WO2013118611A1 - Aluminum alloy sheet for di can body - Google Patents
Aluminum alloy sheet for di can body Download PDFInfo
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- WO2013118611A1 WO2013118611A1 PCT/JP2013/051901 JP2013051901W WO2013118611A1 WO 2013118611 A1 WO2013118611 A1 WO 2013118611A1 JP 2013051901 W JP2013051901 W JP 2013051901W WO 2013118611 A1 WO2013118611 A1 WO 2013118611A1
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- aluminum alloy
- alloy plate
- amount
- side wall
- cold
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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
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21D22/00—Shaping without cutting, by stamping, spinning, or deep-drawing
- B21D22/20—Deep-drawing
- B21D22/28—Deep-drawing of cylindrical articles using consecutive dies
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21D35/00—Combined processes according to or processes combined with methods covered by groups B21D1/00 - B21D31/00
- B21D35/002—Processes combined with methods covered by groups B21D1/00 - B21D31/00
- B21D35/005—Processes combined with methods covered by groups B21D1/00 - B21D31/00 characterized by the material of the blank or the workpiece
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21D51/00—Making hollow objects
- B21D51/16—Making hollow objects characterised by the use of the objects
- B21D51/26—Making hollow objects characterised by the use of the objects cans or tins; Closing same in a permanent manner
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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
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- 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
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- 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
Definitions
- the present invention relates to a packaging container used for beverages and foods, and particularly to an aluminum alloy plate that is DI-formed on the body of a beverage can.
- a bottomed cylindrical body (can body) whose bottom and side walls are integrated, and an upper surface sealed by an opening of the body
- a two-piece can comprising a disc-shaped lid (can lid)
- As a material for such cans aluminum alloy plates such as AA to JIS3000 are widely used in terms of formability, corrosion resistance, strength, and the like.
- the cylindrical portion of the cylindrical can with a height particularly like a beverage can has a lot of drawing-ironing process called DI (Drawing and wall Ironing) molding. Often formed by step processing.
- DI Drawing and wall Ironing
- a can made by such a manufacturing method is called a DI can (hereinafter referred to as “can” as appropriate) and is widely distributed.
- the thickness of the side wall (thinnest part) of the current aluminum alloy can is about 0.105 to 0.110 mm excluding the coating film.
- the tip penetrates the side wall and a hole (pin (Hall) may open and the contents may leak.
- Protrusion contact may include contact of hard foreign matter from the outside during manufacturing (filling contents, tightening the lid, passing through the transport system in the manufacturing process), distribution, and even when handled by consumers. Can be mentioned. Also, in the flanging process, when the edge of the opening is expanded, a crack (flange crack) may occur at the end of the opening.
- the material of the thinned can prevent the occurrence of pinholes on the side walls and cracks in the flanges of the openings, that is, improve the piercing resistance and flanging workability (can expandability) of the side walls. Improvement of the aluminum alloy plate on the side is underway.
- Patent Document 1 discloses a method for designing a can body formed by DI molding or drawing from an aluminum alloy cold-rolled sheet having an aluminum alloy cold-rolled sheet composition having a 3000 series composition. That is, the thickness of the can body subjected to heat treatment equivalent to paint baking is in the range of 0.07 mm to 0.14 mm, the tensile strength in the can axis direction of the wall portion is 300 MPa to 500 MPa, and the elongation is 3% to 8%.
- the puncture strength with respect to the wall thickness (t) after removing the surface film such as a coating film can be converted to the puncture strength of a can having a wall thickness of 0.105 mm to obtain a puncture resistance of 35 N or more. I am doing so. For this reason, the thickness of the wall portion for obtaining the piercing strength is determined from the Mg content, or the Mg content with respect to the predetermined wall portion thickness is determined from the desired piercing strength.
- Patent Document 2 discloses a technique for distributing an intermetallic compound at a specific density and a specific area ratio on the surface of an aluminum alloy cold rolled sheet having a 3000 series composition.
- Patent Documents 3 and 4 a technique for improving strength (piercing resistance) and toughness by controlling the distribution density and area ratio of an intermetallic compound of a predetermined size in an aluminum alloy cold-rolled sheet having the same 3000 series composition. Is disclosed. Furthermore, in Patent Document 5, an aluminum alloy cold-rolled sheet having the same 3000 composition is DI molded at a predetermined processing rate and heat treated at 210 to 250 ° C., thereby controlling work hardening and tensile strength by DI molding. And the technique which improves puncture resistance is disclosed.
- the technology for improving the properties such as DI formability and strength when thinned by specifying the solid solution amount of Si, Cu, Mn, Fe, etc. is also an aluminum alloy having a 3000 series composition for cans.
- Various proposals have been made in the field of sheeting. By the way, it is not a DI can, it is not the purpose of improving puncture resistance, but in Patent Document 6, while preventing thermal deformation during coating heat treatment of the aluminum alloy cold-rolled sheet for bottle cans, ensuring the strength of the can after heat treatment,
- the solid solution amount of Cu and Mg is defined as the amount of Cu in the solution separated from the precipitate having a particle size exceeding 0.2 ⁇ m by the residual extraction method using hot phenol. They are specified as 0.05 to 0.3% and Mg content as 0.75 to 1.6%, respectively.
- DI cans can be made into a large number of can bodies, and a long and wide cold-rolled plate in a coil state can be obtained.
- the number density, area ratio, or distribution of intermetallic compounds as a microstructure across the widthwise direction are not necessarily all representative of the macro.
- the microscopic observation is to measure an arbitrary one place in the plate thickness direction, and the variation in the structure in the plate thickness direction cannot be taken into consideration. For this reason, there is a limit to improving the overall puncture resistance of a can body made from a long and wide cold-rolled sheet.
- the present invention has been made in view of the above-mentioned problems, and a DI can body that can improve stricter puncture resistance (puncture strength) of a can body made from a long and wide cold-rolled plate.
- An object of the present invention is to provide an aluminum alloy plate.
- the gist of the aluminum alloy plate for DI can body of the present invention for solving the above-mentioned problems is, in mass%, Mn: 0.3 to 1.3%, Mg: 1.0 to 3.0%, Si: 0.00. 1 to 0.5%, Fe: 0.1 to 0.8%, respectively, and the balance is made of an aluminum alloy plate having a composition consisting of Al and inevitable impurities.
- the amount of Mn contained in the residue compound having a particle size of more than 0.1 ⁇ m separated by the residue extraction method by 1.0 is 1.0% or less (including 0%) and is separated by the residue extraction method by hot phenol.
- the solid solution amount of Mg in the solution is 0.7% or more and 2.5% or less.
- the aluminum alloy plate further contains one or two of Cu: 0.05 to 0.4%, Cr: 0.001 to 0.1%, Zn: 0.05 to 0.5%. May be.
- the aluminum alloy plate is DI-molded into a can body having a thinnest side wall thickness in the range of 0.085 to 0.110 mm, and the can shaft on the side wall after heat treatment at 200 ° C. for 20 minutes. It is preferable that the 0.2% yield strength in the direction has a strength of 280 MPa to 350 MPa.
- the aluminum alloy plate is DI-molded into a can body having a thinnest side wall thickness in the range of 0.085 to 0.110 mm, and the can body is heat-treated at 200 ° C. for 20 minutes.
- the 0.2% yield strength of the side wall in the can axis direction has a strength characteristic of 280 MPa or more and 350 MPa or less.
- the maximum value is preferably 35 N or more.
- the conventional control of intermetallic compounds is certainly effective for improving the puncture resistance (puncture strength), and it tends to break if there are many large intermetallic compounds in the can body structure. , Puncture resistance decreases.
- the detection means of the intermetallic compound to be controlled is a scanning electron microscope (SEM). ), Etc., and the microstructure of the portion of the coiled wide cold-rolled sheet that is made of DI in a large number of can bodies in the width direction and the thickness direction cannot be represented macroscopically.
- the present inventors do not use a micro observation means such as a scanning electron microscope (SEM), but instead use a so-called macroscopic and average information obtained by a residue extraction method using hot phenol to analyze the coil state. Macroscopically control the structure (intermetallic compound) of the structure of the wide cold-rolled sheet, particularly in the width direction and the thickness direction. Thereby, the puncture resistance can be improved to a target level.
- SEM scanning electron microscope
- an aluminum alloy plate for a can body (hereinafter referred to as an aluminum alloy plate) according to the present invention.
- the composition of the aluminum alloy plate according to the present invention is, by mass, Mn: 0.3 to 1.3%, Mg: 1.0 to 3.0%, Si: 0.1 to 0.5%, Fe: Each of them contains 0.1 to 0.8%, and the balance is made of Al and inevitable impurities.
- the aluminum alloy composition may further contain Cu: 0.05 to 0.4%.
- all the% display regarding a composition (each element content) means the mass%.
- Mn has an effect of improving the strength of the aluminum alloy, and when the aluminum alloy plate is formed on the can body, the side wall strength is increased to ensure buckling strength and puncture resistance. Further, Mn forms an Al—Fe—Mn intermetallic compound in the aluminum alloy and is appropriately dispersed, thereby promoting recrystallization after hot rolling and improving the workability of the aluminum alloy sheet. If the Mn content is less than 0.3%, these effects are insufficient. Therefore, the Mn content is 0.3% or more, preferably 0.4% or more.
- the upper limit of Mn is 1.3%, preferably 1.1%, and more preferably 1.0%.
- Mg 1.0-3.0%
- Mg has the effect of improving the strength of the aluminum alloy.
- the Mg content is less than 1.0%, when the aluminum alloy plate is formed on the can body, the side wall strength is lowered and the puncture resistance is insufficient.
- the Mg content exceeds 3.0%, the work hardening of the aluminum alloy plate becomes excessive, and cracks such as tear-off (fuselage cracks) during ironing, wrinkles and streaks during necking, etc. Is likely to occur. Therefore, the Mg content is in the range of 1.0 to 3.0%, and the upper limit of the Mg content is preferably 2.5%.
- Si forms an Al—Fe—Mn—Si intermetallic compound, and the more appropriately it is distributed, the better the moldability. Therefore, the Si content is 0.1% or more, preferably 0.2% or more. On the other hand, when Si is excessive, many large Al—Fe—Mn—Si intermetallic compounds and Mg—Si intermetallic compounds are formed, and the puncture resistance decreases. For this reason, the upper limit of Si content is 0.5%, preferably 0.4%.
- Fe 0.1-0.8%
- Fe is mixed into the aluminum alloy as a metal impurity, but forms an Al-Fe-Mn intermetallic compound in the aluminum alloy and is appropriately dispersed to promote recrystallization after hot rolling.
- the workability of the aluminum alloy plate is improved.
- Fe is also useful in that it promotes crystallization and precipitation of Mn, and controls the average solid solution Mn amount in the aluminum matrix and the dispersion state of the Mn-based intermetallic compound. Therefore, the Fe content is 0.1% or more, preferably 0.3% or more.
- the upper limit of the Fe content is 0.8%, preferably 0.7%.
- Cu 0.05-0.4%) Cu increases the strength by solid solution strengthening.
- the lower limit when Cu is selectively contained is 0.05% or more, preferably 0.1% or more.
- the upper limit of Cu content is 0.4%, preferably 0.3%.
- the strength improving element having the same effect as Cu examples include Cr and Zn.
- One or two of Cr: 0.001 to 0.1% and Zn: 0.05 to 0.5% are added to Cu. Alternatively, it can be selectively contained instead of Cu.
- the Cr content is 0.001% or more, preferably 0.002% or more.
- the upper limit of Cr content is set to 0.1%, preferably about 0.05%.
- Zn content is 0.05% or more, preferably 0.06% or more.
- the upper limit of Zn content is made into 0.5%, Preferably it is about 0.45%.
- the inevitable impurities include Zr: 0.10% or less, Ti: 0.2% or less, preferably 0.1% or less, and B: 0.05%.
- Zr 0.10% or less
- Ti 0.2% or less
- B preferably 0.1% or less
- the inclusion is allowed without affecting the characteristics of the aluminum alloy sheet according to the present invention.
- Ti also has an effect of refining crystal grains, and if it is contained together with a small amount of B, the effect of refining the crystal grains is further improved.
- the content of these is excessive, a huge Al—Ti system Intermetallic compounds and Ti-B-based coarse particles crystallize and hinder formability.
- the plate width direction of the cold rolled sheet for DI cans In addition, the tissue of the part extending in the plate thickness direction cannot be represented macroscopically. For this reason, the puncture resistance of the can body made from cold-rolled sheets cannot be improved as a whole.
- a so-called macro analysis means based on a residue extraction method using hot phenol is used, so that a wide and long cold-rolled plate in a coil state can be Macroscopically control the intermetallic compound in the structure in the region extending in the plate thickness direction. That is, the starting point of destruction when a protrusion is pushed into the side wall of the can (when piercing) due to the amount of Mn contained in the compound as a residue separated by the residue extraction method using hot phenol (the amount of Mn in the compound residue)
- the amount of the compound containing Mn such as Al—Fe—Mn is defined.
- the starting point of destruction at the time of piercing is a coarse compound having a particle size exceeding 0.1 ⁇ m, which commonly contains Mn, such as an Al—Fe—Mn system.
- Mn such as an Al—Fe—Mn system.
- the aluminum alloy cold-rolled sheet for DI can barrels or DI can body samples formed from DI can be separated by a 0.1 ⁇ m mesh filter when dissolved in hot phenol by a hot phenol residue extraction method. If the content of Mn (Mn in the compound residue) (Mn precipitation amount) contained in the compound as a residue is measured, the Mn containing Mn, such as an Al—Fe—Mn system, which serves as a starting point of the above-described destruction The amount of the compound containing can be found in the structure of the plate or can body.
- the content of Mn contained in the compound as the residue, which is the structure of the aluminum alloy cold-rolled sheet for DI can barrels, or the content of Mg in the separated solution described later is for this DI can barrel.
- the aluminum alloy cold-rolled sheet is DI-molded to form a DI can body (even if the side wall of the DI can body is measured as a sample)
- the difference between the values depends on the portion of the aluminum alloy cold-rolled sheet.
- the aluminum alloy cold-rolled sheet for DI can barrel may be measured as a sample, or the side wall of the DI can cylinder obtained by DI molding of the aluminum alloy cold-rolled sheet for DI can barrel may be measured as a sample.
- the amount of a coarse compound having a particle size exceeding 0.1 ⁇ m and containing Mn such as Al—Fe—Mn in the structure of the plate or can body was separated by a residue extraction method using hot phenol.
- the average content of Mn in the compound is regulated to 1.0% or less.
- the aluminum alloy cold-rolled sheet for the DI can body is DI-molded into a can body having the thinnest side wall thickness in the range of 0.085 to 0.110 mm, and the can body is subjected to heat treatment equivalent to baking of the coating film.
- the 0.2% proof stress in the can axis direction of the side wall of the can body is 280 MPa or more and 350 MPa or less, the piercing resistance of the DI can body is improved.
- the reason why the content of Mn contained in the compound as the residue is “average” is to control macroscopically the amount of Mn-based intermetallic compound in the sheet width direction of the wide cold-rolled sheet. .
- the structure state tends to vary due to the difference in temperature and strain distribution during production.
- the content of Mn is defined as the “average” of the respective can making parts.
- the plate width of the plate in three places, one in the center in the plate width direction at the center in the longitudinal direction of the cold-rolled plate and two at both ends in the plate width direction from this center.
- Samples are taken by sampling from a plurality of locations representing the direction of the can making part, and the amount of each Mn-based intermetallic compound in each part sample of these plates (content of Mn contained in the compound as the residue) Are measured, and the amount of Mn-based intermetallic compound is defined and evaluated as an average value obtained by averaging these measured values.
- Solid solution Mg amount When the amount of solid solution Mg increases, the work hardening characteristics by the solid solution strengthening of the plate and the can body improve, and the deformability of the plate and the can body when the projection is pushed into the side wall of the can (when piercing). Improves puncture resistance. For this reason, in the present invention, the solid solution Mg content of the plate or can body is 0.7% or more and 2.5% or less in terms of the average content of Mg in the solution separated by the residue extraction method using hot phenol. To do.
- the average solid solution amount of Mg in the plate or can body is 0.7% or more and 2.5% in terms of the average content of Mg in the solution separated by the residue extraction method using hot phenol.
- this aluminum alloy plate was DI molded into a can body having a thinnest side wall thickness in the range of 0.085 to 0.110 mm, and the side wall in the direction of the can axis of the side wall after heat treatment equivalent to baking of the coating film was performed.
- the puncture resistance is improved when the 0.2% proof stress is 280 MPa or more and 350 MPa or less.
- the thinned and strengthened DI can body is improved to the target level.
- a piercing needle having a hemispherical surface of 5 mm is pierced perpendicularly to the side wall of the can body at a speed of 50 mm / min, and the maximum value of the measured load until the piercing needle penetrates the side wall of the can body is 35 N or more Improve to level.
- the “solid” of the solid solution amount of Mg in the plate or can body (the content of Mg in the solution separated by the residue extraction method using hot phenol) is defined as “in average” in the compound as the residue. This is to improve the puncture resistance of the can body manufactured from the cold-rolled sheet to the target level, as in the case of the Mn content contained in the steel sheet.
- both ends The solid solution amount of each Mg in each solution separated by the residue extraction method with the hot phenol of each sample collected from a total of three locations representing the can manufacturing site in the plate width direction of the plate,
- the Mg solid solution amount is defined and evaluated as an average value obtained by averaging the measured values.
- the average solid solution amount of Mg in the plate and can body is less than 0.7% in terms of Mg content in the solution separated by the hot phenol residue extraction method, it becomes the starting point of the above-mentioned destruction. Even if the amount of the Al—Fe—Mn compound is reduced, the piercing resistance of the thinned and strengthened DI can barrel cannot be improved beyond the intended level. On the other hand, as the average solid solution amount of Mg increases, the puncture resistance increases. However, if the solid solution Mg amount exceeds 2.5%, the proof strength of the cold-rolled sheet is remarkably increased due to the solid solution strengthening of Mg. It becomes too high and is not necessary for can manufacturing, and the ironing processability is lowered, and tear-off is likely to occur. Therefore, stab resistance and can manufacturing processability (DI moldability) are traded off only by controlling the solid solution Mg amount.
- DI moldability can manufacturing processability
- the aluminum alloy sheet of the present invention includes a casting process for melting and casting the aluminum alloy having the above components to form an ingot, a soaking process for homogenizing the ingot by heat treatment, and hot rolling the homogenized ingot. And a hot rolling process for producing a hot rolled sheet and a cold rolling process for performing cold rolling without annealing the hot rolled sheet.
- an aluminum alloy is melted, cast by a known semi-continuous casting method such as a DC casting method, and cooled to below the solidus temperature of the aluminum alloy to form an ingot.
- a known semi-continuous casting method such as a DC casting method
- the cooling rate is less than 0.5 ° C./sec
- a large amount of coarse intermetallic compounds are crystallized in the ingot.
- the casting speed is 65 mm / min or the cooling speed is faster than 1.5 ° C./second
- ingot cracking or “soot” is likely to occur and the casting yield is lowered. Therefore, in casting, the casting speed is 40 to 65 mm / min, and the cooling speed is 0.5 to 1.5 ° C./second.
- This cooling rate is for the temperature of the central part of the ingot, that is, the temperature of the central part of the surface perpendicular to the casting direction, and the cooling rate from the liquidus temperature to the solidus temperature of the aluminum alloy.
- the soaking process is soaking twice.
- This two-time soaking is distinguished from two-stage soaking.
- Two-stage soaking means cooling after the first soaking, but it is not cooled to 200 ° C. or lower, and after stopping the cooling at a higher temperature, after maintaining at that temperature, Hot rolling is started after reheating to a high temperature.
- the second soaking of the present invention means that after the first soaking, once cooled to a temperature of 200 ° C. or less including room temperature, reheated, and maintained at that temperature for a certain period of time, Hot rolling is started.
- the first soaking temperature is set to 580 ° C. or higher and lower than the melting point temperature.
- the reason for setting the soaking temperature to 580 ° C. or higher is to dissolve the coarse Al—Fe—Mn compound produced during casting.
- the soaking temperature is less than 580 ° C., the coarse Al—Fe—Mn compound remains without being dissolved, and the formability of the cold-rolled sheet to the can body decreases.
- the average cooling rate of the ingot between 500 ° C. and 200 ° C. is set to 80 ° C./hour or more.
- the average cooling rate between these temperatures is less than 80 ° C./hour, not only the amount of Al—Fe—Mn compound generated during cooling increases, but also the amount of Mg—Si compound increases, and the amount of solid solution Mg decreases. descend.
- the Al—Fe—Mn system already dispersed is obtained.
- the amount of the compound increases as a nucleus, it is necessary to cool it to 200 ° C. or lower once. If this condition is not satisfied, the structure of the portion extending in the plate width direction and plate thickness direction of the cold rolled sheet for DI can cannot be made excellent in the piercing resistance of the can body.
- the second soaking temperature is 450 ° C. or higher and 550 ° C. or lower. Then, the average heating rate of the ingot between 200 and 400 ° C. in the second soaking is set to a rate exceeding 30 ° C./hour. This is because the Mg—Si based compound is generated during the temperature increase in the second soaking, but the average heating rate of the ingot between the temperatures of 200 to 400 ° C. is more than 30 ° C./hour, Mg-Si compound is finely and densely formed, and is not only re-dissolved in the process of raising the temperature to 450 ° C or higher to increase the amount of dissolved Mg, but also during the second soaking or hot rolling.
- the amount of coarse Al—Fe—Mn compound to be reduced can be reduced. Therefore, the amount of Mn and the amount of Mg solid solution defined by the residue extraction method using hot phenol can be satisfied, and the puncture resistance can be improved. If this heating rate is low, the Mg—Si based compound will not be finely and densely formed, and the amount of solid solution Mg cannot be increased without re-dissolution during the process of raising the temperature to 450 ° C. or higher.
- the amount of coarse Al—Fe—Mn compound generated during the second soaking or hot rolling also increases. Therefore, there is a high possibility that the amount of Mn or the amount of Mg solid solution defined by the residue extraction method using hot phenol cannot be satisfied and the puncture resistance cannot be improved. For this reason, the structure of the site
- the ingot homogenization may not be completed if the first and second soaking times are less than 2 hours each. On the other hand, even if soaking for more than 8 hours is performed, the effect is not improved and the productivity is lowered. Accordingly, the first and second soaking times are preferably 2 to 8 hours, but are not particularly limited.
- Hot rolling is performed on the ingot homogenized in the soaking process. First, the ingot is roughly rolled, and further is subjected to finish rolling to obtain an aluminum alloy hot rolled plate having a predetermined thickness.
- Hot rough rolling is started in a temperature range of 450 ° C. or higher and 550 ° C. or lower.
- the rough rolling start temperature is lower than 450 ° C., the amount of Mg—Si compound precipitated during the rough rolling increases, so that not only does the solid solution Mg amount decrease, but rolling itself becomes difficult.
- the rough rolling start temperature exceeds 550 ° C., the surface properties of the plate deteriorate due to seizure during rolling.
- the time between passes in rough rolling and the time required from the rolling execution (pass) to the next rolling execution (pass) are made as short as possible.
- the time between the passes is preferably as short as possible within 100 seconds.
- the time between passes here shows the difference in the mill passage time at the center position in the length direction of the plate.
- the amount of Al—Fe—Mn compound and Mg—Si compound precipitated during rough rolling increases as the rolling reduction in the region where the plate thickness is thin and as the time between passes increases.
- the lowest steady speed is set to 50 m / min or more among the steady speeds of all passes of several to several tens of times in the case of a reverse rolling mill.
- the steady speed here is a speed at which the rolling speed (line speed) is maximum and constant per pass.
- the steady speed (the lowest steady speed during the pass) is less than 50 m / min in comparison with all passes in the hot rough rolling, the rolling time becomes long and the Al—Fe—Mn system formed during cooling. The amount of the compound increases, and the amount of the residual Mn becomes excessive. For this reason, if these conditions are not met, the amount of Mn and the amount of Mg solid solution defined by the residue extraction method using hot phenol cannot be satisfied, and the target piercing resistance of the can body may not be obtained.
- the end temperature of this hot rough rolling is preferably 400 ° C. or higher.
- the hot rolling is divided into rough rolling and finish rolling and continuously performed, if the end temperature of the hot rough rolling is too low, the rolling temperature is lowered in the next hot finishing rolling, Edge cracks are likely to occur.
- the aluminum alloy sheet that has been subjected to the hot rough rolling is hot-finished quickly, such as continuously. By rapidly performing hot finish rolling, an increase in Al—Fe—Mn compounds and Mg—Si compounds can be prevented.
- the aluminum alloy sheet that has been subjected to the hot rough rolling is preferably hot finish rolled, for example, within 5 minutes, preferably within 3 minutes.
- the finishing temperature of hot finish rolling is preferably 300 ° C. or higher. If the temperature is less than 300 ° C., the temperature is too low and the entire plate does not recrystallize and partially becomes a processed structure, and thus the ear rate variation in the plate width direction increases in particular.
- the aluminum alloy hot-rolled sheet is cold-rolled without being annealed to finish an aluminum alloy sheet having a predetermined thickness.
- the total rolling rate (cold working rate) in cold rolling is preferably 77 to 90%, and the thickness of the cold rolled sheet after cold rolling is preferably 0.25 to 0.33 mm.
- DI can manufacturing method An example of a method for producing a can body of a DI can from an aluminum alloy plate (cold rolled plate) according to the present invention will be described below.
- an aluminum alloy plate according to the present invention is punched into a disc shape (blanking process), drawn into a shallow cup shape (capping process), and subjected to DI molding. These drawing and ironing processes are repeated a plurality of times to gradually increase the side wall to obtain a bottomed cylindrical shape having a predetermined bottom surface shape and side wall height.
- the plate thickness reduction rate (ironing rate) on the side wall of the can body by these processes is preferably 60 to 70%. Then, the edge of the side wall (opening) is trimmed and trimmed (trimming process). In this state, DI molding is performed on a thin can body having a side wall thickness of 0.085 to 0.110 mm in the thinnest part.
- the can body is degreased and cleaned, and the outer surface and the inner surface are respectively painted and baked (baked), and the 0.2% proof stress is 280 MPa to 350 MPa as the strength of the thinnest side wall in the can axis direction.
- the strength is high.
- this strength is equivalent to the baking of the coating film as the “can heat treatment equivalent to the baking of the coating film of the can body” as used in the present invention, without actually baking (baking) the coating film.
- the strength after heat treatment at 200 ° C. for 20 minutes at a temperature and time can be substituted.
- the can body after baking the coating film becomes the final can body by reducing the diameter of the opening (necking process) and expanding the edge of the opening to the outside (flanging process).
- necking process the diameter of the opening
- frlanging process expanding the edge of the opening to the outside
- Example aluminum alloy plate An aluminum alloy having the composition shown in Table 1 was melted, and an ingot was produced using a semi-continuous casting method at a casting rate and a cooling rate within the preferable numerical ranges described above in common with each example.
- This ingot is soaked twice, and after the first soaking for 4 hours at a soaking temperature of 600 ° C. in common with each example, an average cooling rate (° C./hour) of 500 to 200 ° C. is once brought to room temperature.
- Various changes were made as shown in Table 1 for cooling.
- the second soaking the ingot is heated again from room temperature, and the average heating rate (° C./hour) of 200 to 400 ° C. is changed variously as shown in Table 1, while in each case the 500 ° C. soaking is common.
- a second soaking process was performed for 4 hours at a hot temperature.
- hot rough rolling was started at this temperature.
- the time between passes of the pass number of passes 12 in this hot rough rolling reverse rolling mill
- the time of the pass required from the rolling execution (pass) to the next rolling execution (pass) The maximum time (seconds) was variously changed as shown in Table 1.
- the lowest steady speed (m / min) was variously changed as shown in Table 1.
- the end temperature of the hot rough rolling is 450 ° C.
- the hot finish rolling is started within 3 minutes after the end of the hot rough rolling
- the end temperature of the hot finish rolling is 330 ° C.
- this hot rolled sheet is cold rolled without being roughed (annealed) and without being subjected to intermediate annealing in the middle, and is a coil-like length having a sheet thickness of 0.28 mm and a sheet width of 2000 mm.
- a length aluminum alloy plate was used.
- “ ⁇ ” in the chemical component composition of the aluminum alloy plate indicates that it is below the detection limit.
- the coiled aluminum alloy plate thus obtained was cupped, DI-molded (ironing rate: 65 to 70%), the opening was trimmed, the outer diameter was about 66 mm, and the height (length in the can axis direction) was 124 mm.
- a bottomed cylindrical can body having a side wall thickness of 0.090 mm was used. Furthermore, after this can body was degreased and washed, heat treatment was performed under the conditions of the above-mentioned 200 ° C. for 20 minutes assuming (simulating) baking at the time of painting to obtain a can body test material.
- the average maximum load of all can bodies was 40 N or more. If the overall width direction of the aluminum alloy cold-rolled sheet is excellent in puncture resistance, In addition, it was also evaluated as “ ⁇ ” that was 35 N or more. On the other hand, if the average maximum load of all can bodies was less than 35N, the puncture resistance of the aluminum alloy cold-rolled sheet was poor in the sheet width direction and the entire sheet thickness direction. evaluated.
- the pressure difference between the inside and outside of the can is larger, the deformation of the can body is larger, and the puncture resistance is more severe.
- 1.7 kgf / cm 2 ( 166.6 kPa).
- the actual rupture at the time of piercing of the can body is caused by collisions of various shapes, but it is not possible to evaluate all of them, and there is a demand for evaluation by a stricter evaluation method. Therefore, it was made difficult to increase the puncture strength by adopting the conditions where the internal pressure was lowered and the deformation was increased.
- the tensile test for measuring 0.2% proof stress of the cold-rolled plate and the side wall of the can body is performed by using test pieces taken from the cold-rolled plate and the side wall of the can body (after the heat treatment assumed for paint baking), respectively. While performing according to 2201, the shape of the test piece was a JIS No. 5 test piece, and the test piece was prepared so that the longitudinal direction of the test piece coincided with the rolling direction (can axis direction). The crosshead speed was 5 mm / min, and the test was performed at a constant speed until the test piece broke.
- each of Invention Examples 1 to 11 has a composition of an aluminum alloy within the scope of the present invention, and is manufactured under preferable manufacturing conditions. That is, in the second soaking process of the ingot, the average cooling rate of 500 to 200 ° C. when cooling to room temperature after the first soaking is 80 ° C./hour or more, and the second soaking ingot The average heating rate of 200 to 400 ° C. during reheating from room temperature is 30 ° C./hour or more. And the longest time of the time between passes in hot rough rolling is less than 100 seconds, and the lowest steady speed is 50 m / min or more.
- each example of the invention shows the Mn content in the compound having a particle size of more than 0.1 ⁇ m separated by a hot phenol residue extraction method on a cold-rolled plate (DI-shaped can barrel side wall).
- the average content (Table 1 is abbreviated as the amount of residual Mn) is 1.0% or less, and there are few Mn-based intermetallic compounds.
- the average solid solution amount of Mg in the cold-rolled sheet (DI-molded can body side wall) structure is the Mg content in the solution separated by the residue extraction method using hot phenol (Table 1 shows solid solution Mg The amount is abbreviated to 0.7% or more and 2.5% or less.
- each of the inventive examples is based on the premise that the DI moldability is good, and the aluminum alloy plate is DI molded into a thin can body having a side wall thickness of 0.090 mm at the thinnest portion, and the coating film is baked.
- the puncture resistance is excellent when the 0.2% proof stress in the can axis direction of the side wall after considerable heat treatment is high strength of 280 MPa to 350 MPa.
- Comparative Examples 12 to 15 in Table 1 although the composition of the aluminum alloy is within the scope of the present invention, any of the conditions in the soaking or hot rough rolling is from the preferable conditions of the present invention. It is off. For this reason, each comparative example shows an average content of Mn in a compound having a particle size of more than 0.1 ⁇ m separated by a hot phenol residue extraction method on a cold-rolled plate (DI-shaped can barrel side wall) (Table No. 1 is abbreviated as the amount of residual Mn), or the average solid solution amount of Mg (Table 1 is abbreviated as the solid solution Mg amount) is out of the structure.
- each comparative example has a good DI moldability
- the thinnest side wall thickness is DI molded into the thin can body and the side wall after heat treatment corresponding to the baking of the coating film. Is high in strength, and the puncture resistance in the plate width direction when the internal pressure condition is severe is remarkably inferior.
- the average heating rate of 200 to 400 ° C. at the second soaking temperature is too small, less than 30 ° C./hour.
- the Mg—Si-based compound is not formed finely and with high density, and is not re-dissolved in the process of raising the temperature to 450 ° C. or higher, so that the amount of Mg in the solid solution is too small.
- Comparative Example 18 has an excessive amount of Mn. In Comparative Example 19, the amount of Si is excessive. In Comparative Example 20, the amount of Si is too small. As a result, since these defectives occurred during DI molding, they could not be put into practical use for cans and were stopped because there was no point in carrying out a subsequent piercing test.
- the aluminum alloy plate (cold rolled plate) for DI can body improves the piercing resistance of the can body manufactured from the aluminum alloy cold rolled plate to a target level, and improves the piercing resistance of the can body. Can be ensured. For this reason, the can wall thickness is reduced in thickness and strength, and it is optimal for an aluminum alloy cold-rolled sheet used for a DI can body that requires puncture resistance under more severe use conditions.
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Abstract
Description
ちなみに、DI缶ではなく、耐突き刺し性向上目的でもないが、特許文献6では、ボトル缶用アルミニウム合金冷延板の塗装熱処理時の熱変形を防止し、熱処理後の缶強度を確保するとともに、真円度が高いボトル缶を得るために、CuとMgとの固溶量を、熱フェノールによる残査抽出法により粒子サイズが0.2μmを超える析出物と分離された溶液中のCu量として0.05~0.3%、Mg量として0.75~1.6%として各々規定している。 In addition, the technology for improving the properties such as DI formability and strength when thinned by specifying the solid solution amount of Si, Cu, Mn, Fe, etc. is also an aluminum alloy having a 3000 series composition for cans. Various proposals have been made in the field of sheeting.
By the way, it is not a DI can, it is not the purpose of improving puncture resistance, but in Patent Document 6, while preventing thermal deformation during coating heat treatment of the aluminum alloy cold-rolled sheet for bottle cans, ensuring the strength of the can after heat treatment, In order to obtain a bottle can with high roundness, the solid solution amount of Cu and Mg is defined as the amount of Cu in the solution separated from the precipitate having a particle size exceeding 0.2 μm by the residual extraction method using hot phenol. They are specified as 0.05 to 0.3% and Mg content as 0.75 to 1.6%, respectively.
例えば、特許文献1のようなMg含有量の制御のみからでは、組織中の化合物の存在にも大きく影響される突き刺し強度を、前記要求レベルにすることには限界がある。また、特許文献3に開示された技術は、缶の側壁厚さを0.110mm超に厚くすることにより耐突き刺し性を向上させており、缶の側壁厚さの薄肉化傾向に対応できていない。更に、特許文献5に開示された技術は、缶の塗装時における焼付けの温度範囲が高めに限定されているため、より低温で熱処理したい場合の製缶側の要求には不適である。 However, the handling and use conditions of DI cans are more severe, such as the pressure difference between the inside and outside of the can becoming larger and the can body being easily deformed. The puncture resistance (puncture resistance) is also stricter. On the other hand, the above-described prior art still has room for improvement in order to obtain this strict puncture resistance.
For example, only by controlling the Mg content as in Patent Document 1, there is a limit to setting the puncture strength that is greatly influenced by the presence of a compound in the tissue to the required level. Moreover, the technique disclosed in Patent Document 3 improves the puncture resistance by increasing the thickness of the side wall of the can to more than 0.110 mm, and cannot cope with the tendency of the can to reduce the thickness of the side wall of the can. . Furthermore, since the technique disclosed in Patent Document 5 is limited to a high baking temperature range when painting cans, it is unsuitable for requirements on the can-making side when heat treatment is desired at lower temperatures.
そして、コイル状態の広幅で長尺の冷延板には、その製造条件を最適化したとしても、板幅方向などで温度やひずみの分布がどうしても異なり、マクロ的な機械特性には影響せずとも、ミクロ組織としての金属間化合物の個数密度や面積率あるいは分布に、当然ながらばらつきが生じる。 In addition, the control of the intermetallic compound disclosed in Patent Documents 3 to 5 is certainly effective for improving the puncture resistance. However, in order to evaluate whether or not the provisions of Patent Documents 3 to 5 are satisfied, it is necessary to apply a scanning electron microscope (SEM) such as a magnification of 500 times as a means for detecting an intermetallic compound to be controlled. I wo n’t. However, as is well known, a wide and long cold-rolled sheet in a coiled state can be made into DI in a large number of thousands to tens of thousands of can bodies over the entire part in the width direction and the longitudinal direction of rolling. .
And even if the manufacturing conditions are optimized for a coiled wide and long cold-rolled sheet, the distribution of temperature and strain is inevitably different in the sheet width direction, etc., and it does not affect the macroscopic mechanical properties. In both cases, the number density, area ratio or distribution of the intermetallic compound as a microstructure naturally varies.
本発明に係るアルミニウム合金板の組成は、質量%で、Mn:0.3~1.3%、Mg:1.0~3.0%、Si:0.1~0.5%、Fe:0.1~0.8%を各々含有し、残部がAl及び不可避的不純物からなるものとする。このアルミニウム合金組成に、さらにCu:0.05~0.4%を含有する組成としてもよい。なお、組成(各元素含有量)に関する%表示は全て質量%の意味である。 (Aluminum alloy composition)
The composition of the aluminum alloy plate according to the present invention is, by mass, Mn: 0.3 to 1.3%, Mg: 1.0 to 3.0%, Si: 0.1 to 0.5%, Fe: Each of them contains 0.1 to 0.8%, and the balance is made of Al and inevitable impurities. The aluminum alloy composition may further contain Cu: 0.05 to 0.4%. In addition, all the% display regarding a composition (each element content) means the mass%.
Mnは、アルミニウム合金の強度を向上させる効果があり、アルミニウム合金板が缶胴に成形されたときに、側壁強度を高めて座屈強度や耐突刺し性を確保する。また、Mnはアルミニウム合金中でAl-Fe-Mn系金属間化合物を形成し、適度に分散されることで、熱間圧延後の再結晶が促進されてアルミニウム合金板の加工性が向上する。Mnの含有量が0.3%未満では、これらの効果が不十分である。このため、Mnの含有量は0.3%以上、好ましくは0.4%以上とする。一方、Mnの含有量が1.3%を超えると、アルミニウム合金板の固溶強化が過大となって加工性が低下し、また、Al-Fe-Mn系金属間化合物の生成量が増加して、耐突刺し性が低下する。それゆえ、Mnの上限は1.3%とし、好ましくは1.1%、さらに好ましくは1.0%とする。 (Mn: 0.3 to 1.3%)
Mn has an effect of improving the strength of the aluminum alloy, and when the aluminum alloy plate is formed on the can body, the side wall strength is increased to ensure buckling strength and puncture resistance. Further, Mn forms an Al—Fe—Mn intermetallic compound in the aluminum alloy and is appropriately dispersed, thereby promoting recrystallization after hot rolling and improving the workability of the aluminum alloy sheet. If the Mn content is less than 0.3%, these effects are insufficient. Therefore, the Mn content is 0.3% or more, preferably 0.4% or more. On the other hand, if the Mn content exceeds 1.3%, the solid solution strengthening of the aluminum alloy plate becomes excessive, resulting in a decrease in workability and an increase in the amount of Al—Fe—Mn intermetallic compound produced. As a result, the puncture resistance is reduced. Therefore, the upper limit of Mn is 1.3%, preferably 1.1%, and more preferably 1.0%.
Mgは、アルミニウム合金の強度を向上させる効果がある。Mgの含有量が1.0%未満では、アルミニウム合金板が缶胴に成形されたときに、側壁強度が低くなって耐突刺し性が不足する。一方、Mgの含有量が3.0%を超えると、アルミニウム合金板の加工硬化が過大となって、しごき加工時のティアオフ(胴体割れ)等の割れ、ネッキング加工時のシワやスジ等の不良が発生し易くなる。したがって、Mgの含有量は、1.0~3.0%の範囲とし、Mg量の上限は好ましくは2.5%とする。 (Mg: 1.0-3.0%)
Mg has the effect of improving the strength of the aluminum alloy. When the Mg content is less than 1.0%, when the aluminum alloy plate is formed on the can body, the side wall strength is lowered and the puncture resistance is insufficient. On the other hand, if the Mg content exceeds 3.0%, the work hardening of the aluminum alloy plate becomes excessive, and cracks such as tear-off (fuselage cracks) during ironing, wrinkles and streaks during necking, etc. Is likely to occur. Therefore, the Mg content is in the range of 1.0 to 3.0%, and the upper limit of the Mg content is preferably 2.5%.
Siは、Al-Fe-Mn-Si系金属間化合物を形成し、それが適正に分布している程、成形性が向上する。このため、Siの含有量は0.1%以上、好ましくは0.2%以上とする。一方、Siが過剰になると、Al-Fe-Mn-Si系金属間化合物やMg-Si系金属間化合物の大きなものが多数形成されて、耐突き刺し性が低下する。このため、Si含有量の上限は0.5%、好ましくは0.4%とする。 (Si: 0.1-0.5%)
Si forms an Al—Fe—Mn—Si intermetallic compound, and the more appropriately it is distributed, the better the moldability. Therefore, the Si content is 0.1% or more, preferably 0.2% or more. On the other hand, when Si is excessive, many large Al—Fe—Mn—Si intermetallic compounds and Mg—Si intermetallic compounds are formed, and the puncture resistance decreases. For this reason, the upper limit of Si content is 0.5%, preferably 0.4%.
Feは、地金不純物としてアルミニウム合金中に混入されるが、アルミニウム合金中でAl-Fe-Mn系金属間化合物を形成し、適度に分散されることで、熱間圧延後の再結晶が促進されてアルミニウム合金板の加工性が向上する。また、Feは、Mnの晶出や析出を促進し、アルミニウム基地中の平均固溶Mn量やMn系金属間化合物の分散状態を制御する点でも有用である。このため、Feの含有量は0.1%以上、好ましくは0.3%以上とする。一方、Fe含有量が過剰になると、直径15μmを超えるサイズの巨大な初晶金属間化合物が発生しやすくなり、DI成形性や耐突き刺し性も低下する。したがって、Fe含有量の上限は0.8%、好ましくは0.7%とする。 (Fe: 0.1-0.8%)
Fe is mixed into the aluminum alloy as a metal impurity, but forms an Al-Fe-Mn intermetallic compound in the aluminum alloy and is appropriately dispersed to promote recrystallization after hot rolling. As a result, the workability of the aluminum alloy plate is improved. Fe is also useful in that it promotes crystallization and precipitation of Mn, and controls the average solid solution Mn amount in the aluminum matrix and the dispersion state of the Mn-based intermetallic compound. Therefore, the Fe content is 0.1% or more, preferably 0.3% or more. On the other hand, when the Fe content is excessive, a huge primary intermetallic compound having a diameter exceeding 15 μm is likely to be generated, and the DI moldability and puncture resistance are also lowered. Therefore, the upper limit of the Fe content is 0.8%, preferably 0.7%.
Cuは、固溶強化によって強度を増加させる。このため、Cuを選択的に含有させる場合の下限量は0.05%以上、好ましくは0.1%以上とする。一方、Cuが過剰になると、高強度は容易に得られるものの、硬くなりすぎるために、成形性が低下し、さらには耐食性も劣化する。このため、Cu含有の上限量は0.4%、好ましくは0.3%とする。 (Cu: 0.05-0.4%)
Cu increases the strength by solid solution strengthening. For this reason, the lower limit when Cu is selectively contained is 0.05% or more, preferably 0.1% or more. On the other hand, if Cu is excessive, high strength can be easily obtained, but it becomes too hard, so that formability is lowered and corrosion resistance is also deteriorated. For this reason, the upper limit of Cu content is 0.4%, preferably 0.3%.
このCuと同効の強度向上元素としてはCr、Znが挙げられ、Cr:0.001~0.1%、Zn:0.05~0.5%の一種または二種を、Cuに加えて、あるいはCuに代えて選択的に含有させることができる。選択的に含有させる場合のCrの含有量は0.001%以上、好ましくは0.002%以上とする。一方、Crが過剰になると、巨大晶出物が生成して成形性が低下するので、Cr量の上限は0.1%、好ましくは0.05%程度とする。また、選択的に含有させる場合のZnの含有量は0.05%以上、好ましくは0.06%以上とする。一方、Znが過剰になると耐食性が低下するので、Zn含有量の上限は0.5%、好ましくは0.45%程度とする。 (Cr: 0.001 to 0.1%, Zn: 0.05 to 0.5%)
Examples of the strength improving element having the same effect as Cu include Cr and Zn. One or two of Cr: 0.001 to 0.1% and Zn: 0.05 to 0.5% are added to Cu. Alternatively, it can be selectively contained instead of Cu. When selectively contained, the Cr content is 0.001% or more, preferably 0.002% or more. On the other hand, when Cr is excessive, giant crystals are generated and the formability is lowered. Therefore, the upper limit of Cr content is set to 0.1%, preferably about 0.05%. Further, when Zn is selectively contained, the Zn content is 0.05% or more, preferably 0.06% or more. On the other hand, since corrosion resistance falls when Zn becomes excessive, the upper limit of Zn content is made into 0.5%, Preferably it is about 0.45%.
耐突き刺し性(耐突き刺し強度)の向上のために、本発明でも、DI缶胴用アルミニウム合金板あるいは、これをDI成形したDI缶胴の組織中の、Al-Fe-Mn系化合物などの金属間化合物の制御や固溶Mg量の制御を行う。 (Structure of aluminum can plate for DI can body)
In order to improve the puncture resistance (puncture strength), in the present invention, a metal such as an Al—Fe—Mn compound in an aluminum alloy plate for a DI can body or a DI can body formed by DI molding is used. Control of intermetallic compounds and solid solution Mg amount are performed.
缶の側壁に突起物が押し込まれたときにピンホールが生じる突き刺しのメカニズムは、前記特許文献4にも開示される通り、突起物が接触している部位を中心にして缶の内側へすり鉢状に窪んで変形する際に、この中心部の周縁(すり鉢の傾斜した面)で局所的な減肉およびせん断帯が生じ、このせん断帯端部(缶の内側表面)からクラックが発生するためである。このクラックがせん断帯に沿って伝播することによって破断に至り、この減肉部に金属間化合物の量、特にサイズの大きな金属間化合物が多いと破断し易くなる。 (Mn content in the compound)
The piercing mechanism in which a pinhole is generated when a protrusion is pushed into the side wall of the can is, as disclosed in Patent Document 4, a mortar-like shape toward the inside of the can centering on the portion where the protrusion is in contact This is due to local thinning and shear bands occurring at the periphery of the central part (inclined surface of the mortar) and cracking from the end of the shear band (inner surface of the can) is there. When this crack propagates along the shear band, it breaks, and if the amount of intermetallic compound, particularly a large intermetallic compound, is large in the thinned portion, the crack is easily broken.
このために、後述する実施例の通り、冷延板の長手方向中央部の板幅方向中央部1箇所とこの中央部からの板幅方向両端部2箇所の計3箇所の、板の板幅方向の製缶部位を代表する複数個所からサンプリングして試料を採取する、そして、これらの板の各部位試料の各Mn系金属間化合物量(前記残渣としての化合物に含まれるMnの含有量)を各々測定し、これら測定値を平均化した平均値としてMn系金属間化合物量を規定、評価する。
このMnの平均含有量が1.0%を超えた場合には、板や缶胴の組織中のAl-Fe-Mn系などのMnを含む、粒子サイズが0.1μmを超える粗大な金属間化合物が多くなりすぎる。この結果、缶胴が前記薄肉で前記高強度であり、かつ使用環境が厳しくなった場合の、耐突き刺し性が低下してしまう。 In the present invention, the reason why the content of Mn contained in the compound as the residue is “average” is to control macroscopically the amount of Mn-based intermetallic compound in the sheet width direction of the wide cold-rolled sheet. . In the plate width direction of a wide cold-rolled plate having a width of 1000 mm or more, the structure state tends to vary due to the difference in temperature and strain distribution during production. In order to suppress this variation and increase the uniformity of the structure and improve the overall puncture resistance (uniformly or uniformly) of the DI can body produced from each can in the width direction of the cold-rolled sheet In addition, the content of Mn is defined as the “average” of the respective can making parts.
For this purpose, as in the examples described later, the plate width of the plate in three places, one in the center in the plate width direction at the center in the longitudinal direction of the cold-rolled plate and two at both ends in the plate width direction from this center. Samples are taken by sampling from a plurality of locations representing the direction of the can making part, and the amount of each Mn-based intermetallic compound in each part sample of these plates (content of Mn contained in the compound as the residue) Are measured, and the amount of Mn-based intermetallic compound is defined and evaluated as an average value obtained by averaging these measured values.
When the average content of Mn exceeds 1.0%, between coarse metals with a particle size exceeding 0.1 μm including Mn such as Al—Fe—Mn in the structure of the plate or can body Too much compound. As a result, the piercing resistance is deteriorated when the can body is thin and has high strength and the use environment becomes severe.
固溶Mg量が増加すると、板や缶胴の固溶強化による加工硬化特性が向上し、缶の側壁に突起物が押し込まれたとき(突き刺しのとき)の、板や缶胴の変形能が向上して、耐突き刺し性が向上する。このため、本発明では、板や缶胴の固溶Mg量を、前記熱フェノールによる残渣抽出法により分離された溶液中のMgの平均含有量で0.7%以上、2.5%以下とする。 (Solution Mg amount)
When the amount of solid solution Mg increases, the work hardening characteristics by the solid solution strengthening of the plate and the can body improve, and the deformability of the plate and the can body when the projection is pushed into the side wall of the can (when piercing). Improves puncture resistance. For this reason, in the present invention, the solid solution Mg content of the plate or can body is 0.7% or more and 2.5% or less in terms of the average content of Mg in the solution separated by the residue extraction method using hot phenol. To do.
次に、本発明におけるアルミニウム合金板の製造方法を説明する。本発明のアルミニウム合金板は、前記成分のアルミニウム合金を溶解、鋳造して鋳塊とする鋳造工程と、鋳塊を熱処理により均質化する均熱処理工程と、均質化した鋳塊を熱間圧延して熱間圧延板とする熱間圧延工程と、熱間圧延板を焼鈍することなく冷間圧延する冷間圧延工程によって製造される。そして、この製造方法において、鋳塊の均熱処理を後述する条件によって2回行うとともに、熱間粗圧延も後述する条件によって行い、冷延後のアルミニウム合金板組織を、本発明で規定する、前記熱フェノールによる残渣抽出法による分離残渣化合物中のMnの平均含有量を1.0%以下(0%を含む)とするとともに、Mgの平均固溶量を前記熱フェノールによる残渣抽出法による分離溶液中のMgの平均含有量として0.7%以上、2.5%以下とする。 (Production method)
Next, the manufacturing method of the aluminum alloy plate in this invention is demonstrated. The aluminum alloy sheet of the present invention includes a casting process for melting and casting the aluminum alloy having the above components to form an ingot, a soaking process for homogenizing the ingot by heat treatment, and hot rolling the homogenized ingot. And a hot rolling process for producing a hot rolled sheet and a cold rolling process for performing cold rolling without annealing the hot rolled sheet. And in this manufacturing method, while performing soaking heat treatment of the ingot twice under the conditions described later, hot rough rolling is also performed under the conditions described later, and the aluminum alloy sheet structure after cold rolling is defined in the present invention, Separation solution by residue extraction method with hot phenol The average content of Mn in the residue compound separated by the residue extraction method with hot phenol is 1.0% or less (including 0%), and the average solid solution amount of Mg is the separation solution by the residue extraction method with hot phenol The average Mg content is 0.7% or more and 2.5% or less.
先ず、アルミニウム合金を溶解し、DC鋳造法等の公知の半連続鋳造法により鋳造し、アルミニウム合金の固相線温度未満まで冷却して鋳塊とする。鋳造速度が40mm/分未満、あるいは冷却速度が0.5℃/秒未満と遅いと、鋳塊中に粗大な金属間化合物が多量に晶出する。一方、鋳造速度が65mm/分、あるいは冷却速度が1.5℃/秒をそれぞれ超えて速いと、鋳塊割れや“す”が発生し易くなって鋳造歩留が低下する。したがって、鋳造において、鋳造速度は40~65mm/分、冷却速度は0.5~1.5℃/秒とする。また、この冷却速度は、鋳塊の中央部の温度、すなわち鋳造方向に垂直な面の中央部の温度についてのものであり、アルミニウム合金の液相線温度から固相線温度までの冷却における速度とする。 (Melting, casting)
First, an aluminum alloy is melted, cast by a known semi-continuous casting method such as a DC casting method, and cooled to below the solidus temperature of the aluminum alloy to form an ingot. When the casting rate is less than 40 mm / min or the cooling rate is less than 0.5 ° C./sec, a large amount of coarse intermetallic compounds are crystallized in the ingot. On the other hand, if the casting speed is 65 mm / min or the cooling speed is faster than 1.5 ° C./second, ingot cracking or “soot” is likely to occur and the casting yield is lowered. Therefore, in casting, the casting speed is 40 to 65 mm / min, and the cooling speed is 0.5 to 1.5 ° C./second. This cooling rate is for the temperature of the central part of the ingot, that is, the temperature of the central part of the surface perpendicular to the casting direction, and the cooling rate from the liquidus temperature to the solidus temperature of the aluminum alloy. And
鋳塊を圧延する前に、所定温度で均質化熱処理(均熱処理)することが必要である。熱処理を施すことによって、内部応力を除去し、鋳造時に偏析した溶質元素を均質化し、鋳造時に晶出した金属間化合物を拡散固溶させて、組織が均質化される。 (Soaking)
Before rolling the ingot, it is necessary to perform a homogenization heat treatment (soaking) at a predetermined temperature. By applying heat treatment, internal stress is removed, solute elements segregated during casting are homogenized, and intermetallic compounds crystallized during casting are diffused and dissolved to homogenize the structure.
前記均熱処理工程で均質化された鋳塊に熱間圧延を行う。まず、鋳塊を粗圧延して、さらに仕上げ圧延により、所定の板厚のアルミニウム合金熱間圧延板とする。 (Hot rolling)
Hot rolling is performed on the ingot homogenized in the soaking process. First, the ingot is roughly rolled, and further is subjected to finish rolling to obtain an aluminum alloy hot rolled plate having a predetermined thickness.
450℃以上、550℃以下の温度範囲で、熱間粗圧延を開始する。この粗圧延開始温度が450℃よりも低いと、粗圧延中に析出するMg-Si系化合物の量が増えて、固溶Mg量が減少するだけでなく、圧延自身も困難となる。一方、粗圧延開始温度が550℃を超える場合は、圧延中の焼付きによって板の表面性状が悪化する。 (Hot rough rolling)
Hot rough rolling is started in a temperature range of 450 ° C. or higher and 550 ° C. or lower. When the rough rolling start temperature is lower than 450 ° C., the amount of Mg—Si compound precipitated during the rough rolling increases, so that not only does the solid solution Mg amount decrease, but rolling itself becomes difficult. On the other hand, when the rough rolling start temperature exceeds 550 ° C., the surface properties of the plate deteriorate due to seizure during rolling.
熱間粗圧延が終了したアルミニウム合金板は、連続的など、速やかに熱間仕上圧延する。速やかに熱間仕上圧延することによって、Al-Fe-Mn系化合物やMg-Si系化合物の増加を防止することができる。熱間粗圧延が終了したアルミニウム合金板は、例えば、5分以内、好ましくは3分以内に熱間仕上圧延することが好ましい。熱間仕上圧延の終了温度は300℃以上とすることが好ましい。300℃未満では、温度が低すぎて板全体が再結晶せずに、部分的に加工組織となるため、特に板幅方向の耳率ばらつきが増加する。 (Hot finish rolling)
The aluminum alloy sheet that has been subjected to the hot rough rolling is hot-finished quickly, such as continuously. By rapidly performing hot finish rolling, an increase in Al—Fe—Mn compounds and Mg—Si compounds can be prevented. The aluminum alloy sheet that has been subjected to the hot rough rolling is preferably hot finish rolled, for example, within 5 minutes, preferably within 3 minutes. The finishing temperature of hot finish rolling is preferably 300 ° C. or higher. If the temperature is less than 300 ° C., the temperature is too low and the entire plate does not recrystallize and partially becomes a processed structure, and thus the ear rate variation in the plate width direction increases in particular.
アルミニウム合金熱間圧延板は、焼鈍せずに冷間圧延して所定の板厚のアルミニウム合金板に仕上げる。冷間圧延における総圧延率(冷間加工率)は77~90%、冷延後の冷延板の板厚は0.25~0.33mmとすることが好ましい。 (Cold rolling)
The aluminum alloy hot-rolled sheet is cold-rolled without being annealed to finish an aluminum alloy sheet having a predetermined thickness. The total rolling rate (cold working rate) in cold rolling is preferably 77 to 90%, and the thickness of the cold rolled sheet after cold rolling is preferably 0.25 to 0.33 mm.
本発明に係るアルミニウム合金板(冷延板)からDI缶の缶胴を作製する方法の一例を以下に説明する。先ず、本発明に係るアルミニウム合金板を円板形状に打ち抜いて(ブランキング加工)、浅いカップ形状に絞り加工し(カッピング加工)、DI成形を施す。これら絞り加工さらにしごき加工を複数回繰り返して徐々に側壁を高くして、所定の底面形状および側壁高さの有底筒形状とする。 [DI can manufacturing method]
An example of a method for producing a can body of a DI can from an aluminum alloy plate (cold rolled plate) according to the present invention will be described below. First, an aluminum alloy plate according to the present invention is punched into a disc shape (blanking process), drawn into a shallow cup shape (capping process), and subjected to DI molding. These drawing and ironing processes are repeated a plurality of times to gradually increase the side wall to obtain a bottomed cylindrical shape having a predetermined bottom surface shape and side wall height.
表1に示す組成のアルミニウム合金を、溶解し、半連続鋳造法を用いて、各例とも共通して前記した好ましい数値範囲内の鋳造速度および冷却速度で鋳塊を作製した。 (Sample aluminum alloy plate)
An aluminum alloy having the composition shown in Table 1 was melted, and an ingot was produced using a semi-continuous casting method at a casting rate and a cooling rate within the preferable numerical ranges described above in common with each example.
得られたコイル状のアルミニウム合金板を、カッピング加工、DI成形(しごき加工率65~70%)し、開口部をトリミング加工して、外径約66mm、高さ(缶軸方向長)124mm、側壁厚さ0.090mmの有底筒形状の缶胴とした。さらに、この缶胴を脱脂洗浄の後、塗装時の焼付けを想定(模擬)した前記200℃×20分間の条件での熱処理を行って、缶胴供試材とした。 (Can body)
The coiled aluminum alloy plate thus obtained was cupped, DI-molded (ironing rate: 65 to 70%), the opening was trimmed, the outer diameter was about 66 mm, and the height (length in the can axis direction) was 124 mm. A bottomed cylindrical can body having a side wall thickness of 0.090 mm was used. Furthermore, after this can body was degreased and washed, heat treatment was performed under the conditions of the above-mentioned 200 ° C. for 20 minutes assuming (simulating) baking at the time of painting to obtain a can body test material.
評価は、前記アルミニウム合金冷延板で0.2%耐力および熱フェノール残渣抽出法によるMn系金属間化合物量(化合物残渣におけるMn含有量)、Mg固溶量(分離された溶液中のMg含有量)を測定して行った。また、缶胴(前記塗装焼付け想定の熱処理後)で、DI成形性、耐突き刺し性、0.2%耐力をそれぞれ測定、評価した。これらの結果も表1に示す。 [Evaluation]
Evaluation is 0.2% proof stress with the aluminum alloy cold-rolled sheet and the amount of Mn-based intermetallic compound (Mn content in the compound residue) and Mg solid solution amount (Mg content in the separated solution) Amount) was measured. In addition, DI moldability, puncture resistance, and 0.2% proof stress were measured and evaluated on the can body (after heat treatment assumed for the above-mentioned paint baking). These results are also shown in Table 1.
前記アルミニウム合金冷延板コイルの長手方向中央部の、板幅方向中央部1箇所と、この中央部からの板幅方向両端部2箇所の計3箇所から採取した各試料を熱フェノールにより溶解した際の、0.1μmのメッシュのフィルターによって分離された残渣としての化合物におけるMn(化合物残渣中のMn)含有量を各々測定して平均化し、前記アルミニウム合金冷延板組織中の化合物の平均Mn含有量を分析値として求めた。同時に、前記各試料における、この残渣より分離された各溶液中のMgの含有量を測定して平均化し、前記アルミニウム合金冷延板組織中の平均Mg固溶量を分析値として求めた。 (Tissue = hot phenol residue extraction method)
Each sample collected from a total of three locations, one central portion in the plate width direction of the center portion in the longitudinal direction of the aluminum alloy cold rolled plate coil, and two end portions in the plate width direction from this central portion was dissolved with hot phenol. The Mn content (Mn in the compound residue) in the compound as a residue separated by a 0.1 μm mesh filter was measured and averaged, and the average Mn of the compound in the aluminum alloy cold-rolled sheet structure was measured. The content was determined as an analytical value. At the same time, the Mg content in each solution separated from this residue in each sample was measured and averaged, and the average Mg solid solution content in the aluminum alloy cold-rolled sheet structure was determined as an analytical value.
前記したDI成形では、アルミニウム合金冷延板コイルの長手方向中央部の、前記板幅方向中央部近傍1箇所と、前記両端部2箇所の各近傍の計3箇所から1000枚ずつブランクを切り出し、しごき加工率65%で連続成形(カッピング加工、DI成形)して製缶した。そして、成形時に不良(ティアオフ、ピンホール等)が発生しなかった場合は成形性が優れているとして「○」、不良が発生した場合は成形性不良として「×」で評価した。 (Formability)
In the DI molding described above, 1000 blanks were cut out from a total of three locations in the vicinity of the central portion in the plate width direction of the center portion in the longitudinal direction of the aluminum alloy cold rolled plate coil and in the vicinity of each of the two ends. Cans were made by continuous molding (cupping, DI molding) at an ironing rate of 65%. When no defects (tear-off, pinholes, etc.) occurred during molding, the moldability was evaluated as “◯”, and when defects occurred, the moldability was evaluated as “x”.
各例について、1枚の板から製缶される数多くの缶胴の耐突き刺し性、特に冷延板の板幅方向や板厚方向の各耐突き刺し性が総じて向上されているかを検証した。このために、各例とも、前記アルミニウム合金冷延板コイルの板幅方向中央部、両端部の3箇所から製缶された缶胴が均等に含まれるように、前記成形できた10個全てについて突き刺し試験を実施して、耐突き刺し性を評価した。 (Puncture resistance)
For each example, it was verified whether the piercing resistance of a large number of cans made from a single plate, in particular, the piercing resistance in the plate width direction and the plate thickness direction of the cold-rolled plate was improved as a whole. For this reason, in each example, all the ten pieces that can be formed so that the can bodies made from three places of the center portion in the plate width direction and both end portions of the aluminum alloy cold-rolled plate coil are evenly included. A piercing test was performed to evaluate piercing resistance.
験方法の方が試験条件は厳しく、突刺し強度は低めになる。すなわち、前記2.0kgf/cm2の内圧による試験での突き刺し強度(N)の値と、本発明の試験方法による突き刺し強度(N)の値が例え同じか、あるいは例え、多少低い数値であったとしても、本発明の材料の方が耐突刺し性に優れるといえる。言い換えると、2.0kgf/cm2の内圧試験での耐突き刺し性が優れていたとしても、本発明の1.7kgf/cm2のより低い内圧での耐突き刺し性が優れているとは全く言えない。 The evaluation of puncture resistance so far is usually performed by applying a higher internal pressure of 2.0 kgf / cm 2 (= 196 kPa). For this reason, even with the same test material, the test method of the present invention has stricter test conditions and lower puncture strength. That is, the value of the puncture strength (N) in the test with the internal pressure of 2.0 kgf / cm 2 and the value of the puncture strength (N) according to the test method of the present invention are the same, for example, slightly lower values. Even so, it can be said that the material of the present invention is superior in puncture resistance. In other words, even if the penetration resistance of the internal pressure test of 2.0 kgf / cm 2 was excellent, quite be said penetration resistance at lower internal pressure of 1.7 kgf / cm 2 of the present invention is excellent Absent.
前記冷延板と前記缶胴側壁の0.2%耐力測定のための引張試験は、冷延板と、缶胴(前記塗装焼付け想定の熱処理後)側壁から各々採取した試験片を、JIS Z 2201にしたがって行うとともに、試験片形状はJIS 5号試験片で行い、試験片の長手方向が圧延方向(缶軸方向)と一致するように作製した。また、クロスヘッド速度は5mm/分で、試験片が破断するまで一定の速度で行った。 (0.2% yield strength)
The tensile test for measuring 0.2% proof stress of the cold-rolled plate and the side wall of the can body is performed by using test pieces taken from the cold-rolled plate and the side wall of the can body (after the heat treatment assumed for paint baking), respectively. While performing according to 2201, the shape of the test piece was a JIS No. 5 test piece, and the test piece was prepared so that the longitudinal direction of the test piece coincided with the rolling direction (can axis direction). The crosshead speed was 5 mm / min, and the test was performed at a constant speed until the test piece broke.
本出願は、2012年2月9日出願の日本特許出願(特願2012-026511)に基づくものであり、その内容はここに参照として取り込まれる。 Although the present invention has been described in detail and with reference to specific embodiments, it will be apparent to those skilled in the art that various changes and modifications can be made without departing from the spirit and scope of the invention.
This application is based on a Japanese patent application filed on Feb. 9, 2012 (Japanese Patent Application No. 2012-026511), the contents of which are incorporated herein by reference.
Claims (5)
- 質量%で、Mn:0.3~1.3%、Mg:1.0~3.0%、Si:0.1~0.5%、Fe:0.1~0.8%を各々含有し、残部がAl及び不可避的不純物からなる組成を有するアルミニウム合金板からなり、このアルミニウム合金板の組織として、熱フェノールによる残渣抽出法により分離された粒子サイズが0.1μmを超える残渣化合物に含まれるMn量が、1.0%以下(0%を含む)であるとともに、前記熱フェノールによる残渣抽出法により分離された溶液中のMgの固溶量が、0.7%以上、2.5%以下であることを特徴とするDI缶胴用アルミニウム合金板。 By mass%, Mn: 0.3 to 1.3%, Mg: 1.0 to 3.0%, Si: 0.1 to 0.5%, Fe: 0.1 to 0.8%, respectively And the balance is composed of an aluminum alloy plate having a composition composed of Al and inevitable impurities, and the structure of this aluminum alloy plate is included in the residual compound having a particle size of more than 0.1 μm separated by a residue extraction method using hot phenol The Mn content is 1.0% or less (including 0%), and the solid solution amount of Mg in the solution separated by the hot phenol residue extraction method is 0.7% or more and 2.5%. % Aluminum alloy plate for DI can body.
- 前記アルミニウム合金板がさらにCu:0.05~0.4%を含有する請求項1に記載のDI缶胴用アルミニウム合金板。 The aluminum alloy plate for a DI can body according to claim 1, wherein the aluminum alloy plate further contains Cu: 0.05 to 0.4%.
- 前記アルミニウム合金板がさらにCr:0.001~0.1%、Zn:0.05~0.5%の一種または二種を含有する請求項1または2に記載のDI缶胴用アルミニウム合金板。 The aluminum alloy plate for a DI can body according to claim 1 or 2, wherein the aluminum alloy plate further contains one or two of Cr: 0.001 to 0.1% and Zn: 0.05 to 0.5%. .
- 前記アルミニウム合金板が、最薄部の側壁厚さが0.085~0.110mmの範囲の缶胴にDI成形され、この缶胴が200℃×20分間熱処理された際の、缶胴側壁の缶軸方向の0.2%耐力が280MPa以上350MPa以下である強度特性を有する請求項1乃至3のいずれか1項に記載のDI缶胴用アルミニウム合金板。 The aluminum alloy plate is DI-molded into a can body having a thinnest side wall thickness in the range of 0.085 to 0.110 mm, and when the can body is heat-treated at 200 ° C. for 20 minutes, The aluminum alloy plate for DI can bodies according to any one of claims 1 to 3, which has strength characteristics such that a 0.2% proof stress in a can axis direction is 280 MPa or more and 350 MPa or less.
- 前記アルミニウム合金板の耐突き刺し性が、前記缶胴に1.7kgf/cm2(=166.6kPa)の内圧をかけ、この缶胴側壁の缶底から缶軸方向の距離L=60mmの部位に、先端が半径0.5mmの半球面である突き刺し針を缶胴側壁に対して垂直に速度50mm/分で突き刺し、この突き刺し針が缶胴側壁を貫通するまでの荷重測定値のうちの最大値で35N以上である請求項1または2に記載のDI缶胴用アルミニウム合金板。 The puncture resistance of the aluminum alloy plate is such that an internal pressure of 1.7 kgf / cm 2 (= 166.6 kPa) is applied to the can body, and a distance L in the can axis direction from the can bottom of the can body side wall is L = 60 mm. The maximum value of the measured load until the piercing needle penetrates the can barrel side wall at a speed of 50 mm / min perpendicular to the can barrel side wall. The aluminum alloy plate for DI can body according to claim 1 or 2, wherein the aluminum alloy plate is 35N or more.
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KR1020147022211A KR20140111029A (en) | 2012-02-09 | 2013-01-29 | Aluminum alloy sheet for di can body |
CN201380008215.1A CN104093869B (en) | 2012-02-09 | 2013-01-29 | DI tank body aluminium alloy plate |
PH12014501670A PH12014501670A1 (en) | 2012-02-09 | 2014-07-22 | Aluminum alloy sheet for drawn and ironed can bodies |
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WO2014103924A1 (en) * | 2012-12-27 | 2014-07-03 | 株式会社神戸製鋼所 | Aluminum alloy sheet for di can body |
CN105555979A (en) * | 2013-09-20 | 2016-05-04 | 株式会社神户制钢所 | Aluminum alloy sheet for negative-pressure can lid |
CN106103763A (en) * | 2014-03-31 | 2016-11-09 | 株式会社神户制钢所 | Formability and the aluminium alloy plate of baking application hardening excellence |
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- 2013-01-29 WO PCT/JP2013/051901 patent/WO2013118611A1/en active Application Filing
- 2013-01-29 KR KR1020167017846A patent/KR101666342B1/en active IP Right Grant
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Also Published As
Publication number | Publication date |
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CN104093869A (en) | 2014-10-08 |
KR101666342B1 (en) | 2016-10-13 |
PH12014501670A1 (en) | 2014-10-20 |
KR20140111029A (en) | 2014-09-17 |
CN104093869B (en) | 2017-03-08 |
JP2013163835A (en) | 2013-08-22 |
KR20160084862A (en) | 2016-07-14 |
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