CN106103760A - DR tank body aluminium alloy plate and manufacture method thereof - Google Patents
DR tank body aluminium alloy plate and manufacture method thereof Download PDFInfo
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- CN106103760A CN106103760A CN201480077133.7A CN201480077133A CN106103760A CN 106103760 A CN106103760 A CN 106103760A CN 201480077133 A CN201480077133 A CN 201480077133A CN 106103760 A CN106103760 A CN 106103760A
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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
- 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
Abstract
Even if the present invention provides a kind of also has low earing rate and the DR tank body aluminium alloy of deep drawing quality excellence and manufacture method thereof in the case of using batch stove.nullA kind of DR tank body aluminium alloy plate and manufacture method thereof，Wherein，DR tank body aluminium alloy plate is for be made up of aluminium alloy、It is made for the aluminium alloy plate of production board via hot rolled plate and intermediate annealing plate from this aluminium alloy ingot bar，Wherein，Aluminium alloy contains Si:0.10～0.60 mass % (being designated as " % " below)、Fe:0.10～0.80%、Cu:0.05～0.25%、Mn:0.80～1.50%、Mg:0.80～1.30% and remainder are made up of Al and inevitable impurity，Cube orientation density (CubeO) in production board is more than 2.00 times relative to random orientation density，And，The ratio (CubeO/SO) of CubeO Yu S orientation density (SO) is 0.40～1.00，After pre-burn，There is the proof stress of 180～220MPa and the hot strength of more than 230MPa.
Description
Technical field
The present invention relates to a kind of deep drawing quality is excellent and earing rate is little DR tank body aluminium alloy and manufacture method thereof.
Background technology
The such aluminium alloy of A3004 or A3104 in JIS specification, owing to having mouldability and the corrosion resistance of excellence, is made
Tank body material for aluminium pot is used.The tank body of aluminium pot have the DR tank only manufactured by deep-draw molding and by deep-draw molding and
The DI tank that flatiron molding manufactures.In these aluminium pots, earing rate is important characteristic.Here, earing rate is illustrated.Logical
Often, in the cup after deep-draw molding, high part (" mountain ") and low part (" paddy ") can be produced in the upper end of circumferential part.By this mountain
The value that obtains divided by the meansigma methods of the height of paddy of the difference of meansigma methods of height of meansigma methods and paddy of height be referred to as earing rate.
In the case of earing rate difference, have and carry out with cover producing bad place when crimping engages or making cutting amount increase and reduce finished product
Rates etc. produce harmful effect to production efficiency.
As the shape of ear processed, have the 0/90 degree of ear processed having mountain to erect relative to direction, 0/90 degree of pressure rolling direction and relative to
45 degree of ears processed that direction, 45 degree of pressure rolling direction has mountain to erect.Various ears processed and the relevant property of texture, it is known that Cube is orientated:
(001) ＜ 100 ＞ makes 0/90 degree of ear processed become flourishing, and the beta as rolled structure makes 45 degree of ears processed become flourishing.Need
Bright, cold rolling rate is the highest, and beta is the most flourishing, and 45 degree of ears processed become notable.In order to obtain the earing rate of excellence, need to make
Cube orientation is with rolled structure, particularly S and R orientation: { 123} ＜ 634 ＞ has good balance.
Above-mentioned DR tank body is mainly the purposes of containers for food use, increases with the population in the world, it is contemplated that demand also can increase.
At present, DR tank body is by including the manufacture method manufacture of intermediate annealing operation, and intermediate annealing uses box annealing stove (below, note
For " batch stove ") and continuous annealing furnace (being designated as " CAL " below).Manufacturing cost aspect, CAL is high, for improving production capacity
Equipment investment is the most expensive.Therefore, in order to realize cost degradation, need to use batch stove to manufacture, but compared with CAL,
The control of ear processed is more difficult, has the difficult point easily making 45 degree of ears become prosperity.
Further, since the only molding by deep-draw of DR tank body, need the deep-draw mouldability of height.Specifically, for profundity
The generation of fold when punching property and minimizing deep-draw molding.Deep drawing quality is evaluated by limited drawing ratio, if deep drawing quality is bad, then
Cracking it is susceptible to when molding.If it addition, there is fold during deep-draw molding, the surface quality of goods can be made to significantly reduce.Closely
Nian Lai, for the requirement increasingly stringent of surface quality.
Patent documentation 1 has been recorded the manufacture method of the packaging aluminium alloy plate using deep drawing quality or redrawing property.It addition,
Patent documentation 2 has been recorded the manufacture method of the packaging aluminium alloy with high intensity and low orientated property.It addition, patent documentation 3
～in 5, describe as the technology about above-mentioned texture and the Cube in hot rolled plate, intermediate annealing plate, production board is orientated
Or the aluminium alloy plate with low earing rate that rolled structure is specified.
In patent documentation 1, although attempt by process or the cold rolling rate control ear processed of homogenizing, but the most so, make
Sufficient low earing rate can not be obtained in the case of carrying out intermediate annealing with batch stove.It addition, in the aluminium alloy of patent documentation 2,
There is the worry that fold occurs when deep-draw molding due to high intensity.It is as noted previously, as carrying of the requirement for surface quality
High, it is difficult to the aluminium alloy of patent documentation 2 is applicable to DR tank body material.
On the other hand, although in the technology of patent documentation 3～5 being controlled metal structure, but purposes is limited to DI
Tank purposes.In DI tank purposes, do not use intermediate annealing operation, be formed as high cold rolling rate.The superhard material used is due to tool
There is high elastic limit stress, be susceptible to fold when deep-draw molding, be unsuitable for DR tank purposes.Further, since patent documentation 5
Hot rolled plate tissue is partial, re-crystallization tissue, if plate temperature does not reduces, then can not obtain partial, re-crystallization tissue.Therefore, no
Obtain and do not reduce the pressure rolling speed as one of manufacturing condition, have the problem causing production efficiency to reduce and make manufacturing cost uprise.
Prior art document
Patent documentation
Patent documentation 1: Japanese Laid-Open Patent Publication 63-145758 publication
Patent documentation 2: Japanese Unexamined Patent Publication 1-198454 publication
Patent documentation 3: Japanese Unexamined Patent Publication 2001-40461 publication
Patent documentation 4: Japanese Unexamined Patent Publication 2004-244701 publication
Patent documentation 5: Japanese Unexamined Patent Publication 2004-263253 publication
Summary of the invention
Invent problem to be solved
The present inventor is repeated various experiment and research, it was found that the gold before intermediate annealing operation
Belong in tissue, by making S be oriented in substrate flourishing fully, during suppression recrystallization precipitation, can be in the situation of batch stove
Under also obtain having the aluminium alloy plate of earing rate of excellence.That is, as crystalline orientation, it is known that have between Cube orientation and S orientation
Having the rotation relationship rotating 40 degree along ＜ 111 ＞ axle, in the substrate of S orientation, Cube orientation is easily grown up.Thus, by making this
S orientation becomes flourishing, makes Cube orientation easily grow up.It addition, precipitate hinders the formation that recrystallization suppresses Cube to be orientated, promote
Enter R orientation to be formed.Thus, suppress to separate out granule number by making S orientation become flourishing fully, it is possible to using batch stove
Intermediate annealing operation obtains the earing rate of excellence.
It addition, with or without there is fold during deep-draw molding, result from the proof stress after pre-burn.Blank is burnt
Although the proof stress after burning reduces the generation that can suppress fold, but owing to hot strength also reduces, makes deep drawing quality become
Difference.Consequently found that, suitably regulate proof stress and hot strength by controlling cold rolling rate, it is possible to maintain good deep-draw
Property also suppresses the generation of fold.
It is an object of the invention to provide the aluminium alloy and manufacture method thereof found based on above opinion, this aluminium alloy is for i.e.
Also there is in the case of use batch stove low earing rate and the DR tank body aluminium alloy of deep drawing quality excellence.
For the method solving problem
It is a feature of the present invention that control once cold rolling rate rightly.By improving once cold rolling rate, it is possible to make S orientation become
Obtain flourishing.But, in the case of once cold rolling rate is too high, the PSN from the recrystallization around crystal becomes notable, metal
Tissue becomes the random tissue that Cube orientation density reduces.Its result understands so that 0/90 degree of ear processed cannot be made to become flourishing, lead
Cause 45 degree of ears processed and become flourishing.Thus, the group by controlling once cold rolling rate rightly, before making S be oriented in intermediate annealing operation
Knit and become flourishing, and, suppress the precipitation when precipitation granule number in the tissue before intermediate annealing operation and recrystallization.Thus,
The growth that Cube is orientated can be promoted in annealing operation.That is, promote that 0/90 degree ear processed becomes prosperity, by with secondary cold-rolling work
The good balance of sequence, obtains the earing rate of excellence.It addition, in secondary cold-rolling operation, by suitable control elastic limit
Stress and hot strength, it is possible to obtain good deep drawing quality and meet the aesthetic property of high surface quality.
In the claim 1 of the present invention, obtain a kind of DR tank body aluminium alloy plate, it is characterised in that this DR tank body aluminum
Alloy sheets is to be made up of aluminium alloy, be at least made for production board via hot rolled plate and intermediate annealing plate from the ingot bar of this aluminium alloy
Aluminium alloy plate, wherein, this aluminium alloy contain 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 the most miscellaneous
Matter is constituted, and Cube orientation density (CubeO) in production board is more than 2.00 times relative to random orientation density, and, CubeO
It is 0.40～1.00 with the ratio (CubeO/SO) of S orientation density (SO), after pre-burn, there is the elasticity of 180～220MPa
Limit stress and the hot strength of more than 230MPa.
The claim 2 of the present invention is: in claim 1, and the conductivity of above-mentioned hot rolled plate is 36.0～43.0%IACS.
The claim 3 of the present invention is: in claims 1 or 2, the Cube in above-mentioned intermediate annealing plate is orientated density
(CubeO) it is more than 4.00 times relative to random orientation density, and, the ratio (CubeO/RO) of CubeO Yu R orientation density (RO)
More than 1.00.
The claim 4 of the present invention any one of claims 1 to 3 described in the manufacture of DR tank body aluminium alloy plate
Method, it is characterised in that including: casting is containing 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 inevitable
The casting process of aluminium alloy that constitutes of impurity；The process that homogenizes ingot bar homogenizes treatment process；To the place that homogenizes
Ingot bar after reason carries out the hot-rolled process of hot rolling；The once cold rolling operation of hot rolled plate；The centre that once cold rolling plate is annealed
Annealing operation；Secondary cold-rolling operation with intermediate annealing plate.
The claim 5 of the present invention is: in claim 4, homogenizes in treatment process above-mentioned, and ingot bar is 580～620
Process 1～12 hour at DEG C；Above-mentioned hot-rolled process includes starting temperature 450～610 DEG C and end temp 450～the heat of 550 DEG C
Rough rolling step and end temp 330～the hot finishing stage of 380 DEG C；The pressure rolling rate of above-mentioned once cold rolling operation is 85～95%；
In above-mentioned intermediate annealing operation, once cold rolling plate temperature province more than 200 DEG C with average heating speed 10～100 DEG C/
Hour it is warming up to the annealing temperature of 300～450 DEG C, keeps 1～4 hour in this annealing temperature afterwards；Above-mentioned secondary cold-rolling operation
Pressure rolling rate be 20～40%.
The claim 6 of the present invention is: in claim 4 or 5, is also equipped with after above-mentioned secondary cold-rolling operation secondary
Cold-reduced sheet carries out the final annealing operation annealed.
The claim 7 of the present invention is: in claim 6, and in above-mentioned final annealing operation, secondary cold-rolling plate is 200
Temperature province more than DEG C is warming up to the annealing temperature of 140～190 DEG C with average heating speed 10～80 DEG C/h, exists afterwards
This annealing temperature keeps 2～4 hours.
The effect of invention
Even if by means of the invention it is possible to also obtaining that in the case of using batch stove there is low earing rate and deep drawing quality excellence
DR tank body aluminium alloy.
Detailed description of the invention
1.DR tank body aluminium alloy plate
The aluminium alloy that the DR tank body aluminium alloy plate of the present invention is made up of the alloy specified is constituted, and production board is characterised by
Have and be specifically orientated density (CubeO), and after pre-burn, there is the intensity of regulation.
1.1. the composition of aluminium alloy
First, the restriction reason of each composition involved by aluminium alloy composition is illustrated.
Si:0.10～0.60 mass %
By containing Si, Mg when final annealing and when coating is fired2Si system granule separates out, and contributes to intensity and improves.
When the content of Si is less than 0.10 mass % (being designated as " % " below), it is impossible to obtain this effect, it addition, have to use when casting
Highly purified feed metal, makes cost of material increase.On the other hand, if more than 0.60%, increase, in hot rolling owing to separating out granule
Recrystallizing in operation and intermediate annealing operation is hindered.As its result, the formation of Cube orientation is suppressed, finished product
The earing rate of plate is deteriorated.Wherein, the preferred content of Si is 0.20～0.50%.
Fe:0.10～0.80%
Owing to containing Fe, making the Solid solution precipitation state of Mn be controlled, make Mn system crystal be uniformly dispersed, thus improve
Deep-draw mouldability.When the content of Fe is less than 0.10%, it is impossible to obtain this effect, it addition, have to use high-purity when casting
Feed metal, make cost of material increase.On the other hand, if more than 0.80%, then brilliant due to thick Al-Fe-Mn-Si tying
Thing increases, and the recrystallization in the high displacement density region around the crystal of referred to as PSN prevails.Its result, Cube is orientated
Density reduces, 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, Al-Cu-Mg system and the granule of Al-Cu-Mg-Si system when final annealing and when coating is fired
Separate out, contribute to intensity and improve.When the content of Cu is less than 0.05%, it is impossible to obtain this effect, if more than 0.25%, then intensity becomes
Obtaining too 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, contribute to intensity and 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%, then intensity is too high, and deep-draw mouldability is deteriorated.Wherein, the preferred content of Mn be 0.80～
1.10%.
Mg:0.80～1.30%
By containing Mg, the intensity contributing to being obtained by solid solution improves.It addition, by forming Mg with Si2Si system granule,
Contribute to intensity during final annealing and when coating is fired to improve.When the content of Mg is less than 0.80%, it is impossible to obtain this effect.Separately
On the one hand, if more than 1.30%, then intensity becomes too high, and deep-draw mouldability is deteriorated.Wherein, the preferred content of Mg be 0.90～
1.25%.
In above-mentioned aluminium alloy, Ti, B, V etc. as inevitable impurity can contain less than 0.05%, respectively with whole
Body meter contains less than 0.15%.
1.2. the feature (1) of density it is orientated
Then, the feature of the orientation density of the DR tank body aluminium alloy plate of the present invention is illustrated.In the present invention, make into
Cube orientation density (being designated as " CubeO " below) in product plate is more than 2.00 times relative to random orientation density, and, will
The ratio (CubeO/SO) of CubeO Yu S orientation density (being designated as " SO " below) is defined as 0.40～1.00.
The shape of ear processed is determined by the balance of CubeO and CubeO with rolled structure.Low relative to random orientation at CubeO
In the case of being less than 0.40 in 2.00 times or CubeO/SO, 45 degree of ears processed become flourishing, cause the deterioration of earing rate.The opposing party
Face, in the case of CubeO/SO is more than 1.00, it is impossible to obtains the good balance of 0/90 degree of ear processed and 45 degree of ears processed, leads equally
Cause the deterioration of earing rate.
Preferably CubeO is more than 3.00 times relative to random orientation density.Wherein, the higher limit of this multiplying power is advised the most especially
Fixed, composition and manufacturing condition according to aluminium alloy determine naturally, in the present invention, higher limit are defined as 7.00 times.It addition,
CubeO/SO is preferably 0.50～1.00.
1.3. the feature of intensity
Then, the intensity of the DR tank body aluminium alloy plate of the present invention is illustrated.The present invention specifies, at pre-burn
After there is the proof stress of 180～220MPa and the hot strength of more than 230MPa.Elastic limit after pre-burn
Stress is less than in the case of 180MPa, and the intensity as DR tank body is not enough.On the other hand, the elastic limit after pre-burn should
In the case of power is more than 220MPa, fold can occur during deep-draw molding, make surface quality reduce.Elastic limit after pre-burn
Stress is preferably 190～210MPa.It addition, in the case of the hot strength after pre-burn is less than 230MPa, Limit Drawing
Than reducing, deep drawing quality is deteriorated.Wherein, the hot strength after pre-burn is preferably more than 235MPa.Here, after pre-burn
The higher limit of hot strength does not has special provision, and composition and manufacturing condition according to aluminium alloy determine naturally, by upper in the present invention
Limit value is defined as 255MPa.
1.4. the feature (2) of density it is orientated
Then, the feature of the other orientation density of the DR tank body aluminium alloy plate of the present invention is illustrated.The present invention
In preferably to make the CubeO in intermediate annealing plate be more than 4.00 times relative to random orientation density, and, CubeO Yu R is orientated
The ratio (CubeO/RO) of density (being designated as " RO " below) is defined as more than 1.00.
In the case of CubeO is less than 1.00 relative to random orientation density less than 4 times or CubeO/RO, intermediate annealing
The prosperity of 0/90 degree of ear processed in plate is insufficient, and 45 degree of ears processed during secondary cold-rolling are the most flourishing, and earing rate is deteriorated.
Preferably CubeO is more than 4.50 times relative to random orientation density.Wherein, the higher limit of this multiplying power is advised the most especially
Fixed, composition and manufacturing condition according to aluminium alloy determine naturally, in the present invention, higher limit are defined as 10 times.It addition, CubeO/
RO is preferably more than 1.00.The higher limit of CubeO/RO does not has special provision, and composition and manufacturing condition according to aluminium alloy are natural
Determine, higher limit is defined as 5.00 by the present invention.
The manufacture method of 2.DR tank body aluminium alloy plate
The manufacture method of the DR tank body aluminium alloy plate of the present invention includes: cast the casting of the composition aluminium alloy of above-mentioned regulation
Operation；The process that homogenizes ingot bar homogenizes treatment process；The ingot bar after processing that homogenizes is carried out the hot rolling of hot rolling
Operation；The once cold rolling operation of hot rolled plate；To once cold rolling plate with 300～450 DEG C of intermediate annealing operations annealed；In with
Between the secondary cold-rolling operation of annealed sheet.
2-1. casting process
Cast the aluminium alloy of above-mentioned alloy composition by semi-continuous casting method, make ingot bar.
2-2. homogenizes treatment process
In the treatment process that homogenizes, preferably by the ingot bar that casts at casting process at the temperature heat treatment of 580～620 DEG C
1～12 hour.In the case for the treatment of temperature is less than 580 degree DEG C and the time of process is less than 1 hour, homogenizing effect does not fills
Point.Further, since the precipitation granule number in hot-rolled process becomes many, recrystallizing after hot-rolled process is obstructed.Its result, hot rolling
Remaining pressure rolling tissue in plate, in recrystallization grain, CubeO also reduces.Owing to the CubeO of this hot rolled plate becomes when intermediate annealing
For a part for the core of Cube orientation grain, it is important for not making it reduce.If it addition, treatment temperature is more than 620 DEG C, then at ingot bar
There is oxidation or expand in surface, causes the reduction of surface quality.Even if additionally, the process time can not make effect more than 12 hours
It is further improved, makes production efficiency deteriorate.Wherein, the temperature of the treatment process that homogenizes is more preferably 580～610 DEG C,
The process time is more preferably 1～4 hour.
2-3. hot-rolled process
After the treatment process that homogenizes, ingot bar is implemented hot-rolled process.Hot-rolled process includes hot rough rolling step and hot finishing
Stage.In hot rough rolling step, preferably beginning temperature is set as 450～610 DEG C, end temp is set as 450～550 DEG C.
In the case of beginning temperature is less than 450 DEG C, cause the precipitation of intermetallic compound, and, the temperature rolling plate reduces.Its knot
Really, the tissue after hot finishing remains pressure rolling tissue, make 45 degree of ears processed of production board become flourishing.Exceed starting temperature
In the case of 610 DEG C, the surface rolling plate is oxidized, is rolling plate surface generation problem, make quality reduce in pressure rolling.It addition,
In the case of end temp is less than 450 DEG C, owing to having the drafts reducing every a time to suppress necessity of deformation drag, produce
Efficiency reduces.On the other hand, in the case of end temp is more than 550 DEG C, sintering on the surface rolling plate, surface quality drops
Low.Hot rough rolling step and the pressure rolling time in the hot finishing stage are not particularly limited, within preferably 20 minutes.Wherein, more excellent
Choosing the beginning temperature of hot rough rolling step is 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 as
330～380 DEG C.In the case of end temp is less than 330 DEG C, the driving force of recrystallization is not enough.Its result, remaining in rolling plate
Having rolled structure, make 45 degree of ears processed of production board become flourishing, earing rate is deteriorated.Further, since need to suppress pressure rolling speed, raw
Produce efficiency also to reduce.In the case of end temp is more than 380 DEG C, sintering on the surface rolling plate, surface quality reduces.Its
In, more preferably the end temp in hot finishing stage is set as 330～370 DEG C.
The conductivity of the hot rolled plate after hot-rolled process is preferably 36.0～43.0%IACS.In conductivity less than 36.0%
In the case of IACS, become high solid solution condition, make deep-draw mouldability reduce, ftracture when tank processed.On the other hand, in conduction
In the case of rate is more than 43.0%IACS, the precipitate in hot rolled plate increases, and when intermediate annealing, R orientation preferentially forms, finished product
45 degree of ears processed of plate become flourishing significantly.The conductivity of hot rolled plate is more preferably set as 36.0～42.0%IACS.
The total pressure rolling rate overall for hot-rolled process does not has special provision, is preferably set to 80～95%.Less than 80%
Time, the S orientation density in hot rolled plate reduces, and 0/90 degree of ear processed during self-annealing dies down, during more than 95%, and recrystallization driving force
Too high, ear generation earless processed, cause Cube orientation density during each comfortable intermediate annealing to reduce.Total in hot-rolled process entirety
Pressure rolling rate is more preferably 85～93%.
2-4. once cold rolling operation
After hot-rolled process, hot rolled plate is implemented once cold rolling operation.The pressure rolling rate of once cold rolling operation be preferably 85～
95%.In the case of pressure rolling rate is less than 85%, the prosperity as the S orientation in the karyogenesis site of Cube orientation is insufficient,
In the case of pressure rolling rate is more than 95%, becomes notable as the caryogenic PSN around crystal, make 45 degree when secondary cold-rolling
Ear processed becomes flourishing, causes the deterioration of earing rate.Wherein, the pressure rolling rate of once cold rolling operation is more preferably set as 87～93%.
2-5. intermediate annealing operation
After once cold rolling, cold-reduced sheet is implemented intermediate annealing operation.In intermediate annealing operation, preferably: first, at 200 DEG C
Once cold rolling plate is warming up to the annealing of 300～450 DEG C by above temperature province with average heating speed 10～100 DEG C/h
Temperature, afterwards, keeps 1～4 hour in this annealing temperature.By such intermediate annealing operation, can obtain CubeO relative to
Random orientation is more than 4 times and intermediate annealing plate that CubeO/RO is more than 1.
In the case of the average heating speed of the temperature province more than 200 DEG C is less than 10 DEG C/h, recrystallization and precipitation
Competition become notable, R orientation formation promoted tempestuously.On the other hand, in the case of more than 100 DEG C/h, due to
Involute and the outer volume of coil causes thermograde, produces hot exapnsion poor, rubs, make surface quality drop between overlapping plate
Low.It is above due to recrystallization it addition, temperature province to be limited to 200 DEG C and separates out the reason occurring to compete.Wherein, 200
The average heating speed of the temperature province more than DEG C is more preferably set as 15～80 DEG C/h.
In the case of annealing temperature is less than 300 DEG C and annealing time is less than 1 hour, it is impossible to obtain perfect recrystallization group
Knit.It addition, in the case of annealing temperature is more than 450 DEG C, cold-rolled lubricating oil is sintered in the surface of intermediate annealing plate, surface quality drops
Low.In the case of annealing time was more than 4 hours, production efficiency deteriorates.Wherein, annealing temperature is more preferably set as 330～400
DEG C, annealing time is more preferably set as 2～4 hours.
2-6. secondary cold-rolling operation
Intermediate annealing plate after middle annealing operation is implemented secondary cold-rolling operation.The pressure rolling rate of secondary cold-rolling operation is preferred
It is set as 20～40%.In the case of pressure rolling rate is less than 20%, intensity is not enough.Its result, can not get tank intensity, it addition,
Ftracture during deep-draw molding.In the case of pressure rolling rate is more than 40%, proof stress becomes too high, hot strength and bullet
The ratio of property limit stress also diminishes., there is cracking or fold when deep-draw molding in its result.In the pressure rolling rate situation more than 40%
Under, rolled structure also can be made to become flourishing, therefore, 45 degree of ears processed also become strong.
2-7. final annealing operation
After secondary cold-rolling, it is also possible to possess the final annealing operation that secondary cold-rolling plate is annealed.Thereby, it is possible to adjust
The strength of materials and ductility, it is possible to improve mouldability further.In final annealing operation, with average heating speed 10～80 DEG C/
Hour it is warming up to the annealing temperature of 140～190 DEG C, keeps 2～4 hours in this annealing temperature afterwards.
In the case of average heating speed is less than 10 DEG C/h, production efficiency is deteriorated.On the other hand, more than 80 DEG C/
In the case of hour, heat input is insufficient, it is impossible to the effect sufficiently annealed, and only makes manufacturing cost uprise.Separately
Outward, in the case of annealing temperature is less than 140 DEG C and annealing time is less than 2 hours, the effect of annealing is insufficient.In annealing temperature
In the case of degree is more than 190 DEG C, softening excessively, the strength of materials reduces.In the case of annealing time was more than 4 hours, make production
Degradation in efficiency.Wherein, annealing temperature is more preferably set as 160～180 DEG C, and annealing time is more preferably set as 2～3 hours.
Embodiment
For embodiments of the invention, illustrate based on following described 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 is not limited by these.
To there is the aluminium alloy of the composition of A～U shown in table 1 according to usual method, by DC casting manufacture ingot bar.Point
Not with the condition shown in table 2 ingot bar homogenized process, hot rolling, once cold rolling, intermediate annealing, secondary cold-rolling, finally move back
Fire, has manufactured the end article that thickness is 0.22mm.
[table 1]
[table 2]
Hot rolled plate, intermediate annealing plate and production board are evaluated.Conductivity survey has been carried out firstly, for hot rolled plate
Determine and structure observation.About conductivity, use eddy current electric conductivity measuring apparatus, be determined as authentic strain using copper.Close
In structure observation, use Barker method, the section (L-ST face) of plate is ground and observes.In structure observation, it is formed into
The situation of perfect recrystallization tissue is designated as "○", the situation remaining pressure rolling tissue is designated as "×", is evaluated.
Then, middle annealed sheet structure observation and texture evaluation have been carried out.About structure observation, the section (L-to plate
ST face) evaluated in the same manner as hot rolled plate.About texture evaluation, employ the OIM that TSL company manufactures, plate surface is led to
Cross SEM-EBSD method to carry out.Wherein, the evaluation of CubeO and RO does not considers inclination angle.
To production board, at plate thickness direction, X-ray diffraction instrument is used to be evaluated the part from a surface to 1/4.This
In, the evaluation of CubeO and SO, as during intermediate annealing plate, does not considers inclination angle.
Production board be have rated the most further intensity, earing rate, surface quality, deep drawing quality.About intensity, use No. JIS5
Test film, implements in pressure rolling direction and parallel direction, measures the proof stress after pre-burn and hot strength.Wherein,
Pre-burn condition is set as 205 DEG C × 10 minutes.Wherein, about proof stress, the situation by 185～220MPa specifies
For " qualified ", about the proof stress of hot strength, by defined above for 230MPa be " qualified ", by feelings the most qualified for both sides
Condition be defined as evaluate (intensity) qualified, by either one be underproof situation be defined as evaluate (intensity) defective.
About earing rate, after using the drift drawing and forming of 33mm to be cup type the blank of diameter 57mm, to pressure rolling direction
Cup high be measured, calculated by following formula.
Earing rate (%)={ (height of the average-paddy of the height on mountain average)/average cup height } × 100
Be qualified (zero) for earing rate by 2.8% following provisions, remaining be defined as defective (×).About surface product
Matter, by do not occur fold, expand, sinter, in surface damage, surface oxidation arbitrarily situation be defined as qualified (zero), remaining rule
It is set to defective.About deep drawing quality, cracking will not occurred to occur and can be carried out continuously the situation of DR molding be defined as qualified
(zero), remaining is defined as defective.
Above evaluation result is shown in table 3,4.
[table 3]
[table 4]
In example 1～24 of the present invention, precipitation when hot rolling and annealing is suppressed, while can obtaining appropriate texture
Demonstrate good earing rate.It addition, have also been obtained suitable intensity, there is not cracking or fold when deep-draw molding, obtain
There is deep drawing quality and the aluminium alloy of low earing rate.
In comparative example 25, owing to the content of the Si in aluminium alloy is many, the precipitation quantitative change of intermetallic compound is many.Its result,
Owing to the formation of Cube orientation is suppressed, causing 45 degree of ears processed to become flourishing, earing rate is deteriorated.
In comparative example 26, owing to the content of the Fe in aluminium alloy is many, thick crystal becomes many.Its result, owing to tying again
Time brilliant, the recrystallization 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, owing to Cu content is few, proof stress and hot strength reduce.Its result, causes deep-draw to become
Ftracture during type.
In comparative example 29, owing to Mn content is few, proof stress and hot strength reduce.Its result, causes deep-draw to become
Ftracture during type.
In comparative example 31, owing to Mg content is few, the strength of materials reduces.Its result, causes ftractureing during deep-draw molding.
In comparative example 28, owing to Cu content is many, proof stress becomes too high.Therefore, there is pleat when deep-draw molding
Wrinkle, causes surface quality to reduce.
In comparative example 30, owing to Mn content is many, proof stress becomes too high.Therefore, there is pleat when deep-draw molding
Wrinkle, causes surface quality to reduce.
In comparative example 32, owing to Mg content is many, proof stress is made to become too high.Therefore, occur when deep-draw molding
Fold, causes surface quality to reduce.
In comparative example 33, owing to homogenization temperature is low, Second Phase Particle hinders recrystallization, residual in the tissue of hot rolled plate
Leave pressure rolling tissue.Its result, the driving force of recrystallization becomes too high, the texture randomization of intermediate annealing plate, therefore, causes into
45 degree of ears processed of product plate become flourishing, and earing rate is deteriorated.
In comparative example 35, owing to the time of homogenizing is short, and, 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.Its result, the driving force of recrystallization becomes too high, intermediate annealing
The texture randomization of plate, therefore, causes 45 degree of ears processed of production board to become flourishing, and earing rate is deteriorated.
In comparative example 34, owing to homogenization temperature is high, and, the beginning temperature of hot roughing and end temp are high, occur swollen
Swollen, surface oxidation and sintering, surface quality reduces.
In comparative example 36, owing to beginning temperature and the end temp of hot roughing are low, and, the end temp of hot finishing is low,
The driving force of recrystallization reduces, pressure rolling tissue residue.Its result, the formation of the Cube orientation when intermediate annealing is suppressed, and leads
Causing 45 degree of ears processed and become flourishing, earing rate is deteriorated.
In comparative example 37, owing to the end temp of hot finishing is high, sinter on surface.Further, since secondary cold-rolling rate
Height, proof stress becomes too high, there occurs fold.Additionally, due to secondary cold-rolling rate is high, 45 degree of ears processed are caused to become to send out
Reaching, earing rate is deteriorated.
In comparative example 38, owing to the end temp of hot finishing is low, and, intermediate anneal temperature is low.Its result, pressure rolling tissue
Residual, causes in production board 45 degree of ears processed to become flourishing, and earing rate is deteriorated.
In comparative example 39, owing to the end temp of hot finishing is low, and, programming rate during intermediate annealing is slow.Its result,
Cause recrystallization and compete with separating out, hinder the formation of Cube orientation, cause 45 degree of ears processed of production board to become flourishing, system
Ear rate is deteriorated.
In comparative example 40, owing to programming rate during intermediate annealing is too fast, rub between sheet material, there occurs that surface is damaged
Wound.
In comparative example 41, owing to secondary cold-rolling rate is little, proof stress and hot strength reduce.Its result, causes deep
Ftracture when being washed into type.Further, since intermediate anneal temperature is high, there occurs the sintering of cold-rolled lubricating oil.
In comparative example 42, owing to the end temp of hot finishing is low, and, the intermediate annealing time is short.Its result, pressure rolling tissue
Residual, 45 degree of ears processed in production board become flourishing, cause the deterioration of earing rate.
In comparative example 43, owing to once cold rolling rate is little, fail to make the S orientation in substrate become abundant prosperity.Its result,
The karyogenesis site of Cube orientation is reduced, and in production board, 45 degree of ears processed become flourishing, cause the deterioration of earing rate.
In comparative example 44, owing to cold rolling rate is high for the first time, the recrystallization driving force before annealing becomes big, the formation of Cube orientation
Amount diminishes, and 45 degree of ears processed of production board become flourishing, cause the deterioration of earing rate, it addition, ftracture when deep-draw molding.
Industrial utilizability
As it has been described above, by controlling texture and intensity, also be able to when using box annealing stove to carry out intermediate annealing operation
Obtain low earing rate and good deep drawing quality.Further, since do not use continuous annealing furnace, therefore, it is possible in suppression manufacturing cost,
And it also is able to expect suppression cost in equipment investment.
Claims (7)
1. a DR tank body aluminium alloy plate, it is characterised in that:
It is for being made up of aluminium alloy, being at least made for production board via hot rolled plate and intermediate annealing plate from the ingot bar of this aluminium alloy
Aluminium alloy plate,
Wherein, described 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
Become,
Cube orientation density (CubeO) in production board is more than 2.00 times relative to random orientation density, and, CubeO and S
The ratio (CubeO/SO) of orientation density (SO) is 0.40～1.00, after pre-burn, has the elastic limit of 180～220MPa
Stress and the hot strength of more than 230MPa.
2. DR tank body aluminium alloy plate as claimed in claim 1, it is characterised in that:
The conductivity of described hot rolled plate is 36.0～43.0%IACS.
3. DR tank body aluminium alloy plate as claimed in claim 1 or 2, it is characterised in that:
Cube orientation density (CubeO) in described intermediate annealing plate is more than 4.00 times relative to random orientation density, and,
The ratio (CubeO/RO) of CubeO Yu R orientation density (RO) is more than 1.00.
4. the manufacture method of the DR tank body aluminium alloy plate described in any one of claims 1 to 3, it is characterised in that including:
Casting is containing 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 closed by Al and the aluminum that inevitably impurity is constituted
The casting process of gold；
The process that homogenizes ingot bar homogenizes treatment process；
The ingot bar after processing that homogenizes is carried out the hot-rolled process of hot rolling；
The once cold rolling operation of hot rolled plate；
The intermediate annealing operation that once cold rolling plate is annealed；With
The secondary cold-rolling operation of intermediate annealing plate.
5. the manufacture method of DR tank body aluminium alloy plate as claimed in claim 4, it is characterised in that:
Homogenizing in treatment process described, ingot bar processes 1～12 hour at 580～620 DEG C,
Described hot-rolled process include starting temperature is 450～610 DEG C and end temp is 450～550 DEG C hot rough rolling step and
End temp is the hot finishing stage of 330～380 DEG C,
The pressure rolling rate of described once cold rolling operation is 85～95%,
In described intermediate annealing operation, once cold rolling plate temperature province more than 200 DEG C is with average heating speed 10～100
DEG C/h it is warming up to the annealing temperature of 300～450 DEG C, keeps 1～4 hour in this annealing temperature afterwards,
The pressure rolling rate of described secondary cold-rolling operation is 20～40%.
6. the manufacture method of the DR tank body aluminium alloy plate as described in claim 4 or 5, it is characterised in that:
It is also equipped with the final annealing operation after described secondary cold-rolling operation, secondary cold-rolling plate annealed.
7. the manufacture method of DR tank body aluminium alloy plate as claimed in claim 6, it is characterised in that:
In described final annealing operation, secondary cold-rolling plate temperature province more than 200 DEG C is with average heating speed 10～80
DEG C/h it is warming up to the annealing temperature of 140～190 DEG C, keeps 2～4 hours in this annealing temperature afterwards.
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| CN110337692A (en) * | 2017-02-27 | 2019-10-15 | 株式会社Uacj | Aluminium alloy base plate for magnetic disk and its manufacturing method and the disk for using the aluminium alloy base plate for magnetic disk |
| CN111164228A (en) * | 2017-09-28 | 2020-05-15 | 株式会社Uacj | Aluminum alloy substrate for magnetic disk, method for producing same, and magnetic disk using same |
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| ES2797023T3 (en) | 2014-12-19 | 2020-12-01 | Novelis Inc | Aluminum alloy suitable for high speed aluminum bottle production and bottle manufacturing process |
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| CN111164228A (en) * | 2017-09-28 | 2020-05-15 | 株式会社Uacj | Aluminum alloy substrate for magnetic disk, method for producing same, and magnetic disk using same |
| CN111164228B (en) * | 2017-09-28 | 2021-10-08 | 株式会社Uacj | Aluminum alloy substrate for magnetic disk, method for producing same, and magnetic disk using same |
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| CN106103760B (en) | 2018-06-05 |
| JP6326485B2 (en) | 2018-05-16 |
| WO2015140833A1 (en) | 2015-09-24 |
| JPWO2015140833A1 (en) | 2017-04-06 |
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