CN104060201B - A kind of deformation heat treatment method simultaneously improving 6000 line aluminium alloy intensity and intercrystalline corrosion drag - Google Patents
A kind of deformation heat treatment method simultaneously improving 6000 line aluminium alloy intensity and intercrystalline corrosion drag Download PDFInfo
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Abstract
The invention belongs to aluminium alloy wrought heat treatment method field, can to improve 6000 be the heat treatment method of Al-Mg-Si-Cu intensity of aluminum alloy and intercrystalline corrosion drag simultaneously particularly to a kind of.Aluminium alloy, through solution treatment, quenching, after direct or lack time effect processes, then carries out heavy reduction cold rolling at room temperature deformation, and wherein, after controlling lack time effect process, alloy hardening degree is less than the 95% of peak value timeliness hardness；The drafts (reduction ratio) of cold rolling at room temperature deformation is not less than 80%.The deformation heat treatment method of the present invention is simple, and 6000 line aluminium alloys are after present invention process processes, it is not necessary to carry out subsequent treatment again, can obtain alloy strength and the intercrystalline corrosion drag of excellence simultaneously.
Description
Technical field
The invention belongs to aluminium alloy wrought heat treatment method field, can to improve 6000 be the heat treatment method of Al-Mg-Si-Cu intensity of aluminum alloy and intercrystalline corrosion drag simultaneously particularly to a kind of.
Background technology
6000 is that Al-Mg-Si-Cu aluminium alloy has moderate strength, low-density and the feature such as good mouldability and weldability, is used widely in industries such as automobile making, space flight and aviation and track traffics.But, due to the interpolation of Cu, cause this line aluminium alloy Susceptibility To Intergranular Corrosion to increase considerably, be particularly particularly acute under peak aged (T6), thus limiting this is alloy application in having certain corrosive environment.Secondly as the alloying level of 6000 line aluminium alloys is relatively low, even across peak value Ageing Treatment, the second phase particles negligible amounts of formation, the precipitating reinforcing effect contributed is also relatively limited.At present, this is that alloy strength is generally below 450MPa.Finally, as structural timber, 6000 line aluminium alloy preparation technologies must are fulfilled for industrial production demand.Such as, Deng moulding processs such as channel pressings (ECAP), high pressure torsion (HPT) and accumulation ply rolling (ARB), although being capable of increasing substantially the purpose of intensity of aluminum alloy, but these forced plasticity deforming methods are also difficult in adapt to industrialized production at present.Therefore, how to realize the synchronization raising of 6000 line aluminium alloy intensity and intercrystalline corrosion drag, and forming technology is suitable for aluminium alloy actual industrialization and produces, will be that performance potential is significant with its commercial Application of expansion for excavating 6000.
Summary of the invention
The technical problem to be solved is: provide the more easy method of one, it is achieved the synchronization of 6000 line aluminium alloy intensity and intercrystalline corrosion drag improves.
The technical solution used in the present invention is:
Providing a kind of 6000 is the deformation heat treatment method of Al-Mg-Si-Cu aluminium alloy: aluminium alloy, through solution treatment, quenching, after direct or lack time effect processes, then carries out heavy reduction cold rolling at room temperature deformation,
Above-mentioned solution treatment refers to: Mg, Si, Cu alloying element dissolving in aluminum substrate to form high temperature solid solution body, solid solution treatment process parameter mainly includes solid solubility temperature and solution time, and for different 6000 line aluminium alloys, solid solution temperature scope is different；For different batches, the solution treatment time is also different, and as preferably, solid solubility temperature is typically chosen within the scope of 530-550 DEG C, and solution time is typically chosen within the scope of 1-3h；
Above-mentioned quenching is to adopt Cooling Mode to freeze to get off by high temperature solid solution body, forms room temperature supersaturated solid solution, and as preferably, quenching mode adopts room temperature shrend；
Above-mentioned lack time effect processes and refers to: making room temperature supersaturated solid solution generating portion precipitate out and obtain certain hardenability, aging technique parameter includes aging temp and aging time.As preferably, lack time effect treatment temperature selects within the scope of 160-190 DEG C, and lack time effect processes selection of time within the scope of 1-6h, and controls after lack time effect processes alloy hardening degree less than the 95% of peak value timeliness hardness；
In the present invention, cold roller and deformed operation is to improve 6000 line aluminium alloy intensity important steps further, more it is to ensure that the alloy material requisite step of intercrystalline corrosion drag, in order to obtain high intensity and intercrystalline corrosion drag simultaneously, as preferably, the drafts (reduction ratio) of cold rolling at room temperature deformation is not less than 80%.
The beneficial effects of the present invention is: the deformation heat treatment method of the present invention is simple, 6000 line aluminium alloys are after present invention process processes, it is not necessary to carry out subsequent treatment again, can obtain alloy strength and the intercrystalline corrosion drag of excellence simultaneously.
Accompanying drawing explanation
Fig. 1 is in comparative example 1, the view of corrosion behavior；
Fig. 2 is in comparative example 2, the view of corrosion behavior；
Fig. 3 is in embodiment 1, the view of corrosion behavior；
Fig. 4 is in embodiment 2, the view of corrosion behavior；
Fig. 5 is in comparative example 3, the view of corrosion behavior；
Fig. 6 is in comparative example 4, the view of corrosion behavior.
Detailed description of the invention
In the embodiment of the present invention, the raw material of employing: 6061 types, 6056 types, 6013 type aluminum alloy hot rolling sheet materials original thickness be 4mm.
Test method:
(1) tensile property presses GB GB/T24182-2009 (Metal Mechanic Property test), tests on WTD-30 type electronic tensile test machine；
(2) hardness test carries out on HVZ-5 durometer, and hardness represents with the meansigma methods of 5 tests；
(3) Susceptibility To Intergranular Corrosion test is carried out according to GB GB/T7998-2005 " aluminium alloy IGC method of testing ".Sample is through defat, pickling, alkali cleaning and goes out light, and the etchant solution (30g/LNaCl+10ml/LHCl) temperature 35 ± 3 DEG C soaks 24h.Afterwards, prepare metallographic specimen, on OLYMPUSCK40M metallurgical microscope, after polishing, directly observe corrosion behavior.
For 6061 aluminium alloys:
Comparative example 1:
6061 aluminum alloy hot rolling sheet materials, after 540 DEG C/1h solution treatment and shrend, carry out 180 DEG C/8h timeliness subsequently, reach peak aged (T6), alloy rigidity is 135HV, tensile strength, yield strength and elongation percentage respectively 357MPa, 325MPa and 11.2%, corrosion behavior is intercrystalline corrosion, as shown in Figure 1.
Comparative example 2
6061 aluminum alloy hot rolling sheet materials, after 540 DEG C/1h solution treatment and shrend, carry out 180 DEG C/8h timeliness subsequently, reach peak aged (T6), alloy rigidity is 135HV, carries out the deformation of 80% drafts (reduction ratio) cold rolling at room temperature, the tensile strength of final alloy, yield strength and elongation percentage respectively 648MPa, 637MPa and 3.2% afterwards again, but corrosion behavior is intercrystalline corrosion, as shown in Figure 2.
From comparative example 1,2 it can be seen that after degree alloy hardening after Ageing Treatment reached peak aged, then carry out the cold roller and deformed Susceptibility To Intergranular Corrosion that can not eliminate alloy.
Embodiment 1:
6061 aluminum alloy hot rolling sheet materials, after 540 DEG C/1h solution treatment and shrend, carry out the deformation of 80% drafts (reduction ratio) cold rolling at room temperature, the tensile strength of final alloy, yield strength and elongation percentage respectively 525MPa, 516MPa and 7.5%, corrosion behavior is homogeneous corrosion, as shown in Figure 3.
Embodiment 2:
6061 aluminum alloy hot rolling sheet materials, after 540 DEG C/1h solution treatment and shrend, carry out 180 DEG C/2h lack time effect subsequently to process, now alloy rigidity is 116HV, carry out the deformation of 80% drafts (reduction ratio) cold rolling at room temperature afterwards, the tensile strength of final alloy, yield strength and elongation percentage respectively 612MPa, 597MPa and 4.2%, corrosion behavior is homogeneous corrosion, as shown in Figure 4.
Comparative example 3:
6061 aluminum alloy hot rolling sheet materials, after 540 DEG C/1h solution treatment and shrend, carry out 180 DEG C/2h lack time effect subsequently to process, now alloy rigidity is 116HV, carry out the deformation of 70% drafts (reduction ratio) cold rolling at room temperature afterwards, the tensile strength of final alloy, yield strength and elongation percentage respectively 591MPa, 582MPa and 5.1%, corrosion behavior is intercrystalline corrosion, as shown in Figure 5.
It can be seen that when cold rolling at room temperature deflection is less, alloy Susceptibility To Intergranular Corrosion can not be eliminated in comparing embodiment 2 and comparative example 3.
Comparative example 4:
All the other steps are all identical with comparative example 3, it is only after " cold rolling at room temperature deformation " operates, alloy is carried out 175 DEG C/6h Ageing Treatment again, the tensile strength of final alloy, yield strength and elongation percentage respectively 463MPa, 438MPa and 8.5%, corrosion behavior is homogeneous corrosion, there is good anti intercrystalline corrosion performance, as shown in Figure 6.
Relatively " comparative example 3 " and " comparative example 4 ", it appeared that: when in cold rolling at room temperature deformation operation, time drafts (reduction ratio) is not high enough, good intercrystalline corrosion drag can be reached by follow-up Ageing Treatment, but alloy strength can be greatly reduced because of follow-up Ageing Treatment.
Embodiment 3
6061 aluminum alloy hot rolling sheet materials, after 530 DEG C/1h solution treatment and shrend, carry out 160 DEG C/6h lack time effect subsequently to process, now alloy rigidity is 122HV, carry out the deformation of 90% drafts (reduction ratio) cold rolling at room temperature afterwards, the tensile strength of final alloy, yield strength and elongation percentage respectively 655MPa, 643MPa and 3.2%, corrosion behavior is homogeneous corrosion.
Embodiment 4:
6061 aluminum alloy hot rolling sheet materials, after 530 DEG C/3h solution treatment and shrend, carry out 160 DEG C/1h lack time effect subsequently to process, now alloy rigidity is 110HV, carry out the deformation of 95% drafts (reduction ratio) cold rolling at room temperature afterwards, the tensile strength of final alloy, yield strength and elongation percentage respectively 624MPa, 611MPa and 5.7%, corrosion behavior is homogeneous corrosion.
Embodiment 5:
6061 aluminum alloy hot rolling sheet materials, after 540 DEG C/2h solution treatment and shrend, carry out 190 DEG C/1h lack time effect subsequently to process, now alloy rigidity is 120HV, carry out the deformation of 85% drafts (reduction ratio) cold rolling at room temperature afterwards, the tensile strength of final alloy, yield strength and elongation percentage respectively 641MPa, 636MPa and 4.2%, corrosion behavior is homogeneous corrosion.
Embodiment 6:
6061 aluminum alloy hot rolling sheet materials, after 540 DEG C/2h solution treatment and shrend, carry out 190 DEG C/1h lack time effect subsequently to process, now alloy rigidity is 120HV, carry out the deformation of 85% drafts (reduction ratio) cold rolling at room temperature afterwards, the tensile strength of final alloy, yield strength and elongation percentage respectively 648MPa, 640MPa and 3.8%, corrosion behavior is homogeneous corrosion.
For 6056 aluminium alloys:
Comparative example 5:
6056 aluminum alloy hot rolling sheet materials, after 540 DEG C/2h solution treatment and shrend, carry out 180 DEG C/8h timeliness subsequently, reach peak aged (T6), alloy rigidity is 145HV, tensile strength, yield strength and elongation percentage respectively 415MPa, 385MPa and 9.3%, corrosion behavior is intercrystalline corrosion.
Comparative example 6:
6056 aluminum alloy hot rolling sheet materials, after 540 DEG C/2h solution treatment and shrend, carry out 180 DEG C/8h timeliness subsequently, reach peak aged (T6), alloy rigidity is 145HV, carry out the deformation of 90% drafts (reduction ratio) cold rolling at room temperature, the tensile strength of final alloy, yield strength and elongation percentage respectively 619MPa, 602MPa and 4.3% afterwards, but corrosion behavior is still for intercrystalline corrosion.
It can be seen that after alloy hardening degree reached peak aged after Ageing Treatment, intercrystalline corrosion drag can be caused very big negative effect from comparative example 5,6.
Embodiment 7:
6056 aluminum alloy hot rolling sheet materials, after 540 DEG C/2h solution treatment and shrend, carrying out the deformation of 90% drafts (reduction ratio) cold rolling at room temperature, the tensile strength of final alloy, yield strength and elongation percentage respectively 588MPa, 572MPa and 6.8%, corrosion behavior is homogeneous corrosion.
Embodiment 8:
6056 aluminum alloy hot rolling sheet materials, after 540 DEG C/2h solution treatment and shrend, carry out 160 DEG C/4h lack time effect subsequently to process, now alloy rigidity is 132HV, carry out the deformation of 90% drafts (reduction ratio) cold rolling at room temperature afterwards, the tensile strength of final alloy, yield strength and elongation percentage respectively 686MPa, 679MPa and 3.8%, corrosion behavior is homogeneous corrosion.
Comparative example 7
6056 aluminum alloy hot rolling sheet materials, after 540 DEG C/2h solution treatment and shrend, carry out 160 DEG C/4h lack time effect subsequently to process, now alloy rigidity is 132HV, carry out the deformation of 60% drafts (reduction ratio) cold rolling at room temperature afterwards, the tensile strength of final alloy, yield strength and elongation percentage respectively 613MPa, 595MPa and 4.5%, corrosion behavior is intercrystalline corrosion.
Comparative example 8
All the other steps are all identical with comparative example 7, it is only after " cold rolling at room temperature deformation " operates, alloy is carried out 200 DEG C/4h Ageing Treatment again, the tensile strength of final alloy, yield strength and elongation percentage respectively 542MPa, 527MPa and 7.2%, corrosion behavior is homogeneous corrosion, has good anti intercrystalline corrosion performance.
In like manner: " comparative example 7 " and " comparative example 8 " is compared, it appeared that: when in cold rolling at room temperature deformation operation, time drafts (reduction ratio) is not high enough, good intercrystalline corrosion drag can be reached by follow-up Ageing Treatment, but alloy strength can be greatly reduced because of subsequent treatment.
Embodiment 9:
6056 aluminum alloy hot rolling sheet materials, after 530 DEG C/3h solution treatment and shrend, carry out 160 DEG C/1h lack time effect subsequently to process, now alloy rigidity is 135HV, carry out the deformation of 80% drafts (reduction ratio) cold rolling at room temperature afterwards, the tensile strength of final alloy, yield strength and elongation percentage respectively 653MPa, 645MPa and 5.4%, corrosion behavior is homogeneous corrosion.
Embodiment 10:
6056 aluminum alloy hot rolling sheet materials, after 550 DEG C/3h solution treatment and shrend, carry out 190 DEG C/1h lack time effect subsequently to process, now alloy rigidity is 136HV, carry out the deformation of 95% drafts (reduction ratio) cold rolling at room temperature afterwards, the tensile strength of final alloy, yield strength and elongation percentage respectively 696MPa, 681MPa and 3.5%, corrosion behavior is homogeneous corrosion.
Embodiment 11:
6056 aluminum alloy hot rolling sheet materials, after 550 DEG C/1h solution treatment and shrend, carry out 170 DEG C/2h lack time effect subsequently to process, now alloy rigidity is 131HV, carry out the deformation of 85% drafts (reduction ratio) cold rolling at room temperature afterwards, the tensile strength of final alloy, yield strength and elongation percentage respectively 681MPa, 672MPa and 4.2%, corrosion behavior is homogeneous corrosion.
Embodiment 12:
6056 aluminum alloy hot rolling sheet materials, after 550 DEG C/2h solution treatment and shrend, carry out 160 DEG C/6h lack time effect subsequently to process, now alloy rigidity is 137HV, carry out the deformation of 80% drafts (reduction ratio) cold rolling at room temperature afterwards, the tensile strength of final alloy, yield strength and elongation percentage respectively 706MPa, 693MPa and 2.9%, corrosion behavior is homogeneous corrosion.
Embodiment 13:
6056 aluminum alloy hot rolling sheet materials, after 530 DEG C/2h solution treatment and shrend, carry out 180 DEG C/4h lack time effect subsequently to process, now alloy rigidity is 134HV, carry out the deformation of 80% drafts (reduction ratio) cold rolling at room temperature afterwards, the tensile strength of final alloy, yield strength and elongation percentage respectively 695MPa, 684MPa and 4.7%, corrosion behavior is homogeneous corrosion.
For 6013 aluminium alloys:
Comparative example 9:
6013 aluminum alloy hot rolling sheet materials, after 530 DEG C/1h solution treatment and shrend, carry out 180 DEG C/8h timeliness subsequently, reach peak aged (T6), alloy rigidity is 147HV, tensile strength, yield strength and elongation percentage respectively 420MPa, 390MPa and 8.5%, corrosion behavior is intercrystalline corrosion.
Embodiment 14:
6013 aluminum alloy hot rolling sheet materials, after 530 DEG C/1h solution treatment and shrend, carrying out the deformation of 90% drafts (reduction ratio) cold rolling at room temperature, the tensile strength of final alloy, yield strength and elongation percentage respectively 647MPa, 631MPa and 5.2%, corrosion behavior is homogeneous corrosion.
Embodiment 15:
6013 aluminum alloy hot rolling sheet materials, after 530 DEG C/2h solution treatment and shrend, carry out 180 DEG C/1h lack time effect subsequently to process, now alloy rigidity is 139HV, carry out the deformation of 80% drafts (reduction ratio) cold rolling at room temperature afterwards, the tensile strength of final alloy, yield strength and elongation percentage respectively 682MPa, 669MPa and 4.4%, corrosion behavior is homogeneous corrosion.
Embodiment 16:
6013 aluminum alloy hot rolling sheet materials, after 550 DEG C/3h solution treatment and shrend, carry out 160 DEG C/1h lack time effect subsequently to process, now alloy rigidity is 132HV, carry out the deformation of 90% drafts (reduction ratio) cold rolling at room temperature afterwards, the tensile strength of final alloy, yield strength and elongation percentage respectively 705MPa, 699MPa and 3.5%, corrosion behavior is homogeneous corrosion.
Embodiment 17:
6013 aluminum alloy hot rolling sheet materials, after 540 DEG C/2h solution treatment and shrend, carry out 180 DEG C/4h lack time effect subsequently to process, now alloy rigidity is 142HV, carry out the deformation of 80% drafts (reduction ratio) cold rolling at room temperature afterwards, the tensile strength of final alloy, yield strength and elongation percentage respectively 699MPa, 687MPa and 3.9%, corrosion behavior is homogeneous corrosion.
Embodiment 18:
6013 aluminum alloy hot rolling sheet materials, after 530 DEG C/3h solution treatment and shrend, carry out 190 DEG C/1h lack time effect subsequently to process, now alloy rigidity is 140HV, carry out the deformation of 90% drafts (reduction ratio) cold rolling at room temperature afterwards, the tensile strength of final alloy, yield strength and elongation percentage respectively 718MPa, 706MPa and 3.1%, corrosion behavior is homogeneous corrosion.
Embodiment 19:
6013 aluminum alloy hot rolling sheet materials, after 550 DEG C/1h solution treatment and shrend, carry out 170 DEG C/2h lack time effect subsequently to process, now alloy rigidity is 138HV, carry out the deformation of 95% drafts (reduction ratio) cold rolling at room temperature afterwards, the tensile strength of final alloy, yield strength and elongation percentage respectively 724MPa, 716MPa and 2.7%, corrosion behavior is homogeneous corrosion.
Claims (4)
1. one kind 6000 is the deformation heat treatment method of Al-Mg-Si-Cu aluminium alloy, it is characterized in that: described deformation heat treatment method is, aluminium alloy is through solution treatment, quenching, after direct or lack time effect processes, carry out heavy reduction cold rolling at room temperature deformation again, wherein, the drafts of described cold rolling at room temperature deformation is not less than 80%.
2. as claimed in claim 1 6000 is the deformation heat treatment method of Al-Mg-Si-Cu aluminium alloy, it is characterised in that: described quenching is room temperature shrend.
3. as claimed in claim 1 6000 is the deformation heat treatment method of Al-Mg-Si-Cu aluminium alloy, it is characterised in that: described lack time effect processes the alloy hardening degree produced less than the 90% of peak value timeliness hardness.
4. as claimed in claim 1 6000 is the deformation heat treatment method of Al-Mg-Si-Cu aluminium alloy, it is characterised in that: in described solution treatment, solid solubility temperature is 530-550 DEG C, and solution time is 1-3h.
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