CN108368570A - Tank body aluminium alloy plate and its manufacturing method - Google Patents
Tank body aluminium alloy plate and its manufacturing method Download PDFInfo
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- CN108368570A CN108368570A CN201680071616.5A CN201680071616A CN108368570A CN 108368570 A CN108368570 A CN 108368570A CN 201680071616 A CN201680071616 A CN 201680071616A CN 108368570 A CN108368570 A CN 108368570A
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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
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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
- 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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- 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
- C22F1/05—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 of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions
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- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
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- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Metal Rolling (AREA)
- Conductive Materials (AREA)
- Continuous Casting (AREA)
Abstract
The present invention provides a kind of Al alloy sheets and its manufacturing method with the excellent characteristic as tank body.The tank body is with the composition of Al alloy sheets, using the Al alloys comprising defined composition of alloy as in the plank of material, solid solution Mn amounts after hot rolling are 0.25 mass % or more, it is 0.07 mass % or more that Fe amounts, which are dissolved, as 0.02 mass % or more and solid solution Si amounts, and conductivity is 30.0~40.0%IACS, the tensile strength of rolling direction in cold-reduced sheet is 280~320MPa, the tensile strength of rolling direction after heat treatment in 205 DEG C × 10 minutes is 270~310MPa, and the difference of the yield strength of the rolling direction after the tensile strength of rolling direction and heat treatment in 205 DEG C × 10 minutes is 50MPa or less.
Description
Technical field
The present invention relates to tank body aluminium alloy plate and its manufacturing methods, can be played when more particularly, to manufacture tank body excellent
The aluminium alloy plate of characteristic and its effective manufacturing method.
Background technology
In the past, for tank body aluminium (Al) alloy sheets, it is well known that can be by implementing the place that homogenizes to Al alloy cast ingots
Reason, hot rolling and cold rolling manufacture.Moreover, for tank body Al alloy sheets, after implementing cleaning by degreasing, oiling etc. as needed,
Further via processes such as cup body molding, DI moldings, trimming, cleaning, dry, coating, baking, necking down and crimping processing, can make
Make the tank body of beverage use etc..
However, the tank body of beverage use etc., which needs to have, stands the tank intensity used, and the baking after above-mentioned coating
In roasting process (hereinafter referred to as applying roasting procedure), tank intensity can substantially reduce.It is dropped accordingly, with respect to this tank intensity is prevented
It is low, it is proposed that various suggestions, for example, disclosing following technology.
That is, being that one kind including specific alloy group disclosed in Japanese Unexamined Patent Publication 2012-92431 bulletins (patent document 1)
At Bottle ＆ Can Al alloy cold-reduced sheets, the central diameter represented with α Xiang Wei in being knitted by reducing board group is less than 1 μm of dispersion
Grain, and for as Al6The β phases of (Fe, Mn) series intermetallic compound with as Al-Fe-Mn-Si series intermetallic compounds
α phases there are ratio, keep the maximum at the X-ray diffraction peak of the maximum height H β and α phases at the X-ray diffraction peak of above-mentioned β phases high
It is 0.50 or more to spend in the ratio between H α H β/H α, and the recrystallization ratio of the plate width direction of hot rolled plate is homogenized, plate width direction can be reduced
Earing rate unevenness.
In addition, being that one kind including specific alloy disclosed in Japanese Unexamined Patent Publication 2011-202273 bulletins (patent document 2)
The Bottle ＆ Can of composition Al alloy cold-reduced sheets, by the solid solution capacity of Fe and Mn in control panel tissue, can increase in hot rolled plate at
For a number density of the bigger discrete particles of the nucleation site of recrystallization, promote the central portion of the plate width direction in hot rolled plate
The recrystallization of side, especially plate thickness central part homogenizes the recrystallization ratio of the plate width direction of hot rolled plate, and then reduces the wide side of plate
To earing rate unevenness.
On the other hand, in recent years, the viewpoint based on environmental protection, in the manufacture of Used for Making Beverage Container Body, recycling uses
Beverage can (the UBC crossed：Used Beverage Can) reconstituting piece become an important project.Moreover, in order to cut down material
Dosage is expected, also in the light thin-wall for promoting tank body.Then, since the situation for being mixed into Si or Fe etc. in the reconstituting piece of UBC is more,
Therefore, when the reconstituting piece of recycled UBC, Si or Fe can be contained in obtained Al alloy cast ingots in high concentration.This
In the case of, when heating Al alloy cast ingots, Si and Mn or Fe form intermetallic compound, cause the reduction of Mn solid solution capacities.
As a result, the reduction that the heat-resisting property of softening of Al alloy sheets reduced, applied the tank intensity in roasting procedure is caused to become more to show
The problem of work.In addition, in the case where the strength reduction in considering coating roasting procedure improves the initial strength of Al alloy sheets,
Get thinner the plate thickness in tank skin portion in the presence of the light thin-wall by tank body, DI molding when be more easy to happen asking for tank rupture
Topic.Thus, when manufacturing Used for Making Beverage Container Body, need to limit its dosage in the reconstituting piece of recycling UBC, and new metal is added
To adjust the content of Si.
It should be noted that disclosed in Patent Document 1 is the generation for inhibiting the precipitation particle (α phases) less than 1 μm, and
It is disclosed in Patent Document 2 be only the solid solution capacity of regulation Fe and Mn, promote hot rolling when recrystallization, only control earing rate, therefore,
Tank intensity and earing rate cannot be taken into account, and does not pay attention to the solid solution capacity of Fe, Mn, Si and the fine precipitation particle in cold rolling
(α phases).
Existing technical literature
Patent document
Patent document 1：Japanese Unexamined Patent Publication 2012-92431 bulletins
Patent document 2：Japanese Unexamined Patent Publication 2011-202273 bulletins
Invention content
Problems to be solved by the invention
Here, the present invention is completed using situation as described above as background, the project to be solved is to provide one kind
Al alloy sheets with the excellent characteristic as tank body and its manufacturing method, additionally, it is provided a kind of tank body Al alloy sheets
And its manufacturing method, wherein by will be fine in the solid solution capacity of Fe, Mn, Si in the cold-reduced sheet of Al alloys and cold rolling
Particle (α phases) is precipitated to optimize, the reduction of tank intensity can be effectively inhibited, especially influence the heat of the problems such as tank rupture
The reduction of treated tank intensity.
The solution to the problem
Then, to solve problem as described above, idea of the invention is that a kind of tank body Al alloy sheets, feature
It is, is by using the plank constituted as cold-reduced sheet obtained from the hot rolled plate of material using Al alloys, the Al alloys are with matter
Amount benchmark meter contains：Mn：0.7~1.3%, Mg：0.8~1.5%, Fe：0.25~0.6%, Si：0.25~0.50%, Cu：
0.10~0.30%, Zn：0.25% or less, Ti：0.10% or less and B：0.05% hereinafter, surplus by Al and inevitably it is miscellaneous
Matter forms, and the solid solution Mn amounts in the hot rolled plate are 0.25 mass % or more, solid solution Fe amounts are 0.02 mass % or more and solid solution Si
Amount is 0.07 mass % or more, and conductivity is 30.0~40.0%IACS, the tensile strength of the rolling direction in the cold-reduced sheet
(TS) be 280~320MPa, the tensile strength (ABTS) of rolling direction after heat treatment in 205 DEG C × 10 minutes be 270~
310MPa, and the tensile strength (TS) of aforementioned rolling direction and the rolling direction after heat treatment in 205 DEG C × 10 minutes are bent
The difference for taking intensity (yield strength, ABYS) is 50MPa or less.
In addition, the purport of the present invention also resides in a kind of tank body aluminum alloy hot rolling band, which is characterized in that it is with aluminium alloy
For the hot rolled plate of material, the aluminium alloy is contained in terms of quality criteria：Mn：0.7~1.3%, Mg：0.8~1.5%, Fe：0.25
~0.6%, Si：0.25~0.50%, Cu：0.10~0.30%, Zn：0.25% or less, Ti：0.10% or less and B：0.05%
Hereinafter, surplus is made of Al and inevitable impurity, the aluminum alloy hot rolling band contains the solid solution Mn of 0.25 mass % or more
The solid solution Si amounts of amount, solid solution the Fe amounts and 0.07 mass % or more of 0.02 mass % or more, and there is 30.0~40.0%IACS
Conductivity.
In turn, purport of the invention also resides in a kind of tank body aluminium alloy plate, which is characterized in that it is using aluminium alloy as material
The plank of matter, the aluminium alloy are contained in terms of quality criteria：Mn：0.7~1.3%, Mg：0.8~1.5%, Fe：0.25~
0.6%, Si：0.25~0.50%, Cu：0.10~0.30%, Zn：0.25% or less, Ti：0.10% or less and B：0.05% with
Under, surplus is made of Al and inevitable impurity, and the tensile strength (TS) of the rolling direction of the aluminium alloy plate is 280~
The tensile strength (ABTS) of 320MPa, the rolling direction after heat treatment in 205 DEG C × 10 minutes are 270~310MPa, Er Qieqian
State rolling direction tensile strength (TS) and the rolling direction after heat treatment in 205 DEG C × 10 minutes yield strength (ABYS) it
Difference is 50MPa or less.
It should be noted that the tank body of aforementioned present invention preferably has 28.4%IACS~39.8%IACS with Al alloy sheets
Conductivity.
Moreover, in order to manufacture tank body present invention as described above Al alloy sheets, it includes following process preferably to use
Manufacturing method：(a) prepare using aluminium alloy as the process of the aluminium alloy cast ingot of material, the aluminium alloy is contained in terms of quality criteria
Have：Mn：0.7~1.3%, Mg：0.8~1.5%, Fe：0.25~0.6%, Si：0.25~0.50%, Cu：0.10~
0.30%, Zn：0.25% or less, Ti：0.10% or less and B：0.05% hereinafter, surplus by Al and inevitable impurity group
At；(b) above-mentioned aluminium alloy cast ingot is used, hot rolling is implemented, the solid solution Mn amounts of the process for obtaining hot rolled plate, the hot rolled plate are
0.25 mass % or more, solid solution Fe amounts are 0.02 mass % or more and solid solution Si amounts are 0.07 mass % or more, and conductivity is
30.0~40.0%IACS；(c) cold rolling, the process for forming cold rolled sheet are carried out to the hot rolled plate, the cold rolled sheet rolls
The tensile strength (TS) in direction processed is the tensile strength of the rolling direction after 280~320MPa, heat treatment in 205 DEG C × 10 minutes
(ABTS) it is 270~310MPa, and after the tensile strength (TS) of aforementioned rolling direction and heat treatment in 205 DEG C × 10 minutes
The difference of the yield strength (ABYS) of rolling direction is 50MPa or less.
In addition, in order to advantageously manufacture tank body Al alloy sheets as described above, idea of the invention is that a kind of tank body
With the manufacturing method of Al alloy sheets, which is characterized in that carrying out facing cut by the Al alloy cast ingots of material of Al alloys, the Al is closed
Gold is contained in terms of quality criteria：Mn：0.7~1.3%, Mg：0.8~1.5%, Fe：0.25~0.6%, Si：0.25~
0.50%, Cu：0.10~0.30%, Zn：0.25% or less, Ti：0.10% or less and B：0.05% hereinafter, surplus by Al and not
Evitable impurity composition, then, makes it be heated to 550~620 DEG C of model with 30~120 DEG C/h of heating rate
Interior homogenize process temperature (T) is enclosed, then between the homogenize process temperature (T) holding (145-0.24T) is more than hour,
Thus implement homogenize process, then after above-mentioned homogenize process, immediately or with 10~90 DEG C/h of cooling
Speed is cooled to after the hot rolling start temperature not less than 500 DEG C, is implemented in a manner of making outlet side temperature be 430~550 DEG C
Hot roughing, to formed plate thickness be 20~40mm plank, next by make outlet side temperature be 300~390 DEG C in a manner of into
Row hot finishing, to form the plank that plate thickness is 1.5~4.0mm, then so that total degree of finish is 75% or more and final passage
The average mill speed in stable state portion be that 700~1600m/ minute modes carry out cold rolling, to become the plate of 0.2~1.0mm
It is thick.
It should be noted that one of the preferred embodiment of manufacturing method of the tank body of aforementioned present invention Al alloy sheets is, with
Make the conductivity of the conductivity (S1) and the plank as obtained from aforementioned cold rolling of the plank as obtained from aforementioned hot finishing
(S2) difference (S1-S2) is that the mode of 0.2~1.6%IACS is adjusted.
In addition, the composition of other preferred embodiments of the manufacturing method of the tank body aluminium alloy plate of the present invention is before making to be directed to
In the scanning electron microscope photo for stating the Al alloy cast ingots for implementing homogenize process, a diameter of 0.1 μm~1 μm of particle
Area occupation ratio be 3.5% or more.
In turn, object of the invention also resides in a kind of Used for Making Beverage Container Body, which is characterized in that by above-mentioned tank body aluminium alloy plate
It constitutes.
It should be noted that one of the preferred embodiment of Used for Making Beverage Container Body of aforementioned present invention is closed with aluminium to above-mentioned tank body
Golden plate applies baking processing as defined in implementing.
The effect of invention
Thus, in the tank body for forming the composition of aforementioned present invention in Al alloy sheets, by making the acquisition Al alloy sheets
Including the solid solution capacity of Fe, Mn, Si in the hot rolled plate of the Al alloys of specific composition of alloy and in above-mentioned hot rolled plate
The fine precipitation particle (α phases) being precipitated in cold rolling optimizes, it can be ensured that excellent mouldability, and can assign higher heat-resisting
Softening properties, and excellent tank intensity can be played after heat treatment, thereby, it is possible to be advantageously used for tank body to use
Material.
In addition, manufacturing method of the tank body according to the present invention with Al alloy sheets, industrially can advantageously manufacture with simultaneous
Care for the tank body Al alloy sheets of the excellent characteristic of tank intensity after mouldability as described above and heat treatment etc..
Description of the drawings
Fig. 1 is to indicate for two kinds of different Al alloy materials of composition of alloy, implement compression process at a temperature of 150 DEG C
When conductivity variable quantity chart.
Specific implementation mode
First, the Al alloys for providing the tank body Al alloy sheets of the present invention have following composition of alloy, contain：Mn：0.7
~1.3% (quality criteria, same as below), Mg：0.8~1.5%, Fe：0.25~0.6%, Si：0.25~0.50%, Cu：
0.10~0.30%, Zn：0.25% or less, Ti：0.10% or less and B：0.05% hereinafter, surplus by Al and inevitably it is miscellaneous
Matter forms, and the restriction reason of these alloying components is as described below.
[Mn：0.7~1.3%]
Mn (manganese) is that the basic alloy element in the Al alloy sheets of the present invention is especially being dissolved other than increasing intensity
The heat-resisting property of softening is helped to improve under state.In addition, in manufacturing process, even if there is the impurity element for including inevitably
α phases compound (Al-Mn-Fe-Si systems) is formed with Fe and Si.The hardness of the particle of the intermetallic compound is very high, prevents
The burning of raw material and molding die when molding is viscous and improves the effect of the surface characteristic of container.When the content of the Mn is less than
When 0.7%, it cannot fully show these effects, and when the content of the Mn is more than 1.3%, intensity can be caused to become excessively high and asked
Topic.It should be noted that the preferred content of the Mn is 0.8~1.2%.
[Mg：0.8~1.5%]
Mg (magnesium) is the ingredient for contributing to increase the intensity of container by being solid-solution in Al.When the content of the Mg is less than
When 0.8%, there are problems that final products are difficult to obtain required intensity, and when the content of the Mg is more than 1.5%, it can cause
Because tank intensity, which becomes excessively high, damages mouldability the problem of.It should be noted that the preferred content of the Mg is 1.0~1.3%.
[Fe：0.25~0.6%]
Fe (iron) is that Al is formed together with Mn in casting6(Mn, Fe) phase compound, α phase compounds (Al-Mn-Fe-Si
System) and form Al-Fe-Si based compounds and by the solid lubrication of these intermetallic compounds effect come when preventing molding
The viscous ingredient of the burning of raw material and molding die.When the content of the Fe is less than 0.25%, the quantity of these intermetallic compounds
It tails off, can cause to be adhered to mold when DI is molded and surface characteristic the problem of reducing.On the other hand, when the content of the Fe is more than
When 0.6%, it may appear that because the intermetallic compound of Al-Fe-Mn systems formed too much and as crackle starting point to damage at
The problem of type.It should be noted that the preferred content of the Fe is 0.30~0.50%.
[Si：0.25~0.50%]
Si (silicon) is with α phase compound (Al-Mn- of the formation with solid lubrication effect together with above-mentioned Mn and/or Fe
Fe-Si systems), Al-Fe-Si based compounds to prevent molding when the effect adhered to mold.Content of the effect in Si is less than
It is insufficient when 0.25%, and when the content of Si is more than 0.50%, it may appear that the intermetallic compound of Al-Mn-Fe-Si systems is excessive
Ground forms and becomes the starting point of crackle and reduced to damage mouldability and then be dissolved Mn amounts to which what the heat-resisting property of softening reduced asks
Topic.It should be noted that the preferred content of the Si is 0.30~0.40%.
[Cu：0.10~0.30%]
Cu (copper) forms Al-Cu-Mg series intermetallic compounds in applying roasting procedure and makes its precipitation, to play suppression
System or the effect for preventing the strength reduction in coating roasting procedure.When the content of Cu is less than 0.10%, cannot fully obtain
The effect can cause processing curability when processing and forming to become larger, mouldability drop on the contrary when the content of Cu is more than 0.30%
Low problem.It should be noted that the preferred content of the Cu is 0.15~0.25%.
[Zn：0.25% or less]
Zn (zinc) be improve mouldability ingredient, but its containing quantitative change it is more when, other than cost is got higher, can also cause to be formed
Coarse intermetallic compound and the problem of damage mouldability.Thus, to make the content of Zn be to be carried out in a manner of 0.25% below
It adjusts.It should be noted that the preferred content of the Zn is 0.05~0.20%.
[Ti：0.10% or less and B：0.05% or less]
Ti (titanium) and B (boron) have make cast sturcture imperceptibility, make the crystal generated when casting dispersing mode and
The function of grain structure homogenization.However, when the content that the content of Ti is more than 0.10% or B is more than 0.05%, can generate thick
Big intermetallic compound, to which mouldability reduces.It should be noted that the preferred content of these Ti and B is respectively 0.03%
Below and 0.04% or less.
[the inevitable impurity of Al+：Surplus]
For as the present invention tank body Al alloy sheets material Al alloys for, in addition to above-mentioned alloying component with
Outside, surplus is made of the element other than the alloying component of Al (aluminium) and inevitable impurity, that is, above-mentioned.It should be noted that being
Plate characteristic is not set to deteriorate, the content of above-mentioned inevitable impurity the few the more preferred, be typically set to the defineds such as JIS standards
The upper limit extent value content below of each element of Al alloys.Moreover, becoming the total of each element of above-mentioned inevitable impurity
Content is usually 0.15% or less, preferably 0.10% or less.
Moreover, using the Al alloys of this composition of alloy as material the present invention Al alloy sheets in so that (cold after hot rolling
Before rolling) solid solution Mn amounts be 0.25 mass % or more, solid solution Fe amounts be 0.02 mass % or more and be dissolved Si amounts be 0.07 matter
Amount % or more and conductivity is constituted for the mode of 30.0~40.0%IACS, can show higher resistance to thermal softening as a result,
Property.When the solid solution quantitative change of these elements is more, as described later, by cold rolling, the chemical combination for including Mn, Fe, Si can be imperceptibly formed
Composition granule.In addition, solid solution capacity of these elements in hot rolled plate is limited by content of each element in Al alloys, pass through this
The solid solution capacity of a little elements is 40.0%IACS come the maximum conductivity realized, moreover, even if solid to the maximum extent in addition element
In the case of molten, conductivity is also 30.0%IACS or more.It should be noted that the solid solution capacity when these elements becomes than above-mentioned
When the lower limiting value of defined also lacks, in applying roasting procedure, intensity can significantly reduce.
In addition, for the Al alloy sheets of the present invention, as raw sheet characteristic, the tensile strength with its rolling direction
(TS) characteristic for being 280~320MPa.When above-mentioned tensile strength (TS) becomes less than 280MPa, exists and use above-mentioned Al alloys
The problem of the intensity deficiency of the tank body of plate manufacture, and when above-mentioned tensile strength (TS) is more than 320MPa, it may appear that DI moldings become
Obtain difficult problem.In turn, Al alloy sheets of the invention are with the anti-of the rolling direction after heat treatment in its 205 DEG C × 10 minutes
Tensile strength (ABTS) is the characteristic of 270~310MPa.The tensile strength (ABTS) of rolling direction after the heat treatment becomes small
When 270MPa, there is a problem of tank intensity deficiency, on the other hand, when it is more than 310MPa, DI moldings can be caused to become
Difficult problem.In addition, for the Al alloy sheets of the present invention, so that the tensile strength (TS) and 205 DEG C × 10 of its rolling direction
Mode of the difference (TS-ABYS) of the yield strength (ABYS) of rolling direction after the heat treatment of minute no more than 50MPa is adjusted
Section, thereby, it is possible to advantageously take into account the mouldability of Al alloy sheets with after the heat treatment of the tank body obtained using above-mentioned Al alloy sheets
Tank intensity.
However, when manufacturing the Al alloy sheets of this present invention, first, it will thus provide the material of foregoing Al composition of alloy
Material melts, and after forming Al alloy molten solutions, Al alloy cast ingots are manufactured by well known casting method, such as DC castings.It needs
Bright, above-mentioned Al alloy cast ingots have to be made of the content of Mn, Mg, Fe, Si, Cu, Zn, Ti and B given to this invention
Composition of alloy.
Next, after implementing facing cut same to above-mentioned Al alloy cast ingots, Al alloys of the invention in order to obtain
The characteristic of plate can implement specific homogenize process.That is, above-mentioned homogenize process is implemented by the following method：For implementing
The Al alloy cast ingots of facing cut, are heated to equal in the range of 550~620 DEG C with 30~120 DEG C/h of heating rate
Matter treatment temperature (T：DEG C), then, (145-0.24T) hour (Hr) or more is kept at above-mentioned homogenize process temperature (T)
Between.It should be noted that when above-mentioned heating rate becomes slower than 30 DEG C/h, the holding time of device is elongated, is manufactured into
This increase, and when above-mentioned heating rate becomes faster than 120 DEG C/h, fine particle can be formed in large quantities, and there are intensity changes
Obtain the problem of excessively high, mouldability deteriorates.In addition, when homogenize process temperature (T) gets lower than 550 DEG C, cannot fully obtain
On the other hand the effect of homogenize process when homogenize process temperature (T) becomes 620 DEG C or more, can cause material part molten
The problem of melting, being significantly reduced to mouldability.The homogenize process is in addition to element present in elimination Al alloy cast ingots
It is segregated and is formed other than the feature uniformly organized, also having makes coarse α phase compounds be precipitated, when preventing from being molded to play
The viscous effect of burning feature.Moreover, by making the retention time of the homogenize process be (145-0.24T) more than hour,
Using scanning electron microscope with 100 times~20000 times of multiplying power to the section structures of the processed Al alloy cast ingots into
In the photo of row observation, the area occupation ratio of a diameter of 0.1 μm~1 μm of particle becomes 3.5% or more, viscous this makes it possible to obtain preventing from burning
Effect, and as can ensure the state of the effective heat-resisting property of softening in order to obtain and the solid solution capacity of required Mn, Fe, Si.
It should be noted that the upper limit of the retention time as the homogenize process, considers from viewpoints such as productivities, it usually can be advantageously
Using 30 hours or less, preferably 20 hours or less.
Then, after above-mentioned homogenize process, for Al alloy cast ingots, in addition to can directly (immediately) for hot rolling
In addition, additionally it is possible to which temperature is started with the hot rolling that 10~90 DEG C/h of cooling velocity is cooled to not less than 500 DEG C (500 DEG C or more)
Implement hot rolling after degree.It should be noted that in the case where implementing cooling to Al alloy cast ingots, it is less than in its cooling velocity (slow
In) in the case of 10 DEG C/h or in the case of being cooled to temperature less than 500 DEG C, it may appear that following problem：In its bosher
In sequence, Mn, Fe, Si are precipitated and the solid solution capacity of these elements are made to reduce, and include the micro- of Mn, Fe, Si in following cold rolling as a result,
Fine grain precipitation becomes inadequate, and the heat-resisting property of softening reduces.In addition, being more than 90 DEG C/h of (being faster than) in above-mentioned cooling velocity
In the case of, there is a problem of that the Temperature Distribution in Al alloy cast ingots becomes uneven, final products characteristics and becomes unstable.
In the present invention, for the hot rolling for Al alloy cast ingots, samely by hot roughing and hot finishing
It combines to implement, after hot finishing, forms the plank that plate thickness is 1.5~4.0mm, wherein for above-mentioned through homogenize process
Original sample Al alloy cast ingots or be cooled to the Al alloy cast ingots of set point of temperature so that outlet side temperature is (at the end of hot roughing
Material temperature) it is that 430~550 DEG C of mode implements hot roughing, forms plate thickness as the plank of 20~40mm.Here, ought it is above-mentioned go out
When mouthful side temperature gets lower than 430 DEG C, it may appear that the relatively low problem of the outlet side temperature of the hot next hot finishing of roughing, and work as
When outlet side temperature is more than 550 DEG C, there is the anxiety for generating coarse recrystallization grain in hot rolling and damaging mouldability.In addition, when passing through
When the thickness for the plank that the hot roughing obtains becomes to be thinner than 20mm, there is that degree of finish in next hot finishing is insufficient, hot finishing
After cannot obtain effectively recrystallize tissue anxiety, on the other hand, when its thickness is more than 40mm, can cause in hot finishing adding
Work degree becomes too much, to which anisotropy when DI is molded becomes strong problem.
In turn, in the above-mentioned hot next hot finishing of roughing, so that outlet side temperature (the material temperature at the end of hot finishing
Spend) implement well known mill operation for 300~390 DEG C of mode, form the plank that plate thickness is 1.5~4.0mm.In the hot finishing
In, it is important that adjust recrystallization tissue in the cooling after the coil winding of obtained plank.When the outlet of above-mentioned hot finishing
When side temperature gets lower than 300 DEG C, the formation for recrystallizing tissue can be caused to become inadequate, anisotropy becomes strong or product strong
Degree becomes excessively high problem.It should be noted that when the outlet side temperature is more than 390 DEG C, have recrystallization grain become thick and
Damage the anxiety of DI mouldabilities.In addition, when plate thickness becomes to be thinner than 1.5mm, it may appear that the degree of finish in cold rolling process thereafter is not
Foot, intensity the problem of being lower, on the contrary when plate thickness became to be thicker than 4.0mm, it may appear that the degree of finish in cold rolling process gets higher,
Intensity becomes excessively high problem.Moreover, passing through the hot finishing, it can be ensured that aforementioned solid solution Mn, Fe, Si amount.
Then, for the hot rolled plate obtained as described above, further implement cold rolling, in the present invention, so that above-mentioned cold rolling
Total degree of finish be 75% or more and mode reality that the average mill speed in the stable state portion of final passage is 700~1600m/ minute
Cold rolling is applied, to form the Al alloy sheets that plate thickness is 0.2~1.0mm.It should be noted that the cold rolling pass through it is same
Method is implemented, at this point, when total degree of finish of cold rolling get lower than 75% or the average mill speed in stable state portion become larger than
At 1600m/ minutes, there is the anxiety of insufficient, the heat-resisting property of softening reduction of the precipitation of Mn based compound particles.In addition, in above-mentioned stable state
In the case that the average mill speed in portion is less than 700m/ minutes, there are problems that productivity significant decrease.Thus in turn, when
To the plate thickness of Al alloy sheets become to be thinner than 0.2mm when, there are problems that being difficult to ensure tank intensity, on the other hand, work as plate thickness
When becoming to be thicker than 1.0mm, weight becomes weight, is not suitable as beverage can.
In turn, in the present invention, it is preferred to the conductivity (S1) of the plank (hot rolled plate) obtained by hot finishing above-mentioned
And the side that the difference (S1-S2) of the conductivity (S2) of the plank (cold-reduced sheet) obtained by above-mentioned cold rolling is 0.2~1.6%IACS
Formula, in other words by make the conductivity of cold-reduced sheet for 28.4%IACS~39.8%IACS in the range of in a manner of carry out manufacturing objective Al
Alloy sheets.In the presence of solid solution Mn is abundant, including the compound particle of Mn, Fe, Si are induced and be imperceptibly precipitated, energy by cold working
Enough improve the heat-resisting property of softening.In addition, in fig. 1 it is shown that two experiments constituted for the different Al alloys of the content by Mn
The result of study of piece, the respectively difference of the conductivity before and after the compression test at simulation 150 DEG C of cold rolling, wherein for by comprising
For the test film that the Al alloys of Mn are constituted, increased by the way that conductivity is cold worked, in contrast, being closed for the Al by being not added with Mn
For the test film that gold is constituted, the variation for the conductivity brought by cold working is not almost seen, this is proved by the way that Mn systems are cold worked
Compound particle is precipitated.Although causing conductivity to reduce due to moreover, being strained substantially in cold rolling because processing, pass through Mn systems
The precipitation of compound particle, conductivity increase, and therefore, generally the reduction amount of conductivity is the range of 0.2~1.6%IACS
It is interior.It should be noted that when the reduction amount of above-mentioned conductivity becomes less than 0.2%IACS, cold working degree can be caused insufficient and
On the other hand the problem of intensity deficiency when the reduction amount of above-mentioned conductivity becomes larger than 1.6%IACS, can cause by cold rolling
Insufficient, the heat-resisting property of softening of precipitation particle of Mn, Fe, Si system of induction improves insufficient problem.
Moreover, for the Al alloy sheets of the obtained present invention, necessary processing, shape are implemented in operation same
At target tank body, it may be advantageous to be used as Al systems beverage can etc..For example, for the Al alloy sheets of the present invention, implement as needed de-
Fat cleaning, oiling etc. further add via cup body molding, DI moldings, trimming, cleaning, dry, coating, baking, constriction and crimping
Used for Making Beverage Container Body (cylindrical can) is made in the process of work, installs cover (can end) on it, thus can advantageously make
Make target Al systems beverage can.
Embodiment
In the following, in order to further specifically clear of the invention, the representative embodiment of the present invention is shown, but the present invention is certain
Not by any restriction of the record of these embodiments.Also, it should be understood that in the present invention, in addition to embodiment below with
It outside,, can be based on those skilled in the art's without departing from the purport of the present invention and then other than above-mentioned specific description
Common sense is subject to various changes, amendment, improvement etc. to the present invention.
It should be noted that in following Examples and Comparative Examples, for obtained Al alloy sheets (raw sheets：Cold-reduced sheet)
Or the test material by the hot rolled plate making as in-between product, it is measured or evaluates according to the following method.
(1) tensile strength (TS) of the rolling direction of raw sheet
No. 5 examinations of JIS are made in its rolling direction by each Al alloy sheets (raw sheet) obtained in Examples and Comparative Examples
Material is tested, implements tension test according to JIS-Z-2241, thus measures the tensile strength (TS) of rolling direction.
Tensile strength (ABTS) in rolling direction after heat treatment in (2) 205 DEG C × 10 minutes and yield strength
(ABYS)
For the test material being made of each Al alloy sheets (raw sheet), implement the heat treatment for being equivalent to coating roasting procedure
After (205 DEG C × 10 minutes), implements tension test with above-mentioned (1) equally operation, measure the experiment material after above-mentioned heat treatment respectively
The tensile strength (ABTS) and yield strength (ABYS) of the rolling direction of material.
(3) measurement (phenol dissolution method) of Si, Fe and Mn solid solution capacity
The sample cuttings cut from the hot rolled plate after the hot finishing respectively obtained in Examples and Comparative Examples are impregnated in 170
DEG C phenol in, after thus dissolving matrix composition in Al alloys, add benzyl alcohol, so that the solution is kept liquid condition, together
When be filtered with the filter in the aperture with 0.1 μm.Then, it is dissolved with hydrochloric acid hydrofluoric acid mixed solution and is caught on the filter
The precipitate of collection carries out ICP (Inductively Coupled using solution made of diluting the obtained lysate
Plasma thus) emission spectrographic analysis finds out M, Fe, Si amount of precipitation.In addition, solid solution Mn, Fe, Si amount is by from containing in ingot casting
Above-mentioned amount of precipitation is subtracted in amount to find out.
(4) conductivity
For the plank (hot rolled plate) after hot finishing and the plank (raw sheet after cold rolling：Cold-reduced sheet), conductivity is used respectively
Analyzer (FOERSTER corporation SIGMATEST2.069) is measured in the case where frequency is 960kHz, finds out being averaged for n=3
Value.It should be noted that in the case where the plate thickness of test material is less than 1mm, it will experiment in a manner of making total thickness be 1mm or more
For measuring after material (plate) overlapping.
(5) tank evaluation processed
For the various Al alloy sheets (raw sheet) obtained in Examples and Comparative Examples, respectively in accordance with common tank method processed with
Reduction is 66% progress cup body molding and DI moldings, further after trimming, implements coating baking same, confirmation is
It is no can tank processed.In addition, the burning of the tank skin in the above-mentioned tank operation processed of visual assessment glues situation.
Embodiment 1-
First, the various Al alloys A1~A10 formed with alloying component shown in following table 1 are melted according to well-established law
After refining, by semi-continuous casting method, Al alloy cast ingots are manufactured respectively.Then, and previous same for the obtained Al alloy cast ingots
After implementing facing cut to sample, 600 DEG C of temperature is heated to 40 DEG C/h of heating rate with air furnace, then at 600 DEG C
Temperature implement 10 hours homogenize process.It should be noted that (145-0.24T) is more than hour specified in the present invention
Value is 1 hour or more, and above-mentioned 10 hours homogenize process fully meet the condition.
Then, after above-mentioned homogenize process, direct (immediately) for hot rolling, first so that outlet side temperature be 460~
The mode of 510 DEG C of range, using reversible roll mill, implementing hot roughing same to plate thickness becomes 28mm, then,
In a manner of making the temperature that outlet side temperature is 300~330 DEG C, using 4 tandem roll mills, pass through side same
Method, which implements hot finishing to plate thickness, becomes 2.2mm.Finally, the cold rolling of 3 passages, the Al alloy sheets of manufacture plate thickness 0.28mm are carried out.It should
Total degree of finish in cold rolling process is 87.3%.In addition, at this moment, the average mill speed of final passage is set as 900~1100m/
The range of minute.It should be noted that the outlet side temperature of the final passage in cold rolling is 145~155 DEG C.
For each various planks being made of the Al alloys of the A1~A10 obtained by above-mentioned each process, experiment is made
Material (A1~A10) carries out various performance evaluations, the results are shown in following table 2 according to above-mentioned evaluation assessment.It needs to illustrate
, in following table 2, the difference (S1-S2) of the conductivity (S1) of hot rolled plate and the conductivity (S2) of cold-reduced sheet is in cold rolling
The form of conductivity reduction amount indicates.
[table 1]
[table 2]
Such as by above-mentioned table 1 and table 2 the result shows that, the plank being made of the Al alloys of A1~A10 is not being dried by applying
For the tensile strength (TS) of rolling direction in the state of roasting process without excessively high, their tank processed is good.In addition, can confirm
The Al alloy sheets (test material) of these A1~A10 are higher in the tensile strength (ABTS) of rolling direction after heat treatment, resistance to
Thermal softening is also excellent.
Comparative example 1-
In the various alloying components composition shown in following Table 3, under the conditions of same as above-described embodiment 1, manufacture by
The plank that the various Al alloys of B1~B13 are constituted.Then, for experiment that these are obtained by the manufacturing process of Al sheet alloys
Material (B1~B13), its characteristic of operation evaluation, the results are shown in following table 4 as described above.
[table 3]
[table 4]
Such as by above-mentioned table 3 and table 4 the result shows that, for B1 test materials, since the additive amount of Mn is insufficient,
Solid solution Mn amounts become fewer than prescribed limit, be precipitated when cold rolling it is insufficient, so that conductivity is greatly lowered.As a result, coating baking
Strength reduction amount when processing is larger, and tank intensity is insufficient.In addition, in B2 test materials, it is former since the additive amount of Mn is excessive
The intensity of plate becomes excessively high, therefore the problem of cause to be broken when tank processed.In turn, for B3 test materials, due to Mg
Additive amount it is insufficient, therefore the intensity after the coating baking of raw sheet is insufficient.In B4 test materials, due to the additive amount mistake of Mg
It is more, therefore the intensity of raw sheet becomes excessively high, therefore, the problem of causing to be broken when tank processed.For B5 test materials, by
It is insufficient in the insufficient therefore coarse intermetallic compound of the additive amount of Fe, cause rough surface after tank processed.In addition, due to solid solution
Fe amounts are insufficient, and precipitation when cold rolling is insufficient, therefore intensity is greatly lowered when applying baking.
Moreover, in B6 test materials, since the additive amount of Fe is excessive, coarse intermetallic compound is formed, is drawn
The problem of being broken when playing tank processed.And for B7 test materials, since the additive amount of Si is insufficient, precipitation when cold rolling is not
Foot, therefore the strength reduction applied when baking is larger, tank intensity is insufficient.For B8 test materials, due to the addition of Si
Amount is excessive, the problem of forming coarse intermetallic compound too much, cause to be broken when tank processed.In addition, being tested for B9
For material, since the additive amount of Cu is insufficient, precipitation strength when coating baking is handled becomes insufficient, therefore, by applying
Strength reduction is larger caused by baking, and tank intensity is insufficient.In turn, in the test material of B10, due to the additive amount mistake of Cu
It is more, therefore raw sheet intensity becomes excessively high, the problem of causing to be broken when tank processed.In addition, in the experiment material of B11, B12 and B13
In material, the additive amount difference of Zn, Ti, B are excessive, therefore form coarse intermetallic compound particle too much, when causing tank processed
The problem of being broken.
Embodiment 2-
(Al alloys are formed using the alloying component for providing the A9 test materials in embodiment 1：A9), shown in following table 5
Various manufacturing conditions under, respectively manufacture C1~C13 various Al sheet alloys.It should be noted that being not shown in above-mentioned table 5
Basic manufacturing condition similarly to Example 1.Then, using the various Al alloys of the C1~C13 obtained by its manufacturing process
Plank makes test material (C1~C13) respectively, and progress is similarly evaluated with above-described embodiment, the results are shown in following tables
6。
[table 5]
[table 6]
Such as by above-mentioned table 5 and table 6 the result shows that, for the Al sheet alloys (test material) of C1~C13, respectively
The tensile strength (TS) of rolling direction in the state that coating baking is not carried out is no excessively high, becomes value appropriate, therefore, system
Tank is good.
Comparative example 2-
It is formed using the alloying component of the Al alloys A9 in embodiment 1, under the various manufacturing conditions shown in following table 7,
Manufacture the various Al sheet alloys of D1~D9.It should be noted that the manufacturing condition that do not recorded in above-mentioned table 7 and embodiment 1
Situation is same.Then, for the test material (D1~D9) being made of the Al sheet alloys (cold-reduced sheet) of these D1~D9, evaluation
Its sheet properties, the results are shown in following table 8.
[table 7]
[table 8]
Such as by above-mentioned table 7 and table 8 the result shows that, for D1 test materials, heating when due to homogenize process
Speed is fast, therefore, fine Mn, Fe, Si system particle is formed in heating, intensity increases, and causes what is be broken when tank processed to ask
Topic.In addition, in D2 test materials, since the holding temperature in homogenize process is low, homogenizing effect is insufficient, group
Knitting becomes uneven, there are problems that being broken when tank processed, and on the other hand, the holding temperature in homogenize process is excessively high
In D3 test materials, become the tissue that eutectic melting has occurred, tissue becomes uneven, causes what is be broken when tank processed to ask
Topic.In turn, in D4 test materials, since the retention time ratio (145-0.24T) in homogenize process is short, with display
The formation that the equivalent circle diameter of individual lubricant effect is calculated as 0.1~1.0 μm of Mn, Fe, Si based compound particle becomes inadequate,
Occur to burn in tank rear surface processed viscous.
In addition, in D5 test materials, since the cooling velocity to hot rolling (hot rolling) start temperature is small,
It is precipitated in cooling, the solid solution capacity of Mn, Fe, Si is reduced, Mn, Fe, Si system subparticle when cold rolling (cold rolling)
Precipitation become inadequate, the heat-resisting property of softening reduces, on the other hand, in the big D6 experiments of the cooling velocity to hot rolling start temperature
In material, the temperature of inside ingot becomes uneven, unevenness occurs in material structure, the problem of causing to be broken when tank processed.
In addition, in D7 test materials, since hot rolling start temperature is low, analysed during being cooled to hot rolling start temperature
Go out, the solid solution capacity of Mn, Fe, Si is reduced, and the precipitation of Mn, Fe, Si system subparticle when cold rolling becomes inadequate, the heat-resisting property of softening
It reduces, as a result, the tank intensity after coating baking is insufficient.
In turn, it in the test material of D8, since total degree of finish in cold rolling is insufficient, asks accordingly, there exist intensity is insufficient
Topic.In addition, in D9 test materials, since the mill speed of the final passage in cold rolling process is fast, in cold rolling Mn,
The precipitation of Fe, Si system subparticle becomes inadequate, the problem of causing the heat-resisting property of softening to reduce.
Claims (10)
1. a kind of tank body aluminium alloy plate, which is characterized in that it is by using using aluminium alloy as obtained from the hot rolled plate of material
The plank that cold-reduced sheet is constituted, the aluminium alloy are contained in terms of quality criteria：Mn：0.7~1.3%, Mg：0.8~1.5%, Fe：
0.25~0.6%, Si：0.25~0.50%, Cu：0.10~0.30%, Zn：0.25% or less, Ti：0.10% or less and B：
0.05% hereinafter, surplus is made of Al and inevitable impurity, the solid solution Mn amounts in the hot rolled plate be 0.25 mass % or more,
Solid solution Fe amounts are 0.02 mass % or more and solid solution Si amounts are 0.07 mass % or more, and conductivity is 30.0~40.0%
IACS, after the tensile strength (TS) of the rolling direction in the cold-reduced sheet is 280~320MPa, heat treatment in 205 DEG C × 10 minutes
The tensile strength (ABTS) of rolling direction be 270~310MPa, and the tensile strength (TS) of the rolling direction and 205 DEG C
The difference of the yield strength (ABYS) of rolling direction after heat treatment in × 10 minutes is 50MPa or less.
2. a kind of tank body aluminum alloy hot rolling band, which is characterized in that it is the hot rolled plate using aluminium alloy as material, the aluminium alloy
Contained in terms of quality criteria：Mn：0.7~1.3%, Mg：0.8~1.5%, Fe：0.25~0.6%, Si：0.25~0.50%,
Cu：0.10~0.30%, Zn：0.25% or less, Ti：0.10% or less and B：0.05% hereinafter, surplus by Al and inevitable
Impurity composition, the aluminum alloy hot rolling band contain 0.25 mass % or more solid solution Mn amount, 0.02 mass % or more solid solution
The solid solution Si amounts of Fe amounts and 0.07 mass % or more, and the conductivity with 30.0~40.0%IACS.
3. a kind of tank body aluminium alloy plate, which is characterized in that it is the plank using aluminium alloy as material, and the aluminium alloy is with quality
Benchmark meter contains：Mn：0.7~1.3%, Mg：0.8~1.5%, Fe：0.25~0.6%, Si：0.25~0.50%, Cu：0.10
~0.30%, Zn：0.25% or less, Ti：0.10% or less and B：0.05% hereinafter, surplus by Al and inevitable impurity group
At the tensile strength (TS) of the rolling direction of the aluminium alloy plate is 280~320MPa, after heat treatment in 205 DEG C × 10 minutes
The tensile strength (ABTS) of rolling direction be 270~310MPa, and the tensile strength (TS) of the rolling direction and 205 DEG C
The difference of the yield strength (ABYS) of rolling direction after heat treatment in × 10 minutes is 50MPa or less.
4. tank body aluminium alloy plate according to claim 3, conductivity is 28.4%IACS~39.8%IACS.
5. a kind of manufacturing method of tank body aluminium alloy plate, which is characterized in that have following process：
Prepare using aluminium alloy as the process of the aluminium alloy cast ingot of material, the aluminium alloy is contained in terms of quality criteria：Mn：0.7~
1.3%, Mg：0.8~1.5%, Fe：0.25~0.6%, Si：0.25~0.50%, Cu：0.10~0.30%, Zn：0.25%
Below, Ti：0.10% or less and B：0.05% hereinafter, surplus is made of Al and inevitable impurity；
Using above-mentioned aluminium alloy cast ingot, implement hot rolling, the solid solution Mn amounts of the process for obtaining hot rolled plate, the hot rolled plate are
0.25 mass % or more, solid solution Fe amounts are 0.02 mass % or more and solid solution Si amounts are 0.07 mass % or more, and conductivity is
30.0~40.0%IACS；With,
Cold rolling, the process for forming cold rolled sheet, the tensile strength of the rolling direction of the cold rolled sheet are carried out to the hot rolled plate
(TS) be 280~320MPa, the tensile strength (ABTS) of rolling direction after heat treatment in 205 DEG C × 10 minutes be 270~
310MPa, and the tensile strength (TS) of the rolling direction and the rolling direction after heat treatment in 205 DEG C × 10 minutes are bent
The difference for taking intensity (ABYS) is 50MPa or less.
6. a kind of manufacturing method of tank body aluminium alloy plate, which is characterized in that using aluminium alloy as the Al alloy cast ingots of material into
Row facing cut, the aluminium alloy are contained in terms of quality criteria：Mn：0.7~1.3%, Mg：0.8~1.5%, Fe：0.25~0.6%,
Si：0.25~0.50%, Cu：0.10~0.30%, Zn：0.25% or less, Ti：0.10% or less and B：0.05% hereinafter, remaining
Amount is made of Al and inevitable impurity, then, make its be heated to 550 with 30~120 DEG C/h of heating rate~
Homogenize process temperature (T) in the range of 620 DEG C is then kept for (145-0.24T) hour in the homogenize process temperature (T)
Thus above time implements homogenize process, then after above-mentioned homogenize process, immediately or with 10~90 DEG C/
The cooling velocity of hour is cooled to after the hot rolling start temperature not less than 500 DEG C, so that outlet side temperature is 430~550 DEG C
Mode implement hot roughing, to formed plate thickness be 20~40mm plank, next so that outlet side temperature be 300~390
DEG C mode carry out hot finishing, to form the plank that plate thickness is 1.5~4.0mm, then so that total degree of finish is 75% or more
And the mode that the average mill speed in the stable state portion of final passage is 700~1600m/ minute carries out cold rolling, to become 0.2~
The plate thickness of 1.0mm.
7. the manufacturing method of tank body aluminium alloy plate according to claim 6, which is characterized in that by the hot finishing
The difference (S1-S2) of the conductivity (S1) of obtained plank and the conductivity (S2) of the plank as obtained from the cold rolling is 0.2
~1.6%IACS.
8. the manufacturing method of the tank body aluminium alloy plate described according to claim 6 or 7, wherein implement homogeneous for described
In the scanning electron microscope photo for changing the Al alloy cast ingots of processing, the area occupation ratio of a diameter of 0.1 μm~1 μm of particle is
3.5% or more.
9. a kind of Used for Making Beverage Container Body, which is characterized in that by the tank body aluminium described in claim 1 or claim 3 or claim 4
Alloy sheets are constituted.
10. Used for Making Beverage Container Body according to claim 9 implements it defined coating baking processing.
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| PCT/JP2016/088086 WO2017110869A1 (en) | 2015-12-25 | 2016-12-21 | Aluminum alloy sheet for can body, and method for manufacturing same |
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| CN111020312A (en) * | 2019-12-20 | 2020-04-17 | 山东南山铝业股份有限公司 | Aluminum alloy strip for small-caliber unscrewing bottle and tank and production method thereof |
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| CN113549794A (en) * | 2021-09-22 | 2021-10-26 | 山东宏桥新型材料有限公司 | Aluminum alloy tank produced by using waste aluminum alloy tank |
| CN116949321A (en) * | 2022-04-19 | 2023-10-27 | 宝山钢铁股份有限公司 | Aluminum alloy plate for tank body and manufacturing method thereof |
| CN117286376A (en) * | 2023-11-27 | 2023-12-26 | 中国第一汽车股份有限公司 | Variable yield strength aluminum alloy and preparation method and application thereof |
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2018
- 2018-05-30 US US15/992,662 patent/US20180282848A1/en not_active Abandoned
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2021
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN111020312A (en) * | 2019-12-20 | 2020-04-17 | 山东南山铝业股份有限公司 | Aluminum alloy strip for small-caliber unscrewing bottle and tank and production method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| WO2017110869A1 (en) | 2017-06-29 |
| JP6898254B2 (en) | 2021-07-07 |
| CN108368570B (en) | 2021-02-12 |
| US20210292878A1 (en) | 2021-09-23 |
| JPWO2017110869A1 (en) | 2018-10-11 |
| US20180282848A1 (en) | 2018-10-04 |
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