CN103168111A - Improved 2xxx aluminum alloys, and methods for producing the same - Google Patents

Abstract

New 2xxx aluminum alloy bodies and methods of producing the same are disclosed. The new 2xxx aluminum alloy bodies may be produced by preparing the aluminum alloy body for post-solutionizing cold work, cold working by at least 25%, and then thermally treating. The new 2xxx aluminum alloy bodies may realize improved strength and other properties.

Description

Improved 2XXX aluminium alloy and production method thereof

The cross reference of related application

Present patent application requires the U.S. Provisional Patent Application No.61/381 of submission on September 8th, 2010,040, the U.S. Provisional Patent Application No.61/391 that submitted on October 8th, 2010,461, the U.S. Provisional Patent Application No.61/425 that submitted on December 20th, 2010, the U.S. Provisional Patent Application No.61/437 that submitted on January 28th, 024 and 2011, the right of priority of the every portion in 515.The full content of every portion of above-mentioned patent application all is combined in herein by reference.

Present patent application also is called with the name of submitting on September 8th, 2011 that name that the PCT patent application No.______ of " improved 6XXX aluminium alloy and production method thereof ", on September 8th, 2011 submit to is called the PCT patent application No.______ of " improved 7XXX aluminium alloy and production method thereof " and the name submitted on September 8th, 2011 to be called the PCT patent application No.______ of improved Al-Li alloy and production method thereof relevant.

Background technology

Aluminium alloy is useful in multiple application.Yet, improve a kind of performance of aluminium alloy and do not damage another kind of performance and be difficult to realize.For example, in the situation that the intensity of not falling low-alloyed toughness and increasing alloy is difficult.Other interesting performances of aluminium alloy comprise solidity to corrosion and fatigue crack spreading rate, only for two examples.

Summary of the invention

Roughlly speaking, present patent application relates to improved forging, heat treatable aluminium alloy and production method thereof.Particularly, present patent application relates to improved forging 2xxx alloy product and production method thereof.Usually, the 2xxx alloy product is owing to obtaining improved over-all properties such as cold working after solid solution and cold working postheat treatment etc., as hereinafter describing in further detail.

The 2xxx aluminium alloy is the aluminium alloy that contains copper, wherein the alloying constituent of copper for being dominant except aluminium.For purposes of this application, the 2xxx aluminium alloy is to have 0.5wt.% to the aluminium alloy of the Cu of 8.0wt.%, wherein, and the alloying element of copper for being dominant except aluminium.

Fig. 1 shows the ordinary method for the production of the 2xxx alloy product of mill form.In this ordinary method, 2xxx aluminium alloy body (10) is cast, after this with this aluminium alloy body homogenizing (11) and subsequent hot to intermediate gauge (12).Then, with 2xxx with aluminium alloy body cold rolling (13) to final thickness, after this it is carried out solution heat treatment and quench (14)." solution heat treatment and quenching " etc. is generally called work " solid solution " in this article, mean the aluminium alloy body is heated to suitable temperature, usually more than the solvus temperature, keep the sufficiently long time to enter into sosoloid with the permission soluble elements in this temperature, and enough cooling so that described element is remained in sosoloid rapidly.Can be deposited as mode coarse, incoherent particle by enough cooling limitation solute atomss fast, will remain at the sosoloid that high temperature forms the supersaturation attitude.After solid solution (14), can be randomly with 2xxx aluminium alloy body a small amount of (for example, 1-5%) stretch (15) smooth to realize, heat-treat (16) and randomly through last processing operation (17).Fig. 1 and processing route consistent (the T6 state is in the application's hereinafter definition) for the production of the aluminium alloy of T6 state.

Fig. 2 shows one for the production of the embodiment of the novel method of new 2xxx alloy product.In this novel method, preparation 2xxx aluminium alloy body (100) is used for cold working after solid solution, after this this aluminium alloy body is carried out cold working (200), and heat-treats subsequently (300).This novel method also can comprise optional final processing (400), as hereinafter describing in further detail." cold working after solid solution " etc. means the cold working of aluminium alloy body after solid solution.Be applied to after the solid solution of 2xxx aluminium alloy body cold worked amount normally at least 25%.By the first solution treatment, and at least 25% cold working subsequently, and subsequently with the suitably thermal treatment of 2xxx aluminium alloy body, 2xxx aluminium alloy body can be realized improved performance, as hereinafter describing in further detail.For example, conventional alloy product with respect to T6 and/or T87 state, can obtain 5-40% or higher strength increase, and conventional alloy product is processed in T6 and/or the part of needed time of T87 state the fast 10%-90% of alloy of T6 and/or the processing of T87 state (for example, than) and obtains this strength increase with these.New 2xxx aluminium alloy body also can obtain good ductility, usually obtains the unit elongation higher than 4%, for example 6-16% or higher unit elongation.This new aluminum alloy body can be in the situation that do not have the fracture toughness property loss to obtain strength improving yet.In some cases, new 2xxx aluminium alloy body obtains improved fracture toughness property, for example than the fracture toughness property of the high 5-25% of conventional alloy product that is in T6 and/or T87 state.Also can keep and/or improve other performances (for example, fatigue crack extendability).

A. for the preparation of cold working after solid solution

As shown in Figure 2, this novel method comprises the aluminium alloy body for the preparation of cold working after solid solution (100).Can in many ways for the preparation of the aluminium alloy body of cold working after solid solution (100), comprise and use conventional D.C.casting method (for example, the direct-cooled casting of ingot casting) and continuous metal cast process (for example, double roller continuous casting).As shown in Figure 3, preparation process (100) generally includes to be arranged to the aluminium alloy body to be fit to cold worked form (120), and this aluminium alloy body is carried out solution treatment (140).Setting steps (120) and solid solution step (140) can occur successively or follow each other and occur.Some limiting examples of multiple preparation process (100) are shown in Fig. 4 to Fig. 8, and this describes hereinafter in further detail.Additive method for the preparation of the aluminium alloy body of cold working after solid solution (100) is known to those skilled in the art, although and describe clearly herein, these additive methods are also in the scope of preparation process (100).

In a scheme, preparation process (100) comprises the D.C.casting method.In one embodiment, and with reference to Fig. 4, described setting steps (120) (for example comprises cast aluminium alloy body (122), form with ingot casting or billet), with aluminium alloy body homogenizing (124), hot-work aluminium alloy body (126) and cold working aluminium alloy body (128) randomly.At setting steps (120) afterwards, complete solution treatment step (140).Although (120) will be with the form of ingot casting/billet after casting for the aluminium alloy body, can use the continuous casting operation to complete similar step.

In another embodiment, and with reference to Fig. 5, preparation process (100) comprises cast aluminium alloy body (122), with this aluminium alloy body homogenizing (124) and this aluminium alloy body (126) of hot-work.In the present embodiment, can complete hot-work step (126) so that soluble elements is placed in sosoloid, after this with this aluminium alloy body quenching (not shown), thereby cause solution treatment step (140).This is that setting steps (120) and solution treatment step (140) are followed an embodiment who completes each other.Hot-rolled product that the present embodiment quenches after applicable to the product (for example, section bar) of die quenching and hot rolling etc.

In another scheme, preparation process (100) comprises continuous metal cast process, as belt continuous casting, pole stock casting, double roller continuous casting, double belt continuous casting (for example, Hazelet (Hazelett) casting), traction casting (drag casting) and block casting etc.An embodiment of preparation process (100) is used continuous metal cast process shown in Figure 6.In this embodiment, at approximately identical time (each other concomitantly namely) casting and solid solution aluminium alloy body (142).Casting is arranged to be enough to cold worked form with the aluminium alloy body.When the solidification rate rapid enough during casting, the aluminium alloy body is also by solid solution.In this embodiment, casting/solution treatment step (142) can be included in after casting aluminium alloy body quenching (not shown).The present embodiment is applicable to double roller continuous casting method and Castingother method.Can complete some double roller continuous casting methods of method of Fig. 6 in U.S. Patent No. 7,182,825 and U.S. Patent No. 6,672,368 in be described.

In another embodiment, and with reference to Fig. 7, preparation process (100) comprises cast aluminium alloy body (122), and after casting step (122), then with aluminium alloy body solution treatment (140).In this embodiment, setting steps (120) comprises casting (122).The present embodiment is applicable to double roller continuous casting method and Castingother method.

In another embodiment, and with reference to Fig. 8, preparation process (100) comprises cast aluminium alloy body (122), hot-work aluminium alloy body (126), and cold working aluminium alloy body (128) randomly.In this embodiment, setting steps (120) comprises casting step (122), hot-work step (126) and optional cold working (128) step.At setting steps (120) afterwards, complete solution treatment step (140).The present embodiment is applicable to continuous metal cast process.

Many steps shown in Fig. 2 to Fig. 8 can be completed with batch mode or continuous mode.In an example, cold working step (200) and heat treatment step (300) are completed continuously.In this example, can be entered cold-working operation under envrionment conditions by the aluminium alloy body of solid solution.In view of novel method as herein described can obtain relatively short heat treatment time, can (for example, straight-line type) cold worked aluminium alloy be heat-treated (300) immediately after cold working.Can expect, this class thermal treatment can occur in the exit of contiguous cold working apparatus, perhaps occurs in the independent heating unit that is connected with cold working apparatus.This can boost productivity.

As mentioned above, preparation process (100) generally includes the solid solution of aluminium alloy body.As mentioned above, " solid solution " comprises the quenching (not shown) of aluminium alloy body, described quenching can be by liquid (for example, by the aqueous solution or organic solution), gas (for example, cooling air) or even solid (for example, cooling solid on the one or more sides of aluminium alloy body) is completed.In one embodiment, quenching step comprises makes the aluminium alloy body contact with liquid or gas.In some of these embodiments, quenching occurs in the hot-work that does not have the aluminium alloy body and/or cold worked situation.For example, quenching can be in the situation that do not exist the distortion of aluminium alloy body to occur by submergence, spraying and/or jet drying etc. technology.

those skilled in the art recognize that and to use other preparation processes (100) for the preparation of cold worked aluminium alloy body after solid solution (for example, powder metallurgy process), and recognize that other preparation processes of this class drop in the scope of preparation process (100), as long as they are arranged to be fit to cold worked form (120) also with this aluminium alloy body solid solution (140) with the aluminium alloy body, and no matter whether these setting steps (120) and solution treatment step (140) (for example follow generation, side by side) or successively occur, and no matter whether setting steps (120) occurs before in solution treatment step (140), or vice versa.

B. cold working

Referring again to Fig. 2, and as mentioned above, this novel method comprises a large amount of aluminium alloy bodies of cold working (200)." cold working " etc. means to make aluminium alloy body deformability (for example, not higher than 400 °F) at least one direction with lower than the temperature of hot processing temperature.The Cold-forming process of one or more and combination and other types that can be by rolling, extruding, forging, tractive, ironing (ironing), spinning, roll forming carries out cold working.These Cold-forming process can partly help to produce various 2xxx alloy products (product application vide infra) at least.

I. cold rolling

In one embodiment, and with reference to Fig. 9, cold working step (200) comprises cold rolling step (220) (and comprise in the example of cold rolling step (220) at some, by optional stretching or aligning smooth to realize (240)).In this embodiment, and as mentioned above, cold rolling step (220) is completed afterwards in solution treatment step (140).Cold rolling step (220) is a kind of usually by by the roller applied pressure, the aluminium alloy body thickness being reduced, and the aluminium alloy body is in the manufacturing technology that enters rolling equipment lower than hot rolling (124) temperature used (for example, not higher than 400 °F).In one embodiment, the aluminium alloy body enters rolling equipment under envrionment conditions, that is, cold rolling step (220) begins under envrionment conditions in the present embodiment.

Cold rolling step (220) is reduced by at least 25% with the thickness of 2xxx aluminium alloy body.Cold rolling step (220) can be completed in one or more rolling passes.In one embodiment, cold rolling step (220) is rolled down to final thickness with the aluminium alloy body from intermediate gauge.Cold rolling step (220) can be produced thin plate, sheet material or paper tinsel product.The paper tinsel product is the rolled products that has less than the thickness of 0.006 inch.Light sheet products is the rolled products with thickness of 0.006 inch to 0.249 inch.Plate product is the rolled products with 0.250 inch or larger thickness.

" cold rolling XX% " etc. means XX _CR%, wherein XX _CR% be by cold rolling with the aluminium alloy body from the first thickness T ₁Reduce to the first thickness T ₂The time thickness reduction that realizes, wherein T ₁The thickness of cold rolling step (200) front (for example, after solid solution), T ₂The thickness after cold rolling step (200).In other words, XX _CR% equals:

XX _CR%=(1–T ₂/T ₁)*100%

For example, when the aluminium alloy body from the first thickness (T ₁) 15.0mm reduces to the second thickness (T ₂) during 3.0mm, XX _CR% is 80%.Phrase is as " cold rolling (cold rolling) 80% " and " cold rolling (cold rolled) 80% " and expression formula XX _CRThe %=80% equivalence.

In one embodiment, with cold rolling (220) at least 30% (XX of aluminium alloy body _CR% 〉=30%), that is, thickness is reduced by at least 30%.In other embodiments, with cold rolling (220) at least 35% (XX of aluminium alloy body _CROr at least 40% (XX % 〉=35%), _CROr at least 45% (XX % 〉=40%), _CROr at least 50% (XX % 〉=45%), _CROr at least 55% (XX % 〉=50%), _CROr at least 60% (XX % 〉=55%), _CROr at least 65% (XX % 〉=60%), _CROr at least 70% (XX % 〉=65%), _CROr at least 75% (XX % 〉=70%), _CROr at least 80% (XX % 〉=75%), _CROr at least 85% (XX % 〉=80%), _CROr at least 90% (XX % 〉=85%), _CR% 〉=90%) or more.

In certain embodiments, cold rolling (XX more than 90% _CR%≤90%) be unrealistic or undesirable.In these embodiments, can be with aluminium alloy body cold rolling (220) not higher than 87% (XX _CR%≤87%), as cold rolling (220) not higher than 85% (XX _CR%≤85%), or not higher than 83% (XX _CR%≤83%), or not higher than 80% (XX _CR%≤80%).

In one embodiment, with the aluminium alloy body cold rolling higher than 50% to not higher than 85% (50%＜XX _CR%≤85%).This cold rolling amount can produce the aluminium alloy body with preferred properties.In relevant embodiment, can be with cold rolling 55% to the 85% (55%≤XX of aluminium alloy body _CR%≤85%).In yet another embodiment, can be with cold rolling 60% to the 85% (60%≤XX of aluminium alloy body _CR%≤85%).In yet another embodiment, can be with cold rolling 65% to the 85% (65%≤XX of aluminium alloy body _CR%≤85%).In yet another embodiment, can be with cold rolling 70% to the 80% (70%≤XX of aluminium alloy body _CR%≤80%).

Still with reference to Fig. 9, in the embodiment of this method, can complete optional cold rolling (128) in advance.Pre-cold rolling step (128) can be further reduces to time intermediate gauge with the intermediate gauge (due to hot-rolled step 126) of aluminium alloy body.As an example, optional cold rolling step (128) can be used for producing the inferior intermediate gauge that helps to produce final cold rolling thickness during cold rolling step (220).

Ii. other cold processing techniques

Except cold rolling, and referring again to Fig. 2, can be by one or more and the combination in rolling, extruding, forging, tractive, ironing, spinning, roll forming, and cold working is carried out in the Cold-forming process of independent other types or these methods and cold rolling combination.As mentioned above, usually after solid solution with aluminium alloy body cold working at least 25%.In one embodiment, cold working is processed into its final form (that is, not needing extra hot-work step and/or cold working step to obtain final product form) basically with the aluminium alloy body.

" cold working XX% " (" XX _CW% ") etc. mean one of aluminium alloy body cold working is enough to realize the amount of equivalent plastic strain (hereinafter describing), if described equivalent plastic strain is at least with the cold rolling XX% (XX of aluminium alloy body _CRThe amount of the equivalent plastic strain that %) realizes is equally large.For example, phrase " cold working 68.2% " means amount that is enough to realize equivalent plastic strain of aluminium alloy body cold working, if described equivalent plastic strain is at least with the same large with the amount of cold rolling 68.2% equivalent plastic strain that realizes of aluminium alloy body.Due to XX _CW% and XX _CR% all refers to the amount of the equivalent plastic strain that produces in the aluminium alloy body, as with the cold rolling XX% of aluminium alloy body (or in the situation that cold rolling in fact cold rolling XX% of reality), so these two terms are used to refer to the amount of this equivalent plastic strain in this article interchangeably.

Equivalent plastic strain is relevant to true strain.For example, cold rolling XX%, that is, and XX _CR% can be by the true strain value representation, wherein true strain (ε _True) provided by following formula:

ε _true＝-ln(1-%CR/100) (1)

Wherein %CR is XX _CR%, the true strain value can be converted into the equivalent plastic strain value.In the situation that realize biaxial strain during cold rolling, the equivalent plastic strain of estimation will be than large 1.155 times of true strain value (2 equal 1.155 divided by √ 3).The type of the plastix strain that the biaxial strain representative produces during cold rolling manipulation.Following table 1 provides the form that cold rolling XX% is associated with true strain value and equivalent plastic strain value.

Table 1

These equivalent plastic strain supposition:

A. nonelastic strain;

B. the bingham's plasticity strain keeps constancy of volume; With

C. load is proportional.

For proportional load, above-mentioned and/or other principles can be used for measuring the equivalent plastic strain of multiple cold-working operation.For out-of-proportion load, the equivalent plastic strain that cold working causes can adopt following formula to determine:

${\mathrm{d\ϵ}}_p=\frac{\sqrt{2}}{3}\left[\sqrt{{({\mathrm{d\ϵ}}_1^p-{\mathrm{d\ϵ}}_2^p)}^2+{({\mathrm{d\ϵ}}_1^p-{\mathrm{d\ϵ}}_3^p)}^2+({\mathrm{d\ϵ}}_3^p-{\mathrm{d\ϵ}}_2^p)}\right]---\left(2\right)$

D ε wherein _pEquivalent plastic strain increment, d ε _i ^p(i=l, 2,3) represent the increment of main plastix strain component.Referring to, plasticity (Plasticity), A.Mendelson, Krieger Pub Co; Second edition (August nineteen eighty-three), ISBN-10:0898745829.

Those skilled in the art understand cold working step (200) and can comprise in the first mode and (for example make the aluminium alloy body deformability, compression), and (for example make the aluminium alloy body deformability in the second mode subsequently, stretch), and understand equivalent plastic strain as herein described and refer to by completing the caused accumulation strain of whole distortion behaviour as cold working step (a 200) part.In addition, those skilled in the art understand cold working step (200) will cause the strain inducement, but must not cause the variation of aluminium alloy body final size.For example, can be in the first mode (for example, compression) cold deformation aluminium alloy body, subsequently again with the second mode cold deformation (for example, stretch) this aluminium alloy body, the accumulation results of cold deformation provides the aluminium alloy body that has approximately the final size identical with the front aluminium alloy body of cold working step (200), but because the multiple cold deformation of cold working step (200) operates the strain with increase.Similarly, high accumulation strain can operate and reverse bending operation realization by sequential forming.

By means of method and the additive method well known by persons skilled in the art shown in above, by calculating the equivalent plastic strain that is produced by those cold-working operations, and determine its corresponding XX subsequently _CRThe % value, thus can determine the accumulation equivalent plastic strain of any specific cold-working operation or serial cold-working operation and determine XX _CR%.For example, can the aluminium alloy body is cold drawn, based on cold drawn operating parameters, those skilled in the art can calculate the equivalent plastic strain amount of giving the aluminium alloy body.If cold drawn for example about 0.9552 the equivalent plastic strain that causes, so this cold drawing operation will be equivalent to about 56.3% XX _CR% (true strain value (the ε that 0.9552/1.155 equals 0.8270 _True); And then, when using above-mentioned equation (1), corresponding XX _CR% is 56.3%).Therefore, in this embodiment, XX _CR%=56.3% is although cold working is cold drawn rather than cold rolling.In addition, due to " cold working XX% " (" XX _CW% ") be defined (as above) for the cold working of aluminium alloy body being enough to realize the amount of equivalent plastic strain, if described equivalent plastic strain is at least with only by cold rolling (" XX _CR% ") that the aluminium alloy body thickness is reduced the equivalent plastic strain amount that XX% realizes is equally large, XX _CW% is also 56.3%.When using a series of cold-working operation, can complete similar calculating, and in these cases, will use the accumulation equivalent plastic strain that is produced by described a series of cold-working operations to determine XX _CR%.

As mentioned above, complete cold working step (200) so that the aluminium alloy body is realized XX _CW% or XX _CR% 〉=25%, that is, and 〉=0.3322 equivalent plastic strain." cold working XX% " etc. means XX _CW%.Phrase is as " cold working (cold working) 80% " and " cold working (cold worked) 80% " and expression formula XX _CWThe %=80 equivalence.For the heterogeneity cold-working operation of customization, based on accepting cold working (200) thus the part of aluminium alloy body determine the equivalent plastic strain amount and determine XX _CWOr XX _CRAmount.

In one embodiment, with aluminium alloy body cold working fully (200) to realize and to reach at least 0.4119 equivalent plastic strain (" EPS ") (that is, XX _CW% 〉=30%).In other embodiments, with aluminium alloy body cold working fully (200) with to realize and to reach at least 0.4974 (XX _CWOr at least 0.5899 (XX % 〉=35%), _CWOr at least 0.6903 (XX % 〉=40%), _CWOr at least 0.8004 (XX % 〉=45%), _CWOr at least 0.9220 (XX % 〉=50%), _CWOr at least 1.0583 (XX % 〉=55%), _CWOr at least 1.2120 (XX % 〉=60%), _CWOr at least 1.3902 (XX % 〉=65%), _CWOr at least 1.6008 (XX % 〉=70%), _CWOr at least 1.8584 (XX % 〉=75%), _CWOr at least 2.1906 (XX % 〉=80%), _CWOr at least 2.6588 (XX % 〉=85%), _CWOr higher EPS % 〉=90%).

In certain embodiments, cold working (200) is higher than 90% (XX _CW%≤90% and EPS≤2.6588) be unrealistic or undesirable.In these embodiments, can be with aluminium alloy body cold working (200) not higher than 87% (XX _CW%≤87% and EPS≤2.3564), as cold working (200) not higher than 85% (XX _CW%≤85% and EPS≤2.1906), or not higher than 83% (XX _CW%≤83% and EPS≤2.0466), or not higher than 80% (XX _CW%≤80% and EPS≤1.8584).

In one embodiment, can more than or equal to 50% and less than or equal to 85% scope in (50%≤XX _CW%≤85%) cold working (200) aluminium alloy body.The amount of this cold working (200) can produce the aluminium alloy body with preferred properties.In relevant embodiment, (55%≤XX in 55% to 85% scope _CW%≤85%) cold working (200) aluminium alloy body.In yet another embodiment, (60%≤XX in 60% to 85% scope _CW%≤85%) cold working (200) aluminium alloy body.In yet another embodiment, (65%≤XX in 65% to 85% scope _CW%≤85%) cold working (200) aluminium alloy body.In yet another embodiment, (70%≤XX in 70% to 80% scope _CW%≤80%) cold working (200) aluminium alloy body.

Iii. gradient

Cold working step (200) can be customized in mode substantially uniformly and make the aluminium alloy body deformability, as by rolling or conventional extrusion method mentioned above etc.In other embodiments, cold working step can be customized in cardinal principle mode heterogeneous and make the aluminium alloy body deformability.Therefore, in certain embodiments, this method can produce the aluminium alloy body with customization cold working gradient, namely, the first part of aluminium alloy body accepts the cold working of the first customization amount, the second section of aluminium alloy body connects the cold working of the second customization amount, and wherein the first customization amount is different from the second customization amount.The example that can complete alone or in combination to realize the non-homogeneous cold worked cold-working operation (200) that customizes comprises forging, polishing, shot peening processing, roll forming and spinning etc.This class cold-working operation also can be used in combination with substantially uniform cold-working operation such as cold rolling and/or extruding etc.As mentioned above, for the non-homogeneous cold-working operation of customization, determine the amount of equivalent plastic strain based on the part of the aluminium alloy body of accepting cold working (200).

Iv. cold working temperature

Cold working step (200) can begin in the temperature lower than hot processing temperature (for example, not higher than 400 °F).In a method, when the aluminium alloy body reaches enough low temperature after solid solution (140), beginning cold working step (200).In one embodiment, can begin in the temperature of aluminium alloy body cold working step (200) during not higher than 250 °F.In other embodiments, can be in the temperature of aluminium alloy body not higher than 200 °F, or not higher than 175 °F, or not higher than 150 °F, or not higher than 125 °F, or begin cold working step (200) when lower.In one embodiment, begin cold working step (200) in the time of can being ambient temperature in the temperature of aluminium alloy body.In other embodiments, can begin in higher temperature cold working step (200), for example in the temperature of aluminium alloy body at 250 °F in lower than the scope of hot processing temperature (for example, lower than 500 °F) time.

In one embodiment, there is not in any situation that purpose/significant heating (the autotelic heating of substantial variation in for example, causing the microstructure of aluminium alloy body and/or performance) arranged beginning and/or completing cold working step (200).Those skilled in the art understand the aluminium alloy body can realize that the temperature that is caused by cold working step (200) increases, but this class cold working step (200) still is considered to cold working (200), because described process operation is beginning lower than the temperature that is considered to hot processing temperature.When using a plurality of cold-working operations to complete cold working step (200), each in these operations can adopt any above-mentioned temperature, described temperature can with front or after the temperature used of cold-working operation identical or different.

As mentioned above, usually when reaching enough low temperature, aluminium alloy body (140) after solid solution begins cold working (200).Usually, the aluminium alloy body has not been taked purpose/significant thermal treatment between solution treatment step (140) end and cold working step (200) beginning, that is, described method can solution treatment step (140) complete and cold working step (200) beginning between do not have thermal treatment.In some cases, finish in the near future to begin cold working step (200) (for example, in order to help lend some impetus to cold working) in solution treatment step (140).In one embodiment, after completing, solution treatment step (140) is no more than 72 hours beginning cold working steps (200).In other embodiments, after completing, solution treatment step (140) is no more than 60 hours, or be no more than 48 hours, or be no more than 36 hours, or be no more than 24 hours, or be no more than 20 hours, or be no more than 16 hours, or be no more than 12 hours, or the shorter time begins cold working step (200).In one embodiment, beginning cold working step (200) (for example, for continuous metal cast process) in several minutes or shorter time after solution treatment step (140) is completed.In another embodiment, be accompanied by completing of solution treatment step (140) and begin cold working step (200) (for example, for continuous metal cast process).

In other cases, with respect to solution treatment step (140) to complete through beginning cold working (200) after the long time can be enough.In these cases, can complete in solution treatment step (140) after a week or several weeks or one month or several months complete cold working step (200).

C. thermal treatment

Still with reference to Fig. 2, can complete afterwards heat treatment step (300) in cold working step (200)." thermal treatment " etc. means on purpose to heat the aluminium alloy body so that the aluminium alloy body reaches the temperature of a rising.Heat treatment step (300) can comprise with aluminium alloy body heating for some time and at a temperature that is enough to realize certain state or performance (for example, ductility of the intensity of selection, selection etc.) and heating.

After solution treatment, most of heat treatable alloy, for example the 2xxx aluminium alloy, show performance variation in room temperature.This is known as " natural aging ", can begin immediately after solid solution, or begin after one period incubation period.Different-alloy changes in wide scope in the speed of performance change during natural aging, and the approach that therefore reaches steady state can need only a couple of days or several years.In the situation that do not exist autotelic heating to occur, natural aging is not heat treatment step (300) due to natural aging.Yet natural aging can occur before and/or afterwards at heat treatment step (300).One predetermined time section (for example, from several minutes or a few hours to several weeks or longer time) can occur in heat treatment step (300) in natural aging before.Natural aging can be between solution treatment step (140), cold working step (200) and heat treatment step (300) or any one of these steps after occur.

Heat treatment step (300) is heated to a temperature in selected temperature range with the aluminium alloy body.For the purpose of heat treatment step (300), this temperature refers to the medial temperature of aluminium alloy body during heat treatment step (300).Heat treatment step (300) can comprise a plurality for the treatment of steps, for example in the first Temperature Treatment very first time section, and in second the second time period of Temperature Treatment.The first temperature can be more high or low than the second temperature, and very first time section can be shorter or long than the second time period.

Usually complete heat treatment step (300) so that the microstructure that non-recrystallization is dominant is realized/kept to the aluminium alloy body, such as hereinafter definition.As hereinafter describing in further detail, the microstructure that non-recrystallization is dominant can realize improved performance.In this point, heat treatment step (300) generally includes the temperature that the aluminium alloy body is heated to a rising, but this temperature below the recrystallization temperature of aluminium alloy body, that is, the aluminium alloy body will can not realized the microstructure that non-recrystallization is dominant at this temperature.For example, heat treatment step (300) can comprise and 2xxx aluminium alloy body being heated in 150 °F to 425 °F (perhaps higher) scopes but lower than the temperature of the recrystallization temperature of aluminium alloy body.

Can complete heat treatment step (300) (for example, performance or the performance combination in order to realize expecting/selecting) with any suitable method that continues the time period of one or more selections at the temperature that the aluminium alloy body is maintained one or more selections.In one embodiment, complete heat treatment step (300) in aging oven or suchlike device.In another embodiment, complete heat treatment step (300) in the cycle at baking vanish.The baking vanish cycle is used in car industry and other industries by a baking short time period (for example, 5-30 minute), the paint of coating is solidified.Can produce within the short time period in view of method as herein described and have high-intensity aluminium alloy body, as mentioned below, can complete heat treatment step (300) with baking vanish cycle etc., thereby eliminate the needs to independent heat treatment step and baking vanish step.Similarly, in another embodiment, can complete heat treatment step (300) in coating curing step or suchlike step.

D. cold working and thermal treatment combination

The combination of cold working step (200) and heat treatment step (300) can produce has the aluminium alloy body that improves performance.Think that the microstructure of combination results uniqueness of the high deformation of cold working step (200) and appropriate heat treatment condition, described microstructure can reach the combination (microstructure that vide infra (Microstructure)) of unconsummated intensity and ductility so far.Cold working step (200) helps the generation of the microstructure of gross distortion, and heat treatment step (300) helps precipitation hardening.For at least 25% the time, preferably more than 50%, and when taking suitable heat treatment step (300), can realize improved performance when cold working (200).

In a method, complete cold working step (200) and heat treatment step (300), in order to make the aluminium alloy body realize intensity (for example, tensile yield strength (R _0.2) or ultimate tensile strength (R _m)) increase.One or more strength increases of realizing that can be in L, LT or ST direction.

In one embodiment, complete cold working step (200) and heat treatment step (300), so that this aluminium alloy body is compared the acquisition strength increase with the reference sample (reference-version) of this aluminium alloy body under " cold working state ".In another embodiment, complete cold working step (200) and heat treatment step (300), so that this aluminium alloy body is compared the acquisition strength increase with the reference sample of this aluminium alloy body under the T6 state.In yet another embodiment, complete cold working step (200) and heat treatment step (300), so that this aluminium alloy body is compared the acquisition strength increase with the reference sample of this aluminium alloy body under the T87 state.In another embodiment, complete cold working step (200) and heat treatment step (300), increase so that this aluminium alloy body is compared the higher R-value of acquisition with the reference sample of this aluminium alloy body under the T4 state.These and other performances performance hereinafter partly is described.

" cold working state " (ACWC) means: (i) for the preparation of cold worked aluminium alloy body after solid solution; (ii) with the cold working of aluminium alloy body, (iii) solution treatment step (140) complete and the beginning of cold working step (200) between through being no more than 4 hours, and (iv) the aluminium alloy body is not heat-treated.Should measure the mechanical property of the aluminium alloy body of cold working state in completing 4-14 days of cold working step (200).In order to obtain the reference sample of " cold working state " lower aluminium alloy body, those skilled in the art usually will be for the preparation of cold worked aluminium alloy body (100) after solid solution, subsequently according to this aluminium alloy body of operation cold working as herein described (200), according to above-mentioned requirements, take out its performance under the cold working state of a part of aluminium alloy body measurement.And another part aluminium alloy body is processed according to novel method as herein described, then measure the performance of this part aluminium alloy body, therefore help the reference sample of aluminium alloy body under comparison cold working state and according to the performance of the aluminium alloy body of novel method processing as herein described (for example, relatively intensity, ductility, fracture toughness property).Because the reference sample of aluminium alloy body is that a part by this aluminium alloy body obtains, therefore should have identical composition with this aluminium alloy body by part aluminium alloy body.

" T6 state " etc. means also to be heat-treated to subsequently the aluminium alloy body of maximum strength state (differ with maximum strength and be no more than 1ksi) by solid solution; Be applicable to such alloy body, described alloy body after solid solution without cold working, described alloy body the leveling or aligning aspect the cold working effect can not be identified in the mechanical property limit value.As hereinafter describing in further detail, compare with the aluminium alloy body of T6 state, can realize excellent performance according to the aluminium alloy body that the novel method of this paper is produced.In order to obtain the reference sample of the aluminium alloy body under the T6 state, those skilled in the art will be for the preparation of cold worked aluminium alloy body (100) after solid solution, the part of this aluminium alloy body will be processed to T6 state (that is, the reference aluminium alloy body under the T6 state) subsequently.Process another part of this aluminium alloy body according to novel method as herein described, therefore help the reference sample of the aluminium alloy body under comparison T6 state and according to the performance of the aluminium alloy body of novel method processing as herein described (for example, relatively intensity, ductility, fracture toughness property).Because the reference sample of this aluminium alloy body is that a part from this aluminium alloy body obtains, therefore it has the composition identical with this aluminium alloy body.The reference sample of this aluminium alloy body may need processing (hot-work and/or cold working) the reference sample of this aluminium alloy body is made and the comparable product form of this new aluminum alloy body (for example, setting identical final thickness for rolled products) in solution treatment step (140) before.

" T4 state " etc. mean solid solution and subsequently natural aging treatment to the aluminium alloy body of stable state basically; Be applicable to such alloy body, described alloy body after solid solution without cold working, described alloy body the leveling or aligning aspect the cold working effect can not be identified in the mechanical property limit value.In order to obtain the reference sample of the aluminium alloy body under the T4 state, those skilled in the art will be for the preparation of cold worked aluminium alloy body (100) after solid solution, make subsequently a part of natural aging treatment of this aluminium alloy body to T4 state (that is, the reference sample of the aluminium alloy body under the T4 state).Process another part of this aluminium alloy body according to novel method as herein described, therefore help the reference sample of the aluminium alloy body under comparison T4 state and according to the performance of the aluminium alloy body of novel method processing as herein described (for example, relatively intensity, ductility, fracture toughness property).Because the reference sample of the aluminium alloy body part from this aluminium alloy body obtains, therefore it will have the composition identical with this aluminium alloy body.The reference sample of aluminium alloy body may need processing (hot-work or cold working) the reference sample of this aluminium alloy body is made and the comparable product form of this new aluminum alloy body (for example, setting identical final thickness for rolled products) in solution treatment step (140) before.

" T87 state " etc. means solid solution, cold working 10% (rolling or stretching), and is heat-treated to subsequently maximum strength state (differ with maximum strength and be no more than 1ksi).As hereinafter describing in further detail, with respect to the comparable aluminium alloy body that is in the T87 state, the aluminium alloy body of producing according to novel method as herein described can obtain excellent performance.In order to obtain the reference sample of the aluminium alloy body under the T87 state, those skilled in the art will be for the preparation of cold worked aluminium alloy body (100) after solid solution, a part with this aluminium alloy body is worked into T87 state (that is, the reference sample of the aluminium alloy body under the T87 state) subsequently.Process another part of this aluminium alloy body according to novel method as herein described, therefore help the reference sample of the aluminium alloy body under comparison T87 state and according to the performance of the aluminium alloy body of novel method processing as herein described (for example, relatively intensity, ductility, fracture toughness property).Because the reference sample of the aluminium alloy body part from this aluminium alloy body obtains, therefore it will have the composition identical with this aluminium alloy body.The reference sample of aluminium alloy body may need processing (hot-work and/or cold working) the reference sample of this aluminium alloy body is made and the comparable product form of this new aluminum alloy body (for example, setting identical final thickness for rolled products) in solution treatment step (140) before.

E. microstructure

I. recrystallize

Can complete cold working step (200) and heat treatment step (300), so that the microstructure that non-recrystallization is dominant is realized/kept to the aluminium alloy body.The microstructure that non-recrystallization is dominant means the aluminium alloy body and contains first kind crystal grain (in volume fraction) less than 50%, such as hereinafter definition.

The aluminium alloy body has the microstructure of crystallization." microstructure of crystallization " is the polycrystalline material structure.The microstructure of crystallization has crystal, is called in this article crystal grain." crystal grain " refers to the crystal of polycrystalline material.

" first kind crystal grain " means the crystal grain of the microstructure of those crystallizations that meet " the first crystal grain standard ", definition hereinafter, and adopt OIM (orientation mapping microscopy) sampling step to measure, describe hereinafter.Due to the microstructure of aluminium alloy body uniqueness, the application does not use conventional term " recrystal grain " or " non-recrystallization crystal grain ", and these terms are unclear in some cases and are the objects of dispute.And adopting term " first kind crystal grain " and " Second Type crystal grain ", the amount of the crystal grain of these types can correctly and accurately be measured by the method for calculation that describe in detail in the OIM sampling step.Therefore, term " first kind crystal grain " comprises all crystal grains that meets the first crystal grain standard, no matter and those skilled in the art whether will think this class crystal grain be non-recrystallization or recrystallize.

Completing OIM from T/4 (1/4 plane) position to the surface on L-ST plane analyzes.The size of sample to be analyzed generally will change on thickness.Before measurement, prepare the OIM sample by standard metallographic preparation method of sample.For example, usually use Buehler Si-C sand paper with the manual polishing of OIM sample 3 minutes, then with the Buehler diamond liquid polishing agent craft polishing with about 3 microns median sizes.Sample is processed 30-45 second in the polarization of fluoro-boron aqueous solution middle-jiao yang, function of the spleen and stomach.The phosphate aqueous solution that use contains chromium trioxide is denuded sample, with post-flush and dry.

" OIM sampling step " is as follows:

The software that uses is 5.31 version TexSEM Lab OIM data acquisition softwares (New Jersey EDAX company), and this software is connected to DigiView1612CCD photographic camera (Utah, USA TSL/EDAX) by FIREWIRE (California, USA Apple).SEM is JEOL JSM6510 (Tokyo JEOL company limited).

The OIM operational conditions is 70 ° of inclinations, operating distance 18mm, acceleration voltage 20kV, dynamic focusing and spot size 1 * 10 ^-7Amp.Drainage pattern is graticule mesh.By selecting, thereby gather orientation (that is, do not gather Hough peak information) in analysis.When 80X, for the sample of 2mm thickness, the size of the area (that is, frame) of each scanning is 2.0mm * 0.5mm by 3 microns strides, and for the sample of 5mm thickness, is 2.0mm * 1.2mm.Can use different frame signs according to thickness.The data that gather are with * .osc file output.This data can be used for calculating the volume fraction of first kind crystal grain, and are as mentioned below.

The calculating of the volume fraction of first kind crystal grain: adopt the data of * .osc file and the volume fraction that 5.31 version TexSEM Lab OIM analysis software calculate first kind crystal grain.Before calculating, can purify (single iteration cleanup) with tolerance angle, the smallest grain size=3 data point and single iteration of 15 ° and carry out data purification.Subsequently, use the first crystal grain standard (hereinafter), by the amount of this computed in software first kind crystal grain.

The first crystal grain standard: calculate by the grain orientation discrete (GOS) with 5 ° of crystal grain tolerance angles, the smallest grain size is three (3) individual data points, and confidence index is zero (0)." subregion (apply partition) is adopted in calculating before ", " comprising edge crystal grain (edge grain) " and " ignoring the twin boundaries definition " are all necessary, and should use " crystal grain average orientation " to complete calculating.Any crystal grain of GOS≤3 ° is first kind crystal grain.If the use multiframe is averaged the GOS data so.

" the first crystal particle volume " (FGV) means the volume of the first kind crystal grain of crystalline material.

" non-recrystallization per-cent " etc. is determined by following formula:

U _RX%=(1-FGV)*100%

As mentioned above, this aluminium alloy body generally includes the microstructure that non-recrystallization is dominant, that is, and and FGV＜0.50 and U _RX% 〉=50%.In one embodiment, this aluminium alloy body contains (in volume fraction) (that is, according to the definition that above provides, this aluminium alloy body at least 55% is not (the U of non-recrystallization higher than 0.45 first kind crystal grain _RX% 〉=55%)).In other embodiments, this aluminium alloy body can contain (in volume fraction) not higher than 0.40 first kind crystal grain (U _RX% 〉=60%), or not higher than 0.35 first kind crystal grain (U _RX% 〉=65%), or not higher than 0.30 first kind crystal grain (U _RX% 〉=70%), or not higher than 0.25 first kind crystal grain (U _RX% 〉=75%), or not higher than 0.20 first kind crystal grain (U _RX% 〉=80%), or not higher than 0.15 first kind crystal grain (U _RX% 〉=85%), or not higher than 0.10 first kind crystal grain (U _RXOr lower % 〉=90%).

Ii. texture

This aluminium alloy body can obtain unique microstructure.The microstructure of this uniqueness can be by the R-value explanation of the aluminium alloy body that obtains from the crystalline structure data.The microstructure of aluminium alloy body and its performance (for example, intensity, ductility, toughness, solidity to corrosion etc.) are relevant.

For purposes of this application, generate step according to the R-value and generate the R-value, be described hereinafter.

The R-value generates step:

Instrument: use to have computer-controlled utmost point figure unit and for the treatment of the data acquisition software of diagram data and ODF software (for example, the Rigaku software that the Rigaku diffractometer is included) x ray generator (for example, Rigaku Ultima III diffractometer (U.S. Rigaku, Texas Wood orchid is (The Woodlands) hereby)." X-ray diffraction basis " (the Elements of X-ray Diffraction) that shows according to B.D.Cullity, second edition, 1978 (Addison-Wesley metallurgy and material series book series) and Rigaku obtain repeller figure about the user manual (or other suitable similar diffractometer Hardware Description Manuals) of Ultima III diffractometer and Versatile apparatus.

Sample preparation: from the T/4 position to surface measurement utmost point figure.Therefore, be that 7/8 inch (LT) takes advantage of 1 for the sample (preferably) that generates the R-value ¹/ ₄Inch (L).Specimen size can change based on metering facility.Before measuring the R-value, can prepare in the following manner sample:

1. process rolling plane extremely than T/4 planar thick 0.01 from a side " (if thickness is rational); With

2. chemical milling is to the T/4 position.

The X-ray measurement of utmost point figure: the reflection of utmost point figure (based on the Schulz reflection method)

1. sample is contained on the sample ring carriage with the indication of sample rolling direction

2. with in insertion utmost point figure unit, sample holder unit

3. the direction of sample is navigated to the position of the horizontal plane that is same as utmost point figure unit (β=0 °)

Application standard divergent slit (DS), have Ni K _βThe standard pole figure of spectral filter receives slit (RS) and standard scatter slit (SS) (2 θ and the peak width of determining to depend on radiation used, peak of slit).Rigaku Ultima III diffractometer adopts 2/3deg DS, 5mm RS and 6mm SS.

5. the operating voltage that power settings is become to recommend and electric current (radiation is defaulted as 40KV44mA for Cu, and adopts the Ni spectral filter on Ultima III)

With 5 ° of strides from Al ₍₁₁₁₎, Al ₍₂₀₀₎And Al ₍₂₂₀₎The α at peak=15 °, β=0 ° to α=90 °, β=355 ° measure background intensity and at 1 second (3 utmost point figure are normally enough for accurate ODF) of each stride counting

With 5 ° of strides from Al ₍₁₁₁₎, Al ₍₂₀₀₎, Al ₍₂₂₀₎And Al ₍₃₁₁₎The α at peak=15 °, β=0 ° to α=90, β=355 ° measure peak intensity and each stride counting 1 second

8. during measuring, thereby being vibrated to obtain larger sampling area with per second 2cm, sample improves the sampling statistics

9. from peak intensity subtracting background intensity (this is completed by user's special software usually)

10. (usually being completed by user's special software) proofreaied and correct in absorption

Usually will export data changes into for the form of inputting ODF software.ODF software is data normalization, calculates ODF, and the utmost point figure of normalized again.Utilize this information, adopt the Taylor-Bishop-Hill model (referring to Kuroda, M. wait the people, Texture optimization of rolled aluminum alloy sheets using a genetic algorithm, Materials Science and Engineering A385 (2004) 235-244 and Man, Chi-Sing, On the r-value of textured thin plate metals, International Journal of Plasticity18 (2002) 1683-1706) calculating R-value.

Compare with the material of producing routinely, the aluminium alloy body of producing according to method as herein described can obtain high stdn R-value." stdn R-value " etc. mean with respect to rolling direction 0 ° of angle by the standardized R-value of the R-value of RV-control sample.For example, if the RV-control sample is obtaining 0.300 R-value with respect to rolling direction 0 ° of angle, this R-value and every other R-value can be passed through divided by 0.300 stdn.

" RV-control sample " etc. means to take from the control sample of reference sample aluminium alloy body under the T4 state (in above definition).

" rolling direction " etc. means the L-direction (referring to Figure 13) of rolled products.For non-rolled products, and in the context of mentioning the R-value, the main direction that " rolling direction " etc. means to extend (for example, the direction of extrusion).For purposes of this application, with respect to 0 ° to 90 ° angle of rolling direction and with a plurality of R-values of the increasing amount Calculating material of 5 °.For simple purpose, " orientation angle " is used to refer to phrase " with respect to the angle of rolling direction " sometimes.

" maximum stdn R-value " etc. means the maximum stdn R-value that obtains in any angle with respect to rolling direction.

" maximum RV angle " etc. means to obtain the angle of maximum stdn R-value.

As nonrestrictive example, table 2 provides the R-value (nonstandardized technique and stdn) that contains the RV-control sample and according to the form of the R-value (nonstandardized technique and stdn) of the aluminium alloy body of novel method processing as herein described.

Table 2

Figure 10 is stdn R-value and the stdn R-value of 75% cold working sample and the graphic representation that orientation angle has functional relation of contrast.Figure 10 also comprises the stdn R-value of 25%, 50% and 85% cold worked aluminium alloy body.

As shown in figure 10, the aluminium alloy body of example obtains the R-value more much higher than RV-control sample, particularly between the orientation angle with respect to 20 ° of rolling directions and 70 °.For 75% cold worked alloy body, obtain 8.886 maximum stdn R-value the maximum RV angles of 50 °.The RV-control sample obtains 1.298 maximum stdn R-value the maximum RV angle of 45 °.These R-values can show in the texture of comparing lower new aluminum alloy body with the aluminium alloy body of producing routinely (and so show microstructure).

In a scheme, the aluminium alloy body of processing according to novel method as herein described can be obtained up to few 2.0 maximum stdn R-value.In one embodiment, the new aluminum alloy body can be obtained up to few 2.5 maximum stdn R-value.In other embodiments, it is few 3.0 that the new aluminum alloy body can be obtained up to, and perhaps at least 3.5, perhaps at least 4.0, perhaps at least 4.5, perhaps at least 5.0, at least 5.5, perhaps at least 6.0, perhaps at least 6.5, perhaps at least 7.0, perhaps at least 7.5, perhaps at least 8.0, perhaps at least 8.5, perhaps at least 8.75, or higher maximum stdn R-value.Can obtain maximum stdn R-value the orientation angle of 20 ° to 70 °.In certain embodiments, can obtain maximum stdn R-value the orientation angle of 30 ° to 70 °.In other embodiments, can obtain maximum stdn R-value the orientation angle of 35 ° to 65 °.In another embodiment, can obtain maximum stdn R-value the orientation angle of 40 ° to 65 °.In another embodiment, can obtain maximum stdn R-value the orientation angle of 45 ° to 60 °.In other embodiments, can obtain maximum stdn R-value the orientation angle of 45 ° to 55 °.

In another scheme, can obtain the maximum stdn R-value than RV-control sample high at least 200% at the maximum RV angle of new aluminum alloy body according to the aluminium alloy body of novel method as herein described processing.In this scheme, the stdn R-value of new aluminum alloy body is compared with the stdn R-value of RV-control sample on the angle of the maximum RV of new aluminum alloy body angle appearance.For example, as above shown in Figure 10 and table 2, compare in the stdn R-at identical 50 ° of angles value with the RV-control sample, 75% cold worked aluminium alloy body realizes that at its maximum RV angle of 50 ° 729% stdn R-value increases (8.886/1.219*100%=729%).In one embodiment, at the maximum RV angle of new aluminum alloy body, the aluminium alloy body can be realized the maximum stdn R-value than RV-control sample height at least 250%.In other embodiments, at the maximum RV angle of new aluminum alloy body, this aluminium alloy body can be realized than RV-control sample height 300% at least, or height at least 350%, or height at least 400%, or height at least 450%, or height at least 500%, or height at least 550%, or height at least 600%, or height at least 650%, or height at least 700%, or height at least 750%, or higher maximum stdn R-value.

In another scheme, can obtain maximum stdn R-value than the maximum stdn R-value height at least 200% of RV-control sample according to the aluminium alloy body of novel method as herein described processing.In this scheme, do not consider the angle that maximum stdn R-value occurs, the maximum stdn R-value of new aluminum alloy body is compared with the maximum stdn R-value of RV-control sample.For example, as above shown in Figure 10 and table 2, the maximum stdn R-value that 75% cold worked aluminium alloy body obtains when the orientation angle of 50 ° is 8.886.RV-control sample maximum stdn R-value when the orientation angle of 45 ° is 1.298.Therefore, 75% cold worked aluminium alloy body obtains 685% increase ((8.886/1.298) * 100%=685%) with respect to the RV-control sample on maximum stdn R-value.In one embodiment, the aluminium alloy body can obtain the maximum stdn R-value than the maximum stdn R-value high at least 250% of RV-control sample.In other embodiments, this aluminium alloy body can obtain the maximum stdn R-value height at least 300% than RV-control sample, or height at least 350%, or height at least 400%, or height at least 450%, or height at least 500%, or height at least 550%, or height at least 600%, or height at least 650%, or height at least 700%, or higher maximum stdn R-value.

Iii. Photomicrograph

The Photomicrograph of some 2xxx aluminium alloy bodies of producing according to novel method as herein described is shown in Figure 11 b-Figure 11 e.Figure 11 a is the microstructure of the sample for reference of aluminium alloy body under the T6 state.Figure 11 b-Figure 11 e is respectively the microstructure with 25%, 50%, 75% and 85% cold worked new aluminum alloy body.These Photomicrographs have shown some aspects of using unique microstructure that novel method described herein obtains.As shown in the figure, the crystal grain of new aluminum alloy body is rendered as anisometric (elongation) crystal grain.For 75% and 85% cold worked aluminium alloy body, crystalline-granular texture is rendered as fibrous/rope form, and have a plurality of shear zones.These unique microstructures can be made contributions to the improvement in performance of new aluminum alloy body.

The step of F. carrying out after optional thermal treatment

At heat treatment step (300) afterwards, 2xxx aluminium alloy body can pass through multiple optional final processing (400).For example, follow heat treatment step (300) or after heat treatment step, 2xxx aluminium alloy body can be through multiple additional processing or polishing operation (for example, basically do not affect forming operation, leveling or the straightening operation of mechanical property, as stretching and/or other operations, as cutting, anodizing, japanning, polishing, polishing).Optional final treatment step (400) can not be any can substantial effect aluminium alloy bulk microstructure autotelic/significant thermal treatment (for example, can not be any annealing steps).The microstructure that therefore, can keep the combination by cold working step (200) and heat treatment step (300) to obtain.

In a scheme, one or more optional final treatment steps (400) can follow heat treatment step (300) to complete.In one embodiment, optional final treatment step (400) can comprise moulding, and can follow (for example, side by side) heat treatment step (300) to complete this forming step.In one embodiment, due to the forming operation of following and heat treatment operation, this aluminium alloy body can be basically final form (for example, formed automobile external door panel and/or inner panel during heat treatment step).

G. form

As mentioned above, this aluminium alloy body is to be made by the 2xxx aluminium alloy.The 2xxx aluminium alloy is to contain except aluminium with the aluminium alloy of copper as the alloying constituent that is dominant.For purposes of this application, the 2xxx aluminium alloy has 0.5wt.%Cu and the aluminium alloy of 8.0wt.%Cu at least at the most, and wherein, described copper is the alloying element that is dominant except aluminium.As give a definition, the 2xxx aluminium alloy also can comprise secondary element, element and/or other elements.Copper, secondary element and/or element can promote strain hardening response, precipitation hardening response and combination thereof.In one embodiment, at least some alloying elements promote strain hardening response and precipitation hardening response.And then, can realize the improvement of performance.

In one embodiment, the 2xxx aluminium alloy comprises the Cu of 1.0wt.% at least.In another embodiment, the 2xxx aluminium alloy comprises the Cu of 2.0wt.% at least.In yet another embodiment, 2xxx aluminium alloy body comprises the Cu of 2.5wt.% at least.

In one embodiment, the 2xxx aluminium alloy comprises not the Cu higher than 7.0wt.%.In another embodiment, the 2xxx aluminium alloy comprises not the Cu higher than 6.0wt.%.In another embodiment, the 2xxx aluminium alloy comprises not the Cu higher than 5.0wt.%.In yet another embodiment, the 2xxx aluminium alloy comprises not the Cu higher than 4.5wt.%.

The 2xxx aluminium alloy can comprise secondary element.Secondary element is from by selecting magnesium, silver, lithium and zinc and the group that constitutes thereof.

When using magnesium, the 2xxx aluminium alloy generally includes the Mg of 0.10wt.% at least.In one embodiment, the 2xxx aluminium alloy comprises the Mg of 0.20wt.% at least.The 2xxx aluminium alloy comprises not the Mg higher than 3.0wt.% usually, as not higher than the Mg of 2.5wt.%.In one embodiment, the 2xxx aluminium alloy comprises not the Mg higher than 2.0wt.%.In another embodiment, the 2xxx aluminium alloy comprises not the Mg higher than 1.5wt.%.In other embodiments, magnesium can be used as impurity and exists, and exists with 0.09wt.% or lower level in these embodiments.

When using silver, the 2xxx aluminium alloy comprises the Ag of 0.05wt.% at least usually.In one embodiment, the 2xxx aluminium alloy comprises the Ag of 0.10wt.% at least.In yet another embodiment, the 2xxx aluminium alloy comprises the Ag of 0.15wt.% at least.In another embodiment, the 2xxx aluminium alloy comprises the Ag of 0.20wt.% at least.The 2xxx aluminium alloy comprises not the Ag higher than 3.0wt.% usually.In one embodiment, the 2xxx aluminium alloy comprises not the Ag higher than 2.0wt.%.In other embodiments, the 2xxx aluminium alloy comprises not higher than the Ag of 1.0wt.% or not higher than the Ag of 0.75wt.%.In other embodiments, silver can be used as impurity and exists, and exists with 0.04wt.% or lower level in these embodiments.

When using lithium, the 2xxx aluminium alloy comprises the Li of 0.05wt.% at least usually.In one embodiment, the 2xxx aluminium alloy comprises the Li of 0.25wt.%.In yet another embodiment, the 2xxx aluminium alloy comprises the Li of 0.50wt.% at least.In another embodiment, the 2xxx aluminium alloy comprises the Li of 0.60wt.% at least.The 2xxx aluminium alloy comprises not the Li higher than 3.0wt.% usually.In one embodiment, the 2xxx aluminium alloy comprises not the Li higher than 2.5wt.%.In other embodiments, the 2xxx aluminium alloy comprises not the Li higher than 2.0wt.%.In other embodiments, lithium can be used as impurity and exist, and exists with 0.04wt.% or lower level in these embodiments.

When using zinc, the 2xxx aluminium alloy comprises the Zn of 0.10wt.% at least usually.In one embodiment, the 2xxx aluminium alloy comprises the Zn of 0.25wt.%.In another embodiment, the 2xxx aluminium alloy comprises the Zn of 0.50wt.% at least.The 2xxx aluminium alloy comprises not the Zn higher than 7.0wt.% usually.In one embodiment, the 2xxx aluminium alloy comprises not the Zn higher than 6.0wt.%.In other embodiments, the 2xxx aluminium alloy comprises not the Zn higher than 5.0wt.%, or not higher than the Zn of 4.0wt.%, or not higher than the Zn of 3.0wt.%, or not higher than the Zn of 2.0wt.%.In other embodiments, zinc can be used as impurity and exist, and exists with 0.09wt.% or lower level in these embodiments.

For multiple purpose, the 2xxx aluminium alloy can comprise multiple element, for example strengthen mechanical property, physicals or corrosive nature (namely, intensity, toughness, fatigue resistance, solidity to corrosion), to strengthen the performance under heating up, to help casting, to control casting or to forge crystalline-granular texture, and/or with the enhancing machinability, etc.When having above-mentioned purpose, these element can comprise following one or more: (i) be at most separately one or more in Mn, Si, Fe, Sn, Bi, Pb and the Ni of 2.0wt.%, (ii) be at most separately the Sr of 1.0wt.% and one or more in Sb, (iii) be at most separately one or more in 0.5wt.%V, Cr, Zr, Sc, Ti, Hf, Mo, Co and rare earth element.When having above-mentioned purpose, element is contained in alloy with the amount of 0.01wt.% at least usually.

The 2xxx aluminium alloy can comprise impurity, as iron and silicon.When silicon and/or iron were not contained in alloy as element, silicon and/or iron can be used as impurity and are contained in the 2xxx aluminium alloy.In these embodiments, the 2xxx aluminium alloy comprises not usually higher than the silicon of 0.50wt.% and any in iron.In one embodiment, the 2xxx aluminium alloy comprises not higher than the silicon of 0.25wt.% and any in iron.In another embodiment, the 2xxx aluminium alloy comprises not higher than the silicon of 0.15wt.% and any in iron.In yet another embodiment, the 2xxx aluminium alloy comprises not higher than the silicon of 0.10wt.% and any in iron.In another embodiment, the 2xxx aluminium alloy comprises not higher than the silicon of 0.05wt.% and any in iron.

The 2xxx aluminium alloy contains " other elements " (for example, casting auxiliary agent and impurity except Fe and Si) of low amount usually.Other elements mean, except above-mentioned aluminium, zinc, secondary element (when comprising), element (when comprising) and Fe and Si impurity (when comprising), can be included in any other element of the periodic table of elements in the 2xxx aluminium alloy.Outside deironing and silicon, when any secondary element and/or element were included in alloy as impurity, these elements fell in the scope of " other elements ".For example, if the 2xxx alloy comprises as impurity and not as the zinc of alloy addition, zinc will fall in the scope of " other elements ".As another example, if Mn, Ag and Zr are included in the 2xxx alloy as alloy addition, these element will not fall in the scope of " other elements ", but other element are owing to being included in alloy as impurity, and they will fall in the scope of other elements.Yet, as mentioned above, if silicon or iron are included in the 2xxx alloy as impurity, because they have the impurity limit value of the restriction of self, will can not fall in the scope of " other elements ".

Usually, any element that this aluminium alloy body contains other elements is no more than 0.25wt.%, and total combined amount of these other elements is no more than 0.50wt.%.In one embodiment, each of these other elements is no more than 0.10wt.% separately in the 2xxx aluminium alloy, and total combined amount of these other elements is no more than 0.35wt.% in the 2xxx aluminium alloy.In another embodiment, each of these other elements is no more than 0.05wt.% separately in the 2xxx aluminium alloy, and total combined amount of these other elements is no more than 0.15wt.% in the 2xxx aluminium alloy.In another embodiment, each of these other elements is no more than 0.03wt.% separately in the 2xxx aluminium alloy, and total combined amount of these other elements is no more than 0.1wt.% in the 2xxx aluminium alloy.

In a scheme, the 2xxx aluminium alloy comprises:

0.5 to the Cu of 8.0wt.%, wherein, described Cu is the alloying element that is dominant except aluminium;

One or more following secondary elements randomly:

0.10 to the Mg of 3.0wt.%,

0.05 to the Ag of 3.0wt.%,

0.05 to the Li of 3.0wt.%, and

0.10 to the Zn of 6.0wt.%,

One or more following element randomly:

(i) be at most separately one or more in Mn, Si, Fe, Sn, Bi, Pb and the Ni of 2.0wt.%;

(ii) be at most separately the Sr of 1.0wt.% and one or more in Sb;

(iii) be at most separately one or more in V, Cr, Zr, Sc, Ti, Hf, Mo, Co and the rare earth element of 0.5wt.%;

If be not included in the 2xxx aluminium alloy as element:

The Fe as impurity of 0.5wt.% at the most;

The Si as impurity of 0.5wt.% at the most;

Surplus is aluminium and other elements, and wherein, described other elements are limited to and are no more than separately 0.25wt.%, and amounts to and be no more than 0.5wt.%.

The total amount of main alloying element, secondary alloying element and the 3rd alloying element should be selected so that suitably solid solution of aluminium alloy body (for example, promoting sclerosis when limiting the amount of constituent particle).

in one embodiment, the 2xxx aluminium alloy is following a kind of by in the forging 2xxx aluminium alloy of association of Alcoa definition: 2001, 2002, 2004, 2005, 2006, 2007, 2007A, 2007B, 2008, 2009, 2010, 2011, 2011A, 2111, 2111A, 2111B, 2012, 2013, 2014, 2014A, 2214, 2015, 2016, 2017, 2017A, 2117, 2018, 2218, 2618, 2618A, 22198, 2319, 2419, 2519, 2021, 2022, 2023, 2024, 2024A, 2124, 2224, 2224A, 2324, 2424, 2524, 2025, 2026, 2027, 2028, 2028A, 2028B, 2028C, 2030, 2031, 2032, 2034, 2036, 2037, 2038, 2039, 2139, 2040, 2041, 2044, 2045, 2050, 2056, 2060, 2090, 2091, 2094, 2095, 2195, 2196, 2097, 2197, 2297, 2397, 2098, 2198, 2099 and 2199.

In one embodiment, the 2xxx aluminium alloy comprises and makes the 2xxx aluminium alloy not contain or be substantially free of the amount of the alloying element of solubility constituent particle after solid solution.In one embodiment, the 2xxx aluminium alloy comprises the amount that makes the 2xxx aluminium alloy comprise the alloying element of low amount (for example, limited/minimum) solubility constituent particle after solid solution.In other embodiments, the amount of controlled soluble constituent particle is useful to the 2xxx aluminium alloy.

H. performance

The new 2xxx aluminium alloy body of producing with novel method as herein described can obtain improved over-all properties.

I. intensity

As mentioned above, can complete cold working step (200) and heat treatment step (300), increase to some extent thereby realize comparing with the aluminium alloy body under cold working state and/or T6 state on intensity.Strength property is measured according to ASTM E8 and B557 usually.

In a scheme, with respect to the reference sample of the aluminium alloy body that is in the T6 state, aluminium alloy body of the present invention is being realized at least 5% increase aspect intensity (TYS and/or UTS).In one embodiment, with respect to the reference sample of the aluminium alloy body that is in the T6 state, the tensile yield strength of aluminium alloy body of the present invention has obtained at least 6% increase.in other embodiments, reference sample with respect to the aluminium alloy body under the T6 state, the tensile yield strength of aluminium alloy body of the present invention has increased at least 8%, perhaps tensile yield strength has increased at least 10%, perhaps tensile yield strength has increased at least 12%, perhaps tensile yield strength has increased at least 14%, perhaps tensile yield strength has increased at least 16%, perhaps tensile yield strength has increased at least 18%, perhaps tensile yield strength has increased at least 20%, perhaps tensile yield strength has increased at least 22%, perhaps tensile yield strength has increased at least 24%, perhaps tensile yield strength has increased at least 26%, perhaps tensile yield strength has increased at least 28%, perhaps tensile yield strength has increased at least 30%, perhaps tensile yield strength has increased at least 32%, perhaps tensile yield strength has increased at least 34%, perhaps tensile yield strength has increased at least 36%, perhaps tensile yield strength has increased at least 38%, perhaps tensile yield strength has increased at least 40%, perhaps increase more.These increases can realize on L and/or LT direction.

In a relevant embodiment, with respect to the reference sample of the aluminium alloy body that is in the T6 state, aluminium alloy body of the present invention can be realized at least 6% increase aspect ultimate tensile strength.in other embodiments, reference sample with respect to the aluminium alloy body that is in the T6 state, the ultimate tensile strength of aluminium alloy body of the present invention can realize at least 8% increase, perhaps the ultimate tensile strength increase at least 10%, perhaps the ultimate tensile strength increase at least 12%, perhaps the ultimate tensile strength increase at least 14%, perhaps the ultimate tensile strength increase at least 16%, perhaps the ultimate tensile strength increase at least 18%, perhaps the ultimate tensile strength increase at least 20%, perhaps the ultimate tensile strength increase at least 22%, perhaps the ultimate tensile strength increase at least 24%, perhaps the ultimate tensile strength increase at least 26%, perhaps the ultimate tensile strength increase at least 28%, perhaps the ultimate tensile strength increase at least 30%, perhaps the ultimate tensile strength increase at least 32%, perhaps increase more.These increases can realize on L and/or LT direction.

In a scheme, to compare with the reference sample of aluminium alloy body under the cold working state, aluminium alloy body of the present invention has obtained identical at least tensile yield strength.In one embodiment, compare with the reference sample of aluminium alloy body under the cold working state, the tensile yield strength of this aluminium alloy body has been realized at least 2% increase.in other embodiments, compare with the reference sample of aluminium alloy body under the cold working state, the tensile yield strength of this aluminium alloy body has increased at least 4%, perhaps tensile yield strength has increased at least 6%, perhaps tensile yield strength has increased at least 8%, perhaps tensile yield strength has increased at least 10%, perhaps tensile yield strength has increased at least 12%, perhaps tensile yield strength has increased at least 14%, perhaps tensile yield strength has increased at least 16%, perhaps tensile yield strength has increased at least 18%, perhaps tensile yield strength has increased at least 20%, perhaps tensile yield strength has increased at least 22%, perhaps tensile yield strength has increased at least 24%, perhaps tensile yield strength has increased at least 26%, perhaps tensile yield strength has increased at least 28%, perhaps tensile yield strength has increased at least 30%, perhaps increased more.About ultimate tensile strength, can obtain similar result.These increases can realize on L and/or LT direction.

In a scheme, with respect to the aluminium alloy body that is in the T87 state, aluminium alloy body of the present invention has been realized at least 5% increase aspect tensile yield strength.In one embodiment, with respect to the aluminium alloy body that is in the T87 state, this aluminium alloy body has been realized at least 6% increase aspect tensile yield strength.in other embodiments, with respect to the aluminium alloy body that is in the T87 state, the tensile yield strength of this aluminium alloy body can increase at least 8%, perhaps tensile yield strength can increase at least 10%, perhaps tensile yield strength can increase at least 12%, perhaps tensile yield strength can increase at least 14%, perhaps tensile yield strength can increase at least 16%, perhaps tensile yield strength can increase at least 18%, perhaps tensile yield strength can increase at least 20%, perhaps tensile yield strength can increase at least 22%, perhaps tensile yield strength can increase at least 24%, perhaps tensile yield strength can increase more.These increases can realize on L and/or LT direction.About ultimate tensile strength, can obtain similar result.

In one embodiment, new 2xxx aluminium alloy body reaches the typical tensile yield strength of 65ksi at least on the LT direction.in other embodiments, new 2xxx aluminium alloy body accessible typical tensile yield strength on the LT direction is respectively: 66ksi at least, or 67ksi at least, or 68ksi at least, or 69ksi at least, or 70ksi at least, or 71ksi at least, or 72ksi at least, or 73ksi at least, or 74ksi at least, or 75ksi at least, or 76ksi at least, or 77ksi at least, or 78ksi at least, or 79ksi at least, or 80ksi at least, or 81ksi at least, or 82ksi at least, or 83ksi at least, or 84ksi at least, or 85ksi at least, or 86ksi at least, or 87ksi at least, or 88ksi at least, or 89ksi at least, or 90ksi at least, or 91ksi at least, or 92ksi at least, or 93ksi at least, or 94ksi at least, or higher.Vertically can obtain similar results on (L).

In a relevant embodiment, new 2xxx aluminium alloy body reaches the typical limits tensile strength of 68ksi at least on the LT direction.in other embodiments, new 2xxx aluminium alloy body accessible typical limits tensile strength on the LT direction is respectively: 69ksi at least, or 70ksi at least, or 71ksi at least, or 72ksi at least, or 73ksi at least, or 74ksi at least, or 75ksi at least, or 76ksi at least, or 77ksi at least, or 78ksi at least, or 79ksi at least, or 80ksi at least, or 81ksi at least, or 82ksi at least, or 83ksi at least, or 84ksi at least, or 85ksi at least, or 86ksi at least, or 87ksi at least, or 88ksi at least, or 89ksi at least, or 90ksi at least, or 91ksi at least, or 92ksi at least, or 93ksi at least, or 94ksi at least, or 95ksi at least, or 96ksi at least, or 97ksi at least, or 98ksi at least, or 99ksi at least, or 100ksi at least, or higher.Vertically can obtain similar results on (L).

With respect to the reference sample of the 2xxx aluminium alloy body that is in T6 and/or T87 state, new 2xxx aluminium alloy body can obtain high intensity within the shorter time period.In one embodiment, new 2xxx aluminium alloy body time of realizing its maximum strength is than the reference sample of the aluminium alloy body that is in T6 and/or T87 state soon at least 10%.As an example of the course of processing fast 10%, if the T6 sample of 2xxx aluminium alloy body reaches its maximum strength in the course of processing of 35 hours, so new 2xxx aluminium alloy body will reach its maximum strength within 31.5 hours or shorter time.In other embodiments, compare with the reference sample of the 2xxx aluminium alloy body that is in T6 and/or T87 state, new 2xxx aluminium alloy body reaches the time fast at least 20% of its maximum strength, fast at least 25%, or fast at least 30%, or fast at least 35%, fast at least 40%, or fast at least 45%, or fast at least 50%, fast at least 55%, or fast at least 60%, or fast at least 65%, fast at least 70%, or fast at least 75%, or fast at least 80%, or fast at least 85%, or fast at least 90%, perhaps faster.

In one embodiment, new 2xxx aluminium alloy body reaches its maximum strength in less than the heat treatment time of 10 hours.In other embodiments, new 2xxx aluminium alloy body is less than 9 hours or less than 8 hours or less than 7 hours or less than 6 hours or less than 5 hours or less than 4 hours or less than 3 hours or less than 2 hours or less than 1 hour or less than 50 minutes or less than 40 minutes or less than 30 minutes or less than 20 minutes or less than 15 minutes or reach its maximum strength less than in 10 minutes or still less heat treatment time.Because heat treatment time is shorter, makes with baking vanish cycle or coating curing and come the new 2xxx aluminium alloy body of thermal treatment to become possibility.

Ii. ductility

Aluminium alloy body of the present invention can be realized good ductility and combine with above-mentioned intensity.In a scheme, this aluminium alloy body reaches and surpasses 4% unit elongation (L and/or LT).In one embodiment, this aluminium alloy body obtains at least 5% unit elongation (L and/or LT).In other embodiments, the unit elongation that this aluminium alloy body can reach (L and/or LT) is respectively: at least 6%, or at least 7%, or at least 8%, or at least 9%, or at least 10%, or at least 11%, or at least 12%, or at least 13%, or at least 14%, or at least 15%, or at least 16%, or higher.

Iii. fracture toughness property

New 2xxx aluminium alloy body can be realized good fracture toughness property performance.Toughness properties is usually according to being used for plane strain fracture toughness (for example, K _ICAnd K _Q) ASTM E399 and ASTM B645 and according to being used for plane stress toughness (for example, K _appAnd K _R25) ASTM E561 and B646 measure.

In one embodiment, with respect to the reference sample of the aluminium alloy body that is in T6 and/or T87 state, the toughness drop of new 2xxx aluminium alloy body is no more than 10%.In other embodiments, reference sample with respect to the 2xxx aluminium alloy body that is in T6 and/or T87 state, the toughness drop of new 2xxx aluminium alloy body is no more than 9%, or is no more than 8%, or is no more than 7%, or be no more than 6%, or be no more than 5%, or be no more than 4%, or be no more than 3%, or be no more than 2%, or be no more than 1%.In one embodiment, new 2xxx aluminium alloy body has been realized toughness the toughness with the reference sample of the 2xxx aluminium alloy body that is in the T6 state is identical at least.

In other embodiments, aluminium alloy body of the present invention has been realized improvement aspect fracture toughness property.In these embodiments, with respect to the aluminium alloy body that is in T6 and/or T87 state, the fracture toughness property of this new aluminum alloy body has obtained at least 1% increase.In one embodiment, with respect to the aluminium alloy body that is in T6 and/or T87 state, the fracture toughness property of this new aluminum alloy body has obtained at least 3% increase.In other embodiments, with respect to the aluminium alloy body that is in T6 and/or T87 state, the fracture toughness property of this new aluminum alloy body has obtained at least 5% increase, or fracture toughness property increase at least 7%, or fracture toughness property increase at least 9%, or fracture toughness property increase at least 11%, or fracture toughness property increase at least 13%, or fracture toughness property increase at least 15%, or fracture toughness property increase at least 17%, or fracture toughness property increase at least 19%, or fracture toughness property increase at least 21%, or fracture toughness property increase at least 23%, or fracture toughness property increase at least 25%, or the fracture toughness property increase is more.These increases can realize on L-T and/or T-L direction, and can be about plane strain fracture toughness (for example, K _ICOr K _Q) and/or about plane stress toughness (for example, K _appAnd K _R25).

Iv. stress corrosion cracking

New 2xxx aluminium alloy body can be realized good anti-stress-corrosion crack.Anti-stress-corrosion crack (SCC) property is measured according to ASTM G47 usually.For example, new 2xxx aluminium alloy body can obtain good intensity and/or toughness, and has good SCC solidity to corrosion.In one embodiment, new 2xxx aluminium alloy body reaches 1 grade of solidity to corrosion.In another embodiment, new 2xxx aluminium alloy body reaches 2 grades of solidity to corrosions.In yet another embodiment, new 2xxx aluminium alloy body reaches 3 grades of solidity to corrosions.In another embodiment, new 2xxx aluminium alloy body reaches 4 grades of solidity to corrosions.

V. outward appearance

Aluminium alloy body according to the novel method processing of putting down in writing herein can obtain improved outward appearance.Following appearance standard can use Hunterlab Dorigon II (Hunter Associates Laboratory INC, Reston, VA) or analogous instrument to measure.

Compare with the reference aluminium alloy body that is in the T6 state, the aluminium alloy body of the novel method processing of putting down in writing according to this paper can be realized high at least 5% specular reflectance.In one embodiment, compare with the reference aluminium alloy body that is in the T6 state, new aluminium alloy body obtains high at least 6% specular reflectance.In other embodiments, compare with the reference aluminium alloy body that is in the T6 state, new aluminium alloy body obtains high at least 7% specular reflectance, or high at least 8% specular reflectance, or at least 9% specular reflectance, or high at least 10% specular reflectance, or high at least 11% specular reflectance, or high at least 12% specular reflectance, or high at least 13% specular reflectance, perhaps higher specular reflectance.

Compare with the reference aluminium alloy body that is in the T6 state, the aluminium alloy body of the novel method processing of putting down in writing according to this paper can be realized high at least 10% 2 degree diffusions (2degree diffuseness).In one embodiment, and be in comparing with reference to the aluminium alloy body of T6 state, new aluminium alloy body obtains high at least 12% 2 degree diffusions.In other embodiments, compare with the reference aluminium alloy body that is in the T6 state, new aluminium alloy body obtains high at least 14% 2 degree diffusions, or high at least 16% 2 degree diffusions, or high at least 18% 2 degree diffusions, or high at least 20% 2 degree diffusions, or high at least 22% 2 degree diffusions, or 2 degree diffusions of higher degree.

Compare with the reference aluminium alloy body that is in the T6 state, the aluminium alloy body of the novel method processing of putting down in writing according to this paper can be realized high at least 15% 2 image definitions (2 image clarity).In one embodiment, and be in comparing with reference to the aluminium alloy body of T6 state, new aluminium alloy body obtains high at least 18% 2 image definitions.In other embodiments, compare with the reference aluminium alloy body that is in the T6 state, new aluminium alloy body obtains high at least 21% 2 image definitions, or high at least 24% 2 image definitions, or high at least 27% 2 image definitions, or high at least 30% 2 image definitions, or 2 higher image definitions.

I. product application

Novel method as herein described can have suitability in multiple product is used.In one embodiment, the product of making by novel method as herein described is used for aerospace application, comprising such as wing cover (upper and lower) or stringer/stiffener, fuselage skin or stringer, rib, framework, spar, seat guide rail, dividing plate, bulkhead, empennage (as horizontal stabilizer and drag iron), floor bearer, seat guide rail, hatch door and controlsurface parts (for example, yaw rudder, aileron) etc. on every side.By using this product, can obtain many potential benefits in these parts, such as the toughness that comprises higher intensity, excellent solidity to corrosion, improved fatigue crack germinating and extendability and enhancing etc.The improved combination of these performances can cause weight saving or shortens inspection intervals or cause simultaneously both.

In another embodiment, the product of making by novel method as herein described is used for ordnance/ballistics/Military Application, comprising for example being used for cartridge and armor.Cartridge can comprise the cartridge that those are used for miniweapon and gun or are used for cannon bomb or tank gun cartridge.Other possible ammunition components can comprise sabot and projectile tail.The cannon fuze component is other may using, just as the empennage and the surface that are used for precision-guided bomb and guided missile.Armoring member can comprise armor plate or the structure unit for military vehicle.In these were used, this series products can provide weight or improved reliability or the accuracy that alleviates.

In another embodiment, the product of making by novel method as herein described is used for fastener application, comprising for example being used for bolt, rivet, screw, threaded stud, insert, nut and the securing bolt of industrial engineering and/or space industry.In these were used, this series products can be used for substituting other heavier materials such as titanium alloy or titanium steel, with weight reduction.In other cases, this series products can provide excellent weather resistance.

In another embodiment, the product of making by novel method as herein described is used for the automobile application, comprising such as cover plate (comprising for example, hood, splash pan, car door, roof and luggage hatchcover etc.), wheel and critical strength use, as be used in naked car application (for example, car post, stiffener).In some of these application, this series products can allow to reduce specification and the weight reduction of parts.

In a further embodiment, the product of making by novel method as herein described for example is used for boats and ships and canoe (comprising for example hull, deck, mast and superstructure) in using with Yu Haiyang.In some of these application, described product can be used for that implementation specification reduces and weight reduces.In the situation that some other, described product can be used for replacing the inferior product of solidity to corrosion, thereby causes reliability to strengthen and the life-span increases.

In a further embodiment, the product of making by novel method as herein described is used for the track application, comprising for example being used for dump-bed truck, tank wagon and box car.In the situation that dump-bed truck or tank wagon, this series products can be used for funnel and oil tank itself or be used for supporting structure.In these cases, this series products can provide the weight that alleviates (by reducing specification) or the consistency with the product that transports is strengthened.

In a further embodiment, the product of making by novel method as herein described is used for the ground transport application, for example be used for semitrailer tractor, box trailer, flat-bed trailer, motorbus, sealing van, recreation vehicle (RV), off-road vehicle (ATV), etc.For semitrailer tractor, motorbus, sealing van and recreation vehicle, described product can be used as cover plate or framework, snubber or fuel tank, allows to reduce specification and weight reduction.Correspondingly, described alloy body also can be used in wheel, with weather resistance or weight reduction or the improvement outward appearance that enhancing is provided.

In a further embodiment, the product of making by novel method as herein described is used for the oil gas application, comprising for example being used for riser pipe, auxiliary line, drilling rod, throttling and kill line, production pipeline and downcomer.In these were used, described product can allow to reduce wall thickness and weight is lower.Other purposes can comprise replaces substitute material with the improvement corrosive nature, or replaces substitute material with the consistency of improvement and drilling fluid or production fluid.The described product of this class also can be used for the utility appliance that exploration is used, wherein for example live module and helideck.

In another embodiment, the product of making by novel method as herein described is used in the middle of packaging application, comprising for example being used for lid and label, food cans, bottle, pallet and block.In these were used, benefit can comprise provided the chance that reduces specification and reduce packed weight or Cost reduction.In other cases, this product will have enhancing and the consistency packing content thing or improved solidity to corrosion.

In another embodiment, the product of making by novel method as herein described is used for tamper, for example is used for set lights, mirror and centralized solar energy generation technology, etc.In these were used, this series products can be under given strength level, provide higher volume reflection under the condition of naked, coating or anodic oxidation treatment.

In another embodiment, the product of making by novel method as herein described is used for Application in Building, comprising for example being used for cladding plate/facade, entrance, frame system and the curtain wall system of buildings.In this class was used, this product can provide excellent outward appearance or weather resistance or reduce relevant weight with the thick end and reduce.

In another embodiment, the product of making by novel method as herein described is used for electrical applications, for example is used for junctor, terminal, cable, bus and electric wire, etc.In some cases, for given current capacity, this product can provide the sagging trend of minimizing.High integrality connects the ability that the junctor of being made by this product can have an enhancing to keep in time.In other electric wires or cable, this product can provide improved fatigue property on given current capacity level.

In another embodiment, the product of making by novel method as herein described is used for fiber metal laminate to be used, and for example for the production of can be used for veneer sheet high strength light sheet products, or other can make the product of thickness reduction and weight saving.

In another embodiment, the product of making by novel method as herein described is used for the industrial engineering application, for example diamond plate, work box, bolt web plate (bolting deck), bridge plate and chute, or other have the product of strengthening the property to reduce thickness and reducing weight or materials'use.

In another embodiment, the product of making by novel method as herein described is used for fluid container (tank), for example toroidal memory, dome receptacle and bucket, etc.In some cases, described tank can be used in static the storage.In other cases, described tank can be used as the parts of launch vehicle or flyer.The benefit of these application can comprise that thickness reduces or with holding product consistency strengthen.

In another embodiment, the product of making by novel method as herein described is used for consumer product applications, needs the consumption electronic product of weather resistance or desirable outward appearance as notebook computer, mobile phone, photographic camera, mobile music player, handheld device, computer, TV, microwave oven, cooker, washer/dryer, refrigerator, sports goods or any other.In another embodiment, the product of being made by novel method as herein described is used for medical treatment device, security system and office appliance, etc.

In another embodiment, described novel method is used for cold chambering process, such as for the treatment of the hole to improve fatigue resistance etc., may cause the performance of cold working gradient as above and customization, etc.This cold chambering process is taken turns and airframe applicable to forging, etc.

In another embodiment, described novel method is used for indirect cold-extrusion technology, for example, and for the production of tank, bottle, inhalator jar and gas cylinder, etc.In these cases, described product can provide higher intensity, and this can reduce materials'use.In other cases, the improvement of content consistency can cause the preservation period more grown.

In another embodiment, the product of being made by novel method as herein described is used for heat exchanger applications, for example is used for pipe and radiator element, etc., wherein higher intensity can be interpreted as the minimizing of materials'use.Also can realize improved weather resistance and long life-span.

In another embodiment, described novel method is used for shaping process, and as for the production of heat sink assembly (for example heat pipe), wherein higher intensity is interpreted as the minimizing of materials'use.Also can realize improved weather resistance and long life-span.

New 2xxx alloy product can be used for multilayer and use.For example, using 2xxx aluminium alloy body is possible as the first layer and 1xxx-8xxx alloy as second layer formation multilayer product.Figure 12 shows an embodiment for the production of the method for multilayer product.In the embodiment shown, can produce multilayer product (107), it be homogenized (122) subsequently, hot rolling (126), solid solution, then cold rolling (220), as above-mentioned about as described in Fig. 9.Can cast by multicomponent alloy, the rolling compound and metallurgical method such as compound produces this multilayer product.The multicomponent alloy foundry engieering comprises that the people such as Kilmer are at U.S. Patent Application Publication No.20030079856, the people such as Anderson are at U.S. Patent application No.20050011630, the people such as Chu are at U.S. Patent application No.20080182122, and Novelis is at W02007/098583 (so-called FUSION ^TMCasting) those contents of describing in.

The all respects of the new technology that present patent application proposes, advantage and new feature will be partly articulated in the following description, and will become apparent after those skilled in the art read specification sheets and accompanying drawing, perhaps can know by the one or more embodiment that put into practice this technology that present patent application provides.

Description of drawings

Fig. 1 produces the schema of the ordinary method of alloy product for explanation.

Fig. 2 produces the schema of the novel method of alloy product for explanation.

Fig. 3-8th is for the schema of explanation for the preparation of a plurality of embodiments of cold worked aluminium alloy body after solid solution.

Fig. 9 is the schema for an embodiment of the method for explanation production aluminum alloy body.

Figure 10 is the graphic representation be used to the R-value that has functional relation with orientation angle that multiple aluminium alloy body is described.

Figure 11 a-11e is the light micrograph for the microstructure of explanation aluminium alloy body; Described light micrograph is observed them by the anodic oxidation treatment sample and in polarized light and is obtained.

Figure 12 is be used to a kind of schema of producing the method for multilayer aluminum alloy product is described.

Figure 13 is for L, the LT of explanation rolled products and the schematic diagram of ST direction.

Figure 14-15th is be used to the chart of the heat treatment response that multiple 2xxx+Ag aluminium alloy body is described.

Figure 16-17th is be used to the chart of intensity-toughness properties that multiple 2xxx+Ag aluminium alloy body is described.

Embodiment

Embodiment 1– 2324 alloys and 2024 alloys

With 2324 and 2,024 two kinds of direct-cooled ingot castings that are cast as of 2xxx aluminium alloy.Process these alloys according to being similar to method shown in Fig. 9, and accepted thermal treatment (300) 20 minutes at the temperature of 320 °F to 350 °F after cold working step (200).Mechanical property (intensity, unit elongation) and the toughness properties (unit propagation energy) of these aluminium alloy bodies are provided in table 3-4 below.

The mechanical property of 2324 alloys of the different processing of table 3 –

The mechanical property of 2024 alloys of the different processing of table 4 –

These aluminium alloy bodies have had increased access to strength increase with cold working, and have substantially the unit elongation value higher than 4%.The cold working postheat treatment has increased unit elongation.

Embodiment 2The test of – to the 2xxx+Ag alloy of adopting new technology

To have 2xxx+Ag alloy casting, the homogenizing of the composition of listing in following table 5 and be rolled into the sheet material/thin plate of the intermediate gauge that has respectively about 0.53 inch, 0.32 inch, 0.16 inch (x2) and 0.106 inch.Subsequently, with the final thickness of about 0.08 inch of a cold rolling one-tenth in 0.16 inch sample (contrast), by carrying out solution heat treatment in about 60 minutes in about 970 °F of lower soaking, then carry out cold-water quench, with back draft 1-2% to eliminate stress.Contrast is carried out natural aging treatment about 4 days, then be heat-treated to T6 type state.

Sample to other carries out the first solution heat treatment (adopting identical technique), and the final thickness of 0.08 inch of cold rolling one-tenth, represent respectively approximately 85%, 75%, 50% and 25% cold working subsequently.With about 4 days of all sample natural aging treatment, (290 °F with 330 °F) different time of thermal treatment at two temperature subsequently.Then carry out mechanical test and conductivity test, the test result of each thermal treatment temp is provided in table 6-7.

The composition (all values is weight percentage) of table 5-2xxx+Ag alloy

The intensity (290 °F) of table 6-different heat treatment 2xxx+Ag alloy under the time

The intensity (330 °F) of table 7-different heat treatment 2xxx+Ag alloy under the time

As shown in top table 6-7 and Figure 14-15, the thin plate B-E that makes of adopting new technology has realized the increase of intensity.Positively, has 85%CW and only just realized the intensity of 82.8ksi after 4 hours in thermal treatment at 330 °F of heat treated thin plate B.The alloy that is in the T6 state (thin plate A) according to conventional means processing reaches its measured maximum intensity the thermal treatments of about 36 hours, and only obtains the intensity of about 61.1ksi.In other words, new thin plate B has realized about 35% increase with respect to the material of the preparation of means routinely aspect tensile yield strength, and only adopts the thermal treatment (that is, fast 88.9% of 4 hours; (1-4/36) * 100%=88.9%).In other words, new thin plate B has realized about 35% increase with respect to conventional thin plate A aspect intensity, and for this time that spends be thin plate A reach its highest measurement intensity 61.1ksi required time about 1/10.

If these strength increases, the ductility of expection thin plate B-E can significantly reduce.Yet, as shown in following table 8, measure good unit elongation value.All unit elongation values represent with per-cent.For the sample of heat-treating, measure similar unit elongation value under 290 °F.

The unit elongation (%) (330 °F) of table 8-different heat treatment 2xxx+Ag alloy under the time

The electric conductivity of the measurement under providing 330 °F below in table 9.All conductivity values represent (I.A.C.S.) with IACS per-cent.Arrived similar conductivity values for heat treated sample measurement under 290 °F.

The electric conductivity (330 °F) of table 9-different heat treatment 2xxx+Ag alloy under the time

The presentation of results of embodiment 2, cold working and heat treatment step must suitably complete to obtain improved performance (for example, intensity).As shown in Figure 14-15, inadequate alloy of heat treated time may not can be realized improved performance, as demonstrate strength decreased with comparing under the cold working state.As shown in Figure 14-15, the long alloy of heat treatment time also may not can be realized improved performance, as demonstrate strength decreased with comparing under the cold working state.

Additional mechanical performance to the 2xxx+Ag aluminium alloy is tested, and provides test result in table 10-11 below.Particularly, intensity, unit elongation and fracture toughness property performance have been tested.In this case, with the aluminium alloy body 290 °F of lower thermal treatments 72 hours.These results show that 2xxx+Ag aluminium alloy body can obtain similar intensity and extension property in L direction and LT direction.

The additional mechanical performance (LT) of table 10-2xxx+Ag alloy

The additional mechanical performance (L) of table 11-2xxx+Ag aluminium alloy

(be used for K according to ASTM touchstone ASTM E561 and ASTM B646 _appAnd K _R25) and E399 and B645 (K _IC/ K _Q), carry out the fracture toughness property test.Middle crack is ruptured sample (M (T)) for K _appMeasure.Sample width (W) is 6.3 inches, and thickness (B) is 0.08 inch, Initial crack length (2a ₀) be 1.573 inches, that is, and 2a ₀/ W=0.25.Pressed compact tension fracture sample (C (T)) is used for K _R25And K _QMeasure.Sample width (W) is 2.5 inches, and thickness (B) is 0.07 inch, nominal Initial crack length (a ₀) be 1.25 inches, and (a ₀)/W=0.50.

It will be understood by those skilled in the art that K _Q, K _appAnd K _R25Numerical value usually increase with the increase of test sample width.K _Q, K _appAnd K _R25Also be subjected to the impact of thickness of sample, Initial crack length and test specimen geometrical shape.Therefore, K _Q, K _appAnd K _R25Value can only compare according to the test sample with identical geometrical shape, width, thickness and Initial crack length usually reliably.

2xxx aluminium alloy body has been realized improved fracture toughness property.Although significantly increase with respect to contrast body intensity, new 2xxx+Ag aluminium alloy body has also been realized improved fracture toughness property with respect to reference alloys.This is presented in Figure 16-17.For example, with respect to the contrast thin plate, the thin plate of 75%CW has been realized 34.4% improvement (LT) aspect tensile yield strength, plane strain toughness (K _QT-L) correspondingly improved 17.6%, and plane stress toughness (K _R25T-L) improved 8.1%.The thin plate of 75%CW is also being realized 31.4% improvement with respect to the contrast thin plate aspect tensile yield strength (L).In the combination that realizes these intensity and toughness, also realized good ductility, and the new aluminum alloy body has all been realized the unit elongation of 6.5-10%.

Also tested the crystalline-granular texture of 2xxx+Ag aluminium alloy body according to above-mentioned OIM step.Provide test result in following table 12.

Microstructure (OIM) performance of table 12-2xxx+Ag aluminium alloy

Have greater than 25% cold worked new 2xxx+Ag aluminium alloy body the microstructure that non-recrystallization is dominant, have in all cases the first kind crystal grain (that is, 75% non-recrystallization) that is not more than 0.25 volume fraction.On the contrary, the contrast body is recrystallize almost completely, has the first kind crystal grain of 0.88 volume fraction (that is, 12% non-recrystallization).

Also produce according to above-mentioned R-value the R-value that step has been tested 2xxx+Ag aluminium alloy body.Test result is shown in above-mentioned Figure 10.New 2xxx+Ag aluminium alloy body has high stdn R-value, obtains maximum (the highest) stdn R-value 50 ° of orientation angle.These high R-values show new 2xxx+Ag aluminium alloy body as herein described to be had unique texture and therefore has unique microstructure.Compare with the R-value of contrast body, new 2xxx+Ag aluminium alloy body has obtained about high 322% to 729% maximum R-value (for the purpose of measurement R-value, contrast is in the T4 state, rather than at the T6 state).

Although described a plurality of embodiment of the present invention in detail, the modification of these embodiments and change are apparent for a person skilled in the art.Yet, can be expressly understood that this class is revised and change all falls in the spirit and scope of the disclosure of invention.

Claims (37)

1. method comprises:

(a) for the preparation of cold worked aluminium alloy body after solid solution, wherein, described aluminium alloy body comprises the aluminium alloy with copper of 0.5 to 8.0wt.%, and wherein, described copper is the alloying element that is dominant in aluminium alloy except aluminium;

(i) wherein, described preparation process comprises the solution treatment of aluminium alloy body;

(b) in described preparation process (a) afterwards, the described aluminium alloy body of cold working is more than 50%; And

(c) in described cold working step (b) afterwards, the described aluminium alloy body of thermal treatment;

Wherein, complete described cold working step and described heat treatment step, to realize that compare long cross directional stretch yield strength increases with the reference sample of aluminium alloy body under the cold working state.

2. method according to claim 1, wherein, described preparation process (a) comprising: by the described aluminium alloy body of D.C.casting method casting.

3. method according to claim 2, wherein, described preparation process (a) comprising:

Make described aluminium alloy body homogenizing; And

The described aluminium alloy body of hot-work;

Wherein, described solution treatment step (a) (i) occur in described hot-work step after.

4. method according to claim 3, wherein, described cold working step (b) is the second cold working, and wherein, described preparation process comprises: (i) before described aluminium alloy body is carried out the first cold working in described solution treatment step (a).

5. method according to claim 1, wherein, described preparation process (a) comprising: cast continuously described aluminium alloy body.

6. method according to claim 5, wherein, described preparation process (a) comprising: be accompanied by described continuous casting step, complete described solution treatment step (a) (i).

7. method according to claim 5, wherein, described preparation process (a) comprising: after described continuous casting step, complete described solution treatment step (a) (i).

8. method according to claim 7, wherein, described preparation process (a) comprising: in described solution treatment step (a) (i) before, the described aluminium alloy body of hot-work.

9. according to claim 7 or 8 described methods, wherein, described cold working step (b) is the second cold working, and wherein, described preparation process (a) comprising: in described solution treatment step (a) (i) before, described aluminium alloy body is carried out the first cold working.

10. method according to claim 1, wherein, described solution treatment step (a) (i) comprises described aluminium alloy body is quenched, and wherein, described quenching is not in the situation that described aluminium alloy body exists distortion to occur.

11. method according to claim 1 is included in and carries out during described heat treatment step (c), described aluminium alloy body being shaped.

12. method according to claim 1 wherein, (i) and between described cold working step (b) is not taked autotelic thermal treatment to described aluminium alloy body in described solution treatment step (a).

13. according to claim 1 or 12 described methods, wherein, described solution treatment step (a) (i) complete and described cold working step (b) beginning between through being no more than 60 hours.

14. method according to claim 1, wherein, the temperature that described cold working step (b) is included in described aluminium alloy body begins to carry out described cold working when being no more than 250 °F.

15. according to claim 1 or 14 described methods, wherein, described cold working step (b) is not in the situation that exist the described aluminium alloy body of autotelic heating to occur.

16. method according to claim 1, wherein, described cold working step (b) is cold rolling.

17. method according to claim 1, wherein, described cold working step (b) comprises described aluminium alloy body is rolled into its final shape basically.

18. method according to claim 17, wherein, described cold working step (b) comprises described aluminium alloy body is cold-rolled to final thickness.

19. method according to claim 1, wherein, described cold working step (b) is included in the described aluminium alloy body of cold working at least 55% to 90% scope.

20. method according to claim 19, wherein, described cold working step (b) is included in the described aluminium alloy body of cold working in 60% to 85% scope.

21. method according to claim 19, wherein, described cold working step (b) is included in the described aluminium alloy body of cold working in 70% to 80% scope.

22. method according to claim 1, wherein, described heat treatment step (c) comprises described aluminium alloy body is remained on below its recrystallization temperature.

23. method according to claim 22, wherein, described heat treatment step (c) is included in the described aluminium alloy body of the interior heating of scope of 150-425 °F.

24. 2 described methods, wherein, carry out described cold rolling step (b) and described heat treatment step (c) according to claim 1 and 2, so that described aluminium alloy body obtains the microstructure that non-recrystallization is dominant.

25. method according to claim 1, wherein, described aluminium alloy body obtains the unit elongation greater than 4%.

26. method according to claim 25, wherein, described aluminium alloy body obtains at least 8% unit elongation.

27. an aluminium alloy body comprises 0.5 to 8.0wt.% copper, wherein, described copper is the alloying element that is dominant in described aluminium alloy except aluminium, and wherein, described aluminium alloy body obtains than the tensile yield strength with reference to aluminium alloy body high at least 5%;

Wherein, described have the composition identical with described aluminium alloy body with reference to the aluminium alloy body;

Wherein, described reference aluminium alloy body is worked into the T87 state;

Wherein, described tensile yield strength and its maximum tension yield strength with reference to the aluminium alloy body differs and is no more than 1ksi.

28. aluminium alloy body according to claim 27, wherein, described aluminium alloy body obtains described high at least 5% tensile yield strength and obtains its needed time of maximum tension yield strength soon at least 25% with reference to the aluminium alloy body than described under the T87 state.

29. aluminium alloy body according to claim 28, wherein, described aluminium alloy body obtains described high at least 5% tensile yield strength and obtains its needed time of maximum tension yield strength soon at least 50% with reference to the aluminium alloy body than described under the T87 state.

30. aluminium alloy body according to claim 27, wherein, described aluminium alloy body obtains the unit elongation greater than 4%.

31. aluminium alloy body according to claim 30, wherein, described aluminium alloy body obtains at least 8% unit elongation.

32. aluminium alloy body according to claim 27, wherein, described aluminium alloy body reaches at least 2.0 stdn R-value.

33. aluminium alloy body according to claim 32, wherein, described aluminium alloy body reaches at least 4.0 stdn R-value.

34. aluminium alloy body according to claim 32, wherein, described aluminium alloy body reaches at least 6.0 stdn R-value.

35. aluminium alloy body according to claim 27, wherein, described aluminium alloy body is that non-recrystallization is dominant.

36. aluminium alloy body according to claim 35, wherein, described aluminium alloy body at least 75% is non-recrystallization.

37. a method comprises:

(a) the aluminium alloy body is carried out solution treatment, wherein, described aluminium alloy body comprises the aluminium alloy with copper of 0.5 to 8.0wt.%, and wherein, described copper is the alloying element that is dominant in aluminium alloy except aluminium;

(b) in described solution treatment step (a) afterwards, the described aluminium alloy body of cold working is more than 50%; And

(c) in described cold working step (b) afterwards, the described aluminium alloy body of thermal treatment;

Wherein, complete described cold working step and described heat treatment step, to realize comparing with the reference sample of aluminium alloy body under the cold working state increase of long cross directional stretch yield strength.

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