CN102959109A - Aluminum alloy sheet for forming - Google Patents
Aluminum alloy sheet for forming Download PDFInfo
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- CN102959109A CN102959109A CN2011800307546A CN201180030754A CN102959109A CN 102959109 A CN102959109 A CN 102959109A CN 2011800307546 A CN2011800307546 A CN 2011800307546A CN 201180030754 A CN201180030754 A CN 201180030754A CN 102959109 A CN102959109 A CN 102959109A
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- 238000005204 segregation Methods 0.000 claims abstract description 111
- 238000007493 shaping process Methods 0.000 claims description 33
- 238000001514 detection method Methods 0.000 claims description 13
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- 229910045601 alloy Inorganic materials 0.000 abstract description 39
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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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
- B22D11/003—Aluminium alloys
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/04—Continuous casting of metals, i.e. casting in indefinite lengths into open-ended moulds
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/04—Continuous casting of metals, i.e. casting in indefinite lengths into open-ended moulds
- B22D11/055—Cooling the moulds
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/04—Continuous casting of metals, i.e. casting in indefinite lengths into open-ended moulds
- B22D11/059—Mould materials or platings
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
- B22D11/0622—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by two casting wheels
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
- C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/047—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with magnesium as the next major constituent
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
- B21B2003/001—Aluminium or its alloys
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
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- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Continuous Casting (AREA)
Abstract
The present invention provides an aluminum alloy sheet for forming which is a high-Mg-content Al-Mg alloy sheet reduced in bata-phase precipitation and improved in press formability. This aluminum alloy sheet for forming comprises an Al-Mg alloy containing 6.0-15.0 mass% Mg. In each of square regions, each side of which has the dimension of the whole sheet width (W), that are set in a surface of the alloy sheet, the concentration of Mg is measured at sheet-width-direction measurement points, Px, set at given intervals a and b respectively in the sheet-width direction and the sheet-length direction, and the average of the values of Mg concentration measured at the plurality of sheet-width-direction measurement points (Px) is taken as a sheet-width-direction average Mg concentration (Co). The concentration of Mg is measured at a plurality of sheet-thickness-direction measurement points (Py) set at a given interval in the sheet-thickness direction throughout the whole sheet thickness with respect to the plurality of sheet-width-direction measurement points (Px), and the average of the values of Mg concentration measured at the plurality of sheet-thickness-direction measurement points (Py) is taken as a sheet-thickness-direction average Mg concentration (Ci). The absolute value of the degree of regional Mg segregation (X) defined by the difference (Ci-Co) between the sheet-thickness-direction average Mg concentration (Ci) and the sheet-width-direction average Mg concentration (Co) is 0.5 mass% or less at most and is 0.1 mass% or less on average.
Description
Technical field
The present invention relates to the high Al-Mg of a kind of Mg content is alloy sheets, namely has the shaping aluminium alloy plate of high plasticity.
Background technology
As everyone knows, all the time, as parts or the part usefulness of the carriers such as automobile, boats and ships, flyer or vehicle, machinery, electronic product, building, structure, optical apparatus, implements, the various aluminium alloy plates of widespread use corresponding to each characteristic of every kind of alloy.These aluminium alloy plates are in most situation, by shaping such as stamping grade, as parts or the part of above-mentioned each purposes.From the viewpoint of high formability, in aluminium alloy, strength-ductility balanced superior Al-Mg is that alloy is favourable.Be alloy as this Al-Mg, such as being take JIS A5052, the alloys as representative such as 5182.But, if being alloy sheets, this Al-Mg compares with existing cold-rolled steel sheet, poor ductility then, and plasticity is poor.Therefore, carry out the research that Al-Mg is the composition system of alloy sheets, the optimizing research of creating conditions all the time.
For example, be the Mg content of alloy increasing Al-Mg, so that Mg content is 6 quality %, when surpassing 8 quality % if possible, strength-ductility balanced raising.But, will wait the ingot bar of casting in the common manufacture method of all laggard row hot rollings of thermal treatment by the DC casting, being difficult at the so high Al-Mg of Mg content of industrial manufacturing is alloy sheets.Its reason is, Mg segregation on ingot bar when casting, or when common hot rolling, be that the ductility of alloy significantly descends and cracks easily because of Al-Mg.
On the other hand, the temperature field of avoiding cracking, making the high Al-Mg of Mg content by hot rolling at low temperatures is that alloy sheets also is difficult.Its reason is, in such low temperature rolling, the Al-Mg that Mg content is high is that the resistance to deformation of the material of alloy significantly uprises, and under the ability of the roller mill of present situation, the product size that can make is extremely limited.In addition, for increase Al-Mg be alloy contain the Mg allowance, also propose to add the method for Fe, Si grade in an imperial examination element etc.But, when the content of these element increases, forming easily thick intermetallic compound, the ductility of aluminium alloy plate descends.Therefore, there is boundary in the increase that contains the Mg allowance, is difficult to contain the Mg of the amount that surpasses 8 quality %.
Therefore, proposing to make the high Al-Mg of Mg content with the Continuous casting process of double-roll type etc. is the various motions of alloy sheets.
For example, the aluminium alloys for automobile plate of patent documentation 1 record be a kind of be that the high Al-Mg of Mg content of 6～10 quality % is alloy sheets by the manufacturing of double-roll type Continuous casting process, Mg content.At this, the mean sizes of Al-Mg series intermetallic compound is below the 10 μ m.
In addition, the body of a motor car sealing of patent documentation 2 record with aluminium alloy plate be a kind of be that the Al-Mg of 2.5～8 quality % is alloy sheets by Continuous casting process manufacturing, Mg content.At this, the number of the Al-Mg series intermetallic compound that 10 μ m are above is 300/mm
2Below, the average crystallite particle diameter is 10～70 μ m.
In addition, in patent documentation 3, record a kind of by the manufacturing of double-roll type Continuous casting process, Mg content is that the Al-Mg of 8～14 quality % is alloy sheets.At this, each Mg concentration of in whole thickness range, measuring and with in the relation between the average Mg concentration of its equalization, each Mg concentration is calculated as below the 4 quality % with absolute value from the maximum value of the deviation oscillation of average Mg deviation of concentration, mean value is calculated as below the 0.8 quality % with absolute value.Thus, suppress separating out of Al-Mg series intermetallic compound.
Technical literature formerly
Patent documentation
Patent documentation 1: the Unexamined Patent 7-252571 of Japan communique
Patent documentation 3: the JP 2007-77485 of Japan communique
As patent documentation 1,2 records, the A l-M g series intermetallic compound of crystallization during casting becomes the starting point of destruction easily when stamping.Therefore, be the press formability of alloy sheets in order to improve the high Al-M g of M g content, making A l-M g series intermetallic compound (being also referred to as the β phase) granular is that effectively perhaps, reducing thick β is effective mutually.And, in patent documentation 1,2, accelerate the speed of cooling (casting speed) in the casting process, the A l-M g series intermetallic compound of crystallization when being suppressed at casting.Just there are the following problems: become higher if A l-M g is the Mg content of alloy sheets, then only by the control of the speed of cooling in the casting process, be difficult to β is reduced to the degree that press formability is had no adverse effects mutually.
In patent documentation 3, by being suppressed at the segregation degree (Mg concentration distribution) of the Mg in the whole thickness range according to homogenize thermal treatment and final annealing condition, thus the separating out of Al-Mg series intermetallic compound (β phase) that inhibition is caused by the segregation (density unevenness) of Mg.But the high Al-Mg of Mg content of the use double-roll type Continuous casting process manufacturing of prior art is alloy sheets also produces Mg on plate width direction segregation.Therefore there are the following problems: only be suppressed at the segregation degree of the Mg in the whole thickness range, the β that is difficult to the Al-Mg that Mg content is high and is alloy sheets is reduced to the degree that press formability is had no adverse effects mutually.
Therefore, speed of cooling in casting process, the inhibition based on the segregation degree of the Mg in whole thickness range of casting process later homogenize thermal treatment and final annealing condition, there is also a desire in addition a kind of can the Al-Mg that Mg content is high be the technology that the β of alloy sheets is reduced to the degree that press formability is had no adverse effects mutually.
Summary of the invention
The present invention proposes in order to address this problem, and its problem that will solve is, provide the high Al-Mg of a kind of Mg of reduction content be alloy sheets separate out the shaping aluminium alloy plate that press formability is improved in the β of inside phase.
In order to solve described problem, shaping aluminium alloy plate of the present invention, it contains below the above 15.0 quality % of Mg:6.0 quality %, surplus is Al and impurity, it is characterized in that, in being set in the zone of described shaping with aluminium alloy plate the lip-deep wide square shape as 1 limit take full plate, separate the plate width direction measuring point mensuration Mg concentration that predetermined distance is set a plurality of at plate width direction and plate length direction, the mean value of the Mg concentration that will measure at a plurality of described plate width direction measuring points is as the average Mg concentration of plate width direction (Co), for a plurality of described plate width direction measuring points, separate the thickness of slab direction detection point that predetermined distance is set in the whole thickness range in the thickness of slab direction and measure Mg concentration a plurality of, the mean value of the Mg concentration that will measure at a plurality of described thickness of slab direction detection points is as thickness of slab orientation average Mg concentration (Ci), in the case
Absolute value by the regional Mg degree of segregation (X) of poor (Ci-Co) of described thickness of slab orientation average Mg concentration (Ci) and the average Mg concentration of described plate width direction (Co) definition, its maximum value is below the 0.5 quality %, and its mean value is below the 0.1 quality %.
According to described formation, the regional Mg degree of segregation (X) of the difference definition of the thickness of slab orientation average Mg concentration (Ci) of using aluminium alloy plate by being shaped and the average Mg concentration of plate width direction (Co) is following maximum value and mean value of prescribed value, thus, suppress to be shaped with the slab integral of aluminium alloy plate, to be the segregation of thickness of slab direction and plate width direction two sides' Mg.Therefore, reduce to be shaped with aluminium alloy plate the separating out of the β of inside phase, and the nonaffine deformation when suppressing shaping, the strain concentrating that caused by nonaffine deformation.
Use in the aluminium alloy plate in shaping of the present invention, except described regional Mg degree of segregation (X), preferably when calculating described regional Mg degree of segregation (X), in at least one of described plate width direction measuring point, will be in the Mg concentration of measuring in whole thickness range with predetermined distance on the thickness of slab direction during as thickness of slab direction Mg concentration (Ct), absolute value by the thickness of slab direction Mg degree of segregation (Y) of poor (Ct-Ci) of described thickness of slab direction Mg concentration (Ct) and described thickness of slab orientation average Mg concentration (Ci) definition, its maximum value is below the 4 quality %, and its mean value is below the 0.8 quality %.
According to described formation, except described regional Mg degree of segregation (X), the thickness of slab direction Mg degree of segregation (Y) of the difference definition of the thickness of slab direction Mg concentration (Ct) of using aluminium alloy plate by being shaped and thickness of slab orientation average Mg concentration (Ci) is following maximum value and mean value of prescribed value, thus, further suppress the segregation of Mg.Therefore, further reduce be shaped with aluminium alloy plate the separating out of the β of inside phase, and the nonaffine deformation when further suppressing shaping, the strain concentrating that caused by nonaffine deformation.
With in the aluminium alloy plate, the content of preferred described Mg is above 8 quality % and below 14 quality % in shaping of the present invention.
According to described formation, by Mg content is defined in specialized range, is shaped with intensity, the ductility raising of aluminium alloy plate, and reduces the separating out in the β of inside phase that is shaped with aluminium alloy plate.
With in the aluminium alloy plate, preferred described impurity is the element more than at least a kind that Fe:1.0 quality % is following, Si:0.5 quality % is following, Ti:0.1 quality % is following, B:0.05 quality % is following, Mn:0.3 quality % is following, Cr:0.3 quality % is following, Zr:0.3 quality % is following, V:0.3 quality % is following, Cu:1.0 quality % is following, the Zn:1.0% quality is following in shaping of the present invention.
According to described formation,, be suppressed at the inside that is shaped with aluminium alloy plate and separate out by the Al-Mg series intermetallic compound of the formations such as Al-Mg-(Fe, Si) or by the Al-Mg system intermetallic compound in addition that Al-Fe, Al-Si etc. consists of as the Fe of impurity, the content of Si by restriction.Thus, destroy toughness, press formability raising.In addition, by the content of restriction as Ti, the B of impurity, Mn, Cr, Zr, V, Cu, Zn, do not hinder press formability.
The invention effect
According to shaping aluminium alloy plate of the present invention, reduce the formation of β phase by the segregation that suppresses Mg, can obtain superior press formability.In addition, be shaped with aluminium alloy plate by Mg content is limited to narrower range, perhaps, except Mg, contain the element more than at least a kind of Fe, Si, Ti, B, Mn, Cr, Zr, V, Cu, Zn as impurity, limit its content, thus, press formability further improves.
Description of drawings
Fig. 1 is illustrated in a plurality of measuring points of the Mg concentration of using when calculating shaping of the present invention with the Mg degree of segregation of aluminium alloy plate, (a) is vertical view, (b) is the A-A line sectional view of (a).
Fig. 2 is the sectional view of the structure of employed thin plate continuous casting apparatus when schematically being illustrated in shaping of the present invention with the manufacturing of aluminium alloy plate.
Fig. 3 is the sectional view of the structure of employed thin plate continuous casting apparatus when schematically being illustrated in shaping of the present invention with the manufacturing of aluminium alloy plate.
Fig. 4 is that expression is satisfied the shaping of important document of the present invention with the chart of calculating the result of the regional Mg degree of segregation in the aluminium alloy plate.
Fig. 5 is the shaping of unabridged version invention important document with thumb down with the chart of calculating the result of the regional Mg degree of segregation in the aluminium alloy plate.
Fig. 6 is that expression is satisfied the shaping of important document of the present invention with the chart of calculating the result of the thickness of slab direction Mg degree of segregation in the aluminium alloy plate.
Fig. 7 is the shaping of unabridged version invention important document with thumb down with the chart of calculating the result of the thickness of slab direction Mg degree of segregation in the aluminium alloy plate.
Embodiment
Describe the shaping of the present invention embodiment of aluminium alloy plate in detail.
Shaping of the present invention aluminium alloy plate (below, be called aluminium alloy plate) be the aluminium alloy that contains the Mg of high-content, it is characterized in that the regional Mg degree of segregation X that defines with plate width direction average Mg concentration C o and thickness of slab orientation average Mg concentration C i is limited in below the prescribed value.
At first, form for the chemical ingredients of the aluminium alloy plate of present embodiment, meaning and the numerical definiteness reason thereof of each alloying element described.
The aluminium alloy plate of present embodiment is below the above 15.0 quality % of a kind of Mg:6.0 of containing quality % and surplus is the aluminium alloy of Al and impurity, is that alloy consists of by the high Al-Mg of Mg content namely.In addition, the aluminium alloy plate of present embodiment is that alloy consists of by the high Al-Mg of following Mg content preferably, high Al-Mg is in the alloy at this Mg content, as the element beyond the Mg, contain Fe:1.0 quality % is following, Si:0.5 quality % is following, Ti:0.1 quality % is following, B:0.05 quality % is following, Mn:0.3 quality % is following, Cr:0.3 quality % is following, Zr:0.3 quality % is following, V:0.3 quality % is following, Cu:1.0 quality % is following, the Zn:1.0% quality the is following element more than at least a kind as impurity.
(Mg)
Mg is the intensity that improves the Al alloy sheets, the important alloying element of ductility.At Mg content during less than 6.0 quality %, intensity, ductility is not enough, and the high Al-Mg of Mg content that can't get out is the feature of alloy, and press formability is not enough.On the other hand, when Mg content surpasses 15.0 quality %, even carry out the control of manufacture method, condition, also be difficult to the segregation of the Mg of aluminium alloy plate, be that described regional Mg degree of segregation is defined in the specialized range.Under regional Mg degree of segregation is not defined in situation in the specialized range, the β of aluminium alloy plate phase to separate out change many, press formability significantly descends, the work hardening quantitative change is large in addition, cold-rolling property also descends.Therefore, Mg content be 6.0 quality % above, below the 15.0 quality %, preferably greater than 8 quality %, below the 14 quality %.
(Fe and Si)
Fe and Si are the elements that should as far as possible be constrained to few amount.Fe and Si become by Al-Mg such as the Al-Mg series intermetallic compound of the formations such as Al-Mg-(Fe, Si) or Al-Fe, Al-Si the intermetallic compound beyond being and separate out.Under Fe content surpasses the situation of 1.0 quality %, perhaps, surpass in the situation of 0.5 quality % at Si content, these intermetallic compounds to separate out quantitative change too much, hinder significantly and destroy toughness, plasticity.Consequently, press formability significantly descends.Therefore, Fe content is below the 1.0 quality %, and preferably below the 0.5 quality %, Si content is below the 0.5 quality %, preferably below the 0.3 quality %.
(Ti, B, Mn, Cr, Zr, V, Cu and Zn)
Ti and B have the granular effect of cast panel (ingot bar) tissue, and Mn, Cr, Zr and V have the granular effect of milled sheet tissue.In addition, Cu and Zn also have and put forward high-intensity effect.Therefore, be the scope of press formability in the characteristic that does not hinder alloy sheets of the present invention, allow to contain more than one these elements in order to realize these effects.The allowance of these elements is preferably: Ti:0.1 quality % is following, B:0.05 quality % is following, Mn:0.3 quality % is following, Cr:0.3 quality % is following, Zr:0.3 quality % is following, V:0.3 quality % is following, Cu:1.0 quality % is following, below the Zn:1.0 quality %.
Then, for the average Mg concentration C of the plate width direction of aluminium alloy plate o, thickness of slab orientation average Mg concentration C i and with the regional Mg degree of segregation X of plate width direction average Mg concentration C o and thickness of slab orientation average Mg concentration C i definition, be elaborated with reference to Fig. 1.
(the average Mg concentration of plate width direction: Co)
Shown in Fig. 1 (a), in order to calculate the average Mg concentration C of plate width direction o, at first, in the zone of setting take the wide W of full plate as the square shape on 1 limit, the surface of aluminium alloy plate 60.In the zone of this square shape, namely in the zone that the plate long L identical with the complete wide W of plate by the wide W of full plate and length fences up, on plate width direction, with predetermined distance a, and on the plate length direction, set a plurality of plate width direction measuring point Px with predetermined distance b.At these a plurality of plate width direction measuring point Px, measure aluminium alloy plate 60 in the Mg on surface concentration.The mean value of the Mg concentration of these mensuration is the average Mg concentration C of plate width direction o, and is the index of the segregation degree of the Mg on the plate width direction from the teeth outwards of aluminium alloy plate 60.In addition, in the mensuration of Mg concentration, employing can be carried out the EPMA (electric wire probe microanalyser) of line analysis, measures Mg concentration by the plate width direction scanning at aluminium alloy plate 60.
In addition, reproducibility for the segregation degree of the Mg of the plate width direction that obtains aluminium alloy plate 60, need to set on the surface of aluminium alloy plate 60 zone take the wide W of full plate as the square shape on 1 limit, need to measure aluminium alloy plate 60 in this zone in the Mg on surface concentration.The number (counting) of the plate width direction measuring point Px of setting is not comprising on the plate width direction that the plate end is preferably more than 5 and is more than 5 at the plate length direction, preferably adds up to more than 25 in the zone.And, set the interval a of plate width direction and the interval b of plate length direction, so that the number of plate width direction measuring point Px is more than 25.And then the interval b of plate length direction is preferably set to 0.5～2 times of interval a of plate width direction.
(thickness of slab orientation average Mg concentration: Ci)
Shown in Fig. 1 (b), in order to calculate thickness of slab orientation average Mg concentration C i, at first, in all a plurality of plate width direction measuring point Px that are set in described zone, setting a plurality of thickness of slab direction detection point Py with predetermined distance c T in whole thickness range on the thickness of slab direction.Then, to each thickness of slab direction detection point Py, measure in the Mg of plate depth location concentration (with thickness of slab direction Mg concentration C t synonym described later).The mean value of the Mg concentration of these mensuration is thickness of slab orientation average Mg concentration C i, becomes the index of the segregation degree of the Mg on the thickness of slab direction (plate depth direction) of aluminium alloy plate 60.In addition, in the mensuration of Mg concentration, with above-mentioned same use EPMA, by the section of scanning board cross direction on the thickness of slab direction, thus the Mg concentration in each thickness position part in the scope of full thickness of slab T is measured.
In addition, for the reproducibility of the segregation degree of the Mg on the thickness of slab direction that obtains aluminium alloy plate 60, the interval c of thickness of slab direction is preferably set to below the 0.2mm.Need to prove that the first measuring point of thickness of slab direction detection point Py is complete after measured described plate width direction measuring point Px.
(regional Mg degree of segregation: X)
Zone Mg degree of segregation X is with thickness of slab orientation average Mg concentration (Ci) poor (Ci-Co) definition with the average Mg concentration of plate width direction (Co), in aluminium alloy plate 60 integral body, the i.e. index of the segregation degree of the Mg on thickness of slab direction and plate width direction both sides.And in aluminium alloy plate 60 of the present invention, its maximum value of absolute value of regional Mg degree of segregation X is below the 0.5 quality %, and its mean value is below the 0.1 quality %.Need to prove, the average Mg concentration C of plate width direction o, thickness of slab orientation average Mg concentration C i and regional Mg degree of segregation X are comprised of the chemical ingredients of aluminium alloy plate 60, described laterly create conditions, the cooling conditions when specifically casting, cast panel thickness of slab or the face amount of cutting, the heat-treat condition that homogenizes, the control of final annealing condition.
Under positive side became large situation, the β that causes because of the segregation of Mg became mutually and separates out easily at the maximum value of regional Mg degree of segregation X or mean value.Increase mutually if become the β of the starting point of destruction, then intensity, extensibility descend, and plasticity descends.In addition, under minus side became large situation, the part of the significant step-down of Mg concentration more existed partially at the maximum value of regional Mg degree of segregation X or mean value.In the part of the significant step-down of Mg concentration, the intensity step-down.Therefore, when the tensile deformation that is shaped, only the part of Mg concentration step-down preferentially is out of shape, and produces nonaffine deformation.Therefore, the strain concentration of local during shaping, especially extensibility descends, and plasticity descends.
Therefore, calculate above 0.5 quality %, perhaps with absolute value in the maximum value of regional Mg degree of segregation X, its mean value is calculated with absolute value and is surpassed in the situation of 0.1 quality %, that is, and and at discontented foot any important document of the present invention, or do not satisfy in both sides' the situation of important document, the plasticity of aluminium alloy plate 60 descends.
In aluminium alloy plate 60 of the present invention, except described regional Mg degree of segregation X, the thickness of slab direction Mg degree of segregation Y that is defined by thickness of slab direction Mg concentration C t and thickness of slab orientation average Mg concentration C i preferably is limited in below the prescribed value.
(thickness of slab direction Mg concentration: Ct, thickness of slab orientation average Mg concentration: Ci)
Thickness of slab direction Mg concentration C t is the Mg concentration that a plurality of thickness of slab direction detection point Py of record measure in Fig. 1 (b) as previously mentioned.Thickness of slab orientation average Mg concentration C i is the mean value of the thickness of slab direction Mg concentration C t of mensuration.
But, thickness of slab direction Mg concentration C t and thickness of slab orientation average Mg concentration C i, when calculating described regional Mg degree of segregation X, be that at least one plate width direction measuring point Px in described zone measures, in the Mg of thickness of slab direction concentration.Thickness of slab direction Mg concentration C t preferably calculates according to the value in 1 mensuration of the plate width direction measuring point Px of the wide central part of plate, near more preferably 3 mensuration the wide central part of plate and the wide both ends of plate, and their equalizations are calculated.
(thickness of slab direction Mg degree of segregation Y)
Thickness of slab direction Mg degree of segregation Y is by poor (Ct-Ci) definition of thickness of slab direction Mg concentration (Ct) and thickness of slab orientation average Mg concentration (Ci), is the index of the segregation degree of the Mg of the thickness of slab direction of aluminium alloy plate 60.Thickness of slab direction Mg degree of segregation Y by with described regional Mg degree of segregation X and usefulness, thereby can reproduce well the segregation degree of Mg of the slab integral of aluminium alloy plate 60.And in aluminium alloy plate 60 of the present invention, the absolute value of thickness of slab direction Mg degree of segregation Y is preferably: calculate below 4 quality % with maximum value, and calculate below 0.8 quality % with mean value.Need to prove, thickness of slab direction Mg concentration C t, thickness of slab orientation average Mg concentration C i and thickness of slab direction Mg degree of segregation Y are comprised of the chemical ingredients of aluminium alloy plate 60, described laterly create conditions, the cooling conditions when specifically casting, cast panel thickness of slab or the face amount of cutting, the heat-treat condition that homogenizes, the control of final annealing condition.
Under positive side became large situation, the β that causes because of the segregation of Mg became mutually and separates out easily in the maximum value of thickness of slab direction Mg degree of segregation Y, mean value.Therefore, the β that becomes the starting point of destruction increases mutually, and intensity, extensibility descend, and plasticity descends.In addition, under minus side became large situation, the part of the significant step-down of Mg concentration more existed partially in the maximum value of thickness of slab direction Mg degree of segregation Y, mean value.Therefore, at the part of so significant step-down of Mg concentration, intensity step-down.Therefore, during tensile deformation in shaping, only the part of Mg concentration step-down preferentially is out of shape, and produces nonaffine deformation.Therefore, the strain concentration of local during shaping, especially extensibility descends, and plasticity descends.
Therefore, calculate above 4 quality % with absolute value in the maximum value of thickness of slab direction Mg degree of segregation Y, perhaps, its mean value is calculated with absolute value and is surpassed in the situation of 0.8 quality %, and the plasticity of aluminium alloy plate 60 descends.That is, in the situation that does not satisfy described any important document, or in the situation of the important document that does not satisfy both sides, the plasticity of aluminium alloy plate 60 descends.
(average crystallite particle diameter)
Preferred its surperficial average crystallite particle diameter of aluminium alloy plate of the present invention is below 100 μ m.
Average crystallite particle diameter granular by making the aluminium alloy plate surface is below 100 μ m, thereby press formability improves.Surpass 100 μ m and in the situation of thickization, press formability descends easily at the average crystallite particle diameter, produce easily crackle or the unfavorable condition such as coarse when being shaped.On the other hand, the average crystallite particle diameter is meticulous, produces when stamping that 5000 line aluminium alloy plates are peculiar, SS (tensile deformation) mark.From this viewpoint, the average crystallite particle diameter is preferably more than the 20 μ m.
Alleged crystallization particle diameter refers to the maximum diameter of the crystal grain of plate length direction among the present invention.This crystallization particle diameter is after aluminium alloy plate mechanical polishing is become 0.05～0.1mm, use 100 times the observation by light microscope electrolytically etching the surface, on described L direction, measure with the line method of cutting thus.1 measures line length is made as 0.95mm, with each 3 of each visual fields, adds up to and observes 5 visual fields, and entirely measuring thus line length is 0.95 * 15mm.
Below, the manufacture method of described aluminium alloy plate is described.
Aluminium alloy plate of the present invention is made through melt-casting operation, the heat treatment step that homogenizes, cold rolling process, final annealing operation.Below, each operation is described.
＜melt-casting operation 〉
The melt-casting operation is that the high Al-Mg of Mg content that will have described chemical ingredients composition is alloy melting, uses the thin plate Continuous casting process to make the operation of cast panel from liquation.As the thin plate Continuous casting process, graphite stationary die formula Continuous casting process preferably.
Graphite stationary die formula Continuous casting process is to use thin plate continuous casting apparatus 10 shown in Figure 2 to carry out.At first, the liquation 2 that will store in keeping stove 1 injects the inside of continuous casting mold 3 (graphite stationary die 4) from being cast into mouthful 1a.Then, on one side by water jacket 5 cooling graphite stationary die 4, liquation 2 solidifies in graphite stationary die 4 on one side.Thus, obtain the cast panel 6 of thin thickness of slab.The cast panel 6 of making is transported to subsequent processing by roller 7.In the method, compare with the DC casting, speed of cooling is fast, therefore can obtain trickle cast structure, and press formability improves.In addition, can obtain the thickness of slab about thinner 5mm, therefore can omit the existing DC ingot bar (operations such as the hot roughing system after the casting of implementing in the thickness 200～600mm), hot finishing system.
(speed of cooling)
In graphite stationary die formula Continuous casting process, if the thickness of slab of cast panel 6 is the scope of 5～20mm, then the speed of cooling in the casting is 15 ℃/s.If speed of cooling is slow, then the segregation degree of Mg becomes large, be difficult to Mg degree of segregation (below, described regional Mg degree of segregation X and thickness of slab direction Mg degree of segregation Y are called the Mg degree of segregation) be suppressed within the scope of the invention the possibility of separating out of the β phase that existence can't suppress to cause thus.In addition, mutually general thickization of β has the tendency of separating out in a large number.Consequently, the remarkable possibility that descends of the press formability of aluminium alloy plate uprises.
Need to prove, be difficult to directly measure this speed of cooling.Therefore, speed of cooling is according to (the dendrite Secondary Branch interval: DAS) by known method (for example, dendritic arm interval of the cast panel 6 of casting, light metal association, distribution on August 20th, 1988, the method for middle records such as " measuring methods of aluminium dendritic arm interval and speed of cooling ") obtain.Namely, measure with the intersection method in the cast structure of cast panel 6 of casting, mutually the equispaced d of adjacent dendrite secondary arm (Secondary Branch) (field of view number is more than 3, number of hits is more than 10), use this d, according to following formula, d=62 * C-0.337 (wherein, d: dendrite secondary arm interval (mm), C: speed of cooling (℃/s)), obtain speed of cooling.Therefore, can say that also this speed of cooling is setting rate.
(fluid injection temperature)
In graphite stationary die formula Continuous casting process, fluid injection temperature when liquation 2 fluid injections are in the graphite stationary die 4 is more than liquidus temperature+50 ℃ and the scope below liquidus temperature+250 ℃, is preferably more than liquidus temperature+100 ℃ and below liquidus temperature+150 ℃.The fluid injection temperature is in the situation less than liquidus temperature+50 ℃, and liquation solidifies in mold easily, produces easily the cast panel fracture.Surpass in the fluid injection temperature in the situation of liquidus temperature+250 ℃, the speed of cooling during casting is slack-off, and it is large that the segregation degree of Mg becomes.In this case, be difficult to the Mg degree of segregation is suppressed within the scope of the invention, can't suppress the decline of the separating out of the β phase that causes because of the Mg degree of segregation, plasticity.
(Hubbing method)
In graphite stationary die formula Continuous casting process, for the stabilization that realizes casting, make the roller 7 that transports cast panel 6 at casting direction periodically to the reverse rotation of casting direction, cast panel 6 is retreated.Backward travel length is the scope that 0.5mm is above, 5mm is following, preferably 1mm above, below the 3mm.In addition, if hold-time below the 1s is arranged before retreating, then castibility is more stable.
Surpass in the situation of 5mm in backward travel length, the segregation layer of the high Mg concentration that produces on the surface of cast panel 6 is invaded intralamellar part when retreating, produce cast panel crackle thereby fracture at this position.On the other hand, in the situation of backward travel length less than 0.5mm, solid-liquid section is not compressed, in the solid-liquid section zone of easily fracture, and cast panel 6 fractures.Therefore, backward travel length is the scope that 0.5mm is above, 5mm is following.
(average casting speed)
In graphite stationary die formula Continuous casting process, by graphite stationary die 4 casting liquation 2 time, average casting speed is the scope that 100mm/min is above and 500mm/min is following, preferably more than the 250mm/min and below the 350mm/min.In the average situation of casting speed less than 100mm/min, liquation 2 be cast into mouthful 1a near solidify rapidly, thus, during with roller 7 drawing this position pull out the resistance increase, so cast panel 6 ruptures easily.Surpass in the situation of 500mm/min in average casting speed, near cast panel outlet 4a, produce by the not enough liquation that causes of cooling and leak.
(casting thickness of slab)
In graphite stationary die formula Continuous casting process, the thickness of slab of the cast panel 6 of continuous casting is the scope that 5mm is above, 20mm is following.In the situation of thickness of slab less than 5mm, liquation 2 be cast into mouthful 1a near solidify rapidly, with roller 7 drawing the time, the resistance of pulling out at this position increases, so cast panel 6 ruptures easily thus.Surpass in the situation of 20mm at thickness of slab, the speed of cooling of casting is significantly slack-off, and it is large that the segregation degree of Mg becomes.In this case, may be difficult to the Mg degree of segregation is suppressed within the scope of the invention, possibly can't suppress separating out of the β phase that causes because of the Mg degree of segregation.In addition, the β tendency that general thickization arranged mutually or separate out in a large number.Consequently, the remarkable possibility that descends of press formability uprises.
(face is cut processing)
In graphite stationary die formula Continuous casting process, produce the Mg segregation on the surface of cast panel 6 easily.Therefore, the face that preferably carries out the plate two sides of the cast panel 6 made with specified amount cutting is cut processing.By cut the Mg segregation section that removes the plate two sides that processes by face, the Mg degree of segregation can be suppressed within the scope of the invention thus.The degree of depth of Mg segregation section is because corresponding to backward travel length, so the face amount of cutting is the backward travel length of described Hubbing method.
More than, for the thin plate continuous casing, be illustrated as an example of graphite stationary die formula Continuous casting process example, but be not limited to this.So long as the Mg degree of segregation of aluminium alloy plate can be suppressed within the scope of the invention method, which kind of method can, for example, can be the double-roll type Continuous casting process.
The double-roll type Continuous casting process is to use thin plate continuous casting apparatus 100 as shown in Figure 3 to carry out.At first, from keep stove 200 for nozzle for liquid 400 to fluid injection liquation 300 between a pair of water-cooled copper mold (two roller 500) of rotation, liquation 300 solidifies.After just having solidified, between this pair roller 500, depress and chilling, obtain thus the cast panel 600 of thin thickness of slab.As this double-roll type Continuous casting process, known have hunt's method (Hunter method), a 3C method etc.In the method, can obtain the thickness of slab of 1 thinner～13mm, therefore can be omitted in the existing DC ingot bar (operations such as the hot roughing after the casting of implementing in the thickness 200～600mm), hot finishing.
＜heat treatment step homogenizes 〉
The homogeneous heating treatment step is the cast panel 6 of making according to described operation to be implemented the heat treated operation that homogenizes of regulation.More than 400 ℃, below the liquidus temperature, carry out the thermal treatment that homogenizes of necessary time.Using continuous heat treating furnace, in the heat treated situation of implementing to homogenize based on the cast panel 6 of thin plate Continuous casting process, heat treatment time was standard below (1s) at 1 second.By this thermal treatment that homogenizes, the segregation degree of Mg diminishes, and the Mg degree of segregation can be suppressed within the scope of the invention.
In the thermal treatment that homogenizes, in the process, if heat-up rate and speed of cooling are little, then probably produce Al-Mg series intermetallic compound (β phase) when the intensification of cast panel 6 and in when cooling the two the way.Especially, the high temperature field of possibility that produces the β phase is that the temperature of cast panel central part is 200～400 ℃ scope when heating up, and is the scope of thermal treatment temp～100 ℃ of homogenizing when cooling.Therefore, in order to suppress the generation of β phase, when homogenizing the thermal treatment temp heating, the temperature of preferred cast panel central part be the average heating speed in 200～400 ℃ the scope be 5 ℃/more than the s.In addition, from homogenizing thermal treatment temp when cooling, preferably 5 ℃ of the average cooling rates of the scope of the thermal treatment temp that homogenizes～100 ℃/more than the s.
＜cold rolling process 〉
Cold rolling process is to the operation below the above 13mm of thickness of slab, for example 0.1mm of product plate with cast panel 6 cold-rolling treatment after the thermal treatment of having implemented to homogenize.By cold rolling, the processed systematism of cast structure.Therefore, in the situation thick by the thickness of slab of cold rolling cast panel 6, preferably add process annealing in cold rolling way, making final cold rolling cold rolling rate is below 60%.Need to prove that the degree of cold rolling worked structure also exists with ... cold rolling cold rolling rate, therefore, because above-mentioned set organizational controls, residual cast structure sometimes also, but in the scope of not damaging plasticity, mechanical characteristics, allow.
＜final annealing operation 〉
The final annealing operation is the cold-reduced sheet of making according to described operation to be implemented the operation of the final annealing of regulation.In the final annealing operation, more than 400 ℃ and less than liquidus temperature (℃) temperature under cold-reduced sheet is implemented final annealing.By this final annealing, the segregation degree of Mg diminishes, and M g degree of segregation can be suppressed within the scope of the invention the decline of the separating out of the β phase that can suppress to cause thus, press formability.
During less than 400 ℃, the possibility that can't obtain the melt effect is high in the final annealing temperature, and then, do not reduce the effect of the segregation degree of Mg.Therefore, the final annealing temperature is preferably more than 450 ℃.And then, behind this final annealing, need to cool off with 10 ℃/average cooling rate more than the s, fast as far as possible 500～300 ℃ temperature range.Slow at the average cooling rate behind the final annealing and in the situation less than 10 ℃/s, in process of cooling, the segregation degree of Mg becomes large on the contrary.In this case, the Mg degree of segregation can't be suppressed within the scope of the invention, existence can't suppress the possibility of the decline of the separating out of β phase that the Mg degree of segregation causes, press formability.In addition, average cooling rate be preferably 15 ℃/more than the s.
[embodiment]
Below, embodiments of the invention are described.
The Al-Mg that various chemical ingredientss shown in the table 1 are formed is the liquation of alloy (embodiment A～E, Comparative Example F, G), by described graphite stationary die formula Continuous casting process and double-roll type Continuous casting process, under the conditions shown in Table 2, be cast as each thickness of slab shown in the table 2.Then, each cast panel is cut processing, after the thermal treatment that homogenizes, is not being carried out in the situation of hot rolling by enforcement face optionally under the conditions shown in Table 2, is cold rolled to thickness of slab 1.0mm or thickness of slab 11.0mm.Need to prove, in cold rolling, do not carry out process annealing.Then, with described each cold-reduced sheet under the temperature shown in the table 2 and cooling conditions, carry out final annealing (be 1 second below in the hold-time under the annealing temperature) with continuous annealing furnace, making and be shaped with aluminium alloy plate (embodiment No.1～5, comparative example No.6～20).At this, make shaping aluminium alloy plate (comparative example No.6) by the manufacture method of using the double-roll type Continuous casting process of record in the patent documentation 3.
In addition, the condition of graphite stationary die formula Continuous casting process is: backward travel length: 3mm, average casting speed: 300mm/min, casting temp (fluid injection temperature): liquidus temperature+140 ℃.In the double-roll type Continuous casting process, the peripheral speed of two rollers is 70m/min, and the fluid injection temperature with liquation during to two roller fluid injection is liquidus temperature+20 ℃, does not carry out the lubricated of two roller surfaces.
In the calculating of the liquidus temperature of each alloy, use Thermodynamic Calculation Software Thermo-CalcVer.R (Al-DATA Ver.6).
For the shaping that obtains aluminium alloy plate (embodiment No.1～5, comparative example No.6～22), the regional Mg degree of segregation X of each alloy sheets and thickness of slab direction Mg degree of segregation Y calculate and estimate according to following order.Its result is as shown in table 2.
In addition, the regional Mg degree of segregation X of embodiment No.1 calculates the result as shown in Figure 4, and the regional Mg degree of segregation X of comparative example No.6 calculates the result as shown in Figure 5.And the thickness of slab direction Mg degree of segregation Y of embodiment 1 calculates the result as shown in Figure 6, and the thickness of slab direction Mg degree of segregation Y of comparative example No.16 calculates the result as shown in Figure 7.
(regional Mg degree of segregation X calculating and estimating)
At first, be shaped with on the surface of aluminium alloy plate, setting length on one side is the zone of the square shape of 100mm.Then, on the plate width direction in this zone, (interval a) does not contain the plate end at interior setting 5 points, on the plate length direction, sets 5 points with 25mm interval (interval b) with the 16.6mm interval.Thus, set the plate width direction measuring point Px (No.1～25) (with reference to Fig. 1 (a)) of 25 of totals.Then, be determined at each measuring point aluminium alloy plate in the Mg on surface concentration, the mean value of the Mg concentration of calculating at each measuring point is made as the average Mg concentration C of plate width direction o.
Then, each measuring point in plate width direction measuring point Px (No.1～25) is set a plurality of thickness of slab direction detection point Py (with reference to Fig. 1 (b)) with 0.01mm interval (interval c) on the thickness of slab direction.Then, be determined at the Mg concentration of the aluminium alloy plate of each measuring point (regulation thickness of slab position (prescribed depth position)), the mean value of the Mg concentration of calculating at each measuring point and be set as thickness of slab orientation average Mg concentration C i.
Then, according to thickness of slab orientation average Mg concentration C i and the average Mg concentration C of the plate width direction o at each measuring point of plate width direction measuring point Px (No.1～25), calculate the regional Mg degree of segregation X (with reference to Fig. 4, Fig. 5) by both poor (Ci-Co) definition.Need to prove that the mensuration of Mg concentration is used EPMA (NEC x-ray microanalyser processed: JXA-8800RL).
In the evaluation of regional Mg degree of segregation X, the maximum value of regional Mg degree of segregation X is that 0.5 quality % is chosen as satisfied (zero) when following at absolute value, is chosen as discontented foot (*) when surpassing 0.5 quality %.In addition, the mean value of regional Mg degree of segregation X is that 0.1 quality % is chosen as satisfied (zero) when following at absolute value, is chosen as discontented foot (*) when surpassing 0.1 quality %.
(thickness of slab direction Mg degree of segregation Y calculating and estimating)
Select 1 point (No.13) among the described plate width direction measuring point (No.1～25), will this measuring point measure in the Mg concentration of thickness of slab direction (a plurality of thickness of slab direction detection point Py) as thickness of slab direction Mg concentration C t.Then, use conduct at the aforementioned thickness of slab orientation average Mg concentration C i that calculates, thus, to calculate the thickness of slab direction Mg degree of segregation Y by both poor (Ct-Ci) definition at the mean value of the Mg of each measuring point concentration.Need to prove that if thickness of slab direction detection point Py is 0.01mm or 1.0mm, then thickness of slab direction detection point Py is positioned at the surface (with reference to Fig. 6, Fig. 7) of alloy sheets.
In the evaluation of thickness of slab direction Mg degree of segregation Y, the maximum value of thickness of slab direction Mg degree of segregation Y is that 4 quality % are chosen as satisfied (zero) when following at absolute value, is chosen as discontented foot (*) when surpassing 4 quality %.In addition, the mean value of thickness of slab direction Mg degree of segregation Y is that 0.8 quality % is chosen as satisfied (zero) when following at absolute value, is chosen as discontented foot (*) when surpassing 0.8 quality %.
(average crystallite particle diameter)
In addition, with aluminium alloy plate (embodiment No.1～5, comparative example 6～22), according to described measuring method, measure the average crystallite particle diameter of each alloy sheets for the shaping that obtains.
Embodiment No.1～5, comparative example No.6～10,12～17,19～22 average crystallite particle diameter are in the scope of 30～60 μ m.In addition, comparative example No.11,18 average crystallite particle diameter surpass 100 μ m.
(evaluation of press formability)
And then, for the shaping that obtains aluminium alloy plate (embodiment No.1～5, comparative example No.6～22), according to the press formability of following each alloy sheets of sequence evaluating.Its result is as shown in table 2.
The test film that use is taked from alloy sheets carries out tension test, measures tensile strength (TS (MPa)), general extension (EL (%)).Press formability is being estimated by the strength-ductility balanced value of (TS) * (EL) definition, when strength-ductility balanced value is 11000 to be evaluated as qualified (zero) when above, less than being evaluated as defective (*) at 11000 o'clock.
In addition, taking of test film is the long side direction that spreads all over alloy sheets, separates from the space to be five carrying out arbitrarily more than the 100mm.(TS) value and (EL) mean value of the measured value of 5 test films of value use.And then tension test is carried out based on JIS Z2201, and the test film shape is carried out with JI S5 test film.It is consistent with the rolling direction of alloy sheets that test film is made into long side direction.Need to prove that pinblock speed is that 5mm/ divides, carry out until the test film fracture with constant speed.
[table 1]
[table 2]
From table 1,2 result as can be known, satisfy the comparative example No.6 of the embodiment No.1 of important document of the present invention～5 and discontented unabridged version invention important document～22 and compare, superior aspect press formability.
Specifically, comparative example No.6 is the alloy sheets of record in the patent documentation 3, but that Mg degree of segregation (regional Mg degree of segregation) is failed is within the scope of the invention suppressed, so press formability is poor.Although comparative example No.7,14 can suppress within the scope of the invention for the Mg degree of segregation, Mg content is lower than lower value, and therefore strength-ductility balanced low, press formability is poor.Comparative example No.8,15 is because Mg content surpasses higher limit, so the Mg degree of segregation is large, and press formability is poor.Comparative example No.9,10,16,17 is because the thermal treatment that homogenizes, so the Mg degree of segregation is large, and press formability is poor.Comparative example No.11,18 is because the speed of cooling in when casting is slow, so the Mg degree of segregation is large, and press formability is poor.Comparative example No.12,19 is because the final annealing temperature is low, so the Mg degree of segregation is large, press formability is poor.Comparative example 13,20 is because the speed of cooling during final annealing is slow, so the Mg degree of segregation is large, press formability is poor.Cut processing although comparative example 21 has carried out the face of the plate two sides cutting 1.75mm of the cast panel that will be made by the double-roll type Continuous casting process, Mg degree of segregation (regional Mg degree of segregation) is failed within the scope of the invention suppressed, so press formability is poor.Comparative example 22 is cut processing owing to face is not carried out on the plate two sides of the cast panel made by graphite stationary die formula Continuous casting process, so the Mg degree of segregation is large, press formability is poor.
More than, embodiments of the present invention and embodiment are illustrated, but the invention is not restricted to above-mentioned embodiment, in the scope of claim record, can carry out various changes and implement.The application is based on the Japanese patent application (Patent 2010-187756) of application on August 25th, 2010, and its content is incorporated in this as reference.
Nomenclature
A, b, c interval
The L plate is long
The W plate is wide
The T thickness of slab
Px plate width direction measuring point
Py thickness of slab direction detection point
1 keeps stove
1a is cast into mouth
2 liquations
3 continuous casting molds
4 graphite stationary die
The outlet of 4a cast panel
5 water jackets
6 cast panels
7 rollers
10 thin plate continuous casting apparatus
100 thin plate continuous casting apparatus
200 keep stove
300 liquations
400 for nozzle for liquid
500 pairs of rollers
600 cast panels
Claims (4)
1. shaping aluminium alloy plate, it contains below the above 15.0 quality % of Mg:6.0 quality %, and surplus is Al and impurity, it is characterized in that,
In being set in the zone of described shaping with aluminium alloy plate the lip-deep wide square shape as 1 limit take full plate, separate the plate width direction measuring point mensuration Mg concentration that predetermined distance is set a plurality of at plate width direction and plate length direction, the mean value of the Mg concentration that will measure at a plurality of described plate width direction measuring points is as the average Mg concentration of plate width direction (Co)
For a plurality of described plate width direction measuring points, separate the thickness of slab direction detection point that predetermined distance is set in the whole thickness range in the thickness of slab direction and measure Mg concentration a plurality of, the mean value of the Mg concentration that will measure at a plurality of described thickness of slab direction detection points is as thickness of slab orientation average Mg concentration (Ci), in the case
Absolute value by the regional Mg degree of segregation (X) of poor (Ci-Co) of described thickness of slab orientation average Mg concentration (Ci) and the average Mg concentration of described plate width direction (Co) definition, its maximum value is below the 0.5 quality %, and its mean value is below the 0.1 quality %.
2. shaping aluminium alloy plate as claimed in claim 1 is characterized in that,
Except described regional Mg degree of segregation (X),
When calculating described regional Mg degree of segregation (X), at least one of described plate width direction measuring point, will be in the Mg concentration of measuring in whole thickness range with predetermined distance on the thickness of slab direction during as thickness of slab direction Mg concentration (Ct),
Absolute value by the thickness of slab direction Mg degree of segregation (Y) of poor (Ct-Ci) of described thickness of slab direction Mg concentration (Ct) and described thickness of slab orientation average Mg concentration (Ci) definition, its maximum value is below the 4 quality %, and its mean value is below the 0.8 quality %.
3. shaping aluminium alloy plate as claimed in claim 1 or 2 is characterized in that,
The content of described Mg is above 8 quality % and below 14 quality %.
4. shaping aluminium alloy plate as claimed in claim 1 or 2 is characterized in that,
Described impurity is the element more than at least a kind that Fe:1.0 quality % is following, Si:0.5 quality % is following, Ti:0.1 quality % is following, B:0.05 quality % is following, Mn:0.3 quality % is following, Cr:0.3 quality % is following, Zr:0.3 quality % is following, V:0.3 quality % is following, Cu:1.0 quality % is following, the Zn:1.0% quality is following.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2010-187756 | 2010-08-25 | ||
| JP2010187756A JP5427143B2 (en) | 2010-08-25 | 2010-08-25 | Aluminum alloy sheet for forming |
| PCT/JP2011/068979 WO2012026469A1 (en) | 2010-08-25 | 2011-08-23 | Aluminum alloy sheet for forming |
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| Publication Number | Publication Date |
|---|---|
| CN102959109A true CN102959109A (en) | 2013-03-06 |
| CN102959109B CN102959109B (en) | 2015-11-25 |
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| Application Number | Title | Priority Date | Filing Date |
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| CN201180030754.6A Expired - Fee Related CN102959109B (en) | 2010-08-25 | 2011-08-23 | Shaping aluminium alloy plate |
Country Status (6)
| Country | Link |
|---|---|
| US (1) | US20130112323A1 (en) |
| JP (1) | JP5427143B2 (en) |
| KR (1) | KR101520195B1 (en) |
| CN (1) | CN102959109B (en) |
| DE (1) | DE112011102796T5 (en) |
| WO (1) | WO2012026469A1 (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105238959A (en) * | 2015-10-15 | 2016-01-13 | 郭进标 | Tungsten doped aluminum alloy and preparation method thereof |
| CN105543587A (en) * | 2015-11-20 | 2016-05-04 | 江苏大学 | Ultrahigh-strength nano-crystalline Al-Mg aluminum alloy material and preparation method thereof |
| CN110643863A (en) * | 2019-08-29 | 2020-01-03 | 金榀精密工业(苏州)有限公司 | High-strength automobile part outer shell and forming method |
| CN111411271A (en) * | 2020-05-07 | 2020-07-14 | 南京至美畅和科技会展股份有限公司 | High-strength aluminum alloy material for exhibition shelf |
| CN112218962A (en) * | 2017-12-21 | 2021-01-12 | 诺维尔里斯公司 | Aluminum alloy products exhibiting improved bond durability and/or having phosphorus-containing surfaces and methods of making the same |
| CN114058915A (en) * | 2021-10-29 | 2022-02-18 | 安徽省恒泰动力科技有限公司 | Rare earth doped aluminum-magnesium alloy product and preparation process thereof |
Families Citing this family (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP5920723B2 (en) | 2011-11-21 | 2016-05-18 | 株式会社神戸製鋼所 | Aluminum-magnesium alloy and its alloy plate |
| WO2015027030A1 (en) * | 2013-08-21 | 2015-02-26 | Taheri Mitra Lenore | Selective grain boundary engineering |
| GB201503608D0 (en) * | 2015-03-03 | 2015-04-15 | Spex Services Ltd | Improved tool |
| KR101816202B1 (en) | 2015-12-31 | 2018-01-09 | 최창민 | Aluminum alloy for high strength |
| KR101694831B1 (en) * | 2016-03-25 | 2017-01-11 | 조일알미늄(주) | Aluminium alloy composition for car body and method of casting |
| TWI769061B (en) * | 2021-08-19 | 2022-06-21 | 中國鋼鐵股份有限公司 | Negative segregation slab and method for producing the same |
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| JP2010187756A (en) | 2009-02-16 | 2010-09-02 | Olympus Corp | Image processing apparatus, image processing method, and image processing program |
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- 2010-08-25 JP JP2010187756A patent/JP5427143B2/en not_active Expired - Fee Related
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- 2011-08-23 KR KR1020137004523A patent/KR101520195B1/en active IP Right Grant
- 2011-08-23 WO PCT/JP2011/068979 patent/WO2012026469A1/en active Application Filing
- 2011-08-23 US US13/810,765 patent/US20130112323A1/en not_active Abandoned
- 2011-08-23 CN CN201180030754.6A patent/CN102959109B/en not_active Expired - Fee Related
- 2011-08-23 DE DE112011102796T patent/DE112011102796T5/en not_active Ceased
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| JPH08199278A (en) * | 1995-01-27 | 1996-08-06 | Nippon Steel Corp | Aluminum alloy sheet excellent in press formability and baking finish hardenability and its production |
| CN101107373A (en) * | 2005-01-19 | 2008-01-16 | 株式会社神户制钢所 | Aluminum alloy plate and process for producing the same |
| JP2007077485A (en) * | 2005-09-16 | 2007-03-29 | Kobe Steel Ltd | Aluminum alloy sheet for forming |
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Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105238959A (en) * | 2015-10-15 | 2016-01-13 | 郭进标 | Tungsten doped aluminum alloy and preparation method thereof |
| CN105543587A (en) * | 2015-11-20 | 2016-05-04 | 江苏大学 | Ultrahigh-strength nano-crystalline Al-Mg aluminum alloy material and preparation method thereof |
| CN112218962A (en) * | 2017-12-21 | 2021-01-12 | 诺维尔里斯公司 | Aluminum alloy products exhibiting improved bond durability and/or having phosphorus-containing surfaces and methods of making the same |
| CN110643863A (en) * | 2019-08-29 | 2020-01-03 | 金榀精密工业(苏州)有限公司 | High-strength automobile part outer shell and forming method |
| CN111411271A (en) * | 2020-05-07 | 2020-07-14 | 南京至美畅和科技会展股份有限公司 | High-strength aluminum alloy material for exhibition shelf |
| CN114058915A (en) * | 2021-10-29 | 2022-02-18 | 安徽省恒泰动力科技有限公司 | Rare earth doped aluminum-magnesium alloy product and preparation process thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| KR20130059398A (en) | 2013-06-05 |
| DE112011102796T5 (en) | 2013-05-29 |
| JP2012046776A (en) | 2012-03-08 |
| WO2012026469A1 (en) | 2012-03-01 |
| JP5427143B2 (en) | 2014-02-26 |
| CN102959109B (en) | 2015-11-25 |
| KR101520195B1 (en) | 2015-05-13 |
| US20130112323A1 (en) | 2013-05-09 |
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