WO2014103924A1 - Di缶胴用アルミニウム合金板 - Google Patents
Di缶胴用アルミニウム合金板 Download PDFInfo
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- WO2014103924A1 WO2014103924A1 PCT/JP2013/084234 JP2013084234W WO2014103924A1 WO 2014103924 A1 WO2014103924 A1 WO 2014103924A1 JP 2013084234 W JP2013084234 W JP 2013084234W WO 2014103924 A1 WO2014103924 A1 WO 2014103924A1
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- alloy plate
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- side wall
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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
- 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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- 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 plate for a DI can body, which is a packaging container used for beverages and foods, and in particular, DI molded 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 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.
- Patent Document 1 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 the compound in the tissue to the required level.
- the technique disclosed in Patent Document 2 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 to reduce the thickness of the side wall of the can.
- 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.
- the control of the intermetallic compounds disclosed in Patent Documents 3 to 5 is certainly effective in improving the puncture resistance, there is still room for improvement in order to obtain the strict puncture resistance. is there. *
- the present invention has been made in view of the above problems, and provides an aluminum alloy plate for a DI can body that can satisfy the stricter piercing resistance (piercing strength) required for a thinned can body. With the goal.
- 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: 0.7 to 3.0%, Si: 0.00.
- the aggregate of atoms includes a total of five or more of either or both of Mg atoms and Cu atoms, and Mg contained therein Atoms that satisfy these conditions, regardless of whether the atom is an atom or a Cu atom, the distance between the reference atom and any one of the other adjacent atoms is 0.80 nm or less. the average density of 1 ⁇ 10 collection of 24 / M 3 to be regulated to below.
- the aluminum alloy plate may further contain one or two of Cr: 0.001 to 0.1% and Zn: 0.05 to 0.5%.
- 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 this can body is heat-treated at 200 ° C. for 20 minutes. It is preferable that 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 aluminum alloy plate of 3000 series composition which is a material for the DI can body
- DI molding a can body
- paint baking process heat treatment
- it promotes subgraining of the can body structure
- the puncture resistance is improved.
- it is difficult to quantitatively define the degree of subgraining in this can body structure by structural factors such as dislocation density and crystal grain shape.
- the superiority or inferiority of the puncture resistance between 3000-based aluminum alloy plates containing Cu varies greatly depending on the existence state of a specific atomic aggregate that can be analyzed by a three-dimensional atom probe field ion microscope. I found out. That is, as the number of specific atom aggregates defined in the present invention is smaller, the subgraining of the above-described structure proceeds and the puncture resistance is improved, and conversely, the larger the number of specific atom aggregates is, It has been found that the sub-graining of the can body structure does not progress and the puncture resistance is inferior.
- the existence state (average density) of the atomic aggregates defined in the present invention can be an index representing the relationship with the puncture resistance when a 3000 series aluminum alloy plate containing Cu is formed into a can body.
- the presence state (average density) of the specific atomic aggregate (cluster) of the 3000 series aluminum alloy plate containing Cu is controlled to be required for a thinned can body.
- the puncture resistance can be improved to a level that can satisfy more severe puncture resistance (puncture strength).
- 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 for DI can barrels according to the present invention is, by mass, Mn: 0.3 to 1.3%, Mg: 0.7 to 3.0%, Si: 0.1 to 0.5 %, Fe: 0.1 to 0.8%, Cu: 0.01 to 0.4%, respectively, and the balance is made of Al and inevitable impurities.
- the aluminum alloy composition may further contain one or two of Cr: 0.001 to 0.1% and Zn: 0.05 to 0.5%.
- all the% display regarding a composition 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—Mn—Fe 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, when the Mn content exceeds 1.3%, the amount of coarse Al—Mn—Fe intermetallic compound produced increases, and the puncture resistance decreases. Therefore, the upper limit of Mn is 1.3%, preferably 1.1%, and more preferably 1.0%.
- Mg 0.7-3.0%
- Mg has the effect of improving the strength of the aluminum alloy.
- the content of Mg is less than 0.7%, 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 0.7 to 3.0%, preferably 1.0 to 2.6%, more preferably 1.2 to 2.2%.
- 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—Mn—Fe—Si intermetallic compounds and MgSi 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-Mn-Fe 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 Mn average solid solution 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 0.01-0.4%
- the lower limit of the Cu content is 0.01% or more, preferably 0.05% or more.
- the upper limit of Cu content is 0.4%, preferably 0.3%.
- Cr 0.001 to 0.1%, Zn: 0.05 to 0.5%)
- Zn 0.05 to 0.5%
- 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
- B 0.05%
- 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 piercing resistance of a can body made of an aluminum alloy plate of 3000 series composition is a sub-structure of the can body structure when this material plate is subjected to paint baking after being made into a can body (DI molding). Improve by graining.
- This subgrain is also called a substructure or subcrystal, and is a small structure formed in a crystal grain.
- the inside of this subgrain becomes a partial dislocation-free region, and when the deformation is applied, the activity of the slip surface becomes possible. For this reason, even when a so-called piercing is applied to the can body during pin use or handling, so-called piercing occurs, the work hardening due to the accumulation of new dislocations appears in the piercing portion. The piercing property is improved.
- the degree of subgraining of the can body tissue differs depending on the analysis of the existence state of the atomic aggregate by means of a three-dimensional atom probe field ion microscope, and the atomic aggregate (aggregate density) defined by the present invention is different. It has been found that the smaller the), the more the tissue becomes subgrained and the better the puncture resistance.
- a 3000 series aluminum alloy plate containing Cu this is controlled by controlling the average density, which is an existence state of an aggregate of atoms containing at least Mg atoms or Cu atoms, as measured by a three-dimensional atom probe field ion microscope.
- the degree of subgraining of the can body structure and the puncture resistance of the plate can be controlled. Thereby, the puncture resistance of the 3000 series aluminum alloy plate containing Cu can be improved to a stricter level required for the thinned can body.
- sub-graining and puncture resistance of the can body structure out of the aggregate of atoms measured by a three-dimensional atom probe field ion microscope per structure of 3000 series aluminum alloy plate containing Cu for DI can body. Defines a particular set of atoms that can be controlled.
- the specific aggregate of atoms includes a total of 5 or more of either or both of Mg atoms and Cu atoms, and any of these atoms of Mg or Cu atoms can be used as a reference. Is an aggregate of atoms satisfying the condition that the distance between each atom and any one of the other adjacent atoms is 0.80 nm or less.
- the aggregate (cluster) of atoms defined in the present invention is not necessarily composed of only two atoms, Mg atoms and Cu atoms, and in many cases includes Al atoms of the parent phase. Moreover, it may contain atoms, such as Mn, Si, and Fe, which are other alloy elements. Depending on the component composition of the 3000 series aluminum alloy, atoms such as Cr, Zn, V, Ti, etc. contained as selective elements and impurities may be included in the aggregate of atoms, and these other atoms may be counted by 3DAP analysis. Inevitable.
- the level is small compared to the total number of Mg atoms and Cu atoms. Therefore, even when such other atoms are included in the aggregate, those satisfying the conditions of the prescribed distance between Mg atoms and Cu atoms and the prescribed total number are Mg atoms as the aggregate of atoms of the present invention. And functions in the same manner as an aggregate of atoms consisting only of Cu atoms.
- the atoms adjacent to each other may be not only atoms different from Mg atoms and Cu atoms, but also Mg atoms and Cu atoms.
- Mg atom or Cu atom is not detected and is zero (even if only Mg atom or Cu atom), or between Mg atoms or Cu atoms If any one of the atoms satisfies the adjacent distance (0.80 nm or less) and the number (5 or more), it is an aggregate of atoms defined in the present invention, and an aggregate of atoms defined in the present invention. As an average number density.
- this aggregate of atoms does not contain any Mg atom or Cu atom If so, it is not an aggregate of atoms defined by the present invention, and does not count. That is, the aggregate of atoms defined in the present invention necessarily includes both Mg atoms and Cu atoms, or atoms of either Mg atoms or Cu atoms.
- the definition of the distance of atoms in the aggregate of atoms is that any atom of Mg atom and Cu atom included in the aggregate of atoms is adjacent to the atom (reference Mg atom or Cu atom). It is only necessary that the distance between each other atom (Mg atom, Cu atom or other atom) is 0.80 nm or less. That is, all the distances between the reference atom and all other atoms adjacent to the reference Mg atom or Cu atom may be 0.80 nm or less. Also, there may be adjacent atoms at a distance away from this, as long as there is at least one other atom that satisfies this distance.
- the Mg atoms and Cu atoms included in the aggregate of atoms in a total of 5 or more satisfy the distance relationship with other adjacent atoms.
- an aggregate of atoms in the DI can body material aluminum alloy sheet structure which is defined as described above and measured by 3DAP analysis, is 1 ⁇ 10 24 atoms / average density of the aggregate of atoms. Restrict to m 3 or less. This promotes the subgraining of the can body structure when the material aluminum alloy plate is subjected to a paint baking process after being made on the can body, and improves the piercing resistance of the can body.
- a 3000 series aluminum alloy plate containing Cu can be made into a can body, and then subgraining is promoted when subjected to a paint baking process. Slip surface activity in a dislocation-free area. For this reason, even when a so-called piercing is applied to the can body during pin use or handling, so-called piercing occurs, the work hardening due to the accumulation of new dislocations appears in the piercing portion. The piercing property is improved.
- the upper limit of the average density of the specific atomic aggregate includes zero atoms that cannot be detected or measured and are regarded as nonexistent. However, it is not necessary to deliberately reduce the number of aggregates of atoms to 0, and the average density may be regulated to 1 ⁇ 10 24 / m 3 or less, which is preferable from the viewpoint of not reducing the production efficiency of the material plate. As an indication of the lower limit, the presence of 1 ⁇ 10 22 pieces / m 3 or more is allowed.
- 3D atom probe field ion microscope In the field of aluminum alloy materials, for example, a method for measuring the average density of an aggregate of atoms with a three-dimensional atom probe field ion microscope is exemplified in Japanese Patent Application Laid-Open No. 2011-184895. In this publication, an atomic assembly contributing to improvement of press formability of a 5000 series aluminum alloy plate containing Zn is measured by a three-dimensional atom probe field ion microscope. And as an aggregate of these atoms, a total of 20 or more of either or both of Mg atoms and Cu atoms is included, and any of these atoms of Mg or Cu atoms is used as a reference.
- the distance between each atom and any one of the other adjacent atoms is defined as 0.80 nm or less.
- fills such conditions with the average density of 1 * 10 ⁇ 4 > piece / micrometer ⁇ 3 > or more is proposed.
- This analysis by a three-dimensional atom probe field ion microscope is widely used for analysis of structures and atomic aggregates in the fields of high-density magnetic recording films and electronic devices, aluminum alloy materials, steel materials, and copper alloy materials. Yes.
- 3D Atom Probe Field Ion Microscope 3DAP 3D Atom Probe Field Ion Microscope, hereinafter abbreviated as 3DAP
- 3DAP is a field ion microscope (FIM) equipped with a time-of-flight mass spectrometer.
- the local analyzer is capable of observing individual atoms on a metal surface with a field ion microscope and identifying these atoms by time-of-flight mass spectrometry.
- 3DAP is a very effective means for structural analysis of atomic aggregates because it can simultaneously analyze the type and position of atoms emitted from a sample.
- This 3DAP uses an ionization phenomenon of sample atoms under a high electric field called field evaporation.
- field evaporation When a high voltage necessary for the field evaporation of sample atoms is applied to the sample, the atoms are ionized from the sample surface and pass through the probe hole to reach the detector.
- This detector is a position-sensitive detector, and it is detected by measuring the time of flight to the individual ion detector along with mass analysis of individual ions (identification of elements that are atomic species).
- the determined position (atomic structure position) can be determined simultaneously. Therefore, 3DAP has the feature that the atomic structure at the tip of the sample can be reconstructed and observed three-dimensionally because the position and atomic species of the atom at the tip of the sample can be measured simultaneously. Further, since field evaporation occurs sequentially from the tip surface of the sample, the distribution of atoms in the depth direction from the sample tip can be examined with atomic level resolution.
- the sample to be analyzed must be highly conductive, such as metal, and the shape of the sample is generally very fine with a tip diameter of around 100 nm ⁇ or less. Need to be needle-shaped. For this reason, a sample is taken from the central portion of the aluminum alloy plate, etc., and this sample is cut and electropolished with a precision cutting device to produce a sample having an ultra-fine needle tip for analysis.
- a measuring method for example, using “LEAP3000” manufactured by Imago Scientific Instruments, a high pulse voltage of the order of 1 kV is applied to an aluminum alloy plate sample whose tip is shaped like a needle, and several millions from the sample tip. This is done by ionizing atoms continuously. The ions are detected by a position sensitive detector, and a pulse voltage is applied. From the time of flight from when each ion jumps out of the sample tip until it reaches the detector, mass analysis of ions (atomic species) Element identification).
- this three-dimensional atom map is further analyzed using a Maximum Separation Method, which is a method of defining atoms belonging to precipitates and clusters.
- This method is a method in which the specified maximum distance d max between solute atoms and the minimum number of atoms N min constituting the cluster are given as parameters.
- the cluster is defined by defining the maximum interval d max between adjacent Mg and Cu atoms as 0.80 nm and the total minimum number of atoms N min as 5 as Mg and Cu atoms. From this result, the cluster dispersion state is evaluated, and the number density of the clusters (the specified average density when the number of measurement samples is 3 or more) is quantified.
- Detection efficiency of atoms by 3DAP is currently limited to about 50% of the ionized atoms, and the remaining atoms cannot be detected. If the detection efficiency of atoms by 3DAP is greatly changed in the future or the like, the measurement result by 3DAP of the average number density (atom / m 3 ) of the aggregate of atoms defined by the present invention may change. There is sex. Therefore, in order to give reproducibility to the measurement of the average number density of the aggregate of atoms, it is preferable that the detection efficiency of atoms by 3DAP is substantially constant at about 50%.
- the aluminum alloy sheet of the present invention includes a casting process in which an aluminum alloy having the above composition is melted and cast into an ingot, a soaking process in which the ingot is homogenized by heat treatment, and the homogenized ingot is hot-rolled. 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
- 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./sec, ingot cracking or “shrinkage” or “shrinkage cavity” is likely to occur. The yield drops.
- 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 aggregation of Mg and Cu atoms regulated in the present invention increases. To do.
- 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.
- the average heating rate of the ingot between the temperatures of 200 to 400 ° C. in the second soaking is set to a rate of 30 ° C./hour or more, preferably over 30 ° C./hour. This is because the Mg—Si-based compound is generated during the temperature rise in the second soaking, and in particular, by setting the average heating rate of the ingot between the temperatures of 200 to 400 ° C. above 30 ° C./hour.
- the amount of the Mg and Cu atom aggregates regulated in the present invention is suppressed. If the heating rate is low, the amount of Mg and Cu atom aggregates regulated in the present invention cannot be suppressed, and the upper limit may be exceeded.
- 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.
- the ingot homogenized in the soaking process is hot-rolled, but this hot rolling condition may be in the range of ordinary methods or general conditions, first roughly rolling the ingot, and further by finish rolling, An aluminum alloy hot-rolled plate having a predetermined thickness is used.
- the hot-rolled sheet is cold-rolled without pre-annealing and without intermediate annealing between passes, and finished to 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.
- the total rolling ratio in the cold rolling is, of course, determined by the relationship with the desired thickness of the cold-rolled sheet, but preferable winding for controlling the average density of Mg and Cu atoms within the scope of the present invention. In order to set the temperature range, the above range is preferable.
- the coiling temperature after the cold rolling needs to be in the range of 120 to 160 ° C. If the coil is not wound in such a warm temperature range, the cold rolled sheet structure is not likely to be the range of the Mg and Cu atoms defined in the present invention.
- the winding temperature exceeds 160 ° C.
- the average density of the aggregate of Mg and Cu specified in the present invention exceeds 1 ⁇ 10 24 / m 3 , and the can body is made into a can body. Subgrain formation upon heat treatment at 20 ° C. for 20 minutes is suppressed, and puncture resistance is reduced.
- this winding temperature is in a state such as a room temperature of less than 120 ° C. as in ordinary cold rolling, the strength immediately after winding becomes high and the elongation is low. Will fall.
- the rolled-up plate (coil) is sufficient to cool the plate with the rolling rate and the amount of lubricating oil and coolant used from the viewpoint of controlling heat generation as well as lubrication.
- the temperature is set to around room temperature.
- the heat generated by the process is rather accelerated, and the coiling temperature after cold rolling is set to the high temperature side, and the temperature is 120 to 160 ° C., preferably 120 to 145 ° C. A zone.
- DI can manufacturing method An example of a can manufacturing method for producing a can body of a DI can from a material 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) of the side wall of the can body by these processes is preferably 60 to 70%.
- the edge of the side wall (opening) is trimmed and trimmed (trimming process).
- 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 2 for cooling.
- the second soaking the ingot was heated again from room temperature, and the average heating rate (° C./hour) of 200 to 400 ° C. was changed variously as shown in Table 2.
- a second soaking process was performed for 4 hours at a hot temperature.
- hot rolling was started at a temperature of 500 ° C., the end temperature was 330 ° C., and a hot rolled plate having a thickness of 2.0 to 3.0 mm was obtained.
- the hot-rolled sheet is cold-rolled without being roughened (annealed) and without being subjected to intermediate annealing in the middle, and the sheet thickness is 0.28 mm.
- the sheet thickness is 0.28 mm.
- the total (total) rolling reduction (%) and the coiling temperature (° C.) of the cold rolling were changed as shown in Table 2.
- 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 the 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 during coating, thereby obtaining a can body test material.
- tissue measurement by 3DAP Measurement by the 3DAP method is performed by cutting three test pieces each having a length of 30 mm and a width of 1 mm from the cold-rolled plate by 1 mm in the width direction with a cutting device, and then thinning the test piece by electrolytic polishing. Then, a needle-like sample having a tip radius of about 50 nm was prepared. For this reason, the measurement location measures the vicinity of the center of the plate thickness.
- the sample with the tip shaped like a needle is subjected to 3DAP measurement using the “LEAP3000”, and the density of atoms aggregates (pieces / m 3 ) defined in the present invention for each of the three test pieces is measured. And averaged (averaged density).
- the measurement volume by the 3DAP method is approximately 1.0 ⁇ 10 ⁇ 24 to 10 ⁇ 21 m 3 .
- the rolling direction of the aluminum alloy plate on the side wall of the can body is A puncture needle whose tip is a hemispherical surface with a radius of 0.5 mm is placed perpendicular to the side wall at a speed of 50 mm / min at a position that matches the can axis direction and the distance L in the can axis direction from the can bottom is 60 mm. Pierced with. And the load (N) until a piercing needle penetrates a side wall was measured, and the obtained maximum load was made into the piercing strength.
- 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 10 has the composition of the aluminum alloy within the scope of the present invention, and is manufactured under preferable manufacturing conditions. For this reason, in each invention example, as shown in Table 2, the cold rolled sheet is within the range of the average density of the aggregate of atoms defined in the present invention.
- 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 11 to 20 in Tables 1 and 2 are out of the composition range of the aluminum alloy, or the conditions in the soaking and cold rolling are out of the preferable conditions of the present invention. For this reason, each comparative example deviates from the average density of the aggregate of atoms defined in the present invention of the cold rolled sheet, is inferior in 0.2% proof stress, is inferior in DI moldability, and all It is inferior to piercing.
- the average heating rate of 200 to 400 ° C. at the second soaking temperature is too small, less than 30 ° C./hour.
- the aggregate of atoms defined in the present invention generated during heating increases, the average density exceeds the upper limit, and the puncture resistance is inferior.
- Comparative Example 14 the coiling temperature in cold rolling is too high, the number of atomic aggregates defined in the present invention of the cold rolled sheet is increased, the average density exceeds the upper limit, and the puncture resistance is inferior. ing.
- Comparative Example 17 has an excessive amount of Mn.
- Comparative Example 18 the amount of Si is excessive.
- Comparative Example 19 the amount of Fe is excessive.
- Comparative Example 20 does not contain Cu. As a result, the strength of the can body is low, and the puncture resistance in the plate width direction when the internal pressure conditions are severe is also poor.
- 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
本発明に係るDI缶胴用アルミニウム合金板の組成は、質量%で、Mn:0.3~1.3%、Mg:0.7~3.0%、Si:0.1~0.5%、Fe:0.1~0.8%、Cu:0.01~0.4%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Cr:0.001~0.1%、Zn:0.05~0.5%の一種または二種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。
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-Mn-Fe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、粗大なAl-Mn-Fe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。
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0.7%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、0.7~3.0%の範囲とし、好ましくは1.0~2.6%、より好ましくは1.2~2.2%とする。
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-Mn-Fe-Si系金属間化合物やMgSi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。
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-Mn-Fe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Mn平均固溶量や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、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。
Cuは、固溶強化によって強度を増加させる。このため、Cuを必須に含有させる。Cu含有量の下限量は0.01%以上、好ましくは0.05%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。
原子の集合体と耐突き刺し性:
以上のアルミニウム合金組成を前提として、耐突き刺し性(耐突き刺し強度)の向上のために、本発明では、DI缶胴用アルミニウム合金板の組織中に存在する、ごく微細な原子の集合体の制御を行う。
本発明では、DI缶胴用のCuを含む3000系アルミニウム合金板の組織につき、3次元アトムプローブ電界イオン顕微鏡により測定される原子の集合体のうち、缶胴組織のサブグレイン化と耐突き刺し性とを制御できる特定の原子の集合体を規定する。
本発明では、以上のように規定され、かつ3DAP分析により測定される、DI缶胴用素材アルミニウム合金板組織における原子の集合体を、この原子の集合体の平均密度で1×1024個/m3以下に規制する。これによって、素材アルミニウム合金板が缶胴に製缶された後に塗装焼付け処理を受けた際の、缶胴組織のサブグレイン化を促進させ、缶胴の耐突き刺し性を向上させる。
原子の集合体の平均密度を、3次元アトムプローブ電界イオン顕微鏡によって測定する方法は、アルミニウム合金材の分野では、例えば、日本国特開2011-184795号公報などが例示される。この公報では、Znを含む5000系アルミニウム合金板の、プレス成形性の向上に寄与する原子集合体を、3次元アトムプローブ電界イオン顕微鏡により測定している。そして、この原子の集合体として、Mg原子かCu原子かのいずれかまたは両方を合計で20個以上含むとともに、これら含まれるMg原子かCu原子のいずれの原子を基準としても、その基準となる原子と隣り合う他の原子のうちのいずれかの原子との互いの距離が0.80nm以下と規定している。そして、このような条件を満たす原子の集合体を1×104個/μm3以上の平均密度で含むことによって、ストレッチャーストレインマークの発生を抑制したアルミニウム合金板を提案している。
但し、これら3DAPによる原子の検出効率は、現在のところ、イオン化した原子のうちの50%程度が限界であり、残りの原子は検出できない。この3DAPによる原子の検出効率が、将来的に向上するなど、大きく変動すると、本発明が規定する原子の集合体の平均個数密度(個/m3)の3DAPによる測定結果が変動してくる可能性がある。したがって、この原子の集合体の平均個数密度の測定に再現性を持たせるためには、3DAPによる原子の検出効率は約50%と略一定にすることが好ましい。
次に、本発明におけるDI缶胴用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、前記組成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、冷間圧延も後述する特定の条件によって行い、冷延後のアルミニウム合金板組織を、本発明で規定する組織とする。
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」あるいは「ひけ巣(Shrinkage cavity)」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。
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。
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が、この熱延条件は常法あるいは一般的な条件の範囲で良く、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。
熱間圧延板は、事前に焼鈍せずに、またパス間での中間焼鈍もせずに、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。冷間圧延における総圧延率は、勿論、冷延板の所望板厚との関係で決まるが、MgとCuの原子の集合体の平均密度を本発明範囲内に制御するための、好ましい巻き取り温度範囲とするためにも、前記範囲とすることが好ましい。
本発明に係る素材アルミニウム合金板(冷延板)からDI缶の缶胴を作製する製缶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。これらの加工による缶胴の側壁の板厚減少率(しごき加工率)は、60~70%とすることが好ましい。そして、側壁(開口部)の縁を切り落として整える(トリミング加工)。この状態で、最薄部の側壁厚さが0.085~0.110mmの範囲の薄肉の缶胴にDI成形される。
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。
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。
前記アルミニウム合金冷延板の組織を、3次元アトムプローブ電界イオン顕微鏡と分析解析ソフトとを用いた前記測定方法により、本発明で規定した原子の集合体の平均密度を測定した。また、缶胴へのDI成形性、0.2%耐力も各々測定した。そして、缶胴(前記塗装焼付け想定の熱処理後)での、耐突き刺し性、0.2%耐力もそれぞれ測定、評価した。これらの結果を表1に続く表2に示す(表1、2の番号は互いに共通する)。
3DAP法による測定は、前記冷延板から、幅方向に1mmずつ間隔をあけて、長さ30mm×幅1mmの試験片を切削装置で3個切りだし、その後電解研磨により、試験片を細く加工し、先端の半径が約50nmの針状試料を作製した。このため測定箇所は、板厚の中心部近傍を測定していることになる。この先端を針状に成形した試料を前記「LEAP3000」を用いて3DAP測定を行い、前記3個の試験片それぞれの本発明で規定する原子の集合体の密度(個/m3)を測定して、平均化(平均密度化)した。ちなみに3DAP法による測定体積はおおよそ1.0×10-24~10-21m3である。
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。
各例について、製缶された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。
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。
本出願は、2012年12月27日出願の日本特許出願(特願2012-285870)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。
Claims (4)
- 質量%で、Mn:0.3~1.3%、Mg:0.7~3.0%、Si:0.1~0.5%、Fe:0.1~0.8%、Cu:0.01~0.4%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であって、3次元アトムプローブ電界イオン顕微鏡により測定された原子の集合体として、その原子の集合体が、Mg原子かCu原子かのいずれかまたは両方を合計で5個以上含むとともに、これら含まれるMg原子かCu原子のいずれの原子を基準としても、その基準となる原子と隣り合う他の原子のうちのいずれかの原子との互いの距離が0.80nm以下であり、これらの条件を満たす原子の集合体の平均密度を1×1024個/m3以下に規制することを特徴とするDI缶胴用アルミニウム合金板。
- 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に記載のDI缶胴用アルミニウム合金板。
- 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または2に記載のDI缶胴用アルミニウム合金板。
- 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に記載のDI缶胴用アルミニウム合金板。
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KR1020157016843A KR101718264B1 (ko) | 2012-12-27 | 2013-12-20 | Di 캔 몸체용 알루미늄 합금판 |
CN201380068059.8A CN104903481B (zh) | 2012-12-27 | 2013-12-20 | Di罐体用铝合金板 |
AU2013367319A AU2013367319B2 (en) | 2012-12-27 | 2013-12-20 | Aluminum alloy sheet for DI can body |
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JP2012-285870 | 2012-12-27 | ||
JP2012285870A JP5848694B2 (ja) | 2012-12-27 | 2012-12-27 | Di缶胴用アルミニウム合金板 |
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PCT/JP2013/084234 WO2014103924A1 (ja) | 2012-12-27 | 2013-12-20 | Di缶胴用アルミニウム合金板 |
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KR (1) | KR101718264B1 (ja) |
CN (1) | CN104903481B (ja) |
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Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN106661681A (zh) * | 2014-09-10 | 2017-05-10 | 株式会社神户制钢所 | 罐体用铝合金板 |
CN114457264A (zh) * | 2022-01-28 | 2022-05-10 | 邹平宏发铝业科技有限公司 | 一种冲压灯具用5系铝合金带材及其加工方法 |
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JP6000437B1 (ja) * | 2015-03-19 | 2016-09-28 | 株式会社神戸製鋼所 | 缶胴用アルミニウム合金板 |
WO2016147816A1 (ja) * | 2015-03-19 | 2016-09-22 | 株式会社神戸製鋼所 | 缶胴用アルミニウム合金板 |
CN106756671B (zh) * | 2016-11-28 | 2018-05-01 | 广西南南铝加工有限公司 | 罐体用铝合金卷材制备方法 |
FR3122666A1 (fr) * | 2021-05-04 | 2022-11-11 | Constellium Neuf-Brisach | FEUILLES D’ALUMINIUM 5xxx POUR FABRICATION DE CANETTES |
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AU2013367319B2 (en) | 2016-11-03 |
KR101718264B1 (ko) | 2017-03-20 |
CN104903481B (zh) | 2017-03-15 |
CN104903481A (zh) | 2015-09-09 |
AU2013367319A1 (en) | 2015-07-02 |
JP2014125677A (ja) | 2014-07-07 |
KR20150087419A (ko) | 2015-07-29 |
JP5848694B2 (ja) | 2016-01-27 |
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