said to be uniformly dispersed.
  • the number ratio of relatively coarse dispersed particles having a size of 0.3 m or more and 1 ⁇ m or less is the total number of dispersed particles. 20% of the existing number. That is, it can be said that dispersed particles of various sizes, such as the number ratio of relatively small dispersed particles, the small size force, and the large size are dispersed.
  • Dispersion particles having a size of 0.3 m or more when the number ratio of the relatively small dispersion particles is larger than that of the structure of the present invention in Fig. 2 or dispersion particles of various sizes are dispersed.
  • the ratio of the number of particles is less than 15% of the total number of dispersed particles, it becomes the same as conventional fine dispersion of dispersed particles.
  • the original soft PFZ force is easily recrystallized, and accordingly, the precipitation zone is also recrystallized to form coarse crystal grains.
  • the cube orientation also tends to develop. Therefore, as in the conventional case, although the average grain size of the crystal grains is small, so-called so-called mixed grains in which coarse recrystallized grains are mixed in part, and the uniformity and isotropy of the crystal grains are lost. Easy!
  • the dispersed particles to be analyzed and measured have a size (center of gravity diameter) of 0.05 m or more as observed by a TEM of 5000 to 15000 times. This is because the presence of dispersed particles of 0.05 m or more greatly affects the moldability as described above, and the dispersed particles of less than 0.05 m have a small influence. In addition, small dispersed particles of less than 0.05 / zm are excluded from the scope of the present invention, because they are subject to large variations in measurement due to this measurement, which is difficult to observe and measure even with TEM.
  • the particle size of the dispersed particles is determined with a transmission electron microscope (TEM) having a plate structure. More Specifically, the specimen at the center of the plate thickness and the upper surface of the rolled surface is mirror-polished, and the structure of the polished surface is 5000 to 15000 times TEM (for example, HF-2000 Field Emission Transmission Electron Microscope made by Hitachi Using a mirror, observe 10 fields of view with a size of about 10 / z mX about 15 m.
  • TEM transmission electron microscope
  • the number of dispersed particles having a size of 0.05 to 1 ⁇ m is counted and converted to the number per 300 ⁇ m 2 .
  • Each measured number of dispersed particles was calculated as an average value in the observation of the 10 fields of view.
  • the number of dispersed particles having a size of 0.3 m or more is set to the above-described dispersion of 0.05 to Lm. Similar to the number of particles. Then, the ratio (%) of the number of dispersed particles having a size of 0.3 / z m or more to the total number of dispersed particles having a size of 0.05 to 1 ⁇ m was determined.
  • the crystal grains of the aluminum alloy cold-rolled sheet are elongated in the rolling direction with an average aspect ratio of 2 or more compared with ordinary equiaxed grains.
  • thermal deformation at the time of coating heat treatment can be suppressed and the strength of the can after heat treatment can be ensured with respect to high-speed heat treatment that has been shortened at a higher temperature.
  • ironing strength is imparted, and formability such as DI molding is secured, and then specified by the present invention.
  • the strength of the can after heat treatment can be secured under the above-described component composition and the solid solution and precipitation state structure described later. This also suppresses thermal deformation during paint heat treatment.
  • the average aspect ratio of the crystal grains is less than 2, it is not much different from normal equiaxed grains, and the above effects are insufficient, so it is not possible to suppress thermal deformation during coating heat treatment and to ensure the strength of the can after heat treatment. .
  • the average aspect ratio of the crystal grains is preferably 2.1 or more.
  • the aspect ratio of the crystal grains is determined by the crystal grain structure of the hot-rolled sheet and the cold rolling rate in the process without intermediate annealing.
  • the upper limit of the average aspect ratio of the crystal grains is determined by the capability limit of the manufacturing process for producing elongated grains such as hot rolling or cold rolling, but the level is about 4.
  • the average external ratio of crystal grains is measured by upper surface observation (polarization observation) at the center in the thickness direction. After tempering (before bottle can molding), the center of the plate in the thickness direction and the upper surface of the rolled surface are subjected to mechanical polishing, electrolytic polishing, and anodizing treatment with Barker's solution, followed by polarization observation.
  • the crystal grain structure is polarized and observed from the upper surface of the central portion in the plate thickness direction of the plate, a difference in black and white appears due to a difference in crystal orientation.
  • the maximum length in the rolling direction and the maximum length in the plate width direction of each crystal grain are measured for the crystal grains in the field where the contour can be clearly observed.
  • the (maximum length in the rolling direction) Z (maximum length in the plate width direction) of each individual crystal grain is calculated as the aspect ratio.
  • X Using an optical microscope with a magnification of 100, the number of crystal grains to be measured is 100, and the average aspect ratio of the crystal grains is obtained from the average value of the aspect ratios of the crystal grains.
  • the average crystal grain size can be obtained by averaging the maximum length in the rolling direction of the individual crystal grains with the 100 measured crystal grains.
  • the A1 alloy cold-rolled sheet of the present invention can be produced without greatly changing the conventional soaking, hot-rolling and cold-rolling production processes.
  • the plate structure after hot rolling and cold rolling is the dispersed particle structure specified in the present invention, and the basic material properties (ear ratio, strength), formability, and ironing workability for bottle can molding
  • Homogeneous heat treatment (soaking) temperature is 550 ° C or higher, preferably 650 ° C or lower. If the soaking temperature is too low, too much time will be spent on homogeneity and productivity will be reduced, and if the soaking temperature is too high, the surface of the lump will swell, so set the soaking temperature in the above range. . More preferable average
  • the heat temperature is 580 ° C or higher (especially 590 ° C or higher) and 615 ° C or lower (especially 610 ° C or lower).
  • the soaking time is preferably as short as possible, for example, 6 hours or less, as long as the soot lump can be homogenized.
  • soaking time is as short as possible to improve the efficiency of soaking process.
  • the cooling rate after the soaking treatment inevitably exceeds the upper limit of 25 ° CZhr.
  • the dispersed particle structure defined in the present invention is not obtained, and dispersed particles having a relatively small number of dispersed particles or a particle having various sizes are dispersed as compared with the structure of the present invention shown in FIG.
  • the number ratio of dispersed particles having a size of 0.3 m or more is less than 15% with respect to the total number of dispersed particles. For this reason, it becomes the same as the conventional fine dispersion of dispersed particles.
  • the soaking process may be performed in a plurality of stages, but at least the cooling rate after the final soaking process is slow cooling like the above cooling rate.
  • Handling of the ingot after completion of the soaking may be performed by hot and rough rolling after cooling and reheating, or by hot rough rolling without cooling excessively.
  • the cooling rate from the soaking process to the hot rough rolling start temperature should be slow cooling like the above cooling rate.
  • the end temperature of hot rough rolling is preferably set to 420 ° C or higher. Further preferable end temperatures are 430 ° C or higher (especially 440 ° C or higher) and 470 ° C or lower (especially 460 ° C or lower).
  • the aluminum alloy sheet that has been subjected to the hot rough rolling is desirably subjected to hot finish rolling as quickly as possible. By rapidly performing hot finish rolling, it is possible to prevent recovery of strain accumulated in hot rough rolling, and it is possible to increase the strength of the cold-rolled sheet obtained thereafter.
  • the aluminum alloy sheet that has been subjected to hot rough rolling is preferably hot-rolled within 5 minutes, preferably within 3 minutes, for example.
  • the finishing temperature of hot finish rolling is preferably 310 to 350 ° C.
  • the hot finish rolling process is a process of finishing a sheet to a predetermined size. Since the structure after rolling is recrystallized by self-heating, the end temperature affects the recrystallized structure. Hot finishing By setting the end temperature of rolling to 310 ° C or higher, the final sheet structure is screened with a structure in which the average aspect ratio is 3 or more and stretched along with the subsequent cold rolling conditions. If the finishing temperature of hot finish rolling is less than 310 ° C, the average aspect ratio is unlikely to increase even if the cold rolling rate of the subsequent cold rolling is increased.
  • the final plate structure becomes a structure stretched in the rolling direction with an average aspect ratio of 3 or more, and coarse Mg Si or the like precipitates, and the dispersed particles defined in the present invention Pair
  • tandem hot rolling mill with 3 or more stands as the hot finishing mill.
  • the rolling rate per stand can be reduced, and strain can be accumulated while maintaining the surface properties of the hot-rolled sheet. Therefore, the strength of the cold-rolled sheet and its DI compact can be increased. It can be further increased.
  • the total rolling reduction of hot finish rolling is desirably 80% or more.
  • the final sheet structure is a structure that is elongated in the rolling direction with an average aspect ratio of S3 or more, and the dispersed particles defined in the present invention. Easy to organize. In addition, the strength of the cold rolled sheet and its DI compact can be increased.
  • the thickness of the alloy sheet after hot (finishing) rolling is preferably about 1.8 to 3 mm.
  • the plate thickness is preferably about 1.8 to 3 mm.
  • the plate thickness is set to 1.8 mm or more, it is possible to prevent the surface properties (seizure, rough skin, etc.) of the hot rolled plate and the plate thickness profile from being damaged.
  • the plate thickness is set to 3 mm or less, it is possible to prevent the rolling rate from becoming too high when manufacturing cold rolled plates (usually, plate thickness: about 0.28 to 0.35 mm). Can reduce the ear rate.
  • the sheet thickness after cold rolling is about 0.28 to 0.35 mm in terms of forming into a bottle can.
  • a tandem rolling machine in which two or more rolling stands are arranged in series.
  • a single rolling stand has a single stage and is repeatedly rolled (passed) to cold-roll to a predetermined thickness.
  • the number of passes (passing plates) can be reduced, and the rolling rate per pass can be increased.
  • the rolling mill is not limited to a tandem rolling mill as long as it can recover sufficiently by cold rolling and sufficiently generate subgrains.
  • finish annealing may be performed at a temperature lower than the recrystallization temperature. Finish annealing recovers the work structure and improves DI moldability and can bottom moldability.
  • the temperature of the finish annealing is preferably about 100 to 150 ° C, particularly about 115 to 150 ° C. By setting the temperature to 100 ° C or higher, the processed structure can be sufficiently recovered. On the other hand, by controlling the temperature to 150 ° C or less, excessive precipitation of solid solution elements can be prevented, and DI moldability and flange moldability can be further enhanced.
  • the finish annealing time is preferably 4 hours or less (particularly about 1 to 3 hours). By avoiding excessive annealing, excessive precipitation of solid solution elements can be prevented, and DI moldability can be further improved. Can be increased.
  • finish annealing is basically unnecessary because sub-grains can be generated at lower temperatures and continuously.
  • the total amount of other elements in both the inventive example and the comparative example is unavoidable impurity elements, Zr, Bi, Sn, Ga, V, Co, Ni, Ca, Contain 0.03% or more of Mo, Be, Pb, W in the total content of these elements!
  • the rate of temperature increase in soaking is the rate of temperature increase from 300 ° C to the soaking temperature (maximum temperature).
  • the cooling rate after the soaking is from the soaking temperature to a temperature range of 450 to 550 ° C (up to the starting temperature if the hot rough rolling starting temperature force is higher than 50 ° C). Show.
  • the obtained hot-rolled sheet was cold-rolled by a tandem rolling mill or a single rolling mill and commonly used to produce a plate material for a bottle can (cold-rolled sheet) having a final sheet thickness of 0.3 mm. Finish annealing (final annealing) after this cold rolling was not performed.
  • the aluminum plate was forcibly cooled using an aqueous emulsion solution so that the temperature of the plate did not rise above 250 ° C.
  • a test piece was taken from the plate material (coil) for bottle can after cold rolling, and the structure of the test piece was measured as described above (however, the TEM magnification was 10,000 times).
  • the number of dispersed particles having a size of ⁇ (individual ⁇ 300 m 2 ), the number ratio (%) of dispersed particles having a size of 0.3 / zm or more among these dispersed particles, and the average aspect ratio of crystal grains Each was investigated. These results are shown in Table 3 (continued from Table 2) and Table 5 (continued from Table 4).
  • the tensile strength and 0.2% resistance of the test piece were measured by a tensile test according to JIS Z 2201. Specimen shape It was prepared with ⁇ O IS No. 5 specimen, and the specimen was prepared so that the longitudinal direction of the specimen coincided with the rolling direction. The crosshead speed was 5 mmZ and the test was performed at a constant speed until the test piece broke.
  • test piece was simulated at 200 ° C by simulating a can coating baking process.
  • a blank was also collected from the plate material for the bottle can, and after applying a lubricant [DA Stuart, Nalco 6461], it was molded into a cup shape by a 40% deep drawing test using an Eriksen tester. investigated.
  • FIG. Fig. 3 is a developed view of a cup obtained by DI molding a plate for a bottle can body.
  • the heights of the ears (Tl, T2, T3, T4; referred to as minus ears) occurring in the 0 °, 90 °, 180 °, and 270 ° directions were measured.
  • Measure the height of the ears (Yl, Y2, Y3, Y4; called plus ears) that occur in the directions of °, 135 °, 225 °, and 315 °.
  • the heights Y1 to Y4 and Tl to T4 are the heights from the bottom of the cup. From each measured value, the average ear rate is calculated based on the following formula.
  • Average Ear Rate (%) [ ⁇ (Y1 + Y2 + Y3 + Y4) (T1 + T2 + T3 + T4) ⁇ / ⁇ 1/2 ⁇ ( ⁇ 1 + Y2 + Y3 + Y4 + T1 + T2 + T3 + T4) ⁇ ] X 100
  • the allowable range was + 0% to + 3.5%.
  • the neck formability of the plate material for bottle cans was evaluated.
  • a neck part is formed by applying a die neck force to the vicinity of the opening of the above-mentioned DI can body for bottle cans (good product without breakage) formed for iron moldability evaluation. It was.
  • the neck forming conditions were as follows: the outer diameter of the can body was 66.2 mm, the neck part was formed in four steps, and the uppermost neck outer diameter was 60.3 mm.
  • the shape of wrinkles after neck processing per 10,000 cans was determined, and the neck formability was evaluated.
  • the screw formability of the plate material for bottle cans was evaluated.
  • a two-piece bottle can was manufactured by providing a threaded part for attaching a screw cap on the outer periphery near the mouth of the neck part (good product without wrinkles) of the molded can after the neck processing, and the screw moldability was evaluated. .
  • the screw buckling strength is axial to the molded can (2-piece bottle can) molded up to the above threaded part.
  • Invention Examples 1 to 5 and 20 to 24 are excellent in ear rate. And it has excellent moldability required in each molding process of 2-piece bottle cans such as iron moldability, neck moldability, and screw moldability. In addition, the screw buckling strength is also excellent.
  • Invention Examples 1 to 5 in Table 3 are excellent in high-temperature characteristics in which the average aspect ratio of crystal grains is 3 or more and the resistance (strength) decrease after baking is small.
  • Comparative Examples 6 to 9 in Table 3 and Comparative Examples 25 to 28 in Table 5 are within the composition range of the present invention, but the cooling rate after soaking is too high, Over 25 ° CZhr. Therefore, the dispersed particle structure does not become the dispersion particle structure defined in the present invention, and the dispersed particles having a size of not less than 0 when the number ratio of the small dispersed particles is large or dispersed particles of various sizes are dispersed. Is less than 15% of the total number of dispersed particles.
  • Comparative Example 12 Mg is too high, and the deterioration of formability (particularly ironing workability) due to high work hardening is large.
  • Comparative Example 16 Si is too low and + ears are growing. In addition, the ironing ability is reduced due to the lack of ⁇ phase. In Comparative Example 17, Si is too high, and + ears due to remaining unrecrystallized crystals are growing. In addition, the caloric property is decreasing.
  • Comparative Example 18 Fe is too low and unrecrystallized remains. In addition, if the amount of crystallized material is small, the ironing ability is lowered.
  • Comparative Example 19 Fe is too high and + ears are growing. In addition, the amount of crystallized material increases too much, and the ironing workability deteriorates due to the promotion of crack propagation during processing.
  • Comparative Examples 10 to 19 in Table 3 are produced under the preferred production conditions with a cooling rate after soaking.
  • the alloy composition deviates from the composition of the present invention.
  • each forming process of a two-piece bottle can such as iron formability, neck formability, screw formability, etc.
  • Each formability required in is poor.
  • the screw buckling strength and high temperature characteristics are inferior.
  • the present invention can provide an aluminum alloy cold-rolled sheet for bottle cans having excellent neck part formability and thread formability. Therefore, it is suitable for severe and required characteristic applications such as a more compact two-piece bottle can that is excellent in formability and is required to have no strength reduction even when heat-treated with a thin wall.

Abstract

La présente invention concerne une tôle en alliage d'aluminium laminée à froid pour bouteille canette ayant une composition contenant de 0,7 à 1,5 % en masse de Mn, de 0,8 à 1,7 % en masse de Mg, de 0,1 à 0,7 % en masse de Fe, de 0,05 à 0,5 % en masse de Si et de 0,1 à 0,6 % en masse de Cu, le complément étant composé d’Al et d’impuretés inévitables. Dans la structure, le nombre de particules dispersées ayant une taille de 0,05 à 1 µm, lorsqu’il est déterminé par l’intermédiaire d’un examen par MEC avec un grossissement de 5 000 à 15 000, est de 50 à 400 pour 300 µm2, la proportion de particules dispersées ayant une taille supérieure à 0,3 µm parmi ces particules dispersées étant de 15 à 70 % en nombre sur la base de la totalité des particules dispersées.
PCT/JP2006/318241 2005-11-02 2006-09-14 Tole en alliage d’aluminium laminee a froid pour bouteille canette ayant une excellente capacite de formation de col et procede de production de la tole en alliage d’aluminium laminee a froid WO2007052416A1 (fr)

Priority Applications (3)

Application Number Priority Date Filing Date Title
EP06797959A EP1944384A4 (fr) 2005-11-02 2006-09-14 Tole en alliage d aluminium laminee a froid pour bouteille canette ayant une excellente capacite de formation de col et procede de production de la tole en alliage d aluminium laminee a froid
US12/090,879 US20080302454A1 (en) 2005-11-02 2006-09-14 Cold-Rolled Aluminum Alloy Sheet for Bottle Can with Excellent Neck Part Formability and Process for Producing the Cold-Rolled Aluminum Alloy Sheet
CA002625098A CA2625098A1 (fr) 2005-11-02 2006-09-14 Feuilles d'aluminium laminees a froid pour bouteilles, presentant une aptitude au formage superieure pour former un col et methode de fabrication connexe

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JP2005-319864 2005-11-02
JP2005319864A JP3913260B1 (ja) 2005-11-02 2005-11-02 ネック部成形性に優れたボトル缶用アルミニウム合金冷延板

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WO2012043582A1 (fr) * 2010-09-30 2012-04-05 株式会社神戸製鋼所 Feuille d'alliage d'aluminium laminée à froid pour une canette
JP2012092431A (ja) * 2010-09-30 2012-05-17 Kobe Steel Ltd ボトル缶用アルミニウム合金冷延板
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CN102703776A (zh) * 2012-06-08 2012-10-03 中铝瑞闽铝板带有限公司 Led电视机用铝合金基材及其生产方法
WO2020045537A1 (fr) * 2018-08-31 2020-03-05 株式会社Uacj Feuille d'alliage d'aluminium
JPWO2020045537A1 (ja) * 2018-08-31 2021-08-26 株式会社Uacj アルミニウム合金板
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US20080302454A1 (en) 2008-12-11
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CN101268207A (zh) 2008-09-17
JP3913260B1 (ja) 2007-05-09
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EP1944384A1 (fr) 2008-07-16

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