CN103526079A - A can aluminum alloy plate and a manufacturing method thereof - Google Patents

A can aluminum alloy plate and a manufacturing method thereof Download PDF

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Publication number
CN103526079A
CN103526079A CN201310281052.6A CN201310281052A CN103526079A CN 103526079 A CN103526079 A CN 103526079A CN 201310281052 A CN201310281052 A CN 201310281052A CN 103526079 A CN103526079 A CN 103526079A
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aluminium alloy
quality
alloy plate
tank body
slab
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岩村信吾
横井洋
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Sumitomo Light Metal Industries Ltd
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Sumitomo Light Metal Industries Ltd
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Abstract

The purpose of the invention is to provide a can aluminum alloy plate capable of relieving decrease in can strength and a can fracture problem and a manufacturing method thereof. On a cross section of the can aluminum alloy plate, the area ratio of [alpha] AlMnFeFi intermetallic compound phase with equivalent circle diameters below 1 [mu]m is below 2.3 percent. On a cross section of the can aluminum alloy plate, a material organization is divided into hexagonal micro elements with areas of 0.035[mu] m2 and the average orientation of the micro elements are measured. When the average value of orientation difference of any micro element and a micro element adjacent to micro element is [theta] degree, wherein the value of the [theta] is below 0.9, the tensile strength of the can aluminum alloy plate in a rolling direction is below 320MPa.

Description

Aluminium alloy plate and manufacture method thereof for tank body
Technical field
The present invention relates to aluminium alloy plate and manufacture method thereof for tank body.
Background technology
Tank body forms by aluminium alloy ingot bar is implemented to homogenize processing, hot rolling and cold rolling manufacture with aluminium alloy plate.As required this tank body is implemented cleaning by degreasing, is coated with wet goods processing with aluminium alloy plate, and, through cup be shaped, DI (Drawing and Ironing) is shaped, finishing, clean, dry, application, baking, necking down and flange manufacturing procedure manufacture Used for Making Beverage Container Body.
Used for Making Beverage Container Body need have tank intensity that can resistance to use, and still, in the roasting procedure after above-mentioned application (following, to be called coating baking operation), tank intensity will reduce greatly.The technical scheme that prevents that tank intensity from reducing is disclosed in JP 2000-248326 communique and JP 2006-283113 communique.
In JP 2000-248326 communique, disclose by the composition range of strict regulation Mg, thereby even while making in alloying constituent that the content of Si is high, also can maintain the intensity of Used for Making Beverage Container Body.In addition, in JP 2006-283113 communique, disclose by regulation and homogenized and process and hot-rolled condition, thereby the heat-resisting property of softening is improved.
Summary of the invention
the problem that invention will solve
In recent years, the viewpoint based on environment protection, in Used for Making Beverage Container Body is manufactured, the reconstituting piece of the used beverages can of recycle (UBC:Used Beverage Can) becomes an important problem.And, in order to cut down the usage quantity of material, also advancing the thin-wall light-weighted of tank body.In reconstituting piece due to UBC, sneak into Si and/or Fe etc. more, when recycling the reconstituting piece of UBC, in aluminium alloy ingot bar by the Si that contains high density and/or Fe.In this case, in the heat treated of aluminium alloy ingot bar, Si will form intermetallic compound with Mn and/or Fe, thereby cause the minimizing of the solid solution capacity of Mn.Its result is that the heat-resisting property of softening of aluminium alloy plate reduces, and the reduction of the tank intensity in coating baking operation will become more remarkable.In addition, if consider the strength decreased causing due to coating baking operation, and while making aluminium alloy plate there is high early strength, when making the thickness of slab of tank skin portion become thinner because of tank body thin-wall light-weighted, when DI is shaped, more easily there is tank body and break.Therefore, when the reconstituting piece of recycle UBC is manufactured Used for Making Beverage Container Body, need limit its usage quantity, and by adding new aluminium ingot to adjust the content of Si.
And, in the technology of recording at JP 2000-248326 communique, if considered especially when tank body is thin-wall light-weighted, can not solve the problem that the tank body when DI is shaped breaks.In addition,, in the technology of recording at JP 2006-283113 communique, if when the content of the Si in aluminium alloy ingot bar is high, can not prevent the reduction of tank intensity.
The present invention in view of above some and make, the object of the present invention is to provide a kind of tank body aluminium alloy plate, when even the content of the Si in aluminium alloy ingot bar is high, it also can alleviate the problem that tank intensity reduces and tank body breaks, and the manufacture method of described tank body with aluminium alloy plate is provided.
the technical scheme of dealing with problems
Tank body of the present invention comprises with aluminium alloy plate: below Mn:0.5~1.5 quality %, Mg:0.8~1.5 quality %, Fe:0.2~0.6 quality %, Si:0.25~0.4 quality %, Cu:0.1~0.3 quality %, Zn:0.25 quality %, below Ti:0.1 quality %, below B:0.05 quality %, remainder is comprised of A1 and inevitable impurity
At described tank body, with on the cross section of aluminium alloy plate, the Area Ratio of the α AlMnFeSi intermetallic compound of diameter of equivalent circle below 1 μ m is below 2.3%,
At described tank body, with on the cross section of aluminium alloy plate, material structure is divided into to have area be 0.035 μ m 2the small key element of hexagon, and measure the average orientation of small key element described in each, when the mean value of the misorientation of described small key element arbitrarily and the described small key element that is adjacent is θ °, the value of θ is below 0.9,
Described tank body is below 320MPa by the tensile strength in the rolling direction of aluminium alloy plate.
When even the content of Si is high, tank body of the present invention also can alleviate with aluminium alloy plate the problem that tank intensity in coating baking operation reduces, and the DI problem that tank body breaks while being shaped.
The manufacture method of aluminium alloy plate of the present invention is,
Aluminium alloy ingot bar is implemented at the temperature of 550~620 ℃, the above processing that homogenizes in 1 hour, described aluminium alloy ingot bar comprises below Mn:0.5~1.5 quality %, Mg:0.8~1.5 quality %, Fe:0.2~0.6 quality %, Si:0.25~0.4 quality %, Cu:0.1~0.3 quality %, Zn:0.25 quality %, below Ti:0.1 quality %, below B:0.05 quality %, remainder is comprised of A1 and inevitable impurity
And under the condition of setting up in following formula (1), carry out cooling,
From initial passage, to final passage, under the condition of the accumulative total hold-time in the temperature range of 450~500 ℃ within 600 seconds, carry out thickness of slab to be rolled to the hot roughing of 20~40mm,
In outlet side temperature, be, under the condition of 300~360 ℃, to carry out thickness of slab to be rolled to the hot finishing of 1.5~3.0mm,
Carry out afterwards thickness of slab to be rolled to the cold rolling of 0.20~0.35mm.
H(T1+T2)/2≤1000(℃·h)…(1)
T1: the degree of depth of upper layer of the described aluminium alloy ingot bar of distance be 40mm part, described in homogenize material temperature while processing (℃)
T2: the degree of depth of upper layer of the described aluminium alloy ingot bar of distance be the material temperature of hot roughing 40mm part, described while starting (℃)
H: desired time (h) when the material temperature that is 40mm part in the degree of depth of upper layer of the described aluminium alloy ingot bar of distance arrives T2 from T1
When even the content of Si is high, according to the present invention, the tank body of manufacturing also can alleviate with aluminium alloy plate the problem that tank intensity in coating baking operation reduces, and the DI problem that tank body breaks while being shaped.
Accompanying drawing explanation
Fig. 1 means, in order to obtain in the calculation method of value of θ, and the mode chart of the position relationship of small key element and the small key element that is adjacent arbitrarily on test materials cross section.
The explanation of Reference numeral
Dx, Dx1, Dx2, Dx3, Dx4, Dx5, the small key element of Dx6
θ x1, θ x2, θ x3, θ x4, θ x5, θ x6 misorientation
Embodiment
Below will describe embodiments of the present invention.Mn is the basic alloy element in aluminium alloy plate for tank body of the present invention, except gaining in strength, especially, under solid solution condition, contributes to improve the heat-resisting property of softening.In addition in ,Mn manufacturing process, form α phase compound (Al-Mn-Fe-Si system).The hardness of this intermetallic compound particles is very high, when DI is shaped, can prevent the burning sticky (being resulting burning sticky (adhesion) in the friction producing because starting material directly contact with mould) of starting material and mould between the two, and can improve the surface property of tank body.When the content of Mn be 0.5 quality % less than time, can not fully realize above-mentioned effect.And when the content of Mn surpasses 1.5 quality %, it is too high that intensity becomes, meanwhile, the A16 generating during casting (Mn, Fe) crystallisate becomes thick, and will therefore cause the reduction of DI plasticity and necking down and flange plasticity etc.
Mg increases tank intensity by solid solution in aluminium.When the content of Mg be 0.8 quality % less than time, be difficult to obtain required tank intensity, and when the content of Mg is during over 1.5 quality %, because tank intensity becomes too high, will damage DI plasticity.
In when casting, Fe forms A16 (Mn, Fe) phase, α phase compound (Al-Mn-Fe-Si system), Al-Fe-Si based compound together with Mn, and the burning of starting material and mould is glued while being used for preventing DI shaping based on its solid lubrication.When the content of Fe be 0.2 quality % less than time, the amount of above-mentioned intermetallic compound is few, thus when DI is shaped, starting material can reduce surface property with mould adhesion.When the content of Fe surpasses 0.6 quality %, the intermetallic compound that contains Mn will form and become the starting point of crackle too much, therefore, will damage DI plasticity.
Si forms the α phase compound (Al-Mn-Fe-Si system) with solid lubrication effect together with Mn and Fe, and Al-Fe-Si based compound, prevents the adhesion to mould when DI is shaped.When the content of Si be 0.25 quality % less than time, this effect can not realize fully, while being shaped, can there is the adhesion to mould in DI.When the content of Si surpasses 0.4 quality %, the intermetallic compound of Al-Mn-Fe-Si system will form and become the starting point of crackle too much, therefore will damage DI plasticity, and because the amount of solid solution Mn will reduce, the heat-resisting property of softening will reduce.
In the coating baking operation of Cu when tank processed, forming and separate out Al-Cu-Mg is precipitate, and by the strength decreased reducing in coating baking operation.When the content of Cu be 0.1 quality % less than time, can not obtain fully this effect, and when the content of Cu surpasses 0.3 quality %, being shaped adds the work hardening in man-hour and will become greatly, DI plasticity will reduce.
Zn can improve DI plasticity, and still, when its content is high, cost will uprise, and, will damage DI plasticity because forming thick intermetallic compound.Therefore, the content of Zn is preferably below 0.25 quality %.
Ti and B have the cast structure's of making granular, and have the dispersing morphology of crystallisate and the effect of grain structure homogenizing that makes generation when casting.Preferred content is respectively, and Ti:0.15 quality % is following, the scope below B:0.05 quality %, when content surpasses on this, prescribes a time limit, and will generate thick intermetallic compound, and DI plasticity will reduce.
At tank body of the present invention, with on aluminium alloy cross section, the Area Ratio of the α AlMnFeSi intermetallic compound of diameter of equivalent circle below 1 μ m is below 2.3%.When if the Area Ratio of the α AlMnFeSi intermetallic compound of diameter of equivalent circle below 1 μ m is large, will promote the work hardening in cold rolling, and tank body is exceedingly increased by the intensity of aluminium alloy, so it is not suitable for.And be 2.3% when following by making the Area Ratio of the α AlMnFeSi intermetallic compound of diameter of equivalent circle below 1 μ m, can alleviate the problems referred to above.
At tank body of the present invention, with on the cross section of aluminium alloy plate, material structure is divided into to have area be 0.035 μ m 2the small key element of hexagon, and measure the average orientation of each small key element, when the mean value of the misorientation of small key element arbitrarily and the small key element that is adjacent is θ °, the value of θ is below 0.9.Thus, can suppress the reduction of tank intensity in coating baking operation.When the value of θ surpasses 0.9, it is remarkable that the reduction of the tank intensity in coating baking operation will become.
Its reason can be presumed as follows: in due to the cold rolling sheet material that produces work hardening, be formed with dislocation unit.This dislocation unit merges and grows up in coating baking operation, thereby tank intensity is reduced.The density of above-mentioned dislocation unit can represent with θ, and when the value of θ is larger, the reduction of the tank intensity in coating baking operation is more remarkable.In the present invention, by making the value of θ, be below 0.9, suppress the reduction of tank intensity in coating baking operation.
Because tank body of the present invention is below 320MPa by the tensile strength in the rolling direction of aluminium alloy plate, therefore, DI plasticity is good.And the tensile strength in the higher rolling direction of cold worked degree of finish will become higher.
Tank body of the present invention with aluminium alloy plate after the thermal treatment of 10 minutes at 205 ℃, more than the tensile strength in rolling direction is preferably 275MPa.In this case, the tank intensity after coating baking operation will maintain higher state.And the heat treated of 10 minutes is equivalent to the processing in coating baking operation at 205 ℃.In addition, in this case, the reducing amount of the tensile strength causing because of the thermal treatment of 10 minutes at 205 ℃ is 45MPa (the heat-resisting property of softening is high).
It is man-hour that adds of 55%~75% that tank body of the present invention is carried out to thickness of slab decrement with aluminium alloy plate, and the increasing amount of tensile strength is preferably below 50MPa.What above-mentioned thickness of slab decrement was 55%~75% is processed as, and for example, is manufacturing cold rolling that tank body of the present invention reduces with the thickness of slab that tank that carry out after aluminium alloy plate, processed and/or simulation cause because of tank processed.By making the increasing amount of tensile strength, be below 50MPa, and make resistance to deformation be difficult to increase, thereby, in DI is shaped, be difficult for producing tank body and break.
At tank body of the present invention, with in the manufacture method of aluminium alloy plate, for example, first, melt aluminium alloy, for example, by DC, cast and manufacture aluminium alloy ingot bar.Consisting of of aluminium alloy, in mass, comprise below Mn:0.5~1.5%, Mg:0.8~1.5%, Fe:0.2~0.6%, Si:0.25~0.4%, Cu:0.1~0.3%, Zn:0.25%, below Ti:0.1%, below B:0.05%, remainder is comprised of Al and inevitable impurity.
Secondly, for example, carry out the face cutting of aluminium alloy ingot bar and the processing that homogenizes.By homogenizing, process the component segregation that can eliminate solute atoms in aluminium alloy ingot bar, meanwhile, can form α phase compound, burning when described α phase compound prevents that by its solid lubricant effect DI is shaped is sticky.
The temperature (maintenance temperature) of processing that homogenizes is 550~620 ℃, and the preferred hold-time is more than 1 hour.When keep temperature be 550 ℃ less than, or the hold-time be 1 hour less than time, can not obtain the treatment effect that homogenizes fully.When keeping temperature to surpass 620 ℃, on the upper layer of aluminium alloy ingot bar, will produce and expand or the melting of part and form small defect, thereby tank body is reduced significantly by the early strength of aluminium alloy plate and the intensity after coating baking operation.For the upper limit of heat-up time, there is no particular limitation, still, from the viewpoint of production efficiency, is generally below approximately 24 hours.
After homogenizing and finishing dealing with, cooling under the condition of setting up in following formula (1).
H(T1+T2)/2≤1000(℃·h)…(1)
T1: the degree of depth of upper layer of the described aluminium alloy ingot bar of distance be 40mm part, described in homogenize material temperature while processing (℃)
T2: the degree of depth of upper layer of the described aluminium alloy ingot bar of distance be the material temperature of hot roughing 40mm part, described while starting (℃)
H: desired time (h) when the material temperature that is 40mm part in the degree of depth of upper layer of the described aluminium alloy ingot bar of distance arrives T2 from T1
In addition, temperature T 1 and T2 are by carrying out perforate processing and immersioning thermocouple to measure in the degree of depth part of table of distances surface layer 40mm to ingot bar.
When the left side of above-mentioned formula (1) is greater than 1000, after homogenizing and processing, arrive T2 temperature during in, because α AlMnFeSi particle is separated out, solid solution Mn atom reduces, thereby the heat-resisting property of softening is reduced.
From initial passage, to final passage, the accumulative total hold-time in the temperature range of 450~500 ℃ is under the condition within 600 seconds, carries out thickness of slab to be rolled to the hot roughing of 20~40mm.And above-mentioned 450~500 ℃ is the temperature on plate surface, and available contact thermometer is measured.
When the accumulative total hold-time surpasses 600 seconds, owing to will separate out trickle α AlMnFeSi particle in hot roughing, thereby the work hardening quantitative change while making cold working is large, and it is too high that intensity becomes.Thickness of slab when hot roughing completes be 20mm less than time, owing to can not increase draught in ensuing hot finishing, and cause after hot finishing, being difficult to obtain recrystallized structure.When the thickness of slab when hot roughing completes surpasses 40mm, ensuing hot finishing and cold rolling in degree of finish will become large.During degree of finish in being increased in hot finishing, the quality on plate surface will be affected, when be increased in cold rolling degree of finish time, by the problem that produces the intensity of tank body with aluminium alloy plate and became high.
In outlet side temperature, be that under the condition of 300~360 ℃, ensuing hot finishing is rolled to 1.5~3.0mm by thickness of slab.Above-mentioned outlet side temperature is the temperature of the upper layer of the coiled material side of aluminium alloy plate for tank body, and can measure with contact thermometer.In addition, above-mentioned outlet side temperature is for just having completed the temperature of the tank body use aluminium alloy plate after hot finishing.
When outlet side temperature be 300 ℃ less than time, after hot finishing, can not obtain recrystallized structure, when surpassing 360 ℃, in cooling, will separate out α AlMnFeSi particle, the heat-resisting property of softening will reduce.Ensuing, cold rollingly middle thickness of slab is rolled to 0.2~0.35mm.
[embodiment 1]
1. the manufacture of aluminium alloy plate for tank body
By thering is the aluminium alloy that be grouped into, A1~A10 of the one-tenth shown in table 1, with ordinary method, melt, and make aluminium alloy ingot bar by semicontinuous casting.
[table 1]
Figure BDA00003469502700071
In air furnace, obtained aluminium alloy ingot bar is implemented in to the temperature processing that homogenizes of lower 10 hours of 600 ℃.Afterwards, take thermal history that the value on the left side of above-mentioned formula (1) is 350~480 (℃ h) is cooled to hot rolling by it and starts temperature.It is 490 ℃ that hot rolling starts temperature.
Secondly, from initial passage, to final passage, the accumulative total hold-time in the temperature range of 450~500 ℃ is, under the condition of 350~490 seconds, to carry out thickness of slab to be rolled to the hot roughing of 30mm.And, in outlet side temperature, be, under the condition of 300~330 ℃, to carry out thickness of slab to be rolled to the hot finishing of 2.4mm.That finally, carries out 3 passages cold rollingly manufactures the tank body aluminium alloy plate that thickness of slab is 0.28mm.And the outlet side temperature of cold rolling final passage is 145~155 ℃.
The tank body below the aluminium alloy manufacture with Ai (i=1~10) being formed is called the tank body aluminium alloy plate of Ai with aluminium alloy plate.
2. the evaluation of aluminium alloy plate for tank body
Tank body for A1~A10 is made respectively test materials with aluminium alloy plate, and has carried out following evaluation.Evaluation result is shown in above-mentioned table 1.
(1) tensile strength in rolling direction (not implementing the value under the state of coating baking operation)
Along the rolling direction of test materials, form the test materials of No. 11 defineds of JIS (JIS), and according to JIS, number (numbering of JIS): the regulation of JIS Z2241 is carried out tension test, and measures the tensile strength (TS) in rolling direction.
(2) tensile strength in the rolling direction after thermal treatment in 10 minutes at 205 ℃
Test materials is equivalent to after the thermal treatment (at 205 ℃ 10 minutes) of coating baking operation, equally with above-mentioned (1) carries out tension test, and measure the tensile strength (ABTS) in the rolling direction after thermal treatment.
(3) carry out thickness of slab decrement be 66% cold rolling time the increasing amount of tensile strength
It is 66% cold rolling (CR) that test materials (not implementing the state of coating baking operation) is carried out to thickness of slab decrement.First measure respectively the tensile strength of the test materials of cold rolling front and back, then calculate the increasing amount due to the cold rolling tensile strength producing.
(4) Area Ratio of α AlMnFeSi intermetallic compound
Cross section to test materials (not implementing the state of coating baking operation), grinds and polishing completes mirror finish by sand paper.Afterwards, by thering is the scanning electron microscope of electric field radioactive electron beam gun, at acceleration voltage, be 10kV, ratio of enlargement is under the condition of 1000 times, on the cross section of viewing test material near the part at thickness of slab center.The photo in the cross section of captured test materials is carried out to image analysis, and measure the Area Ratio (with respect to the total area, the ratio of the area that the α AlMnFeSi intermetallic compound of diameter of equivalent circle below 1 μ m is shared) of the α AlMnFeSi intermetallic compound of diameter of equivalent circle below 1 μ m.During analysis, use 10 photos more than visual field, the total area of image analysis is 10000 μ m 2above.
(5) measurement of θ
Cross section to test materials (not implementing the state of coating baking operation), grinds and polishing completes mirror finish by sand paper.Afterwards, by thering is the scanning electron microscope of electric field radioactive electron beam gun, under the condition that is 10kV at acceleration voltage, thering is area, be 0.035 μ m 2the small key element of hexagon on carry out EBSP analysis.
That is, as shown in Figure 1, the cross section of test materials is divided into to have area be 0.035 μ m 2the small key element Di of regular hexagon (i=1,2,3), and measure the average orientation of each small key element Di.Then, the absolute value of the difference of the average orientation of small key element Dx arbitrarily and its 6 small key element Dx1~Dx6 around (following, to be called misorientation) is set as respectively to θ x1~θ x6.And, θ x1~θ x6 sum is set as to the mean value of the misorientation of small key element Dx divided by the value of 6 (numbers of θ x1~θ x6).To belonging to the whole small key element Di in the region of analyzing, calculate the mean value of this misorientation, and, the mean value of the mean value of the misorientation of above-mentioned whole small key element Di is set as to θ.The area in the region of analyzing is 1000 μ m 2above.
(6) tank processed is evaluated
By general pot making equipment, carrying out reduction is that 66% tank processed is processed, and be confirmed whether can tank processed in, it is sticky that the burning of tank skin is tested and evaluated to order.
As shown in table 1, the tank body of A1~A10 with aluminium alloy plate the tensile strength in the rolling direction under the state of not implementing coating baking operation (TS) not too high, tank processed is good.And even if the content of Si is high, the tensile strength (ABTS) in the rolling direction after thermal treatment is also high with aluminium alloy plate for the tank body of A1~A10, the heat-resisting property of softening is good.
(comparative example 1)
With the one-tenth shown in table 2, be grouped into, by the manufacture method identical with described embodiment 1, make the test materials of R1~R13.
[table 2]
Then, the test materials of R1~R13 is carried out and evaluation identical in described embodiment 1.Its result is shown in above-mentioned table 2.
In the test materials of R1, the content of Mn is low, and ABTS reduces, and the minimizing of the total amount of α AlMnFeSi particle, has occurred to burn sticky on tank skin.
In the test materials of R2, the content of Mn is high, and it is too high that TS becomes, and trickle Mn particle increases, large by 66% increase the quantitative change cold rolling and tensile strength that causes.Its result is when tank processed, tank body to have occurred and broken.
In the test materials of R3, the content of Mg is low, and ABTS reduces.
In the test materials of R4, the content of Mg is high, and it is too high that TS becomes, and, large by 66% increase the quantitative change cold rolling and tensile strength that causes.Its result is when tank processed, tank body to have occurred and broken.
In the test materials of R5, the content of Fe is low, and when tank processed, tank skin has occurred to burn sticky.
In the test materials of R6, the content of Fe is high, and thick intermetallic compound particles increases, and when tank processed, tank body has occurred and has broken.
In the test materials of R7, the content of Si is low, and the total amount of α AlMnFeSi particle reduces, and when tank processed, tank skin has occurred to burn sticky.
In the test materials of R8, the content of Si is high, and it is large that the value of θ becomes, and the strength decreased being caused by coating baking operation increases, and ABTS reduces.
In the test materials of R9, the content of Cu is low, and ABTS reduces.
In the test materials of R10, the content of Cu is high, and it is too high that TS becomes, and, large by 66% increase the quantitative change cold rolling and tensile strength that causes.Its result is when tank processed, tank body to have occurred and broken.
In the test materials of R11, the content of Zn is high, tank body has occurred during tank processed and broken.
In the test materials of R12, the content of Ti is high, has more thick intermetallic compound, therefore, when tank processed, tank body has occurred and has broken.
In the test materials of R13, the content of B is high, has more thick intermetallic compound, therefore, when tank processed, tank body has occurred and has broken.
[embodiment 2]
Use the one-tenth of A9 in described embodiment 1 to be grouped into, under the creating conditions shown in table 3, manufacture the tank body aluminium alloy plate of B1~B7.And, identical with described embodiment 1 of basic manufacture method.
[table 3]
And the final thickness of slab of hot roughing is 30mm, the final thickness of slab of hot finishing is 2.4mm.In addition,, when cold rolling road number of times is 3, final thickness of slab is 0.28mm.In addition, the outlet side temperature of cold rolling final passage is 145~155 ℃.
The tank body of B1~B7 is made respectively to test materials with aluminium alloy plate, and carry out and evaluation identical in described embodiment 1.Evaluation result is shown in above-mentioned table 3.
As shown in table 3, the tank body of B1~B7 with aluminium alloy plate the tensile strength in the rolling direction under the state of not implementing coating baking operation (TS) not too high, tank processed is good.And even if the content of Si is high, the tensile strength (ABTS) in the rolling direction after thermal treatment is also high with aluminium alloy plate for the tank body of B1~B7, the heat-resisting property of softening is good.
(comparative example 2)
Use the one-tenth of A9 in described embodiment 1 to be grouped into, under the creating conditions shown in table 4, manufacture the test materials of R14~R20.And, identical with described embodiment 1 of basic manufacture method, the final thickness of slab of hot roughing is 30mm, the final thickness of slab of hot finishing is 2.4mm.In addition,, when cold rolling road number of times is 3, final thickness of slab is 0.28mm.In addition, the outlet side temperature of cold rolling final passage is 145~155 ℃.
[table 4]
Then, the test materials of R14~R20 is carried out and evaluation identical in described embodiment 1.Its result is shown in above-mentioned table 4.
In the test materials of R14, the treatment temp that homogenizes is low, and the processing that homogenizes of ingot bar is insufficient.Its result is, trickle α AlMnFeSi particle increases, and it is large that 0 value becomes, and ABTS reduces.
In the test materials of R15, the treatment temp that homogenizes is high, because eutectic dissolves, produces small tissue defects, strength decreased.
In the test materials of R16, the treatment time that homogenizes is short, and the processing that homogenizes of ingot bar is insufficient.Its result is, trickle α AlMnFeSi particle increases, and it is large that the value of θ becomes, and ABTS reduces.
In the test materials of R17, the thermal history between starting to hot rolling after the processing that homogenizes does not meet above-mentioned formula (1), and trickle α A1MnFeSi particle increases, and it is large that the value of θ becomes, and ABTS reduces.
In the test materials of R18, in hot roughing, the hold-time of 450~500 ℃ surpasses 600 seconds, and trickle α AlMnFeSi particle significantly increases, and because the increase quantitative change of the 66% cold rolling tensile strength causing is large, and it is large that the value of θ becomes, and ABTS reduces.
In the test materials of R19, the outlet side temperature of hot finishing is low, and TS exceedingly increases, and when tank processed, tank body has occurred and has broken.
In the test materials of R20, the outlet side temperature of hot finishing is high, separates out α AlMnFeSi particle in process of cooling, and ABTS reduces.
And the present invention is not limited only to above-mentioned embodiment, do not departing from the scope of the present invention interior can enforcement with various forms.

Claims (5)

1. a tank body aluminium alloy plate, it comprises:
Below Mn:0.5~1.5 quality %, Mg:0.8~1.5 quality %, Fe:0.2~0.6 quality %, Si:0.25~0.4 quality %, Cu:0.1~0.3 quality %, Zn:0.25 quality %, below Ti:0.1 quality %, below B:0.05 quality %, remainder is comprised of Al and inevitable impurity
At described tank body, with on the cross section of aluminium alloy plate, the Area Ratio of the α AlMnFeSi intermetallic compound of diameter of equivalent circle below 1 μ m is below 2.3%,
At described tank body, use on the cross section of aluminium alloy plate, material structure is divided into and has the small key element of hexagon that area is 0.035 μ m2, and measure the average orientation of small key element described in each, when the mean value of the misorientation of described small key element arbitrarily and the described small key element that is adjacent is θ °, the value of θ is below 0.9
Described tank body is below 320MPa by the tensile strength in the rolling direction of aluminium alloy plate.
2. tank body aluminium alloy plate according to claim 1, wherein, the tensile strength in the rolling direction at 205 ℃ after thermal treatment in 10 minutes is more than 275MPa.
3. tank body aluminium alloy plate according to claim 1 wherein, is below 50MPa in the increasing amount of having carried out the tensile strength that adds man-hour that thickness of slab decrement is 55%~75%.
4. tank body aluminium alloy plate according to claim 2 wherein, is below 50MPa in the increasing amount of having carried out the tensile strength that adds man-hour that thickness of slab decrement is 55%~75%.
5. for the manufacture of the manufacture method of the aluminium alloy plate described in any one in claim 1 to 4, wherein,
Aluminium alloy ingot bar is implemented at the temperature of 550~620 ℃, the above processing that homogenizes in 1 hour, described aluminium alloy ingot bar comprises below Mn:0.5~1.5 quality %, Mg:0.8~1.5 quality %, Fe:0.2~0.6 quality %, Si:0.25~0.4 quality %, Cu:0.1~0.3 quality %, Zn:0.25 quality %, below Ti:0.1 quality %, below B:0.05 quality %, remainder is comprised of Al and inevitable impurity
And under the condition of setting up in following formula (1), carry out cooling,
From initial passage, to final passage, the accumulative total hold-time in the temperature range of 450~500 ℃ is under the condition within 600 seconds, carries out thickness of slab to be rolled to the hot roughing of 20~40mm,
In outlet side temperature, be, under the condition of 300~360 ℃, to carry out thickness of slab to be rolled to the hot finishing of 1.5~3.0mm,
Carry out thickness of slab to be rolled to the cold rolling of 0.20~0.35mm;
H(T1+T2)/2≦1000(℃·h)…(1)
T1: the degree of depth of upper layer of the described aluminium alloy ingot bar of distance be 40mm part, described in homogenize material temperature while processing (℃)
T2: the degree of depth of upper layer of the described aluminium alloy ingot bar of distance be the material temperature of hot roughing 40mm part, described while starting (℃)
H: desired time (h) when the material temperature that is 40mm part in the degree of depth of upper layer of the described aluminium alloy ingot bar of distance arrives T2 from T1.
CN201310281052.6A 2012-07-06 2013-07-05 A can aluminum alloy plate and a manufacturing method thereof Pending CN103526079A (en)

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CN104357771A (en) * 2014-12-09 2015-02-18 郑州大学 Cold rolling thermal treatment process for improving bending property of aluminum magnesium alloy
CN104357771B (en) * 2014-12-09 2017-02-22 郑州大学 Cold rolling thermal treatment process for improving bending property of aluminum magnesium alloy
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CN108368570A (en) * 2015-12-25 2018-08-03 株式会社Uacj Tank body aluminium alloy plate and its manufacturing method
CN106222492A (en) * 2016-08-23 2016-12-14 中铝瑞闽股份有限公司 A kind of threaded mouth vial-type pop can aluminium alloy strips and manufacture method thereof
CN109266888A (en) * 2018-12-03 2019-01-25 东北轻合金有限责任公司 A kind of 308 alloy cast ingot and its preparation method and application

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