CN104862551B - Al Mg Cu Zn line aluminium alloys and aluminum alloy plate materials preparation method - Google Patents
Al Mg Cu Zn line aluminium alloys and aluminum alloy plate materials preparation method Download PDFInfo
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Abstract
The present invention proposes a kind of Al Mg Cu Zn line aluminium alloys and aluminum alloy plate materials preparation method.The Cu contents in alloy are improved on the basis of AA5182 the and AA5023 alloys, and with the addition of Zn simultaneously, the precipitation strength of the transitional face of T-phase in the transitional face of S-phase and Al Mg Zn systems in Al Mg Cu systems is made full use of.It is separated out simultaneously during artificial aging by solid solution and Pre-aging treatment, reach that cooperative reinforcing is acted on.Due to the Cu and Zn of addition simultaneously, make the alloy that there is obvious natrual ageing.Natrual ageing can not only be suppressed by Pre-aging treatment, it is to avoid because baking vanish caused by natrual ageing softens, moreover it is possible to the intensity of alloy is significantly improved after high-temperature aging processing, especially during 180 DEG C/30min artificial aging in short-term.The alloy is applicable not only to the preparation of car inner plate, applies also for other association areas of aluminium alloy.
Description
Technical field
The invention belongs to aluminium alloy and its preparation field, more particularly to it is a kind of can industrial applications Al-Mg-Cu-Zn systems
The preparation method of aluminium alloy and aluminum alloy plate materials.
Background technology
In order to solve environment and the energy problem that China Automobile Industry is brought, automotive light weight technology is increasingly by weight
Depending on.Aluminium alloy is with its high specific strength, good corrosion resistance, surface easy coloring, excellent formability and preferably regeneration
Property etc. a series of good characteristics and as automotive light weight technology optimal material.
Typical aluminium alloys for automobile has 2xxx, 5xxx and 6xxx system alloy.Wherein 5xxx line aluminium alloys are excellent with its
Formability and be widely used in car inner plate.But the AA5182 alloys for being widely used in car inner plate belong to heat treatment can not be strong
AA5023 alloys in the alloy of change, the existing trade mark are relatively low due to Cu contents, can not also meet what should be had as Automobile Plate
The requirement of baking hardenability and high anti-indenture.And due to PLC effects, the meeting in stamping process of 5xxx line aluminium alloys
PLC Zona transformans is formed, declines the surface smoothness of stamping parts, the baking vanish to automobile brings difficulty.
At present, in patent CN103255323, researcher is improved by adding a small amount of Cu and Zn elements
Intensity after the baking vanish of Al-Mg systems alloy, but baking vanish intensity increment is not high；And 240 DEG C are carried out after the aligning proposed in patent
~300 DEG C of stress relief annealing technique can cause quick separate out of Cu, Zn atom of solid solution to form the second thick phase, can cause strong
Change effect to substantially reduce, it is impossible to make full use of the precipitation strength of Cu, Zn element to act on；Furthermore, alloying component in that patent
In the range of, Zn atoms are difficult with the MgZn described in patent2Form separate out.Therefore practical application is very limited.
The content of the invention
The present invention in order to solve existing 5xxx line aluminium alloys baking vanish hardening present in Automobile Plate application process and
The problem of anti-indenture is not enough.Separate out and reach while newly-designed alloying component and its preparation technology take full advantage of Cu and Zn
To invigoration effect so that the timber intensity after baking vanish is greatly improved.
The first object of the present invention is to propose a kind of Al-Mg-Cu-Zn line aluminium alloys composition and its composition range, distinguished
For：
4.0~6.0wt% of Mg；
0.30~1.0wt% of Cu；
1.0~3.5wt% of Zn；
Mn≤0.4wt%；
Fe≤0.4wt%；
Si≤0.4wt%,
Cr≤0.2wt%；
Ti≤0.1wt%；
Surplus is Al and inevitable impurity.
It is preferred that, including 4.2~5.5wt% of Mg；
It is preferred that, including 0.4~0.9wt% of Cu；
It is preferred that, including 1.2~3.0wt% of Zn；
It is preferred that, including 0.1~0.3wt% of Mn；
The second object of the present invention is to propose a kind of preparation technology of Al-Mg-Cu-Zn line aluminium alloys sheet material, the preparation
Technique comprises the following steps：
(a) above-mentioned al alloy component is subjected to founding；
(b) by ingot homogenization annealing, hot rolling, cold rolling, solution hardening, Ageing Treatment obtained by step (a).
Homogenizing annealing in the step (b) is to start the aluminium alloy after founding with 20~40 DEG C/h heating rate
440~470 DEG C of 6~12h of insulation are raised to from room temperature, 470~490 DEG C of guarantors are then warming up to 20~40 DEG C/h heating rate again
5~10h of temperature, is then warming up to 500~540 DEG C of 6~12h of insulation, afterwards with 20~40 with 20~40 DEG C/h heating rate again
DEG C/h rate of temperature fall is cooled to room temperature.
Hot-rolled temperature in the step (b) is 460~510 DEG C, hot rolling total reduction >=90%；Cold rolling total reduction >=
80%.
It is preferred that, in the step (b) it is cold rolling including：First carry out reduction ratio for 40%~60% it is first cold rolling, so
Be incubated 0.5~2h at 350 DEG C~450 DEG C afterwards and carry out intermediate annealings, carry out again afterwards reduction ratio be 50%~70% it is second cold
Roll.
Solid solubility temperature is 520 DEG C~540 DEG C in the step (b), and solid solution soaking time is 5~12min, and quenching mode is
Direct-water-quenching.
Ageing Treatment is to be transferred in aging furnace in 3~6min by the alloy after Water Quenching in the step (b)
Row preageing, pre-age temperature is 60 DEG C~100 DEG C, and preageing soaking time is 8~16h.
(c) stamping, japanning and paint baking.
The present invention by improving the content of Cu and Zn in alloy, and draws on the basis of AA5182 and AA5023 alloys
Enter Pre-aging treatment, this Pre-aging treatment can not only suppress natrual ageing of the alloy in storage transportation, and in advance
The stationary atom cluster of timeliness formation can turn into the Precipitation forming core point during subsequent baking vanish so that sheet material is in the short time
Intensity increment reaches 50MPa during baking vanish, intensity after the baking vanish relative to AA5182 and AA5023, after the baking vanish of novel alloy
Nearly 140MPa and 100MPa has been respectively increased in intensity highest, reaches significantly baking vanish hardening effect.It disclosure satisfy that aluminium alloy vapour
The baking vanish hardening and anti-indenture of sweep.The invention alloy is applicable not only to Automobile Plate, is also applied for other phases of aluminium alloy
Pass field.
Brief description of the drawings
The natrual ageing hardening curve of Fig. 1 1#, 2#, 5#, 6# alloy quenching states.
Fig. 2 6# alloy T4 states, age hardening curves of the T4P states at 180 DEG C, and 6# alloy quenchings state and preageing
Natrual ageing hardening curve after processing.
Embodiment
The present invention is further supplemented and illustrated with reference to specific implementation case.
Ingot casting used of the invention uses common fine aluminium, technical pure Mg, technical pure Zn, intermediate alloy Al-20wt%Si, Al-
50wt%Cu, Al-20wt%Fe, Al-10wt%Mn, Al-10wt%Ti, Al-5wt%Cr founding are formed.Case study on implementation alloy
Specific chemical composition is shown in Table 1.Wherein 1#, 2#, 3#, 4# is refers to alloy, and 5#, 6#, 7# are the alloying component designed by the present invention.
The embodiment alloy specific chemical composition (mass percent, wt%) of table 1
| Mg | Cu | Zn | Mn | Cr | Ti | Fe | Si | Al | |
| 1# | 5.2 | 0 | 0 | 0.2 | 0.05 | 0.02 | 0.2 | 0.1 | Surplus |
| 2# | 5.18 | 0.42 | 0 | 0.2 | 0.05 | 0.02 | 0.2 | 0.1 | Surplus |
| 3# | 5.19 | 0 | 2.0 | 0.2 | 0.05 | 0.02 | 0.2 | 0.1 | Surplus |
| 4# | 5.45 | 0.44 | 0.58 | 0.2 | 0.05 | 0.02 | 0.2 | 0.1 | Surplus |
| 5# | 5.25 | 0.42 | 1.19 | 0.2 | 0.05 | 0.02 | 0.2 | 0.1 | Surplus |
| 6# | 5.0 | 0.44 | 1.93 | 0.2 | 0.05 | 0.02 | 0.2 | 0.1 | Surplus |
| 7# | 4.41 | 0.8 | 1.2 | 0.2 | 0.05 | 0.02 | 0.2 | 0.1 | Surplus |
Alloy cast ingot of the present invention carries out Homogenization Treatments in circulation air stove, then carry out milling face, hot rolling, it is cold rolling, in
Between annealing, it is cold rolling, quenching, Pre-aging treatment.Specific embodiment is as follows：
Homogenization Treatments are carried out to 1#, 2#, 3#, 4#, 5#, 6#, 7# ingot casting, concrete technology is：By the alloy after founding with
30 DEG C/h heating rate is raised to 460 DEG C of insulation 10h from room temperature, is then warming up to 480 DEG C of guarantors again with 30 DEG C/h heating rate
Warm 5h, is then warming up to 520 DEG C of insulation 10h with 30 DEG C/h heating rate again, is then cooled down again with 30 DEG C/h rate of temperature fall
To room temperature.After the ingot mill surface after Homogenization Treatments, then hot rolling is carried out, hot-rolled temperature is 500 DEG C, hot rolling total reduction >=
90%, obtain 6mm hot rolled plates.Carry out again first cold rolling, cold rolling total reduction is 50%, 3mm cold-reduced sheets is obtained, then 450
1h is incubated at DEG C and carries out intermediate annealing, carries out afterwards second cold rolling, cold rolling total reduction is 67%, finally give 1#, 2#, 3#,
The 1mm cold-reduced sheets of 4#, 5#, 6#, 7# alloy.
Comparative example
The 1mm cold-reduced sheets of 1#, 2#, 3#, 4# alloy obtained in aforementioned manners are carried out to 525 DEG C of insulations in salt bath furnace
Direct-water-quenching after 10min solution treatment.Cold-reduced sheet after quenching is divided into two groups, aging furnace is put into 6min after one group of quenching
80 DEG C of insulation 12h Pre-aging treatment is carried out, is then placed in room temperature and obtains T4P states in 7 days；It is placed directly in after another set quenching
Room temperature obtains T4 states in 7 days.The processing of 180 DEG C/30min (simulation baking vanish) artificial aging finally is carried out to T4P states and T4 states alloy, surveyed
The intensity increment before and after alloy baking vanish is measured, concrete outcome is shown in Table 2.Make the nature that room temperature is placed on after 1# and 2# alloy quenchings simultaneously
Age hardening curves, concrete outcome is shown in Fig. 1.Stamping, mopping and paint baking are the actual lifes of typical auto parts and components
Step is produced, present case is in order to verify that the precipitation strength of new component and new technology to Al-Mg systems alloy is acted on, so eliminating punching press
The step for shaping, this is the influence for strengthening increment to baking vanish in order to avoid the deformation in punching course.Actual baking vanish process
It is also to simulate to complete in aging furnace.
Embodiment 1
The 1mm cold-reduced sheets of the 5# alloys obtained in aforementioned manners are carried out to 525 DEG C of insulation 10min solid solution in salt bath furnace
Direct-water-quenching after processing.Cold-reduced sheet after quenching is divided into two groups, being put into aging furnace in 6min after one group of quenching carries out 80 DEG C of guarantors
Warm 12h Pre-aging treatment, then places in room temperature and obtains T4P states in 7 days；Room temperature is placed directly in after another set quenching to obtain within 7 days
To T4 states.The processing of 180 DEG C/30min (simulation baking vanish) artificial aging is finally carried out to T4P states and T4 states alloy, measurement alloy is baked
Intensity increment before and after paint, concrete outcome is shown in Table 2.The natrual ageing hardening that room temperature is placed on after the processing of 5# alloy solid solutions is made simultaneously
Curve, concrete outcome is shown in Fig. 1.
Embodiment 2
The 1mm cold-reduced sheets of the 6# alloys obtained in aforementioned manners are carried out to 525 DEG C of insulation 10min solid solution in salt bath furnace
Direct-water-quenching after processing.Cold-reduced sheet after quenching is divided into two groups, being put into aging furnace in 6min after one group of quenching carries out 80 DEG C of guarantors
Warm 12h Pre-aging treatment, then places in room temperature and obtains T4P states in 7 days；Room temperature is placed directly in after another set quenching to obtain within 7 days
To T4 states.The processing of 180 DEG C/30min (simulation baking vanish) artificial aging is finally carried out to T4P states and T4 states alloy, measurement alloy is baked
Intensity increment before and after paint, concrete outcome is shown in Table 2.The natrual ageing hardening song that room temperature is placed on after 6# alloy quenchings is made simultaneously
Line, concrete outcome is shown in Fig. 1.In order to compare influence of the Pre-aging treatment to 6# alloys during artificial aging, while making 6#
Natrual ageing hardening curve and T4 states and T4P states after alloy solid solution state and Pre-aging treatment is hard in 180 DEG C of artificial aging
Change curve, concrete outcome is shown in Fig. 2.
Embodiment 3
The 1mm cold-reduced sheets of the 7# alloys obtained in aforementioned manners are carried out to 525 DEG C of insulation 10min solid solution in salt bath furnace
Direct-water-quenching after processing.Cold-reduced sheet after quenching is divided into two groups, being put into aging furnace in 6min after one group of quenching carries out 80 DEG C of guarantors
Warm 12h Pre-aging treatment, then places in room temperature and obtains T4P states in 7 days；Room temperature is placed directly in after another set quenching to obtain within 7 days
To T4 states.The processing of 180 DEG C/30min (simulation baking vanish) artificial aging is finally carried out to T4P states and T4 states alloy, measurement alloy is baked
Intensity increment before and after paint, concrete outcome is shown in Table 2.
Embodiment 4
The 1mm cold-reduced sheets of the 6# alloys obtained in aforementioned manners are carried out to 525 DEG C of insulation 10min solid solution in salt bath furnace
Direct-water-quenching after processing.Aging furnace will be put into cold-reduced sheet 6min after quenching and carries out 70 DEG C of Pre-aging treatments for being incubated 15h, so
Placed afterwards in room temperature and obtain within 7 days T4P (1) state, when finally carrying out 180 DEG C/30min (simulation baking vanish) manually to T4P (1) state alloy
Intensity increment before and after effect processing, measurement alloy baking vanish, concrete outcome is shown in Table 2.
Embodiment 5
The 1mm cold-reduced sheets of the 6# alloys obtained in aforementioned manners are carried out to 525 DEG C of insulation 10min solid solution in salt bath furnace
Direct-water-quenching after processing.Aging furnace will be put into cold-reduced sheet 6min after quenching and carries out 90 DEG C of Pre-aging treatments for being incubated 8h, so
Placed afterwards in room temperature and obtain within 7 days T4P (2) state, when finally carrying out 180 DEG C/30min (simulation baking vanish) manually to T4P (2) state alloy
Intensity increment before and after effect processing, measurement alloy baking vanish, concrete outcome is shown in Table 2.
The different-alloy composition of table 2 and the sheet alloy of state pass through the mechanical properties of 180 DEG C/30min before and after the processing
As can be seen from Table 2, Cu and Zn are passed through on the basis of 1# (AA5182), 2# (AA5023), 3#, 4# comparative alloy
Compound addition, and Zn content is greater than 1%, from the point of view of intensity after baking vanish and baking vanish increment, the T4 states of 5#, 7# alloy
Baking finish result than T4P state is good, and 6# alloy T4P states are better than T4 states baking finish result, especially relative to 1# (AA5182)
With 2# (AA5023) alloy, nearly 140Mpa and 100MPa has been respectively increased in intensity after 6# alloy T4P state baking vanish, can expire substantially
The baking vanish hardening and anti-indenture of sufficient car inner plate.It will be seen from figure 1 that due to Zn addition so that 6# alloys relative to
Originally 1#, 2# alloy without natrual ageing effect have very significantly natrual ageing.Reinforcing pair caused by this natrual ageing
Stamping in Automobile Plate is totally unfavorable.And figure it is seen that this natrual ageing was also resulted in the later stage
Have the process of a lowered hardness during 180 DEG C of artificial agings so that 180 DEG C/30min simulation baking vanish after intensity can under
Drop.It can further be seen from figure 2 that the present invention can not only avoid what baking vanish process occurred by carrying out Pre-aging treatment to 6# alloys
Softening, and 180 DEG C of artificial age-hardening's processes in later stage can be substantially speeded up, the baking vanish hardening for greatly improving novel alloy increases
Amount.And it can further be seen from figure 2 that the 6# alloys after Pre-aging treatment are in room temperature placement process, its performance is also very stable
's.In summary, the alloying component and preparation technology designed by the present invention solve the hardening of 5xxx aluminium alloys baking vanish not well
Sufficient the problem of, take full advantage of the Precipitation reinforcing of Cu, Zn atom.And avoided well by Pre-aging treatment due to
Cu, Zn add the adverse effect that caused natrual ageing is hardened for baking vanish simultaneously.Certainly, alloy of the present invention and technique is not only
Suitable for the manufacture of car inner plate, and suitable for other association areas of aluminium alloy.
Although having write out the case study on implementation of the present invention, simply the preferred embodiment of the present invention.It should be pointed out that pair
For one of ordinary skill in the art, some modifications and variations can be made under the premise without departing from the principles of the invention,
These modifications and variations should be considered as protection scope of the present invention.
Claims (1)
1. a kind of Al-Mg-Cu-Zn line aluminium alloys sheet material preparation method, it is characterised in that the chemical composition and its quality of the alloy
Percentage is：4.2~5.5wt% of Mg, 0.4~0.9wt% of Cu, 1.2~3.0wt% of Zn, 0.1~0.3wt% of Mn, Fe≤
0.4wt%, Si≤0.4wt%, Cr≤0.2wt%, Ti≤0.1wt%, surplus are Al and inevitable impurity, and it prepares work
Skill comprises the following steps：
(a) founding is carried out by above-mentioned al alloy component；
(b) ingot casting obtained by step (a) is subjected to homogenizing annealing, hot rolling, cold rolling, solution hardening and Ageing Treatment；
Homogenizing annealing in the step (b) is three-level homogenizing annealing process, is specifically with 20 by the aluminium alloy after founding
~40 DEG C/h heating rate starts to be raised to 440~470 DEG C of 6~12h of insulation from room temperature, then again with 20~40 DEG C/h heating
Speed is warming up to 470~490 DEG C of 5~10h of insulation, is then warming up to 500~540 DEG C of guarantors again with 20~40 DEG C/h heating rate
6~12h of temperature, afterwards with 20~40 DEG C/h rate of temperature fall furnace cooling to room temperature；
Solid solubility temperature is 520 DEG C~540 DEG C in the step (b), and solid solution soaking time is 5~12min, and quenching mode is direct
Water quenching；
Ageing Treatment is that the aluminium alloy after Water Quenching is transferred in 3~6min in aging furnace to carry out in the step (b)
Preageing, pre-age temperature is 60 DEG C~100 DEG C, and preageing soaking time is 8~16h.
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| CN105839036B (en) * | 2016-04-27 | 2017-10-27 | 贵州航天风华精密设备有限公司 | A kind of heat treatment method of almag |
| US11149332B2 (en) | 2017-04-15 | 2021-10-19 | The Boeing Company | Aluminum alloy with additions of magnesium and at least one of chromium, manganese and zirconium, and method of manufacturing the same |
| CN108441725A (en) * | 2018-03-05 | 2018-08-24 | 东莞市宏锦金属制品有限公司 | Aluminium alloy and preparation method thereof |
| CN108546856A (en) * | 2018-05-11 | 2018-09-18 | 铜陵康达铝合金制品有限责任公司 | A kind of anticorrosion aluminium |
| CN109930038B (en) * | 2019-03-29 | 2020-12-29 | 北京科技大学 | Thermomechanical treatment method for Al-Mg-Zn alloy plate |
| CN111218590B (en) * | 2019-12-04 | 2021-07-23 | 中铝材料应用研究院有限公司 | High-strength high-formability aluminum-magnesium-copper alloy plate and preparation method thereof |
| CN111074121B (en) * | 2019-12-31 | 2021-08-31 | 广东中色研达新材料科技股份有限公司 | Aluminum alloy and preparation method thereof |
| EP3848476A1 (en) * | 2020-01-07 | 2021-07-14 | AMAG rolling GmbH | Sheet or strip made of a curable aluminium alloy, vehicle part manufactured from same, its use and a method for producing the sheet or strip |
| CN111206194B (en) * | 2020-02-24 | 2022-01-28 | 湖南人文科技学院 | Thermal mechanical treatment process for preparing aluminum alloy with high comprehensive performance |
| CN113005375A (en) * | 2021-02-22 | 2021-06-22 | 北京科技大学 | Preparation method of Al-Mg-Zn-Cu alloy plate applied after paint baking and used for improving surface quality and strength |
| CN112981288B (en) * | 2021-05-12 | 2021-08-20 | 中国航发北京航空材料研究院 | Annealing method of aluminum alloy ingot |
| CN115369294B (en) * | 2022-08-28 | 2023-09-12 | 北京工业大学 | Heat-resistant Al-Mg-Cu-Zn alloy and heat treatment process |
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| US20060213591A1 (en) * | 2005-03-24 | 2006-09-28 | Brooks Charles E | High strength aluminum alloys and process for making the same |
| US9039848B2 (en) * | 2007-11-15 | 2015-05-26 | Aleris Aluminum Koblenz Gmbh | Al—Mg—Zn wrought alloy product and method of its manufacture |
| JP2009167464A (en) * | 2008-01-16 | 2009-07-30 | Furukawa-Sky Aluminum Corp | Method for producing aluminum alloy material having excellent toughness |
| CN103266245B (en) * | 2012-09-04 | 2016-01-20 | 中南大学 | A kind of low-quenching sensitive Al-Zn-Mg-Cu series alloys |
| CN103255323B (en) * | 2013-05-31 | 2015-07-15 | 浙江巨科铝业股份有限公司 | Al-Mg-Zn-Cu alloy and preparation method thereof |
| CN103343306B (en) * | 2013-07-17 | 2015-10-07 | 北京科技大学 | A kind of remarkable treatment process improving high strength alumin ium alloy deformability and mechanical property |
| CN103789583B (en) * | 2014-01-22 | 2016-06-08 | 北京科技大学 | Quick aging response type Al-Mg-Si-Cu-Zn system Alloy And Preparation Method |
| CN104313413B (en) * | 2014-10-24 | 2016-08-24 | 北京科技大学 | A kind of Al-Mg-Zn system alloy and the preparation method of sheet alloy thereof |
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