CN106103760B - Aluminum alloy sheet for DR can body and method for producing same - Google Patents
Aluminum alloy sheet for DR can body and method for producing same Download PDFInfo
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- CN106103760B CN106103760B CN201480077133.7A CN201480077133A CN106103760B CN 106103760 B CN106103760 B CN 106103760B CN 201480077133 A CN201480077133 A CN 201480077133A CN 106103760 B CN106103760 B CN 106103760B
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- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 58
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 55
- 229910052802 copper Inorganic materials 0.000 claims abstract description 6
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 5
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 5
- 238000000034 method Methods 0.000 claims description 92
- 238000000137 annealing Methods 0.000 claims description 87
- 238000005097 cold rolling Methods 0.000 claims description 50
- 238000005096 rolling process Methods 0.000 claims description 42
- 238000010438 heat treatment Methods 0.000 claims description 11
- 238000005266 casting Methods 0.000 claims description 10
- 238000010792 warming Methods 0.000 claims description 6
- 238000005098 hot rolling Methods 0.000 claims description 5
- 238000012545 processing Methods 0.000 claims description 5
- 239000004411 aluminium Substances 0.000 claims description 4
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 4
- 229910052742 iron Inorganic materials 0.000 claims description 4
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 claims description 2
- 239000010931 gold Substances 0.000 claims description 2
- 229910052737 gold Inorganic materials 0.000 claims description 2
- 238000010304 firing Methods 0.000 abstract 1
- 210000005069 ears Anatomy 0.000 description 24
- 230000000052 comparative effect Effects 0.000 description 21
- 238000001953 recrystallisation Methods 0.000 description 18
- 239000010949 copper Substances 0.000 description 9
- 239000000203 mixture Substances 0.000 description 9
- 230000000694 effects Effects 0.000 description 8
- 239000000463 material Substances 0.000 description 8
- 239000013078 crystal Substances 0.000 description 7
- 230000006866 deterioration Effects 0.000 description 6
- 239000002245 particle Substances 0.000 description 6
- 238000001556 precipitation Methods 0.000 description 6
- 230000015572 biosynthetic process Effects 0.000 description 5
- 238000011156 evaluation Methods 0.000 description 5
- 229910052751 metal Inorganic materials 0.000 description 4
- 239000002184 metal Substances 0.000 description 4
- 239000000047 product Substances 0.000 description 4
- 238000012797 qualification Methods 0.000 description 4
- 230000033228 biological regulation Effects 0.000 description 3
- 239000011248 coating agent Substances 0.000 description 3
- 238000000576 coating method Methods 0.000 description 3
- 238000005336 cracking Methods 0.000 description 3
- 235000013399 edible fruits Nutrition 0.000 description 3
- 238000005516 engineering process Methods 0.000 description 3
- 239000008187 granular material Substances 0.000 description 3
- 239000011159 matrix material Substances 0.000 description 3
- 238000007493 shaping process Methods 0.000 description 3
- 238000005245 sintering Methods 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 238000004458 analytical method Methods 0.000 description 2
- 238000001354 calcination Methods 0.000 description 2
- 230000007812 deficiency Effects 0.000 description 2
- 238000000265 homogenisation Methods 0.000 description 2
- 230000002401 inhibitory effect Effects 0.000 description 2
- 230000005764 inhibitory process Effects 0.000 description 2
- 229910000765 intermetallic Inorganic materials 0.000 description 2
- 239000010687 lubricating oil Substances 0.000 description 2
- 238000000465 moulding Methods 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000010301 surface-oxidation reaction Methods 0.000 description 2
- 230000037303 wrinkles Effects 0.000 description 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910017818 Cu—Mg Inorganic materials 0.000 description 1
- 229910019064 Mg-Si Inorganic materials 0.000 description 1
- 229910019406 Mg—Si Inorganic materials 0.000 description 1
- 229910018643 Mn—Si Inorganic materials 0.000 description 1
- 238000002441 X-ray diffraction Methods 0.000 description 1
- 229910052796 boron Inorganic materials 0.000 description 1
- 230000015556 catabolic process Effects 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 238000002788 crimping Methods 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 238000006731 degradation reaction Methods 0.000 description 1
- 238000006073 displacement reaction Methods 0.000 description 1
- 238000001887 electron backscatter diffraction Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 235000013305 food Nutrition 0.000 description 1
- 230000009931 harmful effect Effects 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 238000004080 punching Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 230000001550 time effect Effects 0.000 description 1
- 231100000732 tissue residue Toxicity 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
Classifications
-
- 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
-
- 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
-
- 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
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Metal Rolling (AREA)
Abstract
The invention provides an aluminum alloy for DR can body with low earing rate and excellent deep drawing property even using a batch furnace and a manufacturing method thereof. An aluminum alloy sheet for DR can bodies is an aluminum alloy sheet which is made of an aluminum alloy ingot and is formed into a finished sheet from the aluminum alloy ingot through a hot rolled sheet and an intermediate annealed sheet, wherein the aluminum alloy contains Si: 0.10 to 0.60 mass% (hereinafter referred to as "%"), Fe: 0.10 to 0.80%, Cu: 0.05 to 0.25%, Mn: 0.80-1.50%, Mg: 0.80 to 1.30% and the remainder comprising Al and unavoidable impurities, wherein the Cube orientation density (Cube O) in the finished sheet is 2.00 times or more as high as the random orientation density, and the ratio (Cube O/SO) of Cube O to S orientation density (SO) is 0.40 to 1.00, and the sheet has an elastic limit stress of 180 to 220MPa and a tensile strength of 230MPa or more after blank firing.
Description
Technical field
The DR tank body aluminium alloy excellent and small earing rate the present invention relates to a kind of deep drawing quality and its manufacturing method.
Background technology
Aluminium alloy as A3004 or A3104 in JIS specifications is due to excellent mouldability and corrosion resistance, making
It is used for the tank body material of aluminium pot.The tank body of aluminium pot has only to be molded by the DR tanks of deep-draw shaping manufacture and by deep-draw
With the DI tanks of flatiron shaping manufacture.In these aluminium pots, earing rate is important characteristic.Here, said for earing rate
It is bright.In general, deep-draw shaping after cup in, high part (" mountain ") and low part can be generated in the upper end of circumferential part
(" paddy ").The height of the difference divided by paddy of the average value of the height on the mountain and the average value of the height of paddy is averaged what is be worth to
Value is referred to as earing rate.In the case of earing rate difference, have and generate bad place when carrying out crimping engagement with cover or make cutting
Amount increases and reduces yield rate etc. and generate harmful effect to production efficiency.
As the shape of ear processed, have has 0/90 degree ear processed that mountain erects and relatively compared with 0/90 degree of pressure rolling direction direction
There are 45 degree of ears processed of mountain standing in 45 degree of pressure rolling direction direction.Various ears processed property relevant with texture, it is known that Cube is orientated：
(001) 100 ＞ of ＜ make 0/90 degree of ear processed become flourishing, and the beta as rolled structure makes 45 degree of ears processed become flourishing.It needs
Illustrate, cold rolling rate is higher, and beta is more flourishing, and 45 degree of ears processed become notable.In order to obtain excellent earing rate, it is necessary to
Cube orientations is made to be orientated with rolled structure, particularly S and R：{ 123 } 634 ＞ of ＜ have good balance.
Above-mentioned DR tank bodies are mainly the purposes of containers for food use, are increased with the population in the world, it is contemplated that demand can also increase
Add.At present, DR tank bodies by include intermediate annealing process manufacturing method manufacture, intermediate annealing using box annealing stove (with
Under, it is denoted as " batch stove ") and continuous annealing furnace (being denoted as below " CAL ").Present aspect is manufactured into, CAL high produces for improving
The equipment investment of ability is also mostly expensive.Therefore, in order to realize cost degradation, it is necessary to be manufactured using batch stove, but with
CAL is compared, and the control of ear processed is more difficult, and having easily makes 45 degree of ears become flourishing difficult point.
Further, since DR tank bodies are only molded the deep-draw mouldability, it is necessary to height by deep-draw.Specifically, it is profundity
Punching property and the generation for reducing fold when deep-draw is molded.Deep drawing quality is evaluated by limited drawing ratio, if deep drawing quality is bad,
Then easily crack at the time of molding.In addition, if when being molded fold occurs for deep-draw, the surface quality of product can be made significantly reduce.
In recent years, the requirement for surface quality is increasingly strict.
The manufacturing method for being packed for aluminium alloy plate using deep drawing quality or redrawing property has been recorded in patent document 1.Separately
Outside, the manufacturing method for being packed for aluminium alloy with high intensity and low orientated property has been recorded in patent document 2.In addition, patent is literary
In offering 3~5, described as the technology in relation to above-mentioned texture for the Cube in hot rolled plate, intermediate annealing plate, production board
Orientation or rolled structure have carried out the defined aluminium alloy plate with low earing rate.
In patent document 1, although attempting to control ear processed by homogenize process or cold rolling rate, only in this way, making
Sufficient low earing rate cannot be obtained in the case of carrying out intermediate annealing with batch stove.In addition, in the aluminium alloy of patent document 2,
Have due to high intensity and the worry of fold occurs when deep-draw is molded.As noted previously, as requirement for surface quality carries
It is high, it is difficult to which that the aluminium alloy of patent document 2 is suitable for DR tank body materials.
On the other hand, although being controlled in the technology of patent document 3~5 metal structure, purposes is limited to DI
Tank purposes.In DI tank purposes, without using intermediate annealing process, be formed as high cold rolling rate.Used superhard material is due to tool
There is high elastic limit stress, fold easily occurs when deep-draw is molded, be unsuitable for DR tank purposes.Further, since patent document 5
Hot rolled plate tissue be partial, re-crystallization tissue, if plate temperature does not reduce, partial, re-crystallization tissue cannot be accessed.Cause
This, it has to the pressure rolling speed as one of manufacturing condition is reduced, having causes production efficiency to reduce and make what manufacture cost became higher
Problem.
Prior art document
Patent document
Patent document 1：Japanese Unexamined Patent Application 63-145758 publications
Patent document 2：Japanese Unexamined Patent Publication 1-198454 publications
Patent document 3：Japanese Unexamined Patent Publication 2001-40461 publications
Patent document 4：Japanese Unexamined Patent Publication 2004-244701 publications
Patent document 5：Japanese Unexamined Patent Publication 2004-263253 publications
The content of the invention
Problems to be solved by the invention
Various experiment and research are repeated in the present inventor, it turns out that, the gold before intermediate annealing process
Belong in tissue, by making S orientations fully flourishing in matrix, precipitation when inhibiting to recrystallize can be in the situation of batch stove
Under also obtain the aluminium alloy plate with excellent earing rate.That is, as crystalline orientation, it is known that Cube is orientated to be had between S orientations
There is the rotation relationship that 40 degree are rotated along 111 ＞ axis of ＜, the Cube orientations easily growth in the matrix of S orientations.As a result, by making
S orientations become flourishing, make the easily growth of Cube orientations.In addition, precipitate hinders recrystallization to inhibit the shape of Cube orientations
Into promotion R is orientated to be formed.Granule number is precipitated and inhibition by the way that S orientations is made to become fully flourishing as a result, can be criticized using
Excellent earing rate is obtained in the intermediate annealing process of formula stove.
In addition, deep-draw whether there is generation fold when being molded, the proof stress after pre-burn is resulted from.By blank
Although the proof stress reduction after calcination can inhibit the generation of fold, since tensile strength also reduces, make deep drawing quality
It is deteriorated.Consequently found that by controlling cold rolling rate suitably regulation elasticity limit stress and tensile strength, it is able to maintain that good
Deep drawing quality and the generation for inhibiting fold.
It is an object of the invention to provide the aluminium alloy and its manufacturing method found based on more than opinion, which is
Even if using also there is low earing rate and the excellent DR tank body aluminium alloys of deep drawing quality in the case of batch stove.
The method used for solving the problem
The present invention is characterized in that properly control once cold rolling rate.By improving once cold rolling rate, S can be orientated
Become flourishing.But in the case where once cold rolling rate is excessively high, the PSN of the recrystallization around crystal becomes notable,
Metal structure becomes the random tissue that Cube orientation densities reduce.Its result is understood so that 0/90 degree of ear processed can not be made to become to send out
It reaches, 45 degree of ears processed is caused to become flourishing.As a result, by properly controlling once cold rolling rate, make S orientations in intermediate annealing process
Preceding tissue becomes flourishing, also, inhibits analysis when granule number is precipitated and recrystallizing in the tissue before intermediate annealing process
Go out.The growth that Cube can be promoted to be orientated in annealing operation as a result,.That is, promote 0/90 degree ear processed become prosperity, by with
The good balance of secondary cold-rolling process, obtains excellent earing rate.In addition, in secondary cold-rolling process, by appropriate
Proof stress and tensile strength are controlled, good deep drawing quality can be obtained and meets the aesthetics of high surface quality.
In the first aspect of the present invention, a kind of DR tank bodies aluminium alloy plate is obtained, which is characterized in that the DR tank body aluminium
Alloy sheets are to be made of aluminium alloy, be at least made for production board via hot rolled plate and intermediate annealing plate from the ingot bar of the aluminium alloy
Aluminium alloy plate, wherein, which contains Si：0.10~0.60 mass %, Fe：0.10~0.80 mass %, Cu：0.05
~0.25 mass %, Mn：0.80~1.50 mass %, Mg：0.80~1.30 mass %, remainder is by Al and unavoidably
Impurity form, the Cube orientation densities (CubeO) in production board are 2.00 times or more compared with random orientation density, also,
The ratio between CubeO and S orientation densities (SO) (CubeO/SO) are 0.40~1.00, after pre-burn, have 180~220MPa
Proof stress and more than 230MPa tensile strength.
The second aspect of the present invention is：In first aspect, the conductivity of above-mentioned hot rolled plate is 36.0~43.0%IACS.
The third aspect of the present invention is：First or second aspect in Cube orientation densities in above-mentioned intermediate annealing plate
(CubeO) it is 4.00 times or more compared with random orientation density, also, the ratio between CubeO and R orientation densities (RO) (CubeO/
RO) more than 1.00.
The fourth aspect of the present invention is the system of the DR tank body aluminium alloy plates described in any one of first~third aspect
Make method, which is characterized in that including：Casting contains Si：0.10~0.60 mass %, Fe：0.10~0.80 mass %, Cu：
0.05~0.25 mass %, Mn：0.80~1.50 mass %, Mg：0.80~1.30 mass % and remainder are by Al and can not
The casting process for the aluminium alloy that the impurity avoided is formed；The homogenize process process of homogenize process is carried out to ingot bar；To equal
Matterization treated ingot bar carries out the hot-rolled process of hot rolling；The once cold rolling process of hot rolled plate；It anneals to once cold rolling plate
Intermediate annealing process；With the secondary cold-rolling process of intermediate annealing plate.
The fifth aspect of the present invention is：In fourth aspect, in above-mentioned homogenize process process, ingot bar is 580~620
When processing 1~12 is small at DEG C；Above-mentioned hot-rolled process includes 450~610 DEG C of start temperature and the heat of 450~550 DEG C of end temp
The hot finishing stage of 330~380 DEG C of rough rolling step and end temp；The pressure rolling rate of above-mentioned once cold rolling process is 85~95%；
In above-mentioned intermediate annealing process, once cold rolling plate is in 200 DEG C or more of temperature region with average heating speed 10~100
DEG C/h be warming up to 300~450 DEG C of annealing temperature, afterwards the annealing temperature keep 1~4 it is small when；Above-mentioned secondary cold-rolling
The pressure rolling rate of process is 20~40%.
The sixth aspect of the present invention is：In 4th or the 5th aspect, it is also equipped with after above-mentioned secondary cold-rolling process to two
The final annealing process that secondary cold-reduced sheet is annealed.
The seventh aspect of the present invention is：In 6th aspect, in above-mentioned final annealing process, secondary cold-rolling plate is at 200 DEG C
Above temperature region is with 10~80 DEG C/h of annealing temperatures for being warming up to 140~190 DEG C of average heating speed, afterwards at this
When annealing temperature holding 2~4 is small.
The effect of invention
By means of the invention it is possible to also obtain that there is low earing rate in the case of even if batch stove is used and deep drawing quality is excellent
Different DR tank body aluminium alloys.
Specific embodiment
1.DR tank body aluminium alloy plates
The DR tank bodies of the present invention are made of with aluminium alloy plate the aluminium alloy that defined alloy forms, and the feature of production board exists
In with specific orientation density (CubeO), and after pre-burn, there is defined intensity.
1.1. the composition of aluminium alloy
First, the restriction reason of each ingredient involved to aluminium alloy composition illustrates.
Si：0.10~0.60 mass %
By containing Si, the Mg when final annealing and coating are fired2Si systems particle is precipitated, and intensity is contributed to improve.
When the content of Si is less than 0.10 mass % (being denoted as below " % "), the effect can not be obtained, in addition, having to make in casting
With the raw metal of high-purity, increase cost of material.On the other hand, if more than 0.60%, increase since particle is precipitated,
Recrystallizing in hot-rolled process and intermediate annealing process is hindered.As a result, the formation of Cube orientations is pressed down
System, the earing rate of production board are deteriorated.Wherein, the preferred content of Si is 0.20~0.50%.
Fe：0.10~0.80%
Due to containing Fe, the Solid solution precipitation state of Mn is controlled, Mn systems crystal is uniformly dispersed, thus carries
Profundity rushes mouldability.When the content of Fe is less than 0.10%, the effect can not be obtained, in addition, having in casting using high-purity
The raw metal of degree, increases cost of material.On the other hand, if more than 0.80%, due to coarse Al-Fe-Mn-Si systems
Crystal increases, and the recrystallization for being known as the high displacement density region around the crystal of PSN prevails.As a result,
Cube orientation densities reduce, and the earing rate of production board is deteriorated.Wherein, the preferred content of Fe is 0.30~0.60%.
Cu：0.05~0.25%
By containing Cu, the particle of Al-Cu-Mg systems and Al-Cu-Mg-Si systems when final annealing and coating are fired
It is precipitated, intensity is contributed to improve.When the content of Cu is less than 0.05%, the effect can not be obtained, if more than 0.25%, intensity
Become excessively high, deep-draw mouldability is deteriorated.Wherein, the preferred content of Cu is 0.10~0.25%.
Mn：0.80~1.50%
By containing Mn, intensity is contributed to improve.When the content of Mn is less than 0.80%, it is impossible to obtain sufficient intensity.Separately
On the one hand, if more than 1.50%, intensity is excessively high, and deep-draw mouldability is deteriorated.Wherein, the preferred content of Mn for 0.80~
1.10%.
Mg：0.80~1.30%
By containing Mg, the intensity obtained by solid solution is contributed to improve.In addition, by forming Mg with Si2Si systems particle,
When final annealing and coating are fired intensity is contributed to improve.When the content of Mg is less than 0.80%, it is impossible to obtain the effect
Fruit.On the other hand, if more than 1.30%, intensity becomes excessively high, and deep-draw mouldability is deteriorated.Wherein, the preferred content of Mg is
0.90~1.25%.
In above-mentioned aluminium alloy, Ti, B, V as inevitable impurity etc. can be respectively containing less than 0.05%, with whole
Body meter contains less than 0.15%.
1.2. the feature (1) of orientation density
Then, the DR tank bodies of the present invention are illustrated with the feature of the orientation density of aluminium alloy plate.In the present invention, make
Cube orientation densities (being denoted as below " CubeO ") in production board are 2.00 times or more compared with random orientation density, also,
The ratio between CubeO and S orientation densities (being denoted as below " SO ") (CubeO/SO) are defined as 0.40~1.00.
The shape of ear processed is determined by the balance of CubeO and CubeO and rolled structure.It is low compared with random orientation in CubeO
In the case that 2.00 times or CubeO/SO are less than 0.40,45 degree of ears processed become flourishing, cause the deterioration of earing rate.The opposing party
Face, in the case where CubeO/SO is more than 1.00, it is impossible to obtain the good balance of 0/90 degree of ear processed and 45 degree of ears processed, equally
Cause the deterioration of earing rate.
It is preferred that CubeO is 3.00 times or more compared with random orientation density.Wherein, the upper limit value of the multiplying power is not special
Regulation according to the composition of aluminium alloy and manufacturing condition determines, upper limit value is defined as 7.00 times in the present invention naturally.In addition,
CubeO/SO is preferably 0.50~1.00.
1.3. the feature of intensity
Then, the DR tank bodies of the present invention are illustrated with the intensity of aluminium alloy plate.It provides in the present invention, burns in blank
The tensile strength of proof stress and more than 230MPa after burning with 180~220MPa.Elastic pole after pre-burn
Stress is limited less than in the case of 180MPa, the intensity as DR tank bodies is insufficient.On the other hand, the elastic pole after pre-burn
Stress is limited more than in the case of 220MPa, when being molded fold can occur for deep-draw, reduce surface quality.Bullet after pre-burn
Property limit stress is preferably 190~210MPa.In addition, in the case that the tensile strength after pre-burn is less than 230MPa, pole
Drawing is limited than reducing, deep drawing quality is deteriorated.Wherein, the tensile strength after pre-burn is preferably more than 235MPa.Here, blank
The upper limit value of tensile strength after calcination does not have special provision, is determined naturally according to the composition of aluminium alloy and manufacturing condition, this hair
It is bright middle upper limit value to be defined as 255MPa.
1.4. the feature (2) of orientation density
Then, the DR tank bodies of the present invention are illustrated with the feature of the other orientation density of aluminium alloy plate.The present invention
In CubeO in intermediate annealing plate is preferably made compared with random orientation density to be 4.00 times or more, also, CubeO and R are taken
More than 1.00 are defined as to the ratio between density (being denoted as below " RO ") (CubeO/RO).
In the case where CubeO is less than 1.00 compared with random orientation density less than 4 times or CubeO/RO, centre is moved back
The prosperity of 0/90 degree of ear processed in fiery plate is insufficient, and 45 degree ears processed during secondary cold-rolling are significantly flourishing, earing rate variation.
It is preferred that CubeO is 4.50 times or more compared with random orientation density.Wherein, the upper limit value of the multiplying power is not special
Regulation according to the composition of aluminium alloy and manufacturing condition determines, upper limit value is defined as 10 times in the present invention naturally.In addition,
CubeO/RO is preferably more than 1.00.The upper limit value of CubeO/RO does not have special provision, according to the composition of aluminium alloy and manufacture item
Part determines naturally, and upper limit value is defined as 5.00 in the present invention.
The manufacturing method of 2.DR tank body aluminium alloy plates
The manufacturing method of the DR tank body aluminium alloy plates of the present invention includes：Cast the casting of above-mentioned defined composition aluminium alloy
Make process；The homogenize process process of homogenize process is carried out to ingot bar；The heat of hot rolling is carried out to the ingot bar after homogenize process
Roll process；The once cold rolling process of hot rolled plate；The intermediate annealing process annealed to once cold rolling plate with 300~450 DEG C；
With the secondary cold-rolling process of intermediate annealing plate.
2-1. casting process
The aluminium alloy of above-mentioned alloy composition is cast by semi-continuous casting method, ingot bar is made.
2-2. homogenize process processes
In homogenize process process, preferably by the ingot bar cast in casting process at 580~620 DEG C of temperature heat
When reason 1~12 is small.In treatment temperature less than 580 degree DEG C and in the case of processing time is small less than 1, homogenizing effect is not
Fully.Further, since the precipitation granule number in hot-rolled process becomes more, recrystallizing after hot-rolled process is obstructed.As a result,
Pressure rolling tissue is remained in hot rolled plate, CubeO is also reduced in grain is recrystallized.Since the CubeO of the hot rolled plate is moved back in centre
A part for the core of grain is orientated when fiery as Cube, it is important not make its reduction.In addition, if treatment temperature is more than 620 DEG C,
Oxidation or expansion then occur on ingot bar surface, causes the reduction of surface quality.In addition, when being more than 12 small even if processing time
Effect cannot be made to be further improved, deteriorate production efficiency.Wherein, the temperature of homogenize process process is more preferably
580~610 DEG C, processing time be more preferably 1~4 it is small when.
2-3. hot-rolled process
After homogenize process process, hot-rolled process is implemented to ingot bar.Hot-rolled process includes hot rough rolling step and hot finishing
Stage.In hot rough rolling step, start temperature is preferably set as 450~610 DEG C, end temp is set as to 450~550 DEG C.
In the case where start temperature is less than 450 DEG C, cause the precipitation of intermetallic compound, also, the temperature for rolling plate reduces.It is tied
Fruit remains pressure rolling tissue in the tissue after hot finishing, makes 45 degree of ears processed of production board become flourishing.Surpass in start temperature
In the case of crossing 610 DEG C, the surface for rolling plate is aoxidized, and is being rolled plate surface generation problem in pressure rolling, is being reduced quality.In addition,
In the case where end temp is less than 450 DEG C, the drafts of every a time is reduced due to having to inhibit necessity of deformation drag,
Production efficiency reduces.On the other hand, in the case where end temp is more than 550 DEG C, it is sintered on the surface for rolling plate, surface
Quality reduces.The pressure rolling time in hot rough rolling step and hot finishing stage is not particularly limited, and is preferably within 20 minutes.Its
In, more preferably by the start temperature of hot rough rolling step be set as 470~580 DEG C, end temp be set as 450~530 DEG C.
After hot rough rolling step, implement the hot finishing stage to rolling plate.In the hot finishing stage, preferably end temp is set
For 330~380 DEG C.In the case where end temp is less than 330 DEG C, the driving force deficiency of recrystallization.As a result, in plate is rolled
Remaining has rolled structure, makes 45 degree of ears processed of production board become flourishing, and earing rate is deteriorated.Further, since it needs to inhibit pressure rolling speed
Degree, production efficiency also reduce.In the case where end temp is more than 380 DEG C, it is sintered on the surface for rolling plate, surface quality
It reduces.Wherein, the end temp in hot finishing stage is more preferably set as 330~370 DEG C.
The conductivity of hot rolled plate after hot-rolled process is preferably 36.0~43.0%IACS.It is less than 36.0% in conductivity
In the case of IACS, become high solid solution condition, make the reduction of deep-draw mouldability, crack in tank processed.On the other hand, leading
In the case that electric rate is more than 43.0%IACS, the precipitate in hot rolled plate increases, and in intermediate annealing, R orientations preferentially form, into
45 degree of ears processed of product plate significantly become flourishing.The conductivity of hot rolled plate is more preferably set as 36.0~42.0% IACS.
There is no special provision for total pressure rolling rate of hot-rolled process entirety, be preferably set to 80~95%.Less than 80%
When, the S orientation densities in hot rolled plate reduce, and 0/90 degree ear processed during self-annealing dies down, and during more than 95%, recrystallization drives
Power is excessively high, and earless occurs for ear processed, and Cube orientation densities during each comfortable intermediate annealing is caused to reduce.In hot-rolled process entirety
Total pressure rolling rate be more preferably 85~93%.
2-4. once cold rolling processes
After hot-rolled process, once cold rolling process is implemented to hot rolled plate.The pressure rolling rate of once cold rolling process is preferably 85~
95%.In the case where pressure rolling rate is less than 85%, the prosperity of the S orientations in the karyogenesis site as Cube orientations is insufficient,
In the case that pressure rolling rate is more than 95%, the PSN as the karyogenesis around crystal becomes notable, makes 45 in secondary cold-rolling
Degree ear processed becomes flourishing, causes the deterioration of earing rate.Wherein, the pressure rolling rate of once cold rolling process be more preferably set as 87~
93%.
2-5. intermediate annealing processes
After once cold rolling, intermediate annealing process is implemented to cold-reduced sheet.In intermediate annealing process, preferably：First, at 200 DEG C
Once cold rolling plate is warming up to 300~450 DEG C of annealing with 10~100 DEG C/h of average heating speed by above temperature region
Temperature, afterwards, when annealing temperature holding 1~4 is small.Intermediate annealing process in this way, it is opposite can to obtain CubeO
In the intermediate annealing plate that random orientation is 4 times or more and CubeO/RO is more than 1.
In the case where the average heating speed of 200 DEG C or more of temperature regions is less than 10 DEG C/h, recrystallization and analysis
The competition gone out becomes notable, and the formation of R orientations is tempestuously promoted.On the other hand, in the case of more than 100 DEG C/h,
It since the involute and outer volume of coil causes temperature gradient, generates that hot exapnsion is poor, rubs between the plate of overlapping, make surface product
Matter reduces.In addition, temperature region is limited to 200 DEG C, the above are due to recrystallizing and being precipitated the reason competed.Wherein,
More preferably it is set as 15~80 DEG C/h in the average heating speed of 200 DEG C or more of temperature regions.
In annealing temperature less than 300 DEG C and in the case of annealing time is small less than 1, it is impossible to obtain perfect recrystallization
Tissue.In addition, in the case where annealing temperature is more than 450 DEG C, cold-rolled lubricating oil is sintered in the surface of intermediate annealing plate, surface quality
It reduces.In the case of annealing time is small more than 4, production efficiency deteriorates.Wherein, annealing temperature be more preferably set as 330~
400 DEG C, annealing time be more preferably set as 2~4 it is small when.
2-6. secondary cold-rolling processes
Secondary cold-rolling process is implemented to the intermediate annealing plate after intermediate annealing operation.The pressure rolling rate of secondary cold-rolling process is excellent
Choosing is set as 20~40%.In the case where pressure rolling rate is less than 20%, intensity deficiency.As a result, it cannot get tank intensity, separately
Outside, crack when deep-draw is molded.In the case where pressure rolling rate is more than 40%, proof stress becomes excessively high, tensile strength
Also become smaller with the ratio between proof stress.As a result, cracking or fold occur when deep-draw is molded.It is more than 40% in pressure rolling rate
In the case of, rolled structure can also be made to become flourishing, therefore, 45 degree of ears processed also become strong.
2-7. final annealing processes
After secondary cold-rolling, can also possess the final annealing process annealed to secondary cold-rolling plate.Thereby, it is possible to adjust
The whole strength of materials and ductility can further improve mouldability.In final annealing process, with average heating speed 10~80
DEG C/h be warming up to 140~190 DEG C of annealing temperature, afterwards the annealing temperature keep 2~4 it is small when.
In the case where average heating speed is less than 10 DEG C/h, production efficiency is deteriorated.On the other hand, more than 80
In the case of DEG C/h, heat input is insufficient, it is impossible to which the effect sufficiently annealed is only to become manufacture cost
It is high.In addition, in annealing temperature less than 140 DEG C and in the case of annealing time is small less than 2, the effect of annealing is insufficient.
In the case that annealing temperature is more than 190 DEG C, softening is excessive, and the strength of materials reduces.Situation when annealing time is more than 4 small
Under, deteriorate production efficiency.Wherein, annealing temperature is more preferably set as 160~180 DEG C, and annealing time is more preferably set as 2
~3 it is small when.
Embodiment
For the embodiment of the present invention, illustrated based on following recorded example of the present invention and comparative example.These are implemented
Example is only used for illustrating the embodiment of an embodiment of the invention, and the present invention limits from these.
The aluminium alloy of composition with A~U shown in table 1 is manufactured into ingot bar according to usual method, by DC castings.
Carry out homogenize process, hot rolling, once cold rolling, intermediate annealing, secondary cold-rolling, final to ingot bar with the condition shown in table 2 respectively
Annealing has manufactured the end article that thickness is 0.22mm.
[table 1]
[table 2]
It is evaluated for hot rolled plate, intermediate annealing plate and production board.Conductivity has been carried out firstly, for hot rolled plate
Measure and structure observation.On conductivity, using vortex electric conductivity measuring apparatus, it is determined using copper as authentic strain.
On structure observation, using Barker methods, the section (L-ST faces) of plate is ground and observed.In structure observation, it will be formed
Situation for perfect recrystallization tissue is denoted as "○", and the situation for remaining pressure rolling tissue is denoted as "×", is evaluated.
Then, structure observation and texture evaluation have been carried out to intermediate annealed sheet.On structure observation, to the section (L- of plate
ST faces) it is evaluated in the same manner as hot rolled plate.It is evaluated on texture, the OIM that TSL companies has been used to manufacture leads to plate surface
Cross the progress of SEM-EBSD methods.Wherein, the evaluation of CubeO and RO does not consider inclination angle.
To production board, in plate thickness direction, the part from a surface to 1/4 is evaluated using X-ray diffraction device.
Here, it is similary when the evaluation of CubeO and SO is with intermediate annealing plate, inclination angle is not considered.
Intensity, earing rate, surface quality, deep drawing quality are also further had rated to production board.On intensity, JIS5 is used
Number test film is implemented in pressure rolling direction and parallel direction, measures the proof stress and tensile strength after pre-burn.Its
In, pre-burn condition is set as 205 DEG C × 10 minutes.Wherein, on proof stress, by the situation of 180~220MPa
" qualification " is defined as, it is on tensile strength, 230MPa is defined above for " qualification ", the situation of both sides' all qualifications is defined as
Evaluate (intensity) it is qualified, it is unqualified that either one is that underproof situation is defined as evaluation (intensity).
On earing rate, by the blank of diameter 57mm using the punch drawing and forming of 33mm for after cup type, to pressure rolling direction
Cup height be measured, calculated by following formula.
Earing rate (%)={ (being averaged for the height of average-paddy of the height on mountain)/average cup height } × 100
By 2.8% following provisions it is qualified (zero) for earing rate, remaining is defined as unqualified (×).On surface product
Matter is defined as qualified (zero), remaining rule by do not occur arbitrary situation in fold, expansion, sintering, surface damage, surface oxidation
It is set to unqualified.On deep drawing quality, cracking will not occur and occur and the molding situations of DR can be carried out continuously and be defined as qualification
(zero), remaining is defined as unqualified.
It is above evaluation result is shown in table 3,4.
[table 3]
[table 4]
In example 1~24 of the present invention, hot rolling and annealing when precipitation be suppressed, the same of appropriate texture can obtained
When show good earing rate.In addition, having obtained appropriate intensity yet, cracking or fold does not occur when deep-draw is molded, obtains
The aluminium alloy with deep drawing quality and low earing rate is arrived.
In comparative example 25, since the content of the Si in aluminium alloy is more, the precipitation quantitative change of intermetallic compound is more.As a result,
Since the formation of Cube orientations is suppressed, 45 degree of ears processed is caused to become flourishing, earing rate is deteriorated.
In comparative example 26, since the content of the Fe in aluminium alloy is more, coarse crystal becomes more.As a result, due to tying again
Recrystallization when brilliant around crystal prevails, and causes 45 degree of ears processed of production board to become flourishing, and earing rate is deteriorated.
In comparative example 27, since Cu contents are few, proof stress and tensile strength reduce.As a result, cause deep-draw into
It cracks during type.
In comparative example 29, since Mn contents are few, proof stress and tensile strength reduce.As a result, cause deep-draw into
It cracks during type.
In comparative example 31, since Mg contents are few, the strength of materials reduces.As a result, deep-draw is caused to be cracked when being molded.
In comparative example 28, since Cu contents are more, proof stress becomes excessively high.Therefore, pleat occurs when deep-draw is molded
Wrinkle, causes surface quality to reduce.
In comparative example 30, since Mn contents are more, proof stress becomes excessively high.Therefore, pleat occurs when deep-draw is molded
Wrinkle, causes surface quality to reduce.
In comparative example 32, since Mg contents are more, proof stress is made to become excessively high.Therefore, when deep-draw is molded
Fold causes surface quality to reduce.
In comparative example 33, since homogenization temperature is low, Second Phase Particle hinders recrystallization, in the tissue of hot rolled plate
Remain pressure rolling tissue.As a result, the driving force of recrystallization becomes excessively high, therefore the texture randomization of intermediate annealing plate, is led
Causing 45 degree of ears processed of production board becomes flourishing, and earing rate is deteriorated.
In comparative example 35, since the time that homogenizes is short, also, the end temp of hot finishing is low, and Second Phase Particle hinders
Recrystallization, remains pressure rolling tissue in the tissue of hot rolled plate.As a result, the driving force of recrystallization becomes excessively high, intermediate annealing
Therefore the texture randomization of plate, causes 45 degree of ears processed of production board to become flourishing, earing rate is deteriorated.
In comparative example 34, since homogenization temperature is high, also, the start temperature of hot roughing and end temp are high, occur swollen
Swollen, surface oxidation and sintering, surface quality reduce.
In comparative example 36, since the start temperature and end temp of hot roughing are low, also, the end temp of hot finishing is low,
The driving force of recrystallization reduces, pressure rolling tissue residue.As a result, the formation of the Cube orientations in intermediate annealing is suppressed, lead
45 degree of ears processed is caused to become flourishing, earing rate is deteriorated.
In comparative example 37, since the end temp of hot finishing is high, it is sintered on surface.Further, since secondary cold-rolling rate
Height, proof stress become excessively high, fold have occurred.Further, since secondary cold-rolling rate is high, 45 degree of ears processed is caused to become to send out
It reaches, earing rate is deteriorated.
In comparative example 38, since the end temp of hot finishing is low, also, intermediate anneal temperature is low.As a result, pressure rolling group
Residual is knitted, 45 in production board degree of ears processed is caused to become flourishing, earing rate is deteriorated.
In comparative example 39, since the end temp of hot finishing is low, also, heating rate during intermediate annealing is slow.It is tied
Fruit causes recrystallization to be competed with being precipitated, and hinders the formation of Cube orientations, causes 45 degree of ears processed of production board to become to send out
It reaches, earing rate is deteriorated.
In comparative example 40, heating rate during due to intermediate annealing is too fast, rubs between plate, surface has occurred
Damage.
In comparative example 41, since secondary cold-rolling rate is small, proof stress and tensile strength reduce.As a result, cause depth
It cracks when being washed into type.Further, since intermediate anneal temperature is high, the sintering of cold-rolled lubricating oil has occurred.
In comparative example 42, since the end temp of hot finishing is low, also, the intermediate annealing time is short.As a result, pressure rolling group
Knit residual, 45 degree of ears processed in production board become flourishing, cause the deterioration of earing rate.
In comparative example 43, since once cold rolling rate is small, fail to make the orientations of the S in matrix to become abundant prosperity.As a result,
The karyogenesis site of Cube orientations is reduced, and 45 degree of ears processed become flourishing in production board, cause the deterioration of earing rate.
In comparative example 44, since first time cold rolling rate is high, the recrystallization driving force before annealing becomes larger, the shape of Cube orientations
Become smaller into amount, 45 degree of ears processed of production board become flourishing, cause the deterioration of earing rate, in addition, being opened when deep-draw is molded
It splits.
Industrial utilizability
As described above, by controlling texture and intensity, also can using box annealing stove when carrying out intermediate annealing process
Obtain low earing rate and good deep drawing quality.Further, since without using continuous annealing furnace, therefore, it is possible to be manufactured into
This, and inhibition cost can be also expected in equipment investment.
Claims (7)
1. a kind of DR tank bodies aluminium alloy plate, it is characterised in that：
It is to be made of aluminium alloy, be at least made for production board via hot rolled plate and intermediate annealing plate from the ingot bar of the aluminium alloy
Aluminium alloy plate,
Wherein, the aluminium alloy contains Si：0.10~0.60 mass %, Fe：0.10~0.80 mass %, Cu：0.05~0.25
Quality %, Mn：0.80~1.50 mass %, Mg：0.80~1.30 mass %, remainder is by Al and inevitable impurity structure
Into,
Cube orientation densities (CubeO) in production board are 2.00 times or more compared with random orientation density, also, CubeO and S
The ratio between orientation density (SO) (CubeO/SO) is 0.40~1.00, after pre-burn, has the elastic limit of 180~220MPa
The tensile strength of stress and more than 230MPa, wherein, pre-burn condition is set as 205 DEG C × 10 minutes.
2. DR tank bodies aluminium alloy plate as described in claim 1, it is characterised in that：
The conductivity of the hot rolled plate is 36.0~43.0%IACS.
3. DR tank bodies aluminium alloy plate as claimed in claim 1 or 2, it is characterised in that：
Cube orientation densities (CubeO) in the intermediate annealing plate are 4.00 times or more compared with random orientation density, also,
The ratio between CubeO and R orientation densities (RO) (CubeO/RO) are more than 1.00.
4. the manufacturing method of the DR tank body aluminium alloy plates described in any one of claims 1 to 3, which is characterized in that including：
Casting contains Si：0.10~0.60 mass %, Fe：0.10~0.80 mass %, Cu：0.05~0.25 mass %, Mn：
0.80~1.50 mass %, Mg：The aluminium that 0.80~1.30 mass % and remainder are made of Al and inevitable impurity closes
The casting process of gold；
The homogenize process process of homogenize process is carried out to ingot bar；
The hot-rolled process of hot rolling is carried out to the ingot bar after homogenize process；
The once cold rolling process of hot rolled plate；
The intermediate annealing process annealed to once cold rolling plate；With
The secondary cold-rolling process of intermediate annealing plate.
5. the manufacturing method of DR tank bodies aluminium alloy plate as claimed in claim 4, it is characterised in that：
In the homogenize process process, ingot bar 580~620 DEG C processing 1~12 it is small when,
The hot-rolled process include start temperature is 450~610 DEG C and end temp is 450~550 DEG C hot rough rolling step and
End temp is 330~380 DEG C of hot finishing stage,
The pressure rolling rate of the once cold rolling process is 85~95%,
In the intermediate annealing process, once cold rolling plate is in 200 DEG C or more of temperature region with average heating speed 10~100
DEG C/h be warming up to 300~450 DEG C of annealing temperature, afterwards the annealing temperature keep 1~4 it is small when,
The pressure rolling rate of the secondary cold-rolling process is 20~40%.
6. the manufacturing method of DR tank bodies aluminium alloy plate as described in claim 4 or 5, it is characterised in that：
It is also equipped with the final annealing process annealed after the secondary cold-rolling process to secondary cold-rolling plate.
7. the manufacturing method of DR tank bodies aluminium alloy plate as claimed in claim 6, it is characterised in that：
In the final annealing process, secondary cold-rolling plate is in 200 DEG C or more of temperature region with average heating speed 10~80
DEG C/h be warming up to 140~190 DEG C of annealing temperature, afterwards the annealing temperature keep 2~4 it is small when.
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| US10604826B2 (en) * | 2015-12-17 | 2020-03-31 | Novelis Inc. | Aluminum microstructure for highly shaped products and associated methods |
| AU2017261184B2 (en) * | 2016-05-02 | 2019-09-05 | Novelis Inc. | Aluminum alloys with enhanced formability and associated methods |
| JP7138396B2 (en) * | 2017-02-01 | 2022-09-16 | 株式会社Uacj | Aluminum alloy plate for can body and manufacturing method thereof |
| JP6437583B2 (en) * | 2017-02-27 | 2018-12-12 | 株式会社Uacj | Aluminum alloy plate for magnetic disk substrate, manufacturing method thereof, and magnetic disk using the aluminum alloy plate for magnetic disk substrate |
| JP6402229B1 (en) * | 2017-09-28 | 2018-10-10 | 株式会社Uacj | Aluminum alloy substrate for magnetic disk, manufacturing method thereof, and magnetic disk using the aluminum alloy substrate for magnetic disk |
| CN112122882A (en) * | 2019-06-25 | 2020-12-25 | 西南铝业（集团）有限责任公司 | Production process of pure aluminum alloy O-state plate |
| EP3875629A1 (en) | 2020-03-03 | 2021-09-08 | Elvalhalcor Hellenic Copper and Aluminium Industry S.A. | Method and installation for producing aluminum can sheet |
| EP4050115A1 (en) | 2021-02-26 | 2022-08-31 | Constellium Rolled Products Singen GmbH & Co.KG | Durable aluminium alloy sheet for decorative applications |
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| JP3587993B2 (en) * | 1998-09-03 | 2004-11-10 | 三菱アルミニウム株式会社 | Manufacturing method of aluminum alloy sheet for deep drawing |
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| CN1183813A (en) * | 1995-03-09 | 1998-06-03 | 戈尔登铝材公司 | Method for making aluminium alloy sheet products |
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| CN106103760A (en) | 2016-11-09 |
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