CN102373353A - Aluminium Alloy Plate Having Excellent Forming Property - Google Patents
Aluminium Alloy Plate Having Excellent Forming Property Download PDFInfo
- Publication number
- CN102373353A CN102373353A CN2011102102237A CN201110210223A CN102373353A CN 102373353 A CN102373353 A CN 102373353A CN 2011102102237 A CN2011102102237 A CN 2011102102237A CN 201110210223 A CN201110210223 A CN 201110210223A CN 102373353 A CN102373353 A CN 102373353A
- Authority
- CN
- China
- Prior art keywords
- line
- alloy plate
- aluminium alloy
- aforementioned
- plate
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Images
Landscapes
- Metal Rolling (AREA)
Abstract
The invention provides an AL-Mg alloy plate having excellent forming property. The AL-Mg alloy plate has no problem of decreasing bending performance caused by age-hardening in room temperature, and low appearance of SS lines. When manufacturing the AL-Mg alloy plate formed by constitutions containing specific Mg and Cu, not only the cooling speed of quenching processing after solution treatment is controlled periodically, but also additional annealing conditions are controlled, thereby a plate tissue existing as Cu cluster, hard to disffuse as Mg, and hard to appear in a zigzag shape that indicated by a heat absorption peak height between 180 to 280 DEG C of a heating curve stating from the room temperature obtained through a differential thermal analysis of the alloy plate to suppress the appearance of the forcing and forming SS lines.
Description
Technical field
The Al-Mg line aluminium alloy plate that the present invention relates to have excellent formability.The said aluminium alloy plate of the present invention is hot rolling making sheet and cold rolling making sheet, refers to modified aluminium alloy plates such as having carried out solution treatment and quench treatment.In addition, also aluminium is called Al below.
Background technology
In recent years, from considering the viewpoint of global environment etc., the light-weighted social desirability of vehicles such as automobile improves day by day.In order to tackle this requirement, as car panel, the material of large-scale body panels (outside plate, inner panel) such as car bonnet, car door, roof especially except steel plate etc. the ferrous materials, is also being studied the application of aluminum alloy materials.
5000 line aluminium alloy plates of the JIS5052 alloy of Al-Mg system and JIS5182 alloy etc. (below be also referred to as Al-Mg be alloy sheets) are owing to ductility and excellent strength, so be used as the press molding starting material that these large-scale body panels are used all the time.
But; As patent documentation 1 etc. is disclosed; If to these Al-Mg is that alloy sheets is carried out tension test; Then have near the yield-point on the stress-strain curve, to produce surrender tensile situation, also have in addition under the higher dependent variable (for example tensile elongation is more than 2%) of the ratio that has surpassed yield-point, produce the situation of spination or stair-stepping zig-zag (vibration) on the stress-strain curve.Phenomenon on these stress-strain curves causes the generation of so-called tension strain (Stretcher Strain) (following also note is made the SS line) in the press molding of reality; This is for the large-scale body panels as molding; Especially the very important outside plate of outward appearance becomes the very big problem of losing commodity value.
This SS line such as known said being divided into: the so-called random line that takes place at the lower position of dependent variable like the irregular banded apperance of flamboyancy, and in dependent variable than the parallel bands of higher position with the parallel ribbon apperance that becomes 50 ° mode with respect to draw direction approximately and take place.Known the former random line is stretched by yield-point and causes that the latter's parallel bands is caused by the zig-zag (vibration) on the stress-strain curve of record in the paragraph 0004 in addition.
The method of these SS lines of various eliminations has been proposed all the time.For example, as main method, known to have Al-Mg be that the crystal grain of alloy sheets is adjusted to thick method to a certain degree.But, even if the inflation method of this crystal grain in the SS line, is not effective in the generation that prevents parallel bands like record in the paragraph 0004.In addition, too mutually big if crystal grain becomes, then be created in table in the press molding on the contrary and the coarse problem that waits other of last appearance.
In addition; Eliminate the method for SS line as other; Also known have a following method: before the press molding to large-scale body panels; Be that the modified material that O material (soft material) or the T4 of alloy sheets handles material etc. applies processing (preprocessing) such as skin-pass processing or leveling processing to Al-Mg in advance, and some strains (prestrain) are provided in advance.But; Even if such preprocessing method when degree of finish becomes too high, also is easy to generate the zig-zag (vibration) on the stress-strain curve of putting down in writing in the paragraph 0004; Even when the press molding of reality, also be related to the generation of the clearly parallel bands of wide cut degree easily.Therefore, the degree of finish of preprocessing is had very big restriction, can't stably prevent the generation of random line when reducing degree of finish.Therefore, in this preprocessing method, owing to the optimal process degree of the generation that prevents parallel bands is opposite with the optimal process degree that prevents random line generation, so can't prevent the two simultaneously.
Relative therewith, in aforesaid patent documentation 1, the few Al-Mg of generation generation, the SS line that has also suppressed the parallel bands of wide cut degree when having proposed to suppress the generation of random line is the method for making of alloy sheets.Particularly, be that the milled sheet of alloy is implemented to carry out the cold working as the preprocessing under the specified conditions afterwards with the solid solution under the specified conditions of cool quickly, quench treatment to Al-Mg, implement the final annealing under the specified conditions again.The soleplate of the coarse grain that to obtain not existing in fact average crystal grain then directly be below the 55 μ m and 150 μ m are above.
Here; Also being known in Al-Mg is in the alloy sheets field; Though may not directly mention the generation that suppresses the SS line, the position of the endothermic peak of heating curve that the thermal distortion that will utilize differential thermal analysis (DSC) to measure alloy sheets obtains, that begin from room temperature and its height are as the index of the press molding property raising of this plate.
For example, having proposed in the patent documentation 2, is the endothermic peak height of the specific position of heating curve that the differential thermal analysis (DSC) of alloy sheets obtains, that begin from room temperature through utilizing Al-Mg, as the index of press molding property raising.This differential thermal analysis (DSC) in the field of aluminium alloy plate by general; Its reason is; In little structure observations such as TEM, can not differentiate and discern and can not directly prove under the situation of existence influential group bunch (intermetallic compound), the endothermic peak position of the specific position through aforementioned heating curve and highly come indirect proof to have or not structural difference such as group bunch or as index to characteristic.
In this patent documentation 2; The Al-Mg that casts the high Mg that surpasses 8 quality % of manufacturing through double-roll type continuously is in the alloy sheets; Making the endothermic peak height between 50～100 ℃ of the heating curve that begins from room temperature is more than the 50.0 μ W, makes the raising of press molding property thus.This follows, this endothermic peak height represent Al-Mg be called as in the alloy sheets tissue β phase the Al-Mg series intermetallic compound have a form (stability of solid solution, precipitation state).
But, in the very important outside plate of nearest large-scale body panels, especially outward appearance, surface texture require level strict more, even these patent documentations 1 or patent documentation 2, it also is inadequate suppressing the countermeasure that the SS line takes place for such requirement.For example, in the patent documentation 1, make stair-stepping zig-zag slight (being documented in the stepped zigzag explanation of evaluation of embodiment of patent documentation 1) as far as possible, therefore can not suppress parallel bands fully as one of SS line.
To this, in the patent documentation 3, the problems referred to above are improved, and proposed not only to suppress the generation of random line, simultaneously also suppress the generation of parallel bands, and suppressed the Al-Mg line aluminium alloy plate that the press molding of car panel etc. is had excellent formability of SS line.In the document 3, for Al-Mg line aluminium alloy plate, especially make it contain Zn 0.1～4.0%, further improve the critical strain amount (ultimate strain amount) that zig-zag takes place.That is,, make the amount of formation increase, further improve thereby make by these increase effects of rolling into a ball bunch ultimate strain amounts that cause as the group's bunch (ultra tiny intermetallic compound) that forms by Al and Mg of the group that comprises Zn etc. bunch through the containing, add of Zn grade in an imperial examination 3 elements.And, suppress zig-zag thus, and suppress to result from this parallel bands, suppress the generation of SS line.
This group that comprises Zn etc. can not be differentiated and discerned in the little structure observations such as FE-TEM about 100,000 times bunch for the size below the Nano grade, can not directly prove its existence.Therefore; Even this patent documentation 3; Also same with aforementioned patent document 2, to having or not the structural difference of group's bunch grade, will utilize differential thermal analysis (DSC) to measure the endothermic peak position and the index of height of specific position of the aforementioned heating curve of thermal distortion as tissue difference.Particularly, the essential factor for the endotherm(ic)peak of aforementioned DSC heating curve between 100～150 ℃ bunch can be inferred by the Al-Mg group that comprises Zn etc., and this endothermic peak height is more than the 200.0 μ W (microwatt).
But the opinion according to inventor etc. in Al-Mg line aluminium alloy plate, when shown in this patent documentation 3, containing Zn in a large number, has produced following new problem: be easy to generate the age hardening in room temperature.This can infer for since in the patent documentation 3 as suppressing wanting to generate and utilizing group's bunch (ultra tiny intermetallic compound) that Zn forms to produce in room temperature easily to cause of excellent stratagem that the SS line takes place.That is, Zn content is many more, at room temperature forms aforementioned group bunch amount and increases more, as a result of can infer at room temperature age hardening excessively to cause.Usually Al-Mg line aluminium alloy plate is not to make the back in aluminium sheet plant to be configured as large-scale body panels etc. in automobile factory, and above interval several weeks is generally arranged usually at once.Therefore, for example the manufacturing of slave plate is through after 1 month, when being configured as large-scale body panels etc., producing age hardening meeting remarkable break-throughs, toughness and press molding property and hindered so new (other) problem on the contrary.
As known said, bunch Al-Mg-Si age hardening, the thermal treatment type who is easy to generate under the room temperature of group that forms with reason Mg, Si is that (6000 are) aluminium alloy plate is compared, and the age hardening at room temperature of Al-Mg line aluminium alloy plate is difficult to produce usually.But of patent documentation 3, even such Al-Mg line aluminium alloy plate, more for a long time, unusual is equally also to show the age hardening under the room temperature with 6000 line aluminium alloy plates at Zn content.
TP in the past
Patent documentation
Patent documentation 1: japanese kokai publication hei 7-224364 communique
Patent documentation 2: TOHKEMY 2006-249480 communique
Patent documentation 3: TOHKEMY 2010-77506 communique
Summary of the invention
In view of above problem; The object of the present invention is to provide do not produce degradation new problem under the toughness that brings by the age hardening under the room temperature, not only suppress by aforementioned surrender stretch the random line that causes generation, also suppress the generation of parallel bands simultaneously; Can suppress the SS line and take place, make Al-Mg line aluminium alloy plate the press molding property raising of car panel.
In order to reach this purpose; Will being intended to of the aluminium alloy plate that has excellent formability of the present invention: it is for to contain Mg:2.0～6.0%, Cu in quality %: surpass 0.3% and be below 2.0%, surplus is the Al-Mg line aluminium alloy plate of Al and unavoidable impurities; The thermal distortion of utilizing differential thermal analysis to measure this this plate obtain from the heating curve that room temperature begins, the endothermic peak height of the maximum between 180～280 ℃ is more than the 5W/g.
The inventor's etc. opinion is following: as the element of the inhibition effect with the generation of SS line, select Cu to replace being easy to generate the Zn of the age hardening under the room temperature.That is,, just can not produce the age hardening under the such room temperature of Zn, have the inhibition effect that the SS line takes place if be Cu.
But the inventor etc. also have following opinion: also exist the generation that does not have the SS line to suppress the situation of effect even contain Cu equally, even the Al-Mg line aluminium alloy plate of for example identical Cu content, the inhibition effect that the SS line is taken place also has bigger difference.Can consider from above-mentioned situation, singly be not to contain Cu, and the difference of the existence (structural state) of the Cu in the Al-Mg line aluminium alloy plate, and the generation state of SS line is also had bigger influence.
For the existence of this Cu further the result of research be that the amount of the fine group of (novel) Cu that the inventor's suppositions of etc.ing is specific bunch (be main fine group bunch) with Cu and have or not existence is a greater impact the inhibition effect of SS line generation.
But in fact the existence of the group of this Cu bunch can not directly be assert.For example, to containing Cu and can generating the Al-Mg line aluminium alloy plate of Cu modified (afterwards stating) group bunch, that implemented specified conditions,, do not find the existence of the group bunch of this Cu even use 100,000 times FE-TEM (transmission electron microscope) to carry out structure observation yet.In other words, the group bunch that can infer this Cu and the Al-Mg series intermetallic compound of aforementioned patent document 2,3 etc. are identical, are the microsizes below the Nano grade.Therefore, adopt, be not sure of the group bunch of this Cu as the SEM of common structure observation method, the analytical procedure of TEM.
In view of the above, inventor etc. studies the existence of group that can not this novel Cu of indirect proof bunch.Find then; To containing Cu and having implemented the modified Al-Mg line aluminium alloy plate of specified conditions; That the thermal distortion of utilizing differential thermal analysis (DSC) to measure this plate obtains, from the heating curve (DSC heating curve) that room temperature begins, between 180～280 ℃, have tangible endotherm(ic)peak.And the height of endothermic peak that should maximum is 5W/g when above, has the inhibition effect that the SS line takes place.
Can be clear and definite be that the endothermic peak between 180～280 ℃ of this DSC heating curve is to be some group's bunch decision of existing in the tissue of alloy sheets by Al-Mg, and the height of this endothermic peak is by the amount decision of some group bunch.And; Of the back; Endotherm(ic)peak between 180～280 ℃ of this DSC heating curve; Only occur in the modified Al-Mg line aluminium alloy plate of specified conditions containing Cu and implemented, though do not contain Cu Al-Mg line aluminium alloy plate, or contain in the modified Al-Mg line aluminium alloy plate that Cu do not implement specified conditions and do not occur.Therefore, clearly the endotherm(ic)peak between 180～280 ℃ of this DSC heating curve at least by the group relevant bunch decision with Cu.
As a result, inventor waits endotherm(ic)peak between 180～280 ℃ that recognize this DSC heating curve to represent to exist to have the amount of group bunch and this group bunch of the novel Cu of the inhibition effect that the SS line takes place.And; Though the endotherm(ic)peak between 180～280 ℃ of the group of this Cu bunch and even DSC heating curve details in the back; But at present clearly in the scope; Modified through the rolling plate that forms in the manufacturing process of plate only, that is, only the control of the speed of cooling through to the quench treatment after the solution treatment time and specific modified (processing) that the additional anneal under 100 ℃ the specified conditions makes up that surpass afterwards generate.The temperature that the control of the speed of cooling when this quench treatment does not depart from top condition or this additional anneal is low excessively, or modified condition departs from when not implementing additional anneal etc. situation under; Even for example contain Cu equally; Do not produce the endotherm(ic)peak between 180～280 ℃ of DSC heating curve yet, and do not have the inhibition effect that the SS line takes place.Therefore, in this case, infer group's bunch not generation of the specific Cu of inhibition effect easily with the generation of SS line.
The present invention is through using the Cu of the age hardening under the room temperature that does not produce aforesaid Zn and so on; Control the tissue of Al-Mg line aluminium alloy plate thus; And hinder free Mg atom to move to transposition; Tissue as Mg diffusion difficulty is difficult to produce saw-toothed projections, can obtain the excellent alloy of SS line property.
Description of drawings
Fig. 1 is the explanatory view of the heating curve that begins from room temperature that obtains of expression differential thermal analysis aluminium alloy plate of the present invention.
Embodiment
Below about embodiment of the present invention, each important document is specified.
(tissue)
To carry out the heating curve (DSC heating curve) that begins from room temperature that differential thermal analysis (DSC) obtains to the Al-Mg line aluminium alloy plate of the Cu of containing of the present invention is shown in Fig. 1 with heavy line.The embodiment table 1 that the DSC heating curve (heavy line) of this Fig. 1 is stated after being, 2 invention example 4.In addition, in the Fig. 1 that merges, as comparative example, the DSC heating curve that does not contain the Al-Mg line aluminium alloy plate of Cu is also represented with fine rule.The embodiment table 1 that the DSC heating curve (fine rule) of this Fig. 1 is stated after being, 2 comparative example 14.
The DSC heating curve (heavy line) of this invention example 4 was curve stably before 180 ℃ of the temperature of transverse axis, not below the endotherm(ic)peak of depression (protruding downwards).But begin to descend downwards after surpassing 180 ℃; Between 180～280 ℃; As the peak that can obviously differentiate with respect to aforementioned curved portion stably, exist in the endotherm(ic)peak (summit, top) of below depression, and this endotherm(ic)peak has certain endothermic peak height.When the DSC heating curve (fine rule) of the existence of the endothermic peak between these 180～280 ℃ and aforementioned comparative example 14 compares, then more obvious.In the DSC heating curve (fine rule) of comparative example 14, between 180～280 ℃, do not have the aforementioned endotherm(ic)peak that can differentiate, through transverse axis 100～300 ℃ all only have curve stably.Additional disclosure once, surpassing 300 ℃ position at transverse axis, to have the bigger exothermal peak of protrusion up be that Al-Mg-Cu from S ' phase is the distinctive peak value of alloy, all same common existence in the DSC heating curve of comparative example.But can consider, the peak of invention example 4 than big former in the peak of comparative example because the existence of aforementioned group bunch promotes the formation of aforementioned S ' phase.
So-called this endothermic peak height is meant the height (W/g) that is present in the longitudinal axis between 180～280 ℃, aforementioned endothermic peak.As far as this endothermic peak height, the position of measuring 150 ℃ of temperature proofread and correct make caloric receptivity and thermal value be 0 after, obtain the maximum endothermic peak height (W/g) that becomes of 180～280 ℃ of scopes.At this moment, measuring from the heat flow (Heat Flow) of the longitudinal axis of the heating curve (differential scanning calorimeter curve) that begins from room temperature is 0.00 reference line, highly becomes the distance (W/g) of the endothermic peak of maximum to it.Additional disclosure once; The scope of the transverse axis of aforementioned endotherm(ic)peak be 180～280 ℃ also with following situation as benchmark: be 0.00 reference line par from the heat flow of DSC heating curve (heavy line) and the longitudinal axis; The position that beginning descends downwards is near 180 ℃, the DSC heating curve (heavy line) behind the peak of aforementioned below depression to the top rise and with the heat flow of the longitudinal axis be near position that 0.00 reference line becomes par is 280 ℃.
In order to make the SS line property raising of Al-Mg line aluminium alloy plate among the present invention, the height of the endotherm(ic)peak between 180～280 ℃ of this DSC heating curve is more than the 5W/g.Can infer; Al-Mg line aluminium alloy plate of the present invention contains Cu and has implemented the modified of specified conditions; Endotherm(ic)peak between 180～280 ℃ of this DSC heating curve representes with Cu to be the existence of main fine group bunch indirectly, and the height of this endothermic peak representes with Cu to be the amount of main fine group bunch.Therefore; Can infer, the endothermic peak between 180～280 ℃ of short of this DSC heating curve, then not existing with Cu is main fine group bunch; As long as the height of this endothermic peak, then representes with Cu to be that the amount of main fine group bunch is too few less than 5W/g.
As after the embodiment that states; As long as the height of the endothermic peak of the maximum between these 180～280 ℃ is more than the 5W/g, can be that the ε c (ultimate strain amount) of the critical strain amount that produces of the zig-zag on the stress-strain curve of stretching experiment of alloy sheets brings up to more than 8%, more preferably brings up to more than 10% then with Al-Mg.On the other hand; Endothermic peak between 180～280 ℃ of short of this DSC heating curve; Perhaps, can not suppress the SS line and take place as long as the age hardening ground that the height of this endothermic peak less than 5W/g, then can't not produce under the room temperature improves the critical strain amount that produces the zig-zag generation.Explain that the higher limit of the height of the endothermic peak of the maximum between these 180～280 ℃ does not have special qualification,, be set at about 20W/g if when the limit made etc. is considered.In addition, the upper limit of aforementioned critical strain amount ε c (ultimate strain amount) also limits especially, if from the limit made etc., be set at about 20%.
Here, for " μ W " (microwatt) stipulated in the aforementioned patent in advance only stipulated heat, the unit " W/g " of the height of this endothermic peak (longitudinal axis of Fig. 1) carried out normalized with the weight (g) of measuring test portion.That is, W is last to have " μ " or do not have, and only is the change (10-6) of the figure place of numerical value, when unit only uses " μ W " regulation, the problem of variation of heat of the variation of test portion weight can take place to consider to be accompanied by.Therefore, among the present invention, for the precision that improves mensuration and reproducibility, more make the regulation of the height of endothermic peak clear, adopted the ratio " W/g " of heat divided by test portion weight.In the differential thermal analysis of aluminum areas, the unit "W / g" rather than "μW" more general, recording (use), for example, light metal Volume 59 No. 8 (2009) 439 - 443 "Copper を Add shi ta Al-Mg-Si Alloys bell a black Hana a cloth of ni and ぼ す natural aging と high I
Aging Full Movies
(added copper Al-Mg-Si alloy bake hardening involves preparation of natural aging and high temperature aging effect) "; Light Metals Volume 56 No. 11 (2006) 673 ~ 679" Al-3% Mg-1% Cu Alloys aging effect and shareholders' Nano precipitated
ni and ぼ す Ag Add Full Movies
(Al-3% Mg-1% Cu alloy hardening and nano precipitated organizations involved in Ag added effect) "; Light Metals 52, No. 2 (2002) 64 ~ 70" Al-Cu Alloys with initial decomposition ni concise analyzes on the micro add elements Full Behavior and Others Toray a mini uni computer Shin Shin Yong (Al-Cu alloy phase decomposition of the initial trace elements added initiatives and Computer Simulation) ", etc..
Can infer; The SS line that produces during the press molding of Al-Mg line aluminium alloy plate, the parallel bands that is especially caused by the zig-zag on the stress-strain curve (vibration) are to fix repeatedly and break away from and produce through being solid-solubilized in free Mg atom pairs transposition in the aluminum matrix.Below, the SS line of the parallel bands that is caused by the zig-zag on the stress-strain curve (vibration) also simply is called SS line or SS line (zig-zag).Relative therewith; Can infer; As long as the group through the specific modified Cu of the present invention that generates bunch is present in the tissue of Al-Mg line aluminium alloy plate; Because the free Mg atom when having hindered the distortion of the plate that is caused by press molding moves to transposition, take place so can suppress SS line (zig-zag).And the group of Cu that uses among the present invention or Cu bunch produces the age hardening under the such room temperature of Zn hardly.
Can infer with this Cu to be that master's the Al-Mg series intermetallic compound etc. of group bunch and aforementioned patent document 2 is identical, be the size below the Nano grade.Therefore, can not differentiate and discern in little structure observation of the FE-TEM about 100,000 times etc., thereby can not directly prove its existence.Therefore, among the present invention, be not directly to limit these group'ss bunch (tissue), but limit the endothermic peak between 180～280 ℃ of aforementioned DSC heating curve.
But, among aforementioned patent document 2,3 and the present invention, be identical if become the intermetallic compound of group bunch, the endotherm(ic)peak of then inevitable DSC heating curve is also identical.Just because of these groups bunch, the composition of intermetallic compound etc. are different each other, so the endotherm(ic)peak of DSC heating curve is different.
In addition, like the DSC heating curve of Fig. 1, in the Al-Mg line aluminium alloy plate of the present invention, there is not in the aforementioned patent document 3 endotherm(ic)peak between 100～150 ℃ of DSC heating curve of regulation.
Additional disclosure once; This patent documentation 3; Also same with aforementioned patent document 2; To the difference that waits tissue that has or not of group bunch, will utilize differential thermal analysis (DSC) even the Al-Mg line aluminium alloy plate identical also different index of each self-organization in the endothermic peak position of specific position in the aforementioned heating curve of the thermal distortion of assay plate with conduct highly.In view of the above, the endotherm(ic)peak of the aforementioned DSC heating curve of the Al-Mg series intermetallic compound of aforementioned patent document 2,3 only between 50～100 ℃, or 100～150 ℃ between so lower TR of ratio the present invention.Relative therewith, the endothermic peak of aforementioned DSC heating curve of the present invention is the endotherm(ic)peak between 180～280 ℃ than above-mentioned higher TR, even if also can be by obvious difference in the TR of endotherm(ic)peak.
Promptly; As far as Al-Mg line aluminium alloy plate of the present invention, do not have in the aforementioned patent document 2 group that comprises Zn etc. bunch of regulation in Al, Mg group bunch of regulation and the aforementioned patent document 3, as shown in Figure 1; There is not the endotherm(ic)peak in these specified temperature zones yet; And, there is not the endotherm(ic)peak between 180～280 ℃ of DSC heating curve among the present invention among Fig. 1 separately of these patent documentations 2,3, so these patent documentations 2,3 do not have group of the present invention bunch yet.
In these patent documentations 2,3, contain Cu of the present invention below 1.0% as element optionally, the impurity Zn that contains trace that allows among the present invention.But; Even if it is for example identical to know that the one-tenth that comprises these Cu is grouped into; Also owing to the difference of the existence of their groups each other bunch is organized difference; The inhibition effect that takes place of SS line not only, and be associated with want among the present invention do not produce the so bigger property difference of age hardening under the room temperature.
The difference of tissue so each other (group bunch) also can prove from the difference of the method for making of each other plate.The Al-Mg line aluminium alloy plate that contains the patent documentation 3 of Zn; As according to the invention; Carry out chilling, carry out slow cooling though the speed of cooling during to the quench treatment after the solution treatment is controlled at high-temperature area at low-temperature region, yet, afterwards as according to the invention; Do not carry out additional anneal (artificial aging processing) above under 100 ℃ the temperature, but only optionally carrying out the additional anneal under 50～100 ℃ low temperature.In the low like this additional anneal temperature, do not generate Cu of the present invention group bunch, and shown in Figure 1 like patent documentation 3, do not have the endotherm(ic)peak between 180～280 ℃ of DSC heating curve.
In addition; The Al-Mg line aluminium alloy plate that contains Zn, the Cu patent documentation 2 below 1.0% as selective element; As according to the invention; Speed of cooling during quench treatment after not controlling solution treatment (final annealing) in 2 stages of the slow cooling that is being mingled with low-temperature region, and only to 500～300 ℃ TR with 10 ℃/carry out chilling more than the S.For this speed of cooling, do not implement to be generally productivity is not reduced and carry out from below 100 ℃ to the slow cooling of room temperature.Therefore, but infer in this patent documentation 2, though clearly do not put down in writing the speed of cooling below 100 ℃, but be generally speed of cooling above about 5 ℃/S.And in this patent documentation 2, only selectivity is carried out the additional anneal under 50～120 ℃ the temperature afterwards.Modified condition does not so generate Cu of the present invention group bunch, and is of Fig. 1 of patent documentation 3, do not have the endotherm(ic)peak between 180～280 ℃ of DSC heating curve.
From such fact, endothermic peak height between 180～280 ℃ of the DSC heating curve in the provable Al-Mg line aluminium alloy plate of the present invention be with aforementioned patent document 3 in the novel group bunch of bunch different other of the group of regulation in the group that has comprised Zn etc. bunch and the aforementioned patent document 3 of regulation.
Aforementioned patent document 2,3 and the present invention are different tissues and the different groups bunch situation as object also can be proved from the effect difference that both reach.As previously mentioned, can not fully suppress the generation of stretcher strain markings in the patent documentation 2.In addition, in the patent documentation 3, can not suppress the room-temperature aging sclerosis.Relative therewith, among the present invention, not only suppressed the room-temperature aging sclerosis, and can suppress simultaneously by surrender the stretch generation of the random line cause and the generation of the parallel bands that is associated with zig-zag on the stress-strain curve.
The present invention uses raw material plate as car panel; Especially under the situation that the surface texture requirement level in the very important outside plate of outward appearance becomes stricter; Perhaps the shaping that is fabricated onto these panels of slave plate needs under the situation of time; Not only can suppress room-temperature aging sclerosis during this period, and SS line property is excellent.That is, not only suppress room-temperature aging sclerosis, and the generation of the random line that can suppress simultaneously to cause by the surrender extensibility with stress-strain curve on the generation of the relevant parallel bands of zig-zag.This result can improve performance and the characteristic of car panel with raw material plate greatly.
(chemical ingredients composition)
It is to process that to be equivalent to as Al-Mg be the duraluminum that the JIS 5000 of alloy is basically that the chemical ingredients of aluminum alloy hot rolling plate of the present invention is formed.Explain the % of the content of each element representes it all is the meaning of quality %.
The present invention especially need satisfy all characteristics such as press molding property, intensity, weldableness, erosion resistance as car panel with raw material plate.Therefore milled sheet of the present invention, even if in 5000 line aluminium alloys, also process in quality % and contain Mg:2.0～6.0%, Cu: surpass 0.3% and be below 2.0%, surplus is the Al-Mg line aluminium alloy plate of Al and unavoidable impurities.Explain that constituent content all is quality %.
This Al-Mg line aluminium alloy plate; As other impurity element, allow to contain respectively below the Fe:0.5% in quality % (comprise 0%), B (boron) that (comprising 0%) below (comprising 0%), the Ti:0.05% below (comprising 0%), the Zr:0.1% below (comprising 0%), the Cr:0.1% below (comprising 0%), the Mn:0.5% below the Si:0.5%, this Ti that in the scope less than the content of Ti, encloses sneak into easily.
And then, as previously mentioned,, be that the age hardening that produces under the room temperature makes the reason of toughness, the decline of press molding property, so do not contain as far as possible owing to Zn as impurity element.In addition,, preferably be restricted to below 0.6%, more preferably be restricted to below 0.1% if, be restricted to less than 1.0% in quality % even if contain.
Mg：2.0～6.0％
Mg improves the work hardening ability, guarantees as car panel with the needed intensity of raw material plate, weather resistance.In addition, make material viscous deformation and improve the fracture crack limit equably, improve plasticity.The content of Mg was less than 0.5% o'clock, and intensity, weather resistance become insufficient.On the other hand, the content of Mg surpasses at 7.0% o'clock, and the manufacturing of plate becomes difficulty, and during press molding, intercrystalline failure takes place easily on the contrary, and press molding property significantly descends.Therefore, the content of Mg is made as 2.0～6.0%, preferably is made as 2.4～5.7% scope.
Cu: surpass 0.3% and be below 2.0%
Can infer that Cu is different with Zn, form the fine group bunch that is the main body with aforesaid Cu, can not make the sclerosis of plate generation chamber warm hardening, the generation of the SS line when suppressing press molding.Cu too is less than 0.3% when following, and the performance that the generation of the SS line during press molding suppresses effect becomes insufficient.In addition, be that the growing amount of group bunch of main body is also not enough with Cu.On the other hand, if the content of Cu surpasses 2.0 quality %, the thick crystal precipitate and the generation quantitative change of precipitate are many, become the destructive starting point thus easily, make the decline of press molding property on the contrary.The content of Cu is made as and surpasses 0.3% and be the scope below 2.0%, is preferably in 0.4～1.9% the scope.
Cu/Mg：0.05～1
Here, in order to bring into play the aforementioned additive effect of Cu, Cu is with respect to the ratio of the content of Mg: Cu/Mg is made as 0.05～1.This than higher limit and lower value be between the higher limit of each other aforementioned content and the lower value or the ratio between preferred higher limit and the lower value calculate, preferably be made as 0.08～0.8 scope.
Other element:
Other element illustration has Fe, Si, Mn, Cr, Zr, Ti etc.These elements are to contain the impurity element more than the quantitative change along with (with respect to the ratio of aluminium ingot (ア Le ミ ウ system ground the gold)) increase of aluminium alloy scrap amount as the fusion raw material.Promptly; From the viewpoint of utilizing again of Al alloy sheets,, be not only the high purity aluminium ingot as the fusion raw material; And 5000 when to be alloy with other Al alloyed scrap material, low-purity Al ingot etc. use as the fusion raw materials, and the mixed volume of these elements (content) must increase.And, be reduced to these elements for example that detectability can raise with inferior cost own, need to allow containing to a certain degree.Aspect this, allow not contain below the Fe:0.5% with quality % score (comprise 0%), (comprising 0%) below (comprising 0%), the Ti:0.05% below (comprising 0%), the Zr:01% below (comprising 0%), the Cr:0.1% below (comprising 0%), the Mn:0.5% below the Si:0.5%, in content range, enclose this Ti and the B (boron) that sneaks into easily less than Ti.
(method of manufacture)
Method of manufacture to plate of the present invention is carried out following specifying.
Among the present invention, before the rolling process to solution treatment, contain about 5182,5082,5083,5056 etc. Mg4.5%, can utilize based on being shaped with Al-Mg is that the method for manufacture of the common manufacturing process of alloy is made.That is, make through casting (DC casting, Continuous casting process), the thermal treatment that homogenizes, each common manufacturing process of hot rolled, becoming thickness of slab is the aluminum alloy hot rolling plate of 1.5～5.0mm.Can be sheet in this stage, Yi Bian can also be before cold rolling or cold rolling optionally carry out the process annealing more than 1 time or 2 times in midway, Yi Bian carry out cold rollingly again, becoming thickness of slab be the sheet of the cold-reduced sheet below the 1.5mm.
Solution treatment:
In order to become plate,, at first, follow the solution treatment and the quench treatment of heating rapidly and cool quickly for these hot-rolled sheets or the cold-reduced sheet of the required thickness of slab that obtains like above operation with tissue of the present invention.Carried out such solution treatment and quench treatment material, be that T4 handles material, compare the balance excellence of intensity and plasticity with the annealed material at intermittence that is accompanied by heating and cooling more slowly.
Here, the fit value of solid solution temperature is according to concrete alloy composition and difference, need be made as more than 450 ℃ in the scope below 570 ℃.In addition, maintenance need be made as in 180 seconds (3 minutes) under this solid solution temperature.Solid solution temperature is during less than 450 ℃, and the solid solution of alloying element becomes insufficient, might intensity and decline such as ductility.On the other hand, if solid solution temperature surpasses 570 ℃, thickization of excessive grain then, plasticity descends and the problem of the coarse generation when being shaped thereby become.If the hold-time under the solid solution temperature surpasses 180 seconds in addition, produce that plasticity that excessive thickization by crystal grain cause descends and the problems such as coarse generation when being shaped.
Quench treatment:
Speed of cooling during quench treatment after the solution treatment need be in the chilling of high-temperature area, these 2 stages of slow cooling of low-temperature region.At first, in the chilling of high-temperature area, the temperature of plate is more than 5 ℃/second from the speed of cooling of (scope) between the solid solubility temperature to 100 ℃.This speed of cooling is during less than 5 ℃/second, in the process of cooling especially at high-temperature area, generate thick precipitate, the growing amount of group bunch tails off, thereby the effect that suppresses the generation of SS line reduces.Therefore, even if after apply preprocessing and annealing and process soleplate, still the SS line might take place.
As plate of the present invention, behind this chilling, the temperature of plate from below 100 ℃ to the speed of cooling of (scope) the low-temperature region of room temperature be for make 180～280 ℃ of aforementioned DSC heating curve between the endothermic peak height be more than the 5W/g, therefore important.The cooling of this low-temperature region needs slow cooling, makes from the speed of cooling to room temperature below 100 ℃ slowly to cool off with the speed of cooling below 1 ℃/minute.Be used for the not special restriction of lower value of slow cooling, but consider preferred more than 0.01 ℃/minute from the efficient of production process.
According to such quenching conditions, can infer that aforementioned Al-Mg is in the tissue of alloy sheets, generating with the Cu atom is the aggregate (roll into a ball bunch) of master's atom.Therefore, if make the chilling speed under the aforementioned high-temperature area of being cooled to of this low-temperature region or surpass aforementioned 1 ℃/minute speed of cooling etc. and make this quenching conditions improper, even if the additional anneal of stating after then carrying out still can not prevent the generation of SS line really.Promptly; If can infer that this quenching conditions is improper, even the additional anneal of stating after then carrying out, the endothermic peak height between 180～280 ℃ of aforementioned DSC heating curve is not more than the 5W/g; Only being positively can prevent the amount of the generation of SS line, is main group bunch and can not generate with Cu.That is, when the cooling of this low-temperature region surpasses 1 ℃/minute speed of cooling, even after apply prestrain and become soleplate and also the SS line might take place.
Apply prestrain:
In order to process plate of the present invention, in order to eliminate the especially random line of SS line of in the past, after having implemented these solution treatment, quenching, again plate is applied the cold working (preprocessing) of prestrain.These are through skin-pass for example, cold rolling or utilize the alternating bending processing of roller type leveler to wait and carry out.So the increase of adjustment yield point value partly makes it to be in the specific scope, carries out the cold working as preprocessing, and the surrender tensile when positively suppressing press molding thus takes place, and can positively prevent the SS line, particularly the generation of irregular grain.Therefore, in the Al-Mg line aluminium alloy plate of the present invention, preferably to carry out press molding again after certain prestrain be prerequisite to apply in advance.In addition, apply such prestrain, the shape control and the residual stress that also become the plate after aforementioned solution treatment, the quench treatment are removed.
The applied amount of prestrain and yield point value increase and somely so existing generally are used to prevent that irregular grain from taking place and the preprocessings carried out are equal to and get final product.For example, utilizing in alternating bending processing that roller type leveler carries out etc. in the skin-pass in cold working, the cold rolling or cold working applies working modulus and is about 1～5% prestrain.Through applying such prestrain (cold working), can in material, import a large amount of deformation bands energetically, can positively prevent to surrender tensile and take place, even be the generation that also can stably prevent irregular grain in the alloy sheets at the fine Al-Mg of crystal grain.Under the high working modulus more than it, under the situation of the such method of manufacture of the present invention who considers not carry out final annealing, ductility, plasticity are reduced, so not preferred.
Additional anneal:
Among the present invention, after this preprocessing, be heated to and surpass 100 ℃ and be that the additional anneal or the artificial aging of the temperature below 200 ℃ handled.In other words, among the present invention, do not carry out heating, the such final annealing of cool quickly rapidly more than 250 ℃ and under the temperature about less than 550 ℃ that are carrying out after this preprocessing usually.
When carrying out additional anneal processing (artificial aging processing); As plate of the present invention; Really be more than the 5W/g in order to make the endothermic peak height between 180～280 ℃ of aforementioned DSC heating curve, after the applying of aforementioned prestrain, be higher than 100 ℃ and be to carry out in the TR below 200 ℃.The treatment time of this additional anneal is in aforementioned temperature scope heating and keep carrying out about 0.5～48 hour.At this moment, this additional anneal temperature more preferably surpasses 150 ℃ and be the scope below 200 ℃.
Low excessively or hold-time of additional anneal temperature does not have the effect of additional anneal when too short, and in additional anneal, not having to generate with Cu is that main group bunch or growing amount are not enough.Therefore, the speed of cooling when only controlling the quench treatment after the aforementioned solution treatment then is main group's bunch deficiency with Cu, and the endothermic peak height between 180～280 ℃ of aforementioned DSC heating curve can not be for more than the 5W/g.Consequently can not prevent the possibility height of the generation of SS line really.
On the other hand, additional anneal is handled when under being higher than 200 ℃ high temperature, carrying out, might be made the endothermic peak height between 180～280 ℃ of aforementioned DSC heating curve can not be on the contrary for more than the 5W/g.Can infer that its reason is to handle through the pyritous additional anneal, be in the tissue of alloy sheets at aforementioned Al-Mg, is not to generate aforementioned group bunch but the reason that generates thicker precipitate.In addition, surpass 200 ℃ of too high or hold-times when long like aforementioned temperature, the undesirable condition of then aforesaid group bunch is same when carrying out the pyritous final annealing simultaneously, might produce and carry out the such problem of recrystallize.
Can know that from the temperature condition of this additional anneal of the present invention to be main group bunch with Cu bunch compare with the group that comprises Zn of aforementioned patent document 3, have at high temperature more and generate such characteristic.In other words, even if turn back to room temperature, even if perhaps remain on room temperature state, also not generating of the present invention is main group bunch with Cu, has the such characteristic of age hardening that does not produce at room temperature.Relative therewith, comprise the group bunch of Zn because generation under low temperature such as room temperature can produce the age hardening under the room temperature.
In addition, among the present invention, do not carry out heating, the such final annealing of cool quickly rapidly more than 250 ℃ and under the temperature about less than 550 ℃ that are carrying out after the aforementioned preprocessing usually.Under the situation of having carried out the aforementioned pyritous final annealing more than 250 ℃; Become easily that temperature is too high, the hold-time is long, speed of cooling is crossed the such condition of recrystallize of carrying out that waits slowly; Lose the effect of utilizing SS line that aforementioned cold working carries out to suppress; Perhaps a part produces thickization of crystal grain, thereby produces the problem of coarse grade when being shaped.In addition; In the heating process or in the cooling process in (process); The intermetallic compound of Al-Mg system etc. is separated out easily in a large number, and can not make the endothermic peak height between 180～280 ℃ of aforementioned DSC heating curve is more than the 5W/g, can not prevent positively that the possibility of generation of SS line is big.In addition; If the intermetallic compound of Al-Mg system etc. is separated out in a large number; The alloy that then comprises beyond Mg, the Cu in generations such as boundary or grains adds thickization of the second phase particle of element, thereby causes the decline of ductility, plasticity or corrosion resistant feeding habits, and the effect that suppresses the SS line also descends.
Among the present invention; Through making up the modified of so special quench treatment condition of aforesaid solution treatment condition, ensuing 2 stages cooling and the additional anneal under the specified conditions respectively, thus the plate tissue that the Al-Mg line aluminium alloy plate that comprises Cu is become do not carry out room-temperature aging, Mg to be difficult to spread.Thus, behind the manufacturing plate, even through more than 1 month; During the counter plate press molding, the ultimate strain amount that has also improved Al-Mg line aluminium alloy plate increases effect, suppresses the zig-zag on the stress-strain curve; Suppress the parallel bands cause thus, can suppress to stretch-generation of strain line.In addition, in the SS line, can also prevent generation by the random line that causes of aforementioned surrender extensibility.
Below enumerating embodiment explains the present invention more specifically; But the present invention is not limit by the system of following embodiment certainly; Can meet aforementioned with after the scope suitable variation situation about also can implement in addition of the order stated, these all are included in the scope of technology of the present invention.
[embodiment]
Then embodiments of the invention are described.Each Al-Mg that forms of invention shown in the manufacturing table 1 example, comparative example is an alloy sheets, that the condition that illustrates with table 2 (continuous table 1) is carried out is modified, make after, tissue, the mechanical characteristics of the plate to this after modified have been carried out mensuration, evaluation respectively.These results also are shown in table 2.Explain that "-" mark of the constituent content in the table 1 representes that the content of this element is below the detectability.
Each method of manufacture (condition) and each example of hot-rolled sheet and cold-reduced sheet all adopts identical common condition to carry out.That is, under 480 ℃,, begin hot rollings at 400 ℃ then to the thick ingot casting of fluid origin 50mm carries out the thermal treatment that homogenizes of 8 times through book mold (book mold) casting.Obtain the hot-rolled sheet that thickness of slab is 3.5mm.This hot-rolled sheet is cold rolled to after the thickness of slab of 1.35mm, with nitre oven 400 ℃, carry out getting for 10 seconds process annealing, carry out cold rolling again and obtain the thick cold-reduced sheet of 1.0mm.
These cold-reduced sheets solution treatment and quench treatment have been carried out with each different condition as shown in table 2.This solution treatment and quench treatment use continuous annealing line (CAL) etc. carry out continuously, use forced air-cooling, spray cooling respectively, in the LV of each temperature province switchboard and their air quantity, the speed of cooling when having controlled quench treatment thus.
After this solution treatment and quench treatment, as the cold working that applies prestrain, each example is all commonly carried out the skin-pass of working modulus 3%.Then, the modifier treatment of carrying out additional anneal or having carried out with the different condition separately shown in the table 2.
Plate after these modifier treatment (manufacturing) downcuts test film (1.0mm is thick); In after the modifier treatment that does not have the influence of room-temperature aging (can ignore) 24 hours, measure, estimate the differential thermal analysis (tissue) of this test film (plate after modified), the characteristic of machinery respectively.
(differential thermal analysis)
Investigation as the tissue of the plate that has just carried out aforementioned modifier treatment (manufacturing); Downcut the discoid test portion of 5 diameter 3mm from the optional position of aforementioned test film, obtain and utilize differential thermal analysis (DSC) to survey the periodic heating curve that begins from room temperature with aforesaid condition.And, the height of the endothermic peak that exists in the scope of the present invention 180～280 ℃ (temperature province) is obtained as the peak of the W/g of the DSC heating curve in this zone.Explain that the height of this endothermic peak (W/g) is as the peaked MV of the W/g of DSC heating curve: the mensuration result's of 5 discoid test portions MV and obtaining.About the collection of these data, as previously mentioned, each example is all commonly in the position of measuring 150 ℃ of temperature, proofreaies and correct so that recept the caloric and after thermal value is 0, obtains the endothermic peak height (W/g) that exists in 180～280 ℃ the scope.At this moment, measuring from the heat flow of the longitudinal axis of the heating curve (differential scanning calorimetry curve) that begins from room temperature is that 0.00 reference line plays highly the distance (W/g) for the endothermic peak (summit) of maximum.
The differential thermal analysis condition, each example is all commonly carried out with following condition.
Testing apparatus: Seiko apparatus (Seiko Instruments Inc.) system DSC220C,
Reference material: fine aluminium,
The test portion container: fine aluminium,
The intensification condition: 15 ℃/min,
Atmosphere is enclosed (in the test portion container): argon gas (gas flow 50ml/min),
Test test portion weight: 24.5～26.5mg.
(mechanical characteristics)
As the investigation of the mechanical characteristics of the plate that has just carried out aforementioned modifier treatment (manufacturing), carry out the tension test of above-mentioned each test film, measure tensile strength (MPa), extensibility (%) respectively.It is No. 5 test films (25mm * 50mmGL * thickness of slab) of the JISZ2201 of right angle orientation that test conditions adopts with respect to rolling direction, carries out tension test.Tension test makes an experiment for 20 ℃ in room temperature based on JISZ2241 (1980) (metal material stretching test method).At this moment, pinblock speed is 5mm/ minute, carries out rupturing until test film with constant speed.
Under the room temperature through the time the characteristic of plate after changing:
In addition; When keeping in order to estimate under the room temperature through the time change (influence of room-temperature aging hardened); In aforementioned modifier treatment (manufacturing) afterwards; Above-mentioned each test film after room temperature keeps one-month period, is carried out tension test with same condition, obtain the increasing amount (room-temperature aging hardening capacity) of the tensile strength of just carrying out aforementioned modifier treatment (manufacturing).
(the SS line is estimated)
Equally; The surrender extensibility (%) in order to carry out keeping estimating, to have studied aforementioned room temperature keeping the tension test after 1 month and dependent variable (the critical strain amount: %) of the jagged zig-zag generation on aforesaid stresses-strain curve through the SS line of the press molding property of the plate after 1 month as aforementioned room temperature.
(evaluation of press molding property)
In addition, same, keep press molding property as room temperature through the plate after 1 month, the extrusion molding test that aforementioned room temperature is kept the drawing sheet after 1 month is carried out as the evaluation that is used as outside plate and becomes the extrusion molding property of problem.
The extrusion molding test uses the bulb of diameter 101.6mm to extrude punching; Test film at length 180mm, width 110mm is coated with the R-303P as lubricant; Carry out extrusion molding test, the generation state of the crackle of visual observation molding with forming speed 4mm/S, wrinkle resistant pressure loading (わ gives as security さ え loading) 200kN.And, the size of pipe crack not, though the average evaluation that the average evaluation that crackle does not have to take place fully is zero, crackle takes place less be *.
Like table 1,2,1～7 control of invention example contains Cu, whether does not contain Zn, satisfies Al-Mg line aluminium alloy of the present invention and forms regulation.In addition, the speed of cooling condition of quench treatment is preferably created conditions with solid solution as aforementioned 2 stages and quench treatment and is made.Endothermic peak height between 180～280 ℃ of the heating curve that begins from room temperature that the thermal distortion of consequently utilizing differential thermal analysis to measure this plate obtains is for more than the 5W/g.
Thus, the tensile strength increasing amount of just carrying out aforementioned modifier treatment (manufacturing) (room-temperature aging hardening capacity) of each invention example reduces, and the press molding property that contains SS line characteristic is excellent.That is, the critical strain that the zig-zag on the stress-strain curve of aluminium alloy plate takes place is more than 8%, and high critical strain is more than 10%, even if also do not have crackle to take place in the test of aforementioned extrusion molding.And; To these excellent SS line characteristics or extrusion molding property (being expressed as press molding property in the table 2); Do not lower the mechanical characteristics level of the excellence of tensile strength that 5000 line aluminium alloy plates of JIS5052 alloy, JIS5182 alloy etc. are had and extensibility etc., can have room-temperature aging sclerosis ground to realize in addition.
But, though be allowance, the invention example 2 of the invention example 6 that contains Zn 0.6% more in a large number and less content 0.02% or do not contain Zn other the invention example relatively, though be the scope that allows, room-temperature aging sclerosis quantitative change is big.
On the other hand, though comparative example 8～13 is identical alloy composition with invention example 1, like table 2, modified condition departs from preferred range respectively.As far as comparative example 8, solid solution temperature is low excessively, in quench treatment, can not carry out the cooling in aforementioned 2 stages.As far as comparative example 9, the speed of cooling in quench treatment in the chilling of high-temperature area is less than 2 ℃/second of lower limit.As far as comparative example 10, the speed of cooling in the quench treatment in the slow cooling of high-temperature area surpasses 1 ℃/second of the upper limit.The additional anneal temperature of comparative example 11 is low excessively less than 100 ℃ of lower limits.The additional anneal temperature of comparative example 12 surpasses 200 ℃ of the upper limits and too high.Comparative example 13 does not carry out additional anneal.
Its result; Endothermic peak height between 180～280 ℃ of the aforementioned DSC heating curve of comparative example 8～13 is less than 5W/g; Though the mechanical characteristics of intensity and extensibility etc. does not have big difference with the invention example; But the critical strain that the zig-zag on the stress-strain curve of aluminium alloy plate takes place is lower, is less than 8%, and SS line characteristic is compared remarkable reduction with the invention example.That is, become and cause aforementioned zigzag tissue easily.
Comparative example 14～17, like table 1,2, though modified condition is a preferred range, alloy composition departs from scope of invention.Comparative example 14 does not contain Cu, and the Cu content of comparative example 15 is very few.The Mg content of comparative example 16 is too much.The Zn content of comparative example 17 is too much.
Its result; Though the room-temperature aging hardening capacity of the comparative example 14,15 that the effect of Cu can not be brought into play is few, intensity is also low, and the critical strain that the zig-zag on the stress-strain curve of aluminium alloy plate takes place is low; Its value is less than 8%, and SS line characteristic is compared significantly low with the invention example.That is, become and cause aforementioned zigzag tissue easily.
Though the room-temperature aging hardening capacity of comparative example 16 is few, intensity is too high, and extensibility reduces, and cracks during press molding, and press molding property (extrusion molding property) is compared step-down with the invention example.
Comparative example 17 is because Zn is too much, and the room-temperature aging hardening capacity surpasses allowed band and becomes big, cracks during press molding, and press molding property (extrusion molding property) is compared reduction with the invention example.
Can know from above embodiment, because the SS line characteristic and press molding property or the mechanical characteristics etc. that have each important document of the present invention concurrently or preferably create conditions etc. have critical meaning so be proved to be.
[table 1]
Utilize possibility on the industry
As described above; According to the present invention; Can provide: there is not to produce the new problem of the toughness reduction that causes by the age hardening under the room temperature etc., the generation of the random line that not only suppresses to cause by aforementioned yield extension, and suppress the generation of parallel bands simultaneously; Can suppress the SS line and take place, to the Al-Mg line aluminium alloy plate of the press molding property raising of car panel.Its result in a large amount of purposes to plate press molding and the said automobile that uses etc., has enlarged the application of Al-Mg line aluminium alloy plate.
Claims (2)
1. aluminium alloy plate that has excellent formability, it is to contain Mg:2.0～6.0%, Cu in quality %: surpass 0.3% and be below 2.0%, and surplus is the Al-Mg line aluminium alloy plate of Al and unavoidable impurities, it is characterized in that,
Utilize differential thermal analysis to measure to obtain from the heating curve that room temperature begins, the endothermic peak height of the maximum between 180～280 ℃ is more than the 5W/g.
2. the aluminium alloy plate that has excellent formability according to claim 1, wherein,
As the index of the plasticity of representing said aluminium alloy plate, the zigzag critical strain of the generation on the stress-strain curve of said aluminium alloy plate is more than 8%.
Applications Claiming Priority (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2010176171 | 2010-08-05 | ||
| JP2010-176171 | 2010-08-05 | ||
| JP2011-092688 | 2011-04-19 | ||
| JP2011092688A JP5600637B2 (en) | 2010-08-05 | 2011-04-19 | Aluminum alloy plate with excellent formability |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN102373353A true CN102373353A (en) | 2012-03-14 |
| CN102373353B CN102373353B (en) | 2016-06-01 |
Family
ID=45792579
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201110210223.7A Expired - Fee Related CN102373353B (en) | 2010-08-05 | 2011-07-26 | The aluminium alloy plate having excellent formability |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN102373353B (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104736732A (en) * | 2012-10-23 | 2015-06-24 | 株式会社神户制钢所 | Aluminum alloy plate for molding |
| CN107641745A (en) * | 2017-08-28 | 2018-01-30 | 扬中市扬子铝加工有限公司 | A kind of aluminum-magnesium alloy wire rod applied to cable and preparation method thereof |
| CN107723528A (en) * | 2017-08-28 | 2018-02-23 | 扬中市扬子铝加工有限公司 | A kind of almag containing rare-earth elements of lanthanum and preparation method thereof |
| CN107739919A (en) * | 2017-11-02 | 2018-02-27 | 陈礼成 | A kind of high-strength aluminium-magnesium alloy and preparation method thereof |
| CN107904455A (en) * | 2017-11-02 | 2018-04-13 | 陈礼成 | A kind of aluminum-magnesium alloy wire rod applied to high-quality cable and preparation method thereof |
| CN110088315A (en) * | 2016-12-16 | 2019-08-02 | 诺维尔里斯公司 | It is resistant to the high intensity and high formable aluminium alloy and its manufacturing method of natural aging hardening |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4777097A (en) * | 1986-01-31 | 1988-10-11 | Toyota Jidosha Kabushiki Kaisha | Composite material including alumina-silica short fiber reinforcing material and aluminum alloy matrix metal with moderate copper and magnesium contents |
| JP2005139537A (en) * | 2003-11-10 | 2005-06-02 | Kobe Steel Ltd | Aluminum alloy sheet having excellent baking finish hardenability |
| JP2006249480A (en) * | 2005-03-09 | 2006-09-21 | Kobe Steel Ltd | Aluminum alloy sheet to be formed |
| CN1946861A (en) * | 2004-04-23 | 2007-04-11 | 日本轻金属株式会社 | Al-mg alloy sheet with excellent formability at high temperatures and high speeds and method of production of same |
| CN101558177A (en) * | 2006-12-13 | 2009-10-14 | 住友轻金属工业株式会社 | High-strength aluminum-base alloy products and process for production thereof |
-
2011
- 2011-07-26 CN CN201110210223.7A patent/CN102373353B/en not_active Expired - Fee Related
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4777097A (en) * | 1986-01-31 | 1988-10-11 | Toyota Jidosha Kabushiki Kaisha | Composite material including alumina-silica short fiber reinforcing material and aluminum alloy matrix metal with moderate copper and magnesium contents |
| JP2005139537A (en) * | 2003-11-10 | 2005-06-02 | Kobe Steel Ltd | Aluminum alloy sheet having excellent baking finish hardenability |
| CN1946861A (en) * | 2004-04-23 | 2007-04-11 | 日本轻金属株式会社 | Al-mg alloy sheet with excellent formability at high temperatures and high speeds and method of production of same |
| JP2006249480A (en) * | 2005-03-09 | 2006-09-21 | Kobe Steel Ltd | Aluminum alloy sheet to be formed |
| CN101558177A (en) * | 2006-12-13 | 2009-10-14 | 住友轻金属工业株式会社 | High-strength aluminum-base alloy products and process for production thereof |
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104736732A (en) * | 2012-10-23 | 2015-06-24 | 株式会社神户制钢所 | Aluminum alloy plate for molding |
| CN104736732B (en) * | 2012-10-23 | 2016-12-14 | 株式会社神户制钢所 | Forming aluminium alloy plate |
| US10221469B2 (en) | 2012-10-23 | 2019-03-05 | Kobe Steel, Ltd. | Aluminum alloy plate for forming |
| CN110088315A (en) * | 2016-12-16 | 2019-08-02 | 诺维尔里斯公司 | It is resistant to the high intensity and high formable aluminium alloy and its manufacturing method of natural aging hardening |
| US11530473B2 (en) | 2016-12-16 | 2022-12-20 | Novelis Inc. | High strength and highly formable aluminum alloys resistant to natural age hardening and methods of making the same |
| CN107641745A (en) * | 2017-08-28 | 2018-01-30 | 扬中市扬子铝加工有限公司 | A kind of aluminum-magnesium alloy wire rod applied to cable and preparation method thereof |
| CN107723528A (en) * | 2017-08-28 | 2018-02-23 | 扬中市扬子铝加工有限公司 | A kind of almag containing rare-earth elements of lanthanum and preparation method thereof |
| CN107739919A (en) * | 2017-11-02 | 2018-02-27 | 陈礼成 | A kind of high-strength aluminium-magnesium alloy and preparation method thereof |
| CN107904455A (en) * | 2017-11-02 | 2018-04-13 | 陈礼成 | A kind of aluminum-magnesium alloy wire rod applied to high-quality cable and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN102373353B (en) | 2016-06-01 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN101684531B (en) | Aluminum alloy board | |
| JP4308834B2 (en) | Method for continuously producing cast aluminum sheets | |
| CN102703773B (en) | Aluminum alloy plate and production process thereof | |
| CN101225491B (en) | Aluminum alloy sheet | |
| AU2003242003B2 (en) | Magnesium alloy plate and method for production thereof | |
| CN101490291B (en) | High-strength aluminum alloy plate and process for producing the same | |
| US7422645B2 (en) | Method of press quenching aluminum alloy 6020 | |
| CN102373353A (en) | Aluminium Alloy Plate Having Excellent Forming Property | |
| CN101422784B (en) | Rolling technique of ultra-fine grained magnesium alloy sheet | |
| CN104114726A (en) | Aluminum alloy sheet with excellent baking-paint curability | |
| CN109280861A (en) | Flat product and its production method with good resistance to ag(e)ing | |
| CN101845574B (en) | Aluminium alloy plate with excellent formability | |
| JP5432632B2 (en) | Aluminum alloy plate with excellent formability | |
| KR101667506B1 (en) | Aluminum alloy plate for forming | |
| JP4854333B2 (en) | High strength steel plate, unannealed high strength steel plate and method for producing them | |
| JP2005194550A (en) | Steel with high strength and excellent cold headability, fastening parts, such as screw and bolt, or formed article, such as shafts, with excellent strength and their manufacturing methods | |
| JP2007186747A (en) | Aluminum alloy material to be formed at high temperature and a high speed, manufacturing method therefor and method for manufacturing formed article from aluminum alloy | |
| JP4412418B2 (en) | Method for producing hot-rolled steel sheet having fine ferrite structure, and hot-rolled steel sheet | |
| JP5600637B2 (en) | Aluminum alloy plate with excellent formability | |
| WO2015009416A1 (en) | High strength-high ductility cold rolled recovery annealed steel | |
| JP5685055B2 (en) | Aluminum alloy plate | |
| JP4865174B2 (en) | Manufacturing method of aluminum alloy sheet with excellent bending workability and drawability | |
| JP3983454B2 (en) | Method for producing high-strength, high-formability aluminum alloy plate and aluminum alloy plate obtained by the production method | |
| JP2003239032A (en) | Aluminum alloy sheet with excellent bendability | |
| JP2005146310A (en) | Mg-CONTAINING Al ALLOY |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20160601 Termination date: 20200726 |
|
| CF01 | Termination of patent right due to non-payment of annual fee |