CN105143484A - Aluminum alloy plate for structural material - Google Patents
Aluminum alloy plate for structural material Download PDFInfo
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- CN105143484A CN105143484A CN201480011852.9A CN201480011852A CN105143484A CN 105143484 A CN105143484 A CN 105143484A CN 201480011852 A CN201480011852 A CN 201480011852A CN 105143484 A CN105143484 A CN 105143484A
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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
- C22C21/10—Alloys based on aluminium with zinc as the next major constituent
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
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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
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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
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/047—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with magnesium as the next major constituent
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- 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
- C22F1/053—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 zinc as the next major constituent
Abstract
The invention provides a 7000-series aluminum alloy plate having a specific composition. The aluminum alloy plate is manufactured by a conventional method and provided with high strength through balance with the Mg content while the Zn content is suppressed, the aluminum alloy plate is also provided with high strength, moldability, and corrosion resistance needed for a structural material, as a composition having a specific heat absorption peak temperature and the maximum height of a heat generation peak on a differential scanning calorimetry curve during room-temperature aging of the manufactured plate.
Description
Technical field
The present invention relates to and processibility is improved, the structural wood aluminium alloy plate of the high strength that erosion resistance is also excellent.So-called aluminium alloy plate of the present invention, referring to milled sheet, is after carrying out solid solution and quench treatment for the plate manufactured through rolling, the plate after more than 2 weeks room-temperature agings, is before formed machining becomes structured material and artificial age-hardening's plate before treatment.
Background technology
In recent years, from the concern for global environment etc., the light-weighted social requirement of car body is surging all the more.In order to tackle such requirement, what carried out is, among car body, by panel (outer panels, the wainscots of hood, car door, roof etc.), with the reinforcing material etc. of bumper reinforcement (bumperR/F) and door anti-collision joist etc., Al alloy material, partially substitutes the ferrous materials of steel plate etc.
But, in order to the more lightweight of car body, among automobile component, also need, in the automotive structural members contributing to light-weighted vehicle frame, beam column etc. especially, also to expand the application of aluminum alloy materials.But, 0.2% yield strength required by these automotive structural members be 350MPa with first-class, compared with described car panel, need high strength.Based on this point, the plasticity that described car panel uses, intensity and excellent corrosion resistance, and because low-alloy composition and JIS to the AA6000 line aluminium alloy plate of recirculation excellence, even if control composition and modified (solution treatment and quench treatment, in addition artificial age-hardening's process is also had), also cannot reach described high strength far away.
Therefore, at the automotive structural members of such high strength, need service requirements have equal high strength as described in reinforcing material and by JIS to the AA7000 line aluminium alloy plate used.But as 7000 line aluminium alloys of Al-Zn-Mg line aluminium alloy, resistance to general corrosion is poor.In addition, because be the precipitate MgZn by making Zn and Mg form
2distribute to high-density and reach the alloy of high strength, so there is the danger that stress corrosion cracking (following, SCC) occurs.In order to be prevented it, have to carry out Wetted constructures, practical situation are, are to use under the degree of 300MPa in 0.2% yield strength, and the feature as high-strength alloy is weak.
For this reason, the composition control of 7000 line aluminium alloys that intensity and this two side of SCC resistance are all excellent, and the organizational controls of precipitate etc., propose to have all the time.
Such as, as the typical example of composition control, in patent documentation 1, utilization be that 7000 line aluminium alloys extrude material, compare by correct proportions formed MgZn
2zn and Mg measure (MgZn
2stoichiometric ratio) and the superfluous Mg added, contribute to high strength, compare MgZn
2stoichiometric ratio, add Mg by surplus, thus suppress MgZn
2amount, does not make SCC resistance reduce and realize high strength.
As the typical example of the organizational controls of precipitate etc., such as, in patent documentation 2,7000 line aluminium alloys after artificial age-hardening is processed extrude material, particle footpath in crystal grain is the precipitate of 1 ~ 15nm, in the observations of transmission electron microscope (TEM), with 1000 ~ 10000/μm
2density exist, reduce the potential difference of intracrystalline and crystal boundary, thus SCC resistance improved.
In addition, although all do not illustrate, the organizational controls that 7000 line aluminium alloys extrude the intensity of material and all excellent composition control example of this two side of SCC resistance and precipitate etc. is routine, extrude material practical in exist in a large number with inundatory ratio.In contrast, in 7000 line aluminium alloy plates, example such as the organizational controls of existing composition control and precipitate etc. is few, little respective panels practical.
Such as, propose in patent documentation 3, be welded to one another in the structured material that forms of cladding plate engaged at 7000 line aluminium alloy plates, in order to improve intensity, the diameter of the precipitation after artificial age-hardening is processed is
(dust) below, and as spherical make it to exist a certain amount of.But, completely not open about the performance of SCC resistance, there is no the data of erosion resistance in embodiment yet.
In addition, in patent documentation 4, cold rolling for carrying out after making molten soup quench solidification, carry out the crystallization precipitate in the crystal grain of 7000 line aluminium alloy plates after artificial age-hardening's process again, by the measurement that the opticmicroscopes of 400 times carry out, make size (area is converted into diameter of equivalent circle of equal value) be less than 3.0 μm, make centre plane integration rate be less than 4.5%, thus intensity and unit elongation are improved.
Control about the set tissue of plate has also proposed.Such as, in patent documentation 5,6, in order to high strength, the high SCC resistance of 7000 tie-plates of implementation structure material, after forging ingot bar, be repeatedly rolled in temperature processing territory, make fine microstructures.This is because, by making fine microstructures, thus suppress to form the crystal boundary of reason that SCC resistance reduces, and form and the essential factor of potential difference of intracrystalline, namely azimuth difference is the big angle crystal boundary of more than 20 °, and the low angle boundary obtaining 3 ~ 10 ° is the set tissue of more than 25%.But, such warm-rolling repeatedly, in the hot rolling, cold rolling mode of ordinary method, be because can not obtain such low angle boundary be more than 25% set tissue carry out.Therefore, operation and ordinary method differ widely, and therefore in making sheet, are being practical method hardly.
Look-ahead technique document
Patent documentation
Patent documentation 1: Japanese Laid-Open 2011-144396 publication
Patent documentation 2: Japanese Laid-Open 2010-275611 publication
Patent documentation 3: the flat 9-125184 publication of Japanese Laid-Open
Patent documentation 4: Japanese Laid-Open 2009-144190 publication
Patent documentation 5: Japanese Laid-Open 2001-335874 publication
Patent documentation 6: Japanese Laid-Open 2002-241882 publication
So, the composition control of 7000 line aluminium alloys of intensity and this two sides excellence of SCC resistance and precipitate, or the motion of the organizational controls etc. of set tissue etc., always also proposed all in the field of extruding material.But, about carry out again after ingot bar is carried out equal thermal treatment hot rolling and cold rolling like this, follow the milled sheet that ordinary method manufactures, actual state is, except the special rollings such as described cladding plate, emergency cooling solidification method, warm-rolling or method for making, what does not propose.
And extrude material and described milled sheet, the manufacturing processed of its hot procedure etc. is completely different, the tissue of the crystal grain of generation and precipitate etc., such as crystal grain is the threadiness etc. along extruding direction elongation, and the milled sheet being equi-axed crystal substantially with crystal grain differs widely.Therefore, described motion of extruding the organizational controls of the composition control and precipitate etc. of material etc., no matter be in 7000 line aluminium alloy plates, or in the automotive structural members be made up of this 7000 line aluminium alloy plate, all can not directly be suitable for, whether the end of bringing up to for intensity and SCC resistance these two aspects effectively it be unclear that.That is, confirm unless actual, otherwise eventually can only rest on the anticipation stage.
Therefore present situation is, at the 7000 line aluminium alloy plates manufactured by described ordinary method, in the organizational controls technology that the both sides of intensity and SCC resistance are all excellent, there is no effective means, the leeway that not clear part is much illustrated in addition.In addition, about resistance to general corrosion, what intervention occurred is that Zn adds the low potential brought, and therefore from the view point of intensity and erosion resistance, needs to reduce Zn addition.But if reduce Zn content, although erosion resistance is improved, the another side improved as the shaping processability of the bendability of necessary characteristic etc. in described structural member is, intensity reduces, thus formation is such and the problem of the technical difficulty of high strength contradiction.
Summary of the invention
In view of the above problem set forth, the object of the invention is to, provide 7000 line aluminium alloy plates such as the structural wood of a kind of automobile component etc., it is the milled sheet manufactured by described ordinary method, having both strength and shaping processability, and erosion resistance is also excellent.
In order to reach this purpose, the main idea of structural wood aluminium alloy plate of the present invention, in mass %, respectively containing Zn:3.0 ~ 6.0%, Mg:1.5 ~ 4.5%, Cu:0.05 ~ 0.5%, and the content [Mg] of the content of Zn [Zn] and Mg meets the relation of [Zn] >=-0.3 [Mg]+4.5, the Al-Zn-Mg line aluminium alloy plate formed that surplus is made up of Al and inevitable impurity, make it in differential scanning calorimetric analysis curve when carrying out room-temperature aging after solid solution and quench treatment are carried out for this plate again, maximum endothermic peak temperature is less than 130 DEG C, and the maximum height of the exothermic peak in the temperature range of 200 ~ 300 DEG C is 50 more than μ W/mg, work hardening exponent n value (10 ~ 20%) is more than 0.22.
Said aluminium alloy plate in the present invention, it is the plate manufactured by rolling, refer to for the laggard row hot rolling of the equal thermal treatment of ingot bar, carry out cold rolling again and become cold-reduced sheet, implement the modifier treatment (state code is T4) of solid solution and quench treatment etc. again, the 7000 line aluminium alloy plates manufactured by ordinary method.In other words, do not comprise as described patent documentation 5,6, by the plate manufactured through the special like this rolling method of repeated multiple times warm-rolling again after forging ingot bar.
And said aluminium alloy plate in the present invention, also refers to that the tissue through room-temperature aging for the 7000 line aluminium alloy plates manufactured in the above described manner specifies, and is the plate being processed to the structured material of certain purposes as former material aluminium alloy plate.Therefore, referring to the plate carrying out after room-temperature aging (room temperature placement) for the plate manufactured in the above described manner, is before formed machining becomes as purposes structured material and artificial age-hardening's plate before treatment.
The present invention suppresses Zn content to improve erosion resistance, on the other hand, increases Mg content in order to ensure intensity, for the tissue through room-temperature aging of 7000 line aluminium alloy plates of this composition, is analyzed by differential scanning calorimeter curve.It found that, in 7000 line aluminium alloy plates of this composition, compared with the 7000 line aluminium alloy plates that Zn content is high, forming of the cluster generated by room-temperature aging is different with effect.
Namely, in the 7000 line aluminium alloy plates suppressing Zn content, the cluster (atom set body) generated by room-temperature aging, not only contribute to the artificial age-hardening's characteristic (BH) after formed machining becomes as the structured material of certain purposes, and contribute to ductility (Work Hardening Characteristic) required when formed machining becomes structured material.Therefore, by controlling these clusters, erosion resistance can not only be improved, and the balance of intensity and ductility (plasticity) can be made to improve, as the milled sheet manufactured by ordinary method, having both strength and shaping processability can be provided, the structure 7000 line aluminium alloy plates that the erosion resistance of SCC resistance etc. is also excellent.
But the composition of such cluster (atom set body) and size or density etc., can not, at that time by the common Observations Means Direct Recognition of SEM and TEM etc., be difficult to be specified quantitatively by the factor of these tissues.
Therefore, in the present invention, for 7000 manufactured line aluminium alloy plates through room-temperature aging tissue, by the analysis based on differential scanning calorimeter curve, indirectly specify described cluster and control.More particularly, in the analysis based on differential scanning calorimeter curve, the temperature of the endothermic peak again corresponding to solid solution of the cluster formed by room-temperature aging is lower, and the Work Hardening Characteristic as ductility more improves.On the other hand, corresponding to the precipitate after artificial age-hardening's process, the maximum height of the exothermic peak in the temperature range of 200 ~ 300 DEG C is higher, and artificial aging precipitate amount is more, and intensity more improves.
In the present invention, because so specify the cluster generated through room-temperature aging, so under the state not being the plate without room-temperature aging after immediately described modifier treatment, carry out the measurement of described differential scanning calorimeter curve, but as target for the plate after more than 2 weeks room-temperature agings (room temperature placement), carry out with artificial age-hardening's plate before treatment before structured material is become for formed machining.
Embodiment
Below, for the mode of enforcement of the present invention, just each important document is illustrated particularly.
Aluminium alloy forms:
First, the chemical composition below with regard to aluminium alloy plate of the present invention forms, and the restriction reason comprising each element is described.Further, the % display of the content of each element is all the meaning of quality %.
The chemical composition composition of aluminium alloy plate of the present invention, as the milled sheet manufactured by ordinary method, has the requirement characteristic of the structural wood as the automobile component desired by the present invention etc., with having both strength and shaping processability, and meets condition premised on erosion resistance.Therefore, 7000 line aluminium alloys of Al-Zn-Mg-Cu system of the present invention consist of, and suppress Zn content to improve erosion resistance, on the other hand, increase the composition of Mg content in order to ensure intensity.
Go out from this viewpoint, the chemical composition composition of aluminium alloy plate of the present invention, in mass %, respectively containing Zn:3.0 ~ 6.0%, Mg:1.5 ~ 4.5%, Cu:0.05 ~ 0.5%, and the content [Mg] of the content of Zn [Zn] and Mg meets the relation of [Zn] >=-0.3 [Mg]+4.5, and surplus is made up of Al and inevitable impurity.In this composition, in addition, as transition element, also can optionally contain Zr:0.05 ~ 0.3%, Mn:0.1 ~ 1.5%, Cr:0.05 ~ 0.3%, Sc:0.05 ~ 0.3% one or more.In addition, except these transition element, or replaced, also can more optionally containing Ag:0.01 ~ 0.2%.
Zn：3.0～6.0％
As the Zn of necessary alloying element, together with Mg, manufactured modified after the room-temperature aging of plate time form cluster and Work Hardening Characteristic improved, the shaping processability of structure-oriented material is improved.In addition, during artificial aging process after formed machining becomes structured material, form precipitation and intensity is improved.Zn content lower than 3.0% time, the undercapacity after artificial aging process.But, if Zn is many and higher than 6.0% containing quantitative change, then grain boundary precipitate MgZn
2increase, easily grain boundary corrosion occurs, erosion resistance deterioration.Therefore, Zn content suppresses more less in the present invention.Therefore, the lower limit of Zn content is 3.0%, is preferably 3.5%.In addition, the upper limit of Zn content is 6.0%, is preferably 4.5%.
Mg：1.5～4.5％
As the Mg of necessary alloying element, together with Zn, manufactured modified after the room-temperature aging of plate time form cluster and Work Hardening Characteristic improved.In addition, form precipitation during artificial aging process after formed machining becomes structured material and intensity is improved.In the present invention, because Zn content suppresses lower, otherwise Mg content is just many.When Mg content is lower than 1.5 quality %, undercapacity, Work Hardening Characteristic reduces.But if higher than 4.5 quality %, then the rolling of plate reduces, SCC susceptibility also grow.Therefore, the lower limit of Mg content is 1.5%, is preferably 2.5%.In addition, the upper limit of Mg content is 4.5%.
The balanced type of Zn and Mg:
In the present invention, in order to ensure the high strength by bringing containing Zn and Mg, importantly not only to control the content of described Zn and Mg, and will the balance of content [Zn] (the quality %) of control Zn and content [Mg] (the quality %) of Mg.For this reason, as the control of its balance, make [Zn] and [Mg] meet the balanced type of [Zn] >=-0.3 [Mg]+4.5, preferably meet the balanced type of [Zn] >=-0.5 [Mg]+5.75.
Be somebody's turn to do [Zn] >=-0.3 [Mg]+4.5 by meeting, according to aftermentioned preferred manufacture method, 0.2% yield strength of the structured material after artificial age-hardening can be made to process reaches more than 350MPa.In addition, by meeting [Zn] >=-0.5 [Mg]+5.75, according to preferred manufacture method described later, 0.2% yield strength of the structured material after artificial age-hardening can be made to process reaches more than 400MPa.
Each content of Zn and Mg, when [Zn] <-0.3 [Mg]+4.5, even if each content of Zn and Mg is in specialized range, even or according to aftermentioned preferred manufacture method, 0.2% yield strength that all there is the structured material after artificial age-hardening can not be made to process reaches the possibility of more than 350MPa.In addition, when the content of Zn and the content of Mg are [Zn] <-0.5 [Mg]+5.75, same 0.2% yield strength that there is the structured material after artificial age-hardening can not be made to process reaches the possibility of more than 400MPa.
Cu：0.05～0.5％
Cu suppresses the SCC susceptibility of Al-Zn-Mg system alloy, has the effect that SCC resistance is improved.In addition, resistance to general corrosion is also made to improve.Cu content lower than 0.05% time, the raising effect of SCC resistance and resistance to general corrosion is little.On the other hand, if Cu content is higher than 0.5%, then all characteristics of rolling and weldability etc. are made to reduce on the contrary.Therefore, the lower limit of Cu content is 0.05%.In addition, the upper limit of Cu content is 0.5%, is preferably 0.4%.
One or more of Zr:0.05 ~ 0.3%, Mn:0.1 ~ 1.5%, Cr:0.05 ~ 0.3%, Sc:0.05 ~ 0.3%
The transition element of Zr, Mn, Cr, Sc, makes the crystal grain miniaturization of ingot bar and end article, contributes to intensity and improves, make it optionally to contain when therefore needing.If containing its any one or two or more, the content of Zr, Mn, Cr, Sc all lower than lower in limited time, then containing quantity not sufficient, intensity reduces.On the other hand, the content of Zr, Mn, Cr, Sc above then forms thick crystallisate in limited time higher than respective, and therefore unit elongation reduces.Therefore, its content contained sometimes is made to be, each scope of Zr:0.05 ~ 0.3%, Mn:0.1 ~ 1.5%, Cr:0.05 ~ 0.3%, Sc:0.05 ~ 0.3%, is preferably each scope of Zr:0.08 ~ 0.2%, Mn:0.2 ~ 1.0%, Cr:0.1 ~ 0.2%, Sc:0.1 ~ 0.2%.
Ag：0.01～0.2％
Ag becomes the artificial aging process after structured material by formed machining, the precipitation contributing to intensity raising is closely separated out imperceptibly, has the effect promoting high strength, therefore make it as required optionally to contain.Ag content lower than 0.01% time, strength-enhancing effect is little.On the other hand, even if Ag content makes it higher than 0.2% to contain, its effect is also saturated, causes high price.Therefore, Ag content is the scope of 0.01 ~ 0.2%.
Other element:
Other element beyond these is inevitable impurity substantially.As melting raw material, except fine aluminium block, also can use aluminium alloy scrap, being mixed into of these impurity elements that (permission) cause thus can be predicted, allow it to be contain separately in the scope of the JIS specification defined of alloy 7000.Such as, Ti, B are impurity as milled sheet, but also have the effect of the crystal grain miniaturization making ingot bar, and therefore the upper limit of Ti is 0.2%, and the upper limit being preferably 0.1%, B is less than 0.05%, are preferably 0.03%.Fe, Si if below Fe:0.5%, below Si:0.5%, then can not impact the characteristic of aluminum alloy rolled plate of the present invention, allow to contain.
Tissue:
Above composition is as prerequisite, 7000 line aluminium alloy plate tissues of the present invention, after the solid solution and quench treatment of this plate, as target in the differential scanning calorimeter curve after more than 2 weeks room-temperature agings, maximum endothermic peak temperature is less than 130 DEG C, and the maximum height of the exothermic peak of the temperature range of 200 ~ 300 DEG C is 50 more than μ W/mg.
Maximum endothermic peak temperature, the solid solution again of the cluster formed when room-temperature aging with this plate is corresponding.This maximum endothermic peak temperature is lower, the thermostability of corresponding cluster lower (more easily decomposing), beyond heat extraction, and the also easy cutting because of dislocation during viscous deformation and decomposing.Therefore, the stability of cluster is lower like this, is more difficult to become the obstruction of dislocation moving when plate formed machining becomes the viscous deformation such as structured material and the reason of strain concentrating.Its target be maximum endothermic peak temperature below 130 DEG C, by meeting this regulation, the stability of cluster is low (instability), and Work Hardening Characteristic improves, and work hardening exponent n value (10 ~ 20%) can be made to be more than 0.22.
In contrast, the stability of this cluster is higher, its maximum endothermic peak temperature uprises and more than 130 DEG C, Work Hardening Characteristic reduces, and work hardening exponent n value (10 ~ 20%) can not be made to be more than 0.22.This is because, the stability of this cluster is higher, although become the obstacle of dislocation moving when plate formed machining becomes the viscous deformation such as structured material, if but cutting cluster and dislocation starts mobile, then in the mobile set of its slip plane dislocation, therefore easily strain concentrating occurs, Work Hardening Characteristic reduces.
The maximum height of the exothermic peak in the temperature range of 200 ~ 300 DEG C, corresponding with the precipitation of the precipitate (artificial aging precipitate) when contributing to the artificial aging process of raising of intensity.Therefore, this exothermic peak height is higher, and the amount of precipitation (density) of artificial aging precipitate is more, can improve intensity.Its target is, the maximum height of the exothermic peak in the temperature range of 200 ~ 300 DEG C has 50 more than μ W/mg, when the maximum height of this exothermic peak is lower than 50 μ W/mg, the possibility that 0.2% yield strength of the structured material after artificial age-hardening can not be made to process reaches more than 350MPa is high.
Work Hardening Characteristic:
According to above composition and tissue and aftermentioned preferred manufacture method, 7000 line aluminium alloy plates of the present invention, shaping processability improves, but is especially in use in formed machining when becoming structured material, in order to ensure bendability, in the present invention, specify work hardening exponent n value (10 ~ 20%).Namely, according to the 7000 line aluminium alloy plates that above composition and tissue and preferred manufacture method described later manufacture, after the solid solution and quench treatment of this plate, making to carry out the work hardening exponent n value (10 ~ 20%) after more than 2 weeks room-temperature agings as target is more than 0.22.
Work hardening, also referred to as strain hardening, if refer to by stress applications such as formed machining, then causes the phenomenon that hardness increases due to viscous deformation.Work hardening causes distortion more to advance by formed machining exactly, and resistance more becomes large, and hardness more increases, and the characteristic value as target of shaping processability is called " n value ".This n value be make the stress σ of the plastic region of more than yield-point and strain stress close like time index n.Approximate expression is carried out according to the formula of the Voce with aluminium matching.N value is higher, easier work hardening, and bear by the part of the bending viscous deformation waiting formed machining to cause harder, its periphery one is with easy distortion, and therefore the bending shaping processability waited improves.In contrast, n value is lower, is more difficult to work hardening, to be subject to the part of viscous deformation at first, the most not hardening by this part of stress, but viscous deformation increasingly occurs, and easily shrinks fracture, and therefore the bending shaping processability waited is low.
(manufacture method)
Below, for the manufacture method of 7000 line aluminium alloy plates of the present invention, be illustrated particularly.
In the present invention, the manufacture method manufacture that can be made up of the common manufacturing process of 7000 line aluminium alloy plates.That is, the common each manufacturing process through casting (DC casting and Continuous casting process), the thermal treatment that homogenizes, hot rolling manufactures, and becomes the aluminum alloy hot rolling band of thickness of slab 1.5 ~ 5.0mm.Secondly, carry out cold rolling and become the cold-reduced sheet of below thickness of slab 3mm.At this moment, also can before cold rolling or cold rolling midway optionally carry out the process annealing of more than 1 time or 2 times.
(melting, casting cooling speed)
First, in melting, casting process, be suitable for the common melting and casting method selecting Continuous casting process, semicontinuous casting method (DC casting) etc., the aluminium alloy that casting smelting is adjusted in above-mentioned 7000 set member compositing ranges melts soup.
(homogenize thermal treatment)
Secondly, for the aluminium alloy ingot bar of described casting, before hot rolling, implement to homogenize thermal treatment.This thermal treatment that homogenizes (equal thermal treatment), by organize homogenize for the purpose of, that is, make the segregation that intracrystalline does not occur in ingot bar tissue.
But, in the present invention, in order to make after described modifier treatment after room-temperature aging, Work Hardening Characteristic when formed machining is structured material, and formed machining is that intensity after artificial aging process after structured material all improves, and carries out equal thermal treatment with two sections or secondary soaking operation.So-called two sections of soaking refer to, although cool after first time soaking, until less than 200 DEG C do not cool, after stopping cooling, maintain with this temperature with higher temperature, direct with this temperature afterwards, or reheat to rear beginning hot rolling at higher temperature.In contrast, so-called secondary soaking, be after first time soaking, be first cooled to the temperature of less than 200 DEG C that comprise room temperature, then reheat, after maintaining certain hour with this temperature, start hot rolling.
In first paragraph in these two sections or secondary soaking operation or first time soaking operation, target is that the compound fine of transition element system is disperseed, make the compound fine of the plasticity having influence on structure-oriented material, in second segment or second time soaking operation, target is the solid solution promoting Zn, Mg, Cu, intensity when Work Hardening Characteristic during raising room-temperature aging and artificial aging process.
For this reason, first paragraph or primary soaking temperature are controlled, at 400 ~ 450 DEG C, preferably to control at 400 ~ 440 DEG C.By in the heating of this temperature range, keep ingot bar, Zr based compound can be made and the compound fine that is made up of Mn, Cr, Sc disperse.When this soaking temperature is lower than 400 DEG C, can not get sufficient micronized effect, Work Hardening Characteristic when cannot realize room-temperature aging improves.In addition, if on the other hand higher than 450 DEG C, then these compound coarsenings, the raising of Work Hardening Characteristic when still cannot realize room-temperature aging.This first paragraph or primary all heat treated hold-time can be about 1 ~ 8 time.
In addition, second segment or secondary equal thermal treatment temp are controlled, 450 DEG C ~ solidus temperature, preferably to control 470 DEG C ~ solidus temperature.By at the heating of this temperature range, maintenance ingot bar, the solid solution of Zn, Mg, Cu can be promoted, the intensity during artificial aging process after solid solution is improved.When this soaking temperature is lower than 450 DEG C, fully cannot obtain the solid solution of these elements, Work Hardening Characteristic during room-temperature aging and the intensity after artificial aging do not increase.In addition, if on the other hand higher than solidus temperature, then there is partial melting, the deterioration in characteristics of machinery, the upper limit is below solidus temperature.Hold-time when this second segment or secondary soaking can be 1 ~ 8 hours.
(hot rolling)
Hot rolling starts temperature higher than under the condition of solidus temperature in hot rolling, because there is burning, so hot rolling itself is difficult.In addition, when hot rolling starts temperature lower than 350 DEG C, load during hot rolling is too high, hot rolling difficulty itself.Therefore, hot rolling starts temperature and selects from the scope of 350 DEG C ~ solidus temperature and carry out hot rolling, becomes the hot-rolled sheet of about 2 ~ 7mm thickness of slab.The cold rolling front annealing (black annealing) of this hot-rolled sheet not necessarily needs, but also can implement.
(cold rolling)
In cold rolling, the above-mentioned hot-rolled sheet of rolling, is made into the cold-reduced sheet (also comprising coiled material) of the final thickness of slab of the expectation of about 1 ~ 3mm.Also process annealing can be carried out between cold rolling pass.
(solution treatment)
Cold rolling rear as modified and carry out solution treatment.About this solution treatment, can be undertaken heating, cooling by common continuous heat-treatment lines, be not particularly limited.But, in order to the miniaturization of the sufficient solid solution capacity and crystal grain that obtain each element, below 450 DEG C ~ solidus temperature, preferably with the solid solution temperature of 480 ~ 550 DEG C, after the hold-time arrives set solid solution temperature, more than 2 seconds or 3 seconds, the scope of less than 30 minutes is carried out.
Average cooling (cooling) speed after solution treatment does not specially require, but the cooling after solution treatment, select or combinationally use the air cooling of fan etc., the enforceable cooling ways such as the water-cooled means of spraying, water spray, impregnating, or the warm quenching-in water in room temperature ~ 100 DEG C.Subsidiary one, solution treatment is only carried out once substantially, but under room-temperature aging sclerosis such as excessively to carry out at the situation, in order to ensure the plasticity towards automobile component, also can implement solution treatment and restoration disposal once again under described preferred condition, also first can cancel the room-temperature aging sclerosis that this excessively carries out.
Then, aluminium alloy plate of the present invention, as former material, is formed and is processed into automobile component, assembles as automobile component.In addition, after formed machining becomes automobile component, implement artificial age-hardening's process separately, become automobile component or car body.
Artificial age-hardening processes:
7000 line aluminium alloy plates of the present invention, after formed machining becomes structured material, are processed by artificial age-hardening, reach the intensity of the expectation of the structured material as automobile component etc., count more than 350MPa with 0.2% yield strength, are preferably more than 400MPa.Carry out the moment of this artificial age-hardening's process, preferred former material 7000 line aluminium alloy plate is after formed machining becomes automobile component.This is because, 7000 line aluminium alloy plates after artificial age-hardening's process, although intensity uprises, plasticity reduces, and also can produce shape complicated because of automobile component and the situation that can not be shaped.
The condition of temperature and time of this artificial age-hardening process, according to the intensity of 7000 line aluminium alloy plates of the intensity expected and former material, or room-temperature aging carry out degree etc., freely determine in the scope of general artificial aging condition (T6, T7).Subsidiary one, if the condition illustrating artificial age-hardening's process, then if the ageing treatment of a section, then the ageing treatment at 100 ~ 150 DEG C carries out 12 ~ 36 hours (comprising overaging region).In addition, in the operation of two sections, in the scope of 70 ~ 100 DEG C, carry out 2 hours more than from the thermal treatment temp of first paragraph, select in the scope (comprising overaging region) that the thermal treatment temp of second segment carries out more than 5 hours in the scope of 100 ~ 170 DEG C.
Embodiment
Make the tissue via described DSC tracing analysis carry out all changes, manufacture 7000 line aluminium alloy cold-reduced sheets of the Al-Zn-Mg-Cu set member composition shown in following table 1,2.For the cold-reduced sheet that these manufacture, measure the maximum endothermic peak temperature in DSC curve when making it room-temperature aging after solid solution and quench treatment are carried out to this plate, and maximum height, the work hardening exponent n value (10 ~ 20%) of exothermic peak in the temperature range of 200 ~ 300 DEG C.In addition, characteristic and the resistance to general corrosion of the machinery of the intensity after also processing for artificial age-hardening etc. are evaluated.The display 8 of these results is in following table 3,4.
The tissue of cold-reduced sheet, mainly makes the equal heat-treat condition shown in table 3,4 carry out all changes and be controlled.Specifically, each example is all common, and 7000 line aluminium alloys be grouped into for each one-tenth shown in following table 1,2 melt soup and carry out DC casting, obtain 45mm thick × 220mm is wide × the long ingot bar of 145mm.For this ingot bar with table 3,4 condition carry out two sections of soaking or secondary soaking.Two sections of soaking are cooled to 250 DEG C after first time soaking, after first stopping cooling, reheats the soaking temperature to second segment and keep, being cooled to after hot rolling starts temperature and starting hot rolling with this temperature.Secondary soaking is after first time soaking, after being first cooled to room temperature, reheating to secondary soaking temperature and keeps, after being cooled to hot rolling and starting temperature, starting hot rolling.Table 3,4 one-shot equal thermal treatment, the second time after first not cooling reheats, and as usual, after keeping, is cooled to hot rolling and starts temperature and start hot rolling with this soaking temperature and time.
After these equal thermal treatments, carry out hot rolling with the beginning temperature shown in table 3,4, manufacture the hot-rolled sheet of thickness of slab 5mmt.For this hot-rolled sheet, carry out the black annealing process of forced air-cooling after implementing to keep 30 seconds with 500 DEG C, carry out being cold-rolled to 2mmt.For this cold-reduced sheet, each example is all common, implements the solution treatment of 500 DEG C × 1 minute, carries out forced air-cooling and be cooled to room temperature after this solution treatment, obtain the modified material of T4.For the aluminium alloy plate after this solution treatment, all common the making it of each example carries out 2 weeks room-temperature agings, extracts tabular test film, carry out dsc measurement and tension test from such plate.Each characteristic adjusts Check by following main points.
Dsc measurement (differential thermal analysis):
Dsc measurement (differential thermal analysis) condition, each example is all common, carries out with following identical conditions.
Testing apparatus: セ イ コ-イ Application ス ツルメン Star society DSC220C,
Reference material: fine aluminium,
Test portion container: fine aluminium,
Elevated Temperature Conditions: 15 DEG C/min,
Atmosphere (in test portion container): argon gas (gas flow 50ml/min),
Test test portion weight: 24.5 ~ 26.5mg.
Further, the test portion of differential thermal analysis extracts, from the aluminium alloy plate after described room-temperature aging must comprise respectively cross over lengthwise direction leading section, central part, 10 the carrying out of rearward end, make observed value equalization respectively.
With the profile (μ W) of the differential thermal analysis obtained respectively divided by test portion weight after making it stdn (μ W/mg), in the interval of 0 ~ 100 DEG C of described differential thermal analysis profile, the datum-plane of the region that the profile of differential thermal analysis is up to the standard as 0, as the maximum height of the exothermic peak from this datum-plane, the highest exothermic peak height among the exothermic peak measuring the temperature range of 200 ~ 300 DEG C.
In addition, simulation forming is processed into the process of the artificial age-hardening after automobile component, implements T6 process for the aluminium alloy plate after described room-temperature aging, and the artificial age-hardening carrying out 90 DEG C × 3hr+140 DEG C × 8hr processes.Extract tabular test film from the central part of the aluminium alloy plate after this artificial age-hardening process, investigate characteristic and the erosion resistance of machinery in the following manner.These results are also presented at table 3,4 respectively.
(characteristic of machinery)
Each example is all common, and the characteristic of machinery carries out the tensile test at room temperature of the rolling right angle orientation of each tabular test film, measures 0.2% yield strength (MPa), breaking elongation (%).Tensile test at room temperature, based on JIS2241 (1980), is tested with room temperature 20 DEG C.Draw speed is that 5mm/ divides, and proceeds to test film fracture with fixing speed.
(n value)
The measurement of n value, is the tabular test film after described artificial age-hardening is processed, as JIS5 tension test sheet (punctuate spacing 50mm), is rolled the tensile test at room temperature of right angle orientation.Then, according to endpoint calculation true stress and the true strain of yield extension, being plotted in transverse axis is strain, the longitudinal axis is in the logarithmically calibrated scale of stress, with 2 points of nominal strain 10%, 20%, the gradient of the straight line that computation and measurement point represents, as n value (10 ~ 20%).
(grain boundary corrosion susceptibility)
In order to evaluate general erosion resistance, for the tabular test film (3 test films) after described artificial age-hardening's process, carry out the grain boundary corrosion sensitivity test of the regulation according to old JIS-W1103.Test conditions is, by test film with room temperature immersion in aqueous nitric acid (30 quality %) after 1 minute, to be immersed in aqueous sodium hydroxide solution (5 quality %) after 20 seconds with 40 DEG C, again with room temperature immersion in aqueous nitric acid (30 quality %) 1 minute, the surface of washing test sheet thus.Thereafter, to be immersed in the state of sodium chloride aqueous solution (5 quality %), circulation 1mA/cm
2the electric current 24 hours of current density, mention test portion afterwards, afterwards, cut off the cross section of grinding test sheet, use opticmicroscope, measure the depth of corrosion apart from test portion surface.Multiplying power is × 100, and depth of corrosion is slight corrosion by the end of less than 200 μm, is evaluated as "○".In addition, be large corrosion during more than 200 μm, be evaluated as "×".
From table 1,3, each example, in aluminium alloy compositing range of the present invention, manufactures in the scope of described preferred manufacturing condition.
Consequently, in differential scanning calorimetric analysis curve when making it room-temperature aging after solid solution and quench treatment are carried out to this plate, maximum endothermic peak temperature is less than 130 DEG C, and the maximum height of the exothermic peak of the temperature range of 200 ~ 300 DEG C is 50 more than μ W/mg, meet the organization prescribed by described DSC tracing analysis.
Therefore, even if after room-temperature aging, work hardening exponent n value (10 ~ 20%) is also up to more than 0.22, and ductility is excellent, and the shaping processability of structure-oriented material is excellent.Meanwhile, even if after room-temperature aging, BH is also excellent, and intensity is high.In addition, erosion resistance is also excellent.
Among these examples, composition meets the example of [Zn] >=-0.3 [Mg]+4.5,0.2% yield strength after artificial age-hardening's process is more than 350MPa, when meeting example 2,4,6,8 ~ 12,16 ~ 19,21 of [Zn] >=-0.5 [Mg]+5.75,0.2% yield strength after artificial age-hardening's process is more than 400MPa simultaneously.
In contrast, each comparative example, as table 2,4, alloy composition departs from the scope of the invention, or manufacturing condition departs from preferred scope, therefore can not have both processibility and intensity.
The comparative example 22 ~ 25 of table 4, if the content of the alloy numbering 22 ~ 25, Zn of table 2, Mg is respectively in specialized range, but asynchronously meets the relation of [Zn] >=-0.3 [Mg]+4.5 and [Zn] >=-0.5 [Mg]+5.75.Therefore, although comprise equal thermal treatment, manufacture in preferred manufacturing condition, but do not meet by the organization prescribed of described DSC tracing analysis, work hardening exponent n value (10 ~ 20%) after room-temperature aging is more than 0.22, but 0.2% yield strength after artificial age-hardening's process, lower than 350MPa, can not have both processibility and intensity.
The comparative example 26 of table 4, the alloy numbering 26, Zn as table 2 departs from lower limit.Comparative example 27, if the alloy numbering 27, Zn of table 2 is higher than the upper limit.Comparative example 28, the alloy numbering 28, Cu as table 2 departs from lower limit.Comparative example 29, if the alloy numbering 29, Cu of table 2 is higher than the upper limit.Therefore, comprise equal thermal treatment, although manufacture in preferred manufacturing condition, do not meet by the organization prescribed of described DSC tracing analysis, work hardening exponent n value (10 ~ 20%) after room-temperature aging, lower than 0.22, can not have both processibility and intensity.In addition, its Zn of comparative example 27 is too much, and its Cu is very few for comparative example 28, and whichever erosion resistance is all poor.
The comparative example 30 ~ 32 of table 4, although the example aluminium alloy using the alloy numbering 2 of table 1, departs from the manufacture of preferred manufacturing condition scope.Comparative example 30 is the equal thermal treatment only having 1 time (being equivalent to secondary soaking).Its soaking temperature of the 1st time of comparative example 31 is too low.Its soaking temperature of the 2nd time of comparative example 32 is too low.Therefore, these equal heat-treat conditions depart from the comparative example of preferable range, do not meet the organization prescribed according to described DSC tracing analysis, work hardening exponent n value (10 ~ 20%) after room-temperature aging is lower than 0.22, or 0.2% yield strength after artificial age-hardening's process is lower than 350MPa, can not have both processibility and intensity.
The comparative example 33 of table 4, if the content of the alloy numbering 30, Zn of table 2, Mg is respectively in specialized range, but meets the relation of [Zn] >=-0.3 [Mg]+4.5 and [Zn] >=-0.5 [Mg]+5.75 simultaneously.Therefore, comprise equal thermal treatment, although manufacture in preferred manufacturing condition, but do not meet by the organization prescribed of described DSC tracing analysis, work hardening exponent n value (10 ~ 20%) after room-temperature aging is the level of 0.22, but 0.2% yield strength after artificial age-hardening's process, lower than 350MPa, can not have both processibility and intensity.
The comparative example 34,35,36 of table 4, the content as the alloy numbering 31,32,33, Mg of table 2 departs from lower limit.Therefore, even if such as satisfied [Zn] >=-0.3 [Mg]+4.5 is related to this two side with [Zn] >=-0.5 [Mg]+5.75, in addition, comprise equal thermal treatment, even if manufacture in preferred manufacturing condition, do not meet by the organization prescribed of described DSC tracing analysis yet.Consequently, the work hardening exponent n value (10 ~ 20%) after room-temperature aging is the level of 0.21 ~ 0.22, but 0.2% yield strength after artificial age-hardening's process is lower than 350MPa, can not have both processibility and intensity.
The comparative example 37,38,39 of table 4, the content as the alloy numbering 34,35,36, Zn of table 2 departs from the upper limit.Therefore, even if meet the relation of [Zn] >=-0.3 [Mg]+4.5 and [Zn] >=-0.5 [Mg]+5.75 simultaneously, in addition, comprise equal thermal treatment, even if manufacture in preferred manufacturing condition, do not meet by the organization prescribed of described DSC tracing analysis yet.Consequently, the work hardening exponent n value (10 ~ 20%) after room-temperature aging is the level of 0.21, can not have both processibility and intensity.In addition, these comparative examples Zn is too much, and erosion resistance is also poor.
The comparative example 40 ~ 43 of table 4, the content as the alloy numbering 37 ~ 40, Mg of table 2 departs from the upper limit.Therefore, even if meet the relation of [Zn] >=-0.3 [Mg]+4.5 and [Zn] >=-0.5 [Mg]+5.75 simultaneously, in addition, comprise equal thermal treatment, even if manufacture in preferred manufacturing condition, do not meet by the organization prescribed of described DSC tracing analysis yet.Consequently, the comparative example 40,41 that Zn is higher, the work hardening exponent n value (10 ~ 20%) after room-temperature aging is low reach 0.21 level, processibility and intensity can not be had both.In addition, the comparative example 42,43 that Zn is lower, the work hardening exponent n value (10 ~ 20%) after room-temperature aging is the level of 0.22, but 0.2% yield strength after artificial age-hardening's process is lower than 350MPa, can not have both processibility and intensity.In addition, these comparative examples Mg is too much, and erosion resistance is also poor.
According to above result, provable aluminium alloy plate of the present invention also has the meaning of the criticality of each important document of the present invention of SCC resistance for combine high strength and high ductibility (plasticity).
[table 1]
[table 2]
[table 3]
[table 4]
In detail and describe the present invention with reference to specific embodiment, but can not depart from the spirit and scope of the present invention and in addition various changes and modifications, this is for very clear practitioner.
The application based on the Japanese patent application (patent application 2013-051608) applied on March 14th, 2013, its content this with reference to and quote.
Utilizability in industry
As described above, the present invention can provide the automobile component of having both strength and plasticity and erosion resistance 7000 line aluminium alloy plates.Therefore, the present invention is also applicable to the Structural Materials for Automobile Parts contributing to the light-weighted vehicle frame of car body, beam column etc., also has the structured material etc. of other purposes in addition.
Claims (4)
1. a structural wood aluminium alloy plate, it is characterized in that, in mass % respectively containing Zn:3.0 ~ 6.0%, Mg:1.5 ~ 4.5%, Cu:0.05 ~ 0.5%, and the content [Mg] of the content of Zn [Zn] and Mg meets the relation of [Zn] >=-0.3 [Mg]+4.5, the Al-Zn-Mg line aluminium alloy plate formed that surplus is made up of Al and inevitable impurity, wherein, in differential scanning calorimetric analysis curve when making it room-temperature aging after solid solution and quench treatment are carried out to this plate, maximum endothermic peak temperature is less than 130 DEG C, and the maximum height of the exothermic peak of the temperature range of 200 ~ 300 DEG C is 50 more than μ W/mg, work hardening exponent n value (10 ~ 20%) is more than 0.22.
2. structural wood aluminium alloy plate according to claim 1, wherein, described aluminium alloy plate is in mass % also containing one or more in Zr:0.05 ~ 0.3%, Mn:0.1 ~ 1.5%, Cr:0.05 ~ 0.3%, Sc:0.05 ~ 0.3%.
3. structural wood aluminium alloy plate according to claim 1 and 2, wherein, described aluminium alloy plate is in mass % also containing Ag:0.01 ~ 0.2%.
4. structural wood aluminium alloy plate according to any one of claim 1 to 3, wherein, the content [Zn] of the Zn of described aluminium alloy plate and the content [Mg] of Mg meet the relation of [Zn] >=-0.5 [Mg]+5.75, and 0.2% yield strength after artificial age-hardening's process is more than 400MPa.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
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| JP2013051608 | 2013-03-14 | ||
| JP2013-051608 | 2013-03-14 | ||
| PCT/JP2014/056567 WO2014142199A1 (en) | 2013-03-14 | 2014-03-12 | Aluminum alloy plate for structural material |
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| Publication Number | Publication Date |
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| CN105143484A true CN105143484A (en) | 2015-12-09 |
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| CN201480011852.9A Pending CN105143484A (en) | 2013-03-14 | 2014-03-12 | Aluminum alloy plate for structural material |
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|---|---|
| US (1) | US20150376742A1 (en) |
| JP (1) | JP6273158B2 (en) |
| CN (1) | CN105143484A (en) |
| WO (1) | WO2014142199A1 (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN105506421B (en) * | 2015-12-31 | 2017-11-03 | 广西南南铝加工有限公司 | A kind of Al Zn Mg Aluminum Alloy Plate materials and preparation method thereof |
| CN110114498A (en) * | 2016-10-24 | 2019-08-09 | 形状集团 | Multistage aluminium alloy for producing vehicle part is formed and hot-working method |
| CN112210734A (en) * | 2019-07-11 | 2021-01-12 | 株式会社神户制钢所 | Method for producing 7000 series aluminum alloy member |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| TWI606122B (en) | 2013-09-30 | 2017-11-21 | 蘋果公司 | Aluminum alloys with high strength and cosmetic appeal |
| JP2015175045A (en) * | 2014-03-17 | 2015-10-05 | 株式会社神戸製鋼所 | Aluminum alloy sheet for constructional material |
| JP2016160515A (en) * | 2015-03-04 | 2016-09-05 | 株式会社神戸製鋼所 | Aluminum alloy sheet |
| EP3294917B1 (en) * | 2015-05-11 | 2022-03-02 | Arconic Technologies LLC | Improved thick wrought 7xxx aluminum alloys, and methods for making the same |
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| MX2019001802A (en) | 2016-08-26 | 2019-07-04 | Shape Corp | Warm forming process and apparatus for transverse bending of an extruded aluminum beam to warm form a vehicle structural component. |
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| KR102457529B1 (en) * | 2017-03-07 | 2022-10-21 | 엘지전자 주식회사 | Aluminum alloy |
| US11345980B2 (en) | 2018-08-09 | 2022-05-31 | Apple Inc. | Recycled aluminum alloys from manufacturing scrap with cosmetic appeal |
| JP2018204116A (en) * | 2018-08-27 | 2018-12-27 | 株式会社神戸製鋼所 | Aluminum alloy sheet |
| US11466352B2 (en) * | 2018-10-23 | 2022-10-11 | Novelis Inc. | Formable, high strength aluminum alloy products and methods of making the same |
| CN115572923B (en) * | 2022-09-09 | 2023-07-21 | 北京航空航天大学 | Method for obtaining aluminum alloy non-isothermal aging system based on in-situ resistance measurement |
Family Cites Families (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS60234955A (en) * | 1984-05-08 | 1985-11-21 | Kobe Steel Ltd | Manufacture of al-zn-mg alloy superior in stress corrosion cracking resistance |
| JPH0794701B2 (en) * | 1991-04-01 | 1995-10-11 | 住友軽金属工業株式会社 | Manufacturing method of aluminum alloy soft material for welded structure |
| JPH07252573A (en) * | 1994-03-17 | 1995-10-03 | Kobe Steel Ltd | Al-zn-mg-cu alloy excellent in toughness and its production |
| JP2002371333A (en) * | 2001-04-10 | 2002-12-26 | Nippon Steel Corp | Aluminum alloy sheet superior in formability, coating/ baking hardenability and corrosion resistance, and manufacturing method therefor |
| KR101333915B1 (en) * | 2005-02-01 | 2013-11-27 | 티모시 랭건 | Aluminum-zinc-magnesium-scandium alloys and methods of fabricating same |
| CN101484603B (en) * | 2006-07-07 | 2011-09-21 | 阿勒里斯铝业科布伦茨有限公司 | Aa7000-series aluminium alloy products and a method of manufacturing thereof |
| JP5083816B2 (en) * | 2007-11-08 | 2012-11-28 | 住友軽金属工業株式会社 | Al-Zn-Mg-Cu alloy extruded material excellent in warm workability, production method thereof, and warm worked material using the extruded material |
| JP5276341B2 (en) * | 2008-03-18 | 2013-08-28 | 株式会社神戸製鋼所 | Aluminum alloy material for high pressure gas containers with excellent hydrogen embrittlement resistance |
| JP5342201B2 (en) * | 2008-09-26 | 2013-11-13 | 株式会社神戸製鋼所 | Aluminum alloy plate with excellent formability |
| JP2010159489A (en) * | 2008-12-09 | 2010-07-22 | Sumitomo Light Metal Ind Ltd | Method for molding 7,000 series aluminum alloy material, and formed product molded by the same |
| JP5432632B2 (en) * | 2009-03-24 | 2014-03-05 | 株式会社神戸製鋼所 | Aluminum alloy plate with excellent formability |
| JP5431795B2 (en) * | 2009-06-05 | 2014-03-05 | 株式会社Ｕａｃｊ | Welding method of Al material |
| MX352255B (en) * | 2010-09-08 | 2017-11-16 | Alcoa Inc Star | Improved 6xxx aluminum alloys, and methods for producing the same. |
-
2014
- 2014-03-04 JP JP2014041713A patent/JP6273158B2/en not_active Expired - Fee Related
- 2014-03-12 CN CN201480011852.9A patent/CN105143484A/en active Pending
- 2014-03-12 US US14/767,096 patent/US20150376742A1/en not_active Abandoned
- 2014-03-12 WO PCT/JP2014/056567 patent/WO2014142199A1/en active Application Filing
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105506421B (en) * | 2015-12-31 | 2017-11-03 | 广西南南铝加工有限公司 | A kind of Al Zn Mg Aluminum Alloy Plate materials and preparation method thereof |
| CN110114498A (en) * | 2016-10-24 | 2019-08-09 | 形状集团 | Multistage aluminium alloy for producing vehicle part is formed and hot-working method |
| CN112210734A (en) * | 2019-07-11 | 2021-01-12 | 株式会社神户制钢所 | Method for producing 7000 series aluminum alloy member |
Also Published As
| Publication number | Publication date |
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| JP6273158B2 (en) | 2018-01-31 |
| WO2014142199A1 (en) | 2014-09-18 |
| JP2014198899A (en) | 2014-10-23 |
| US20150376742A1 (en) | 2015-12-31 |
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