CN105555979A - Aluminum alloy sheet for negative-pressure can lid - Google Patents
Aluminum alloy sheet for negative-pressure can lid Download PDFInfo
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- CN105555979A CN105555979A CN201480051267.1A CN201480051267A CN105555979A CN 105555979 A CN105555979 A CN 105555979A CN 201480051267 A CN201480051267 A CN 201480051267A CN 105555979 A CN105555979 A CN 105555979A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
- C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Containers Opened By Tearing Frangible Portions (AREA)
- Insertion Pins And Rivets (AREA)
- Metal Rolling (AREA)
Abstract
Provided is an Al-Mg-Mn-based aluminum alloy sheet for a negative-pressure can lid which contains Mn at a relatively high concentration, said sheet exhibiting excellent rivet formability even when the thickness thereof is reduced to less than 0.220 mm. The aluminum alloy sheet for a negative pressure can lid contains 0.10-0.40 mass% of Si, 0.20-0.40 mass% of Fe, 0.10-0.30 mass% of Cu, 0.30-1.00 mass% of Mn, 1.00-2.00 mass% of Mg, and further contains, if necessary, 0.05-0.25 mass% of Zn, with the remainder consisting of Al and unavoidable impurities. If the mass percentage of Fe is denoted as [Fe], the mass percentage of Mn is denoted as [Mn] and the mass percentage of Mg is denoted as [Mg], inequality (1) is satisfied. (1): 1.05<=[Fe]+1.07[Mn]+0.27[Mg]<=1.65
Description
Technical field
The present invention relates to negative pressure cover aluminium alloy plate, relate to and guaranteeing that in the necessary intensity as cover, rivet plasticity is excellent especially, be suitable for the negative pressure cover aluminium alloy plate of thin-walled property.
Background technology
Always, particularly as the packaging vessel of beverage, the aluminium pot of the two-piece type be made up of barrel and the cap of bottomed cylindrical is widely used.
< is about the general manufacturing process > of cover
Form the cover of such aluminium pot, with operation manufacture as follows.First, for the cover aluminium alloy plate as former material, implement the chromic salt process for guaranteeing erosion resistance etc. change into process after, described in implementing, change into the one or both sides of the cover aluminium alloy plate of process, carry out application and baking.
Secondly, by after the described cover aluminium alloy plate of application, baking is die-cut into set shape, carries out housing (シ ェ Le) and be shaped.Then, on the cover aluminium alloy plate through described housing molding, be shaped and be used for and the seaming portion (flanging part) of tank body seaming detection and as cover, carry out the compound lining injecting rubber to the seaming portion of this cover.Thereafter, the conversion carrying out comprising following operation is shaped: implement the rivet forming process that film bubble is shaped and button is shaped; Implement the indentation processing of the Pocket Machining of opening portion, implement striped projection (PVC one De) the embossing forming process of the processing of concavo-convex and word etc.; And implement the staking out forming process of additional draw ring.Finally, after filling content to tank body, seaming is carried out to described tank body and the cover implementing described formed machining, carries out cleaning and sterilization.
< is about the requirement characteristic > of cover
When cover and tank body seaming detection, if the size of flanging part has deviation, then there is seaming bad, strict dimensional precision is required for cover.In addition, after not being only required in seaming, even if because of the heating of sterilization process cause in press the compressive strength rising also can not reverse (warpage), and require be delivered to human consumer on hand after, when holding up draw ring (or pull-up) and carrying out can opening, tap hole can be opened without barrier.
< is about the requirement characteristic > of material
In order to obtain such cover, for the aluminium alloy plate as material, require the plasticity being configured as cover, for the low ANISOTROPIC DEFORMATION suppressing seaming bad, for obtaining the strength of materials of compressive strength, for the rivet plasticity and tearability (can opening) etc. of avoiding can opening bad.
On the other hand, all the time, as the cover aluminium alloy of the negative-pressure cup of fruit juice, coffee, black tea etc., use AA5052 and AA5021, but requiring characteristic in view of described, obtaining developing (patent documentation 1 ~ 6) about comparing the technology that existing alloy contains the negative pressure cover aluminium alloy plate of the Mn of higher concentration.
[prior art document]
[patent documentation]
Patent documentation 1: No. 2013-23757, Japanese Unexamined Patent Publication
Patent documentation 2: No. 2005-179758, Japanese Unexamined Patent Publication
Patent documentation 3: No. 2001-348638, Japanese Unexamined Patent Publication
Patent documentation 4: No. 2001-214248, Japanese Unexamined Patent Publication
Patent documentation 5: No. 7-197176, Japanese Unexamined Patent Publication
Patent documentation 6: No. 6-316739, Japanese Unexamined Patent Publication
But, in the embodiment of patent documentation 1 ~ 6, manufacture be the negative pressure cover aluminium alloy plate of the thickness of slab with 0.23 ~ 0.25mm.On the other hand, in recent years, from the view point of reducing costs and saving resource, requiring the further thin-walled property (thickness of slab: lower than 0.220mm) of beverage container, needing negative pressure cover aluminium alloy plate also corresponding thin-walled property.If make negative pressure cover aluminium alloy plate thin-walled property, then compressive strength and rivet plasticity reduce, but about compressive strength, by the design of cover shape, can be guaranteed to a certain extent.Therefore, as negative pressure cover aluminium alloy plate, guaranteeing of rivet plasticity is particularly required.
Cover aluminium alloy plate described in patent documentation 1 ~ 6, by than existing alloy (AA5052, AA5021) higher Mnization, thus Al-Fe-Mn series intermetallic compound is increased, this contributes to the lancinating raising of described aluminium alloy plate and the reduction of ANISOTROPIC DEFORMATION (earing rate).But on the other hand, the Al-Fe-Mn series intermetallic compound of increase becomes starting point and the travel path of be full of cracks, causes disadvantageous effect to the rivet plasticity of described aluminium alloy plate.Therefore, the cover aluminium alloy plate described in patent documentation 1 ~ 6, being also far from being can abundant correspondence thin-walled property further.
Summary of the invention
The present invention in view of prior art the problems referred to above point and formed, its object is to, provide one to compare existing alloy, the negative pressure cover aluminium alloy plate of the Mn containing higher concentration, wherein, even if when making its further thin-walled property, still possess excellent rivet plasticity.
In order to solve described problem, the present inventors find when carrying out various research for the rivet plasticity of the aluminium alloy plate of the Mn containing higher concentration, making after each element in aluminium alloy is set scope, by Fe, Mn, Mg amount being managed in the scope of set relational expression, then rivet plasticity improves.
Negative pressure cover aluminium alloy plate of the present invention, at more than 0.10 quality % and the scope of below 0.40 quality % contains Si, at more than 0.20 quality % and the scope of below 0.40 quality % contains Fe, at more than 0.10 quality % and the scope of below 0.30 quality % contains Cu, at more than 0.30 quality % and the scope of below 1.00 quality % contains Mn, at more than 1.00 quality % and the scope of below 2.00 quality % contains Mg, surplus is made up of Al and inevitable impurity, if the quality % of Fe is [Fe], the quality % of Mn is [Mn], when the quality % of Mg is [Mg], meet following inequality (1).
1.05≤[Fe]+1.07[Mn]+0.27[Mg]≤1.65…(1)
Aluminium alloy plate of the present invention, preferably can also contain Zn at more than 0.05 quality % in the scope of below 0.25 quality %.
Aluminium alloy plate of the present invention, though than existing negative pressure cover aluminium alloy plate more thin-walled property (such as lower than 0.220mm) time, still demonstrate excellent rivet plasticity.In addition, aluminium alloy plate of the present invention, for obtaining the strength of materials of compressive strength, becoming the plasticity, also excellent for the low ANISOTROPIC DEFORMATION, lancinating etc. suppressing seaming bad of cover, mainly can be suitable for as the negative pressure cover of SOT (StayOnTab: remain-type draw ring) formula.
Accompanying drawing explanation
Fig. 1 is the sectional view of the bulging test illustrated for evaluating rivet plasticity.
Embodiment
First, the one-tenth of negative pressure cover aluminium alloy plate of the present invention is grouped into is described.
More than <Si:0.10 quality % and below 0.40 quality % >
Si forms Mg-Si system, Al-Fe-Mn-Si system crystallization thing in aluminium alloy, has the effect of the recrystallize after promoting hot rolling.When the content of Si is lower than 0.10 quality %, the amount of waste that can use in the starting material of aluminium alloy plate reduces, and the purity that aluminium ingot needs uprises, and therefore cost increases.On the other hand, when the content of Si is higher than 0.40 quality %, in the operation by the end of hot rolling, there is fine Al-Fe-Mn-Si system precipitate and hinder the recrystallize after hot rolling in a large number in aluminium alloy, rivet plasticity is reduced.Therefore, the content of Si is more than 0.10 quality % and below 0.40 quality %.
More than <Fe:0.20 quality % and below 0.40 quality % >
Fe forms Al-Fe-Mn system, Al-Fe-Mn-Si system crystallization thing in aluminium alloy, has the effect of the recrystallize after promoting hot rolling.When the content of Fe is lower than 0.20 quality %, described crystallization thing is not enough, and the recrystallize after hot rolling is insufficient, and rivet plasticity reduces.On the other hand, when the content of Fe is higher than 0.40 quality %, the crystallization thing in aluminium alloy plate is large, is formed in addition superfluously, and rivet plasticity reduces.Therefore, the content of Fe is more than 0.20 quality % and below 0.40 quality %.
More than <Cu:0.10 quality % and below 0.30 quality % >
Cu has the effect that the intensity of aluminium alloy plate is improved.When the content of Cu is lower than 0.10 quality %, the intensity of aluminium alloy plate is insufficient, and compressive strength when being configured as cover is not enough.On the other hand, when the content of Cu is higher than 0.30 quality %, the intensity of aluminium alloy plate is superfluous, and rivet plasticity reduces.Therefore, the content of Cu is more than 0.10 quality % and below 0.30 quality %.
More than <Mn:0.30 quality % and below 1.00 quality % >
Mn has the effect that the intensity of aluminium alloy plate is improved, and in aluminium alloy plate, form Al-Fe-Mn system, Al-Fe-Mn-Si system crystallization thing, has the effect of the recrystallize after promoting hot rolling.When the content of Mn is lower than 0.30 quality %, the intensity of aluminium alloy plate is insufficient, and recrystallize after hot rolling is insufficient, and rivet plasticity reduces.On the other hand, when the content of Mn is more than 1.00 quality %, the crystallization thing in aluminium alloy plate is large, is formed in addition superfluously, rivet plasticity is reduced.Therefore, in the scope of the content of Mn, lower limit is 0.30 quality %, and be preferably more than 0.50 quality %, the upper limit is 1.00 quality %, is preferably below 0.50 quality %.
More than <Mg:1.00 quality % and below 2.00 quality % >
Mg has the effect that the intensity of aluminium alloy plate is improved.When the content of Mg is lower than 1.00 quality %, the intensity of aluminium alloy plate is insufficient, and compressive strength when being configured as cover is not enough.On the other hand, when the content of Mg is higher than 2.00 quality %, the intensity of aluminium alloy plate is superfluous, and rivet plasticity reduces.Therefore, in the scope of the content of Mg, lower limit is 1.00 quality %, and be preferably more than 1.2 quality %, the upper limit is 2.00 quality %, is preferably 1.80 quality %, is more preferably below 1.50 quality %.
More than <Zn:0.05 quality % and below 0.25 quality % >
Zn makes the crystal grain miniaturization of aluminium alloy plate, has the effect that rivet plasticity is improved, therefore adds as required.When the content of Zn is lower than 0.05 quality %, cannot fully obtain described effect.On the other hand, when the content of Zn is higher than 0.25 quality %, among cooling after hot rolling etc., Al-Cu-Mg-Zn system precipitate generation grain boundary segregation, rivet plasticity reduces on the contrary.Therefore, when adding Zn, in the scope of content, lower limit is 0.05 quality %, and be preferably 0.08%, be more preferably more than 0.12%, the upper limit is below 0.25 quality %.
The inevitable impurity > of <
Aluminium alloy plate of the present invention, in addition also containing inevitable impurity.As inevitable impurity, Cr, Ti, Zr are respectively below 0.15 quality %, are preferably respectively below 0.05 quality %, as other element, allow in the scope of below 0.05 quality %, to contain V, Ni, In, Sn, Ga etc. respectively.
The aforementioned inequality of < (1) >
Fe, Mn form the crystallization thing of Al-Fe-Mn system, Al-Fe-Mn-Si system in aluminium alloy.In hot rolling, be formed with nonaffine deformation region, strain concentrating at the neighborhood of this crystallization thing, this region becomes recrystallization nucleus, promotes the recrystallize after hot rolling.In addition, Mg makes the accumulation strain in hot rolling increase, and has the effect of the recrystallize after promoting hot rolling.The amount of the accumulation strain that the amount of the crystallization thing that Fe, Mn are formed and Mg bring is complementary from the viewpoint of the recrystallize promoted after hot rolling.If can obtain suitable recrystallized structure after hot rolling, then the rivet plasticity of the cold-reduced sheet (sheet) after cold rolling improves.
On the other hand, if the content of Fe, Mn is superfluous, then form thick crystallization thing, in addition, Mg makes the solidus temperature of aluminium alloy reduce when casting, and crystallization thing is grown.If thick crystallization thing is formed, then this crystallization thing becomes starting point and the travel path of crackle, and rivet plasticity reduces.Therefore, in order to suppress the formation of thick crystallization thing, and obtain suitable positive recrystallized structure after hot rolling, make cold rolling after the rivet plasticity of cold-reduced sheet (sheet) improve, need with the suitable content having relation management Fe, Mn, Mg.
In Al-Mg-Mn line aluminium alloy, the formation of thick crystallization thing, be with [Fe], [Mn], [Mg] for parameter, depend on the size of [Fe]+1.07 [Mn]+0.27 [Mg], this value higher than 1.65 time, thick crystallization produce are raw.On the other hand, the value of [Fe]+1.07 [Mn]+0.27 [Mg] lower than 1.05 time, the effect of Fe, Mn and Mg is not enough, can not obtain suitable recrystallized structure after hot rolling.Namely, be in the scope of 1.05 ~ 1.65 at [Fe]+1.07 [Mn]+0.27 [Mg], the formation of thick crystallization thing can be suppressed, and obtain suitable recrystallized structure after hot rolling, make cold rolling after cold-reduced sheet (sheet) rivet plasticity improve.
Aluminium alloy plate of the present invention, by with casting, the thermal treatment that homogenizes, hot rolling and cold rolling operation manufacture.
Casting uses semicontinuous casting method (DC casts: DirectChill casts).
About the thermal treatment that homogenizes, the ingot bar obtained via DC casting to be kept at 480 ~ 620 DEG C the condition of 2 ~ 10 hours, carry out 1 time or 2 times.When treatment temp is lower than 480 DEG C, homogenizing of solute element is insufficient, if treatment temp is higher than 620 DEG C, then the melting (burning) of locality likely occurs on the surface of ingot bar.If the hold-time is more than 2 hours, then can homogenize, if more than 10 hours, then waste energy cost.This thermal treatment that homogenizes, holds a concurrent post the preparation heating of subsequent hot rolled.
Hot rolling preferably combination roughing (reversible rolling) and finish rolling (continuous rolling) and carry out.The end temp (coiling temperature) of hot rolling is 300 ~ 370 DEG C.By batching in this temperature, hot-rolled sheet becomes recrystallized structure.In order to obtain excellent rivet plasticity in the aluminium alloy plate after cold rolling, the recrystallize rate of hot-rolled sheet is needed to be more than 90% (non-recrystallization portion is lower than 10%).When coiling temperature is below 300 DEG C, the recrystallize rate of hot-rolled sheet reduces, and the rivet plasticity of the cold-reduced sheet (sheet) after cold rolling reduces.
The cold rolling shrinkage of rolling with 80 ~ 93% is carried out, and does not carry out process annealing before cold rolling or in way.Cold rolling roll shrinkage lower than 80% time, as the undercapacity of cover, if higher than 93%, then yield strength excessively improves, and plasticity reduces, and ANISOTROPIC DEFORMATION (earing rate) becomes large in addition.
Further, manufacturing process described above and condition, compare with condition with the manufacturing process of existing negative pressure cover aluminium alloy plate, do not change especially.
[embodiment]
By semicontinuous casting method (DC), make the aluminium alloy shown in table 1 become the ingot bar of thick 600mm, the facing of 15mm is carried out for ingot bar top layer and makes slab.Homogenize thermal treatment, hot rolling and cold rolling are implemented for this slab, is processed into the negative pressure cover aluminium alloy plate of thickness of slab 0.210mm eventually.Homogenize the condition processed, and coiling temperature and the cold rolling shrinkage of rolling of hot rolling show in Table 1.
Using the aluminium alloy plate (hot rolling material) after hot rolling as examination material, try to achieve recrystallize rate by following main points.In addition, the aluminium alloy plate (cold-reduced sheet) after cold rolling tries material as confession, measures 0.2% yield strength and rivet plasticity by following main points.
< recrystallize Shuai Measuring determines >
Test film is cut for examination material from each, imbed grinding resin in the mode can observing the cross section parallel with thickness of slab direction with rolling direction, same cross section to be ground and as minute surface, then after etching, utilize the observation by light microscope crystal structure of multiplying power 100 times, measure recrystallize rate.If be t for the thickness of slab of examination material, the thickness of the recrystallized structure that thickness of slab direction is measured is t
r, the thickness in identical non-recrystallization portion is t
ntime, t=t
r+ t
n, recrystallize rate is according to (t
r/ t) × 100 calculating.Further, recrystallized structure is made up of equi-axed crystal, and non-recrystallization portion is the worked structure of extending along rolling direction.The proper range of recrystallize rate is more than 90%.If recrystallize rate is more than 90%, then can not there is problem in the rivet plasticity of the cold-reduced sheet (aluminium alloy plate) after cold rolling.In Table 1, it is more than 90% that zero mark on recrystallize rate one hurdle is meant to recrystallize rate, and × mark is meant to lower than 90%.
<0.2% yield strength >
For each for examination material, after implementing the thermal treatment of 250 DEG C × 20 seconds carried out with oil bath of simulation coating baking operation, make the JIS-5 tension test sheet that draw direction is parallel with rolling direction, the regulation according to JISZ2241 carries out tension test, tries to achieve 0.2% yield strength.The OK range of 0.2% yield strength is more than 240MPa.If 0.2% yield strength is more than 240MPa, even the cover of then thin-walled property, still meet compressive strength.
The measurement > of < rivet plasticity
For each for examination material, after implementing the thermal treatment of 250 DEG C × 20 seconds carried out with oil bath of simulation coating baking operation, by each test film making 50mm × 50mm for examination material, implement the bulging test of simulation foamed process, try to achieve limit bulging height.Test film 1 as shown in Figure 1, is clipped between upper and lower punch die 2,3, fixes with certain pressure-pad-force by bulging test, makes the central part of drift 4 pairs of test films 1 vertically be pressed into and carry out bulging processing.In punch die 2,3, the internal diameter of die cavity is 6.60mm, and shoulder radii is 0.40mm, and its external diameter of drift 4 is 6.00mm, and the diameter of the central planar portion of head is 1mm, and the shoulder radii of head is 2.50mm.
By this bulging test, there is not crackle and necking down and can carry out the threshold value (limit bulging height) of the bulging height of bulging processing in experiment with measuring sheet 1.The proper range of boundary bulging height is more than 1.45mm.If boundary bulging height is more than 1.45mm, then the button that can be shaped fully highly during actual shaping, rivet has excellent formability, and can firmly fix draw ring by staking out operation.Further, if draw ring is fixing insufficient, then there is draw ring during can opening and come off and problem that tap hole cannot be opened.
As shown in table 1, the content of each composition is in specialized range of the present invention, and Fe, Mn and Mg content meets No.1 ~ 8 of described inequality (1), and the recrystallize rate of hot rolling material is up to more than 90%, the yield strength of cold rolling material is high, and rivet has excellent formability.
On the other hand, the content of any one composition is outside specialized range of the present invention, or Fe, Mn and Mg content does not meet No.9 ~ 23 of described inequality (1), and a certain item of yield strength or rivet plasticity is poorer than No.1 ~ 8.Wherein, No.9 is because Si content is superfluous, No.10 is because Fe is containing quantity not sufficient, No.13 is because Mn is containing quantity not sufficient, No.23 is not because Fe, Mn and Mg content meets described inequality (1) (value at the middle part of inequality (1) is lower than 1.05), so recrystallize rate is all low, rivet plasticity is poor.No.11 is because Cu is containing quantity not sufficient, and No.15 is because Mg is containing quantity not sufficient, so yield strength is all low.No.12,14,16,17,19 because Cu, Mn, Mg, Zn, Fe any one is above superfluous, so rivet plasticity is poor.Specifically, in No.12 in Cu content, No.14 in Mn content, No.16 in Mg content, No.17 in Zn content, No.19 Fe content respectively superfluous.In No.18,20,21,22, Fe, Mn and Mg content does not meet described inequality (1) (value at the middle part of inequality (1) is higher than 1.65), and No.18,20 in addition Fe or Mn is superfluous, and therefore rivet plasticity is poor.
Further, No.18 is equivalent to the alloy C of the embodiment of patent documentation 1, and No.19 is equivalent to the alloy G of the embodiment of patent documentation 1, and No.20 is equivalent to the alloy No.2 of the embodiment of patent documentation 3, and No.21 is equivalent to the alloy No.4 of patent documentation 4.
[explanation of symbol]
1 aluminium alloy plate
2,3 punch dies
4 drifts
Claims (2)
1. a negative pressure cover aluminium alloy plate, it is characterized in that, at more than 0.10 quality % and the scope of below 0.40 quality % contains Si, at more than 0.20 quality % and the scope of below 0.40 quality % contains Fe, at more than 0.10 quality % and the scope of below 0.30 quality % contains Cu, at more than 0.30 quality % and the scope of below 1.00 quality % contains Mn, at more than 1.00 quality % and the scope of below 2.00 quality % contains Mg, surplus is made up of Al and inevitable impurity, if the quality % of Fe is [Fe], the quality % of Mn is [Mn], when the quality % of Mg is [Mg], meet following inequality (1),
1.05≤[Fe]+1.07[Mn]+0.27[Mg]≤1.65…(1)。
2. negative pressure cover aluminium alloy plate according to claim 1, is characterized in that, also at more than 0.05 quality % and the scope of below 0.25 quality % contains Zn.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2013-194734 | 2013-09-20 | ||
| JP2013194734A JP5699192B2 (en) | 2013-09-20 | 2013-09-20 | Aluminum alloy plate for negative pressure can lid |
| PCT/JP2014/072591 WO2015041021A1 (en) | 2013-09-20 | 2014-08-28 | Aluminum alloy sheet for negative-pressure can lid |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN105555979A true CN105555979A (en) | 2016-05-04 |
Family
ID=52688676
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201480051267.1A Pending CN105555979A (en) | 2013-09-20 | 2014-08-28 | Aluminum alloy sheet for negative-pressure can lid |
Country Status (3)
| Country | Link |
|---|---|
| JP (1) | JP5699192B2 (en) |
| CN (1) | CN105555979A (en) |
| WO (1) | WO2015041021A1 (en) |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61152549A (en) * | 1984-12-19 | 1986-07-11 | 東洋製罐株式会社 | Can |
| CN101538665A (en) * | 2008-03-19 | 2009-09-23 | 株式会社神户制钢所 | Aluminum alloy plate for battery box and manufacturing method thereof |
| CN102206775A (en) * | 2010-03-30 | 2011-10-05 | 株式会社神户制钢所 | Aluminum alloy plate for cell box and cell box |
| WO2013118611A1 (en) * | 2012-02-09 | 2013-08-15 | 株式会社神戸製鋼所 | Aluminum alloy sheet for di can body |
Family Cites Families (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS63227738A (en) * | 1987-03-16 | 1988-09-22 | Sumitomo Light Metal Ind Ltd | Corrosion resistant aluminum alloy composite plate and its production |
| JP2000355723A (en) * | 1999-06-16 | 2000-12-26 | Kobe Steel Ltd | Aluminum alloy sheet and its production |
| JP3998387B2 (en) * | 2000-01-28 | 2007-10-24 | 古河スカイ株式会社 | Manufacturing method of aluminum alloy hard plate for can lid |
-
2013
- 2013-09-20 JP JP2013194734A patent/JP5699192B2/en not_active Expired - Fee Related
-
2014
- 2014-08-28 CN CN201480051267.1A patent/CN105555979A/en active Pending
- 2014-08-28 WO PCT/JP2014/072591 patent/WO2015041021A1/en active Application Filing
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61152549A (en) * | 1984-12-19 | 1986-07-11 | 東洋製罐株式会社 | Can |
| CN101538665A (en) * | 2008-03-19 | 2009-09-23 | 株式会社神户制钢所 | Aluminum alloy plate for battery box and manufacturing method thereof |
| CN102206775A (en) * | 2010-03-30 | 2011-10-05 | 株式会社神户制钢所 | Aluminum alloy plate for cell box and cell box |
| WO2013118611A1 (en) * | 2012-02-09 | 2013-08-15 | 株式会社神戸製鋼所 | Aluminum alloy sheet for di can body |
Also Published As
| Publication number | Publication date |
|---|---|
| WO2015041021A1 (en) | 2015-03-26 |
| JP5699192B2 (en) | 2015-04-08 |
| JP2015059251A (en) | 2015-03-30 |
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| C06 | Publication | ||
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Application publication date: 20160504 |