CN104046933A - Thermal-mechanical treatment method for enhancing plasticity and forming property of high strength aluminum alloy sheet - Google Patents
Thermal-mechanical treatment method for enhancing plasticity and forming property of high strength aluminum alloy sheet Download PDFInfo
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Abstract
The invention relates to a thermal-mechanical treatment method for enhancing plasticity and forming property of 7000series aluminum alloy sheet. The method comprises the specific steps are as follows: (1) solid solution treatment; (2) cold deformation; (3) insulation and continuous rolling deformation; and (4) short recrystallization treatment. The treatment method can refine the grain size of aluminum alloy from more than 200 mu m to 10 m and below, and after peak aging treatment on the fine grain, the aluminum alloy sheet gains room temperature strength similar to that of the aluminum alloy sheet obtained by the traditional hot rolling technology, and the significantly improved elongation. Compared with the traditional hot rolling process, a quenched sheet gains improved room temperature forming property, an annealed sheet gains greatly improved room temperature forming property, and peak aged sheet gains greatly improved warm forming property. The fine grain forming property treatment method of 7000 series aluminum alloy sheet provided by the invention has simple process, short cycle, low energy consumption, and great application potential and value in industrial production.
Description
Technical field
The present invention relates to a kind of deformation heat treatment method that improves high strength alumin ium alloy plasticity and plasticity, particularly a kind of grain refining treatment process of aluminum alloy materials, belongs to metallic substance thermomechanical treatment Technology field.
Background technology
It is the important high-strength light structured material of a class that Al-Zn-Mg-Cu (7000) is associated gold, and to be associated metallographic specific tenacity high with Al-Mg-Si (6000), but its plasticity and plasticity are poor.Plasticity and toughness and the corrosive nature of fine grained texture's 7000 line aluminium alloys also can make moderate progress, so crystal grain thinning becomes the method for improving aluminium alloy over-all properties.Aluminium alloy stacking fault energy is higher, and recrystallize is more difficult, and aluminum grain refinement is mainly realized by discontinuous recrystallize.
Middle thermomechanical treatment (ITMT) can realize aluminum grain refinement by discontinuous recrystallize.ITMT technique for 7000 line aluminium alloy grain refinings is the people (J.Wert such as nineteen eighty-two J.Wert at present, et al.Metallurgical Transactions A, 1981,12A:1267) the relatively simple RI-ITMT technique of exploitation, processing step comprises: solution hardening, overaging in 400 ℃/8 hours, middle warm deformation and solid solution and recrystallize treatment are processed.They by this technique by 7075 aluminum grain refinements to 10 μ m, unit elongation obtains obviously and improves.The core concept of RI-ITMT technique is exactly to process while growing by high temperature to obtain macrobead, after acquisition macrobead, continue room temperature or middle warm deformation and form deformation bands around at macrobead, follow-up recrystallize utilizes particle induction Recrystallization nucleation to realize structure refinement while processing.But, RI-ITMT technique needs long high temperature overaging to process, process cycle is long, energy consumption is large, can not produce continuously, therefore, develop a kind of simple to operate, process cycle is short, it is significant to realize suitability for industrialized production and improve the new middle thermomechanical treatment technique of 7000 line aluminium alloy plasticity and plasticity.
Summary of the invention
The object of the invention is to overcome the deficiency of existing technique and develop the 7000 line aluminium alloy Deformation Heat Treatment Microstructures thinning processing methods of recrystallize of a kind of method solution treatment simple, easy to operate, with short production cycle-cold roller and deformed-insulation+continuous modification-in short-term.Solid solution state aluminium alloy after cold roller and deformed again insulation can greatly accelerate that precipitated phase is separated out, alligatoring and obtain large size precipitated phase, the deformation bands around forming at large size precipitated phase (0.5 μ m) after follow-up middle temperature, deformation at room temperature, is conducive to excite Recrystallization nucleation when follow-up recrystallize is processed.The cold rolling mode combining with insulation of this technology utilization replaces simple overaging, greatly shortened the cycle of classical RI-ITMT technique, can under simple operations, obtain fine grained texture, greatly improve the plasticity and toughness of high strength alumin ium alloy, and significantly improve intensity and plastic anisotropy, greatly improve its forming property, can be widely used in precipitation strength type 7000 line aluminium alloys.
The present invention relates to the grain refining processing side of a kind of raising 7000 line aluminium alloy sheet material plasticity and plasticity
Method, comprises the steps:
(1) solid solution
7000 line aluminium alloys carry out solution treatment, solid solubility temperature 460-500 ℃, soaking time 0.5-24h, room temperature shrend;
(2) cold rolling
Mode of texturing is cold rolling, and wherein, R1 deflection is controlled at 30-80%
(3) insulation+continuous modification
The sheet material obtaining by second step, is incubated and continuous modification is processed, and holding temperature T is 200-450 ℃, and soaking time t is fixed as 30min; R2 continuous modification mode is rolling, and deflection is 40-90%, and deformation process is not melted down;
(4) recrystallize in short-term
The sheet material that the 3rd step is obtained quickly heats up to 460-490 ℃ and carries out recrystallize processing, soaking time 10-60min, and the type of cooling is air cooling or room temperature shrend.
Wherein, in step 2, cold rolling reduction is controlled at 40-70%.
Wherein, in step 3, holding temperature is controlled at 250-400 ℃, and soaking time is 30min, continuous modification amount 50-90%, or holding temperature is controlled at 350-400 ℃, and soaking time is 30min, and deflection is controlled at 50-90%.
Wherein, step 2 with the better condition that step 3 cooperatively interacts is: step 2 cold rolling reduction 40%-70%, 350 ℃-450 ℃ of step 3 holding temperatures, soaking time 30min, continuous modification amount 60%-80%.Top condition is: step 2 cold rolling reduction 50%-60%, 350 ℃-400 ℃ of step 3 holding temperatures, soaking time 30min, continuous modification amount 60%-80%.
Wherein, in step 4, temperature rise rate >=1 during recrystallize ℃/s.
Wherein, the recrystallize in short-term step 4 being obtained the sheet material of shrend carry out T6, T76, T74, T73 or T77 ageing treatment.
Wherein, resulting final sheet material is carried out to room temperature plasticity or warm working test, the method that testing method adopts GB GB/T4156-2007 to describe.
Adopt above deformation heat treatment method to process 7000 line aluminium alloy sheet materials, the mode of utilizing cold deformation to combine with insulation replaces simple overaging to accelerate separating out of large size precipitated phase particle, thereby obtain the core that can excite recrystallize, in example operation, the 3rd step isothermal treatment for short time obtains the precipitated phase (mean sizes 0.5 μ m) of some amount after processing, thereby overaging is processed while having replaced RI-ITMT long, greatly shorten the time of a whole set of technique.Sheet material after recrystallize shrend is carried out after T6 ageing treatment, and timber intensity is suitable with traditional hot rolling technology, but unit elongation can obtain significantly raising, thereby plasticity also obtains raising.
By above-mentioned thermomechanical treatment technique, by the cold rolling mode combining with insulation, obtain large size precipitated phase MgZn2 particle, in continuous modification subsequently, at macrobead, can form deformation bands around, and will take precipitated phase as core forming core at recrystallize stage recrystal grain in short-term, thereby obtain tiny recrystallized structure.
Experiment shows, 7000 line aluminium alloys are by above-mentioned solution treatment-cold roller and deformed-insulation+continuous modification-solid solution and recrystallize treatment technique is compared with conventional thermomechanical treatment technique in short-term, technique provided by the invention has shortened preparation time greatly, reduce operation easier, when after obtaining good fine grained texture, aging state 7000 line aluminium alloy sheet materials keep good strength, unit elongation is greatly improved, quenching state, annealed state sheet material room temperature forming property improve obviously, and after quenching state sheet material peak timeliness, warm working performance is largely increased.The great significance of the material that has good intensity and plasticity and toughness concurrently to fields such as aerospace, communications and transportation, is suitable for industrial applications.
Accompanying drawing explanation
Fig. 1 is process flow diagram of the present invention.
Fig. 2 is the tissue of initial state 7075 alloy recrystallizations shrend.
Fig. 3 is the M of solid solution state alloy after cold deformation and isothermal treatment for short time processing in embodiment 1
gzn2 distribution plan.
Fig. 4 is that embodiment 1 interalloy is through the tissue of recrystallize shrend.
Fig. 5 be in embodiment 1 comparative example I alloy through the tissue of recrystallize shrend.
Fig. 6 be in embodiment 1 comparative example II tradition hot rolled alloy through the tissue of recrystallize shrend.
Fig. 7 is that embodiment 2 interalloies are through the tissue of recrystallize shrend.
Fig. 8 a, b are that the alloy of different process in embodiment 3 is through the tissue of recrystallize shrend.
Fig. 9 is that embodiment 4 interalloies are through the tissue of solid solution and recrystallize treatment shrend.。
Figure 10 be in embodiment 5 7050 alloys through the tissue of recrystallize shrend.
Embodiment
Embodiment 1
According to technique shown in Fig. 1, adopting 7075 aluminium alloys is rolling stock.For solute atoms is solidly soluted in matrix, sheet material has been carried out to the solution treatment of 475 ℃/1.5h, room temperature shrend, Fig. 2 is the metallographic structure of undeformed initial quenching state 7075 alloys.Distortion realizes on common duo mill, thick solid solution state 7075 sheet alloys of 15mm are carried out cold roller and deformed, deflection 30% continues cold rolling state alloy on milling train, sheet material to be carried out 80% continuous rolling after 400 ℃ of insulation 30min, and continuous rolling process is not melted down.Final rolled plate is carried out to the recrystallize of 480 ℃/30min and process, after recrystallize completes, the type of cooling adopts respectively shrend (W state) and air cooling (O state).Fig. 4 is the metallographic structure of rolling after the shrend of plate recrystallize, and by linear intercept method, recording the now average grain size of alloy is 9.8 μ m.Adopt two comparative examples, I: the art breading (RI-ITMT) that adopts 7075 aluminium alloys to press J.Wert, it is solid solution-400 ℃/8h overaging-warm-rolling deflection 90%-recrystallize, II: the thick solid solution state 7075 of 15mm is carried out to 400 ℃ of traditional hot rollings (HR), total deformation 88%, other thermal treatment process are identical, and Fig. 5,6 is respectively the metallographic structure after the two recrystallize Water Quenching, the crystal grain of the 100 μ m that are still elongation that visible traditional hot rolling obtains.Subsequently the sheet material of technique of the present invention and the shrend of two contrast technique is carried out to T6 ageing treatment, and aging state sheet material is carried out to Mechanics Performance Testing, as shown in table 1.The air cooling that three kinds of techniques are obtained and the sheet material of shrend carry out the test of room temperature plasticity, and the sheet material of the peak timeliness that three kinds of techniques are obtained carries out the warm working test (T6-200 ℃) of 200 ℃, as shown in table 2.Therefrom can find out, technique of the present invention is compared with traditional hot rolling technology, and peak aging state sheet material has improved plasticity in the situation that obtaining same intensity.Plasticity under three kinds of states of sheet material of the present invention is all higher than traditional hot rolling technology, and suitable with RI-ITMT technique, but the present invention compares greatly and shortened the process time with RI-ITMT technique, is very beneficial for suitability for industrialized production.
Embodiment 2
According to the treatment process of mechanical thermal shown in Fig. 1, adopting 7075 alloys through 475 ℃/1.5h solution treatment is rolling stock (thickness of slab 7.5mm).Carried out cold roller and deformed, deflection 40%, it is 70% continuous modification that cold rolling state sheet material continues to carry out deflection on milling train after 350 ℃ of insulation 30min, does not melt down.By final rolled plate, through 480 ℃/0.5h recrystallize Water Quenching, Fig. 7 is obtained fine grained texture.Finish to gauge plate is through 480 ℃/0.5h solid solution and T6 ageing treatment, now in timber intensity and embodiment 1 quite, sheet material unit elongation is 16.6% (table 1), 200 ℃ of Erichsen numbers are higher than traditional hot rolling technology.
Embodiment 3
According to the treatment process of mechanical thermal shown in Fig. 1, adopting 7075 alloys through 475 ℃/1.5h solution treatment is rolling stock (thickness of slab 7.5mm).Two block of material are realized to 50% deflection on duo mill, and two cold-reduced sheets continue on milling train, to carry out the continuous modification of deflection 70% respectively after 350 ℃, 400 ℃ insulation 30min afterwards, do not melt down.Final rolled plate is processed through 480 ℃/0.5h recrystallize shrend and 120 ℃/24h, can obtain fine grained texture respectively as shown in Fig. 8 a, b, now suitable in timber intensity and embodiment 1, sheet material unit elongation is respectively 16.5%, 16.7%, and this condition also can realize grain refining and improve plasticity (table 1) and the warm working (table 2) of sheet material as seen.
Embodiment 4
According to the treatment process of mechanical thermal shown in Fig. 1, adopting 7075 alloys through 475 ℃/1.5h solution treatment is rolling stock (thickness of slab 7.5mm).Carried out cold roller and deformedly 60%, with by 350 ℃ of insulation 30min, continued afterwards to carry out deflection and be 60% continuous modification on milling train, do not melted down.By the sheet material after rolling through 480 ℃/0.5h recrystallize Water Quenching, the fine grained texture obtaining as shown in Figure 9, the sheet material of 60% cold roller and deformed rear insulation continuous modification 60% unit elongation after recrystallize and T6 processing reaches 16.6% (table 1), and warm working performance is still better than traditional hot-rolled sheet (table 2).
Embodiment 5
According to the treatment process of mechanical thermal shown in Fig. 1, adopting 7050 aluminium alloys is rolling stock (thickness of slab 15mm),
It is carried out to the solution treatment of 475 ℃/1.5h, room temperature shrend.Solid solution state 7050 is carried out to cold roller and deformed 50% to 7.5mm, 7.5mm sheet material is carried out after 400 ℃ of insulation 30min to the continuous modification of deflection 70%, continuous modification process is not melted down.Final rolled plate is processed through 480 ℃/0.5h and 120 ℃/24h,
The average grain size of the tissue that obtains is 9.6 μ m (Figure 10), and now the plasticity of alloy is greatly improved, and unit elongation is up to 20.9%, and warm working excellent performance.
Alloy T6 state room-temperature mechanical property prepared by table 1 the present invention
Table 2 sheet material room temperature plasticity and warm working performance
As can be seen from Figure 3, solid solution state alloy through cold rolling and in short-term in warm insulation can obtain the large size MgZn2 particle of a large amount of 0.5 μ m, in continuous rolling distortion subsequently, can form strong deformation district around at these particles, when solution treatment, as the core of recrystallize, bring out the formation of tiny recrystal grain.Compare technique of the present invention with traditional RI-ITMT technique and can in crystal grain thinning, greatly shorten preparation time.Through the aluminium alloy of processes of the present invention, can obtain the fine grained texture of 6-20 μ m, and technique of the present invention can obtain the fine grained texture suitable with RI-ITMT artwork particle size.
In table 1 and table 2, three of embodiment 1 kinds of technique contrasts can be found out, by simple process of the present invention, can, when realizing grain refining, improve greatly plasticity and the plasticity of sheet alloy.7000 line aluminium alloy schedule of reinforcements mainly rely on precipitation strength, so grain refining is little to the intensity effect of 7000 line aluminium alloys, but grain refining can improve plasticity greatly, thereby contribute to improve plasticity.
7000 line aluminium alloys with precipitation strength feature can accelerate precipitation phase through cold deformation and middle temperature insulation and separate out, also can further impel the alligatoring of precipitated phase or grow up simultaneously, macroparticle can be used as recrystallize core and for grain refining, and for improving plasticity and plasticity.Therefore after technique crystal grain thinning provided by the present invention, can effectively improve high-strength 7075 and plasticity and toughness, the plasticity of 7050 aluminium alloys.Technological principle provided by the present invention is applicable to all 7000 line aluminium alloys simultaneously, by technique of the present invention, is realized structure refinement and is improved plasticity, plasticity, is not limited in 7075 and 7050 aluminium alloys.
Claims (10)
1. a deformation heat treatment method that improves high strength alumin ium alloy sheet material plasticity and plasticity, is characterized in that: the method comprises the following steps:
(1) solution treatment step; (2) cold roller and deformed step; (3) insulation and continuous rolling deforming step; (4) recrystallize treatment step in short-term; Wherein,
In step (1), 7000 line aluminium alloys are carried out to solution treatment, solute atoms is fully solidly soluted in matrix, wherein, solid solubility temperature is 460-500 ℃, and soaking time is 0.5-24h, room temperature shrend after solid solution;
In step (2), solid solution state sheet material is carried out cold roller and deformed, wherein, cold rolling reduction is controlled at 30-80%;
In step (3), the sheet material that step (2) is obtained is incubated and continuous rolling distortion, and wherein, holding temperature is 200-450 ℃, soaking time 30min, and the continuous rolling deflection after insulation is controlled at 40-90%, does not melt down;
In step (4), the sheet material that step (3) is obtained is heated rapidly to 460-490 ℃ and carries out recrystallize processing, soaking time 10-60min, subsequently air cooling or room temperature shrend immediately.
2. the deformation heat treatment method of raising high strength alumin ium alloy sheet material plasticity according to claim 1 and plasticity, is characterized in that, in step (2), cold rolling reduction is controlled at 40-70%.
3. the deformation heat treatment method of raising high strength alumin ium alloy sheet material plasticity according to claim 1 and plasticity, is characterized in that, in step (3), holding temperature is controlled at 250-400 ℃, soaking time 30min.
4. the deformation heat treatment method of raising high strength alumin ium alloy sheet material plasticity according to claim 1 and plasticity, is characterized in that, in step (3), holding temperature is controlled at 350-400 ℃, soaking time 30min.
5. the deformation heat treatment method of raising high strength alumin ium alloy sheet material plasticity according to claim 1 and plasticity, is characterized in that, in step (3), continuous modification amount is 50-90%.
6. treatment process according to claim 1, it is characterized in that, step (2) with the condition that step (3) cooperatively interacts is: step (2) cold rolling reduction 40%-70%, 350 ℃-450 ℃ of step (3) holding temperatures, soaking time 30min, continuous modification amount 60%-80%.
7. treatment process according to claim 1, it is characterized in that, step (2) with the condition that step (3) cooperatively interacts is: step (2) cold rolling reduction 50%-60%, 350 ℃-400 ℃ of step (3) holding temperatures, soaking time 30min, continuous modification amount 60%-80%.
8. the deformation heat treatment method of raising high strength alumin ium alloy sheet material plasticity according to claim 1 and plasticity, is characterized in that, in step (4), and temperature rise rate >=1 when recrystallize is processed ℃/s, air cooling or room temperature shrend after recrystallize completes.
9. the deformation heat treatment method of raising high strength alumin ium alloy sheet material plasticity according to claim 8 and plasticity, is characterized in that, the sheet material after the recrystallize in short-term that step (4) is obtained quenching carries out ageing treatment.
10. the deformation heat treatment method of raising high strength alumin ium alloy sheet material plasticity according to claim 9 and plasticity, is characterized in that, described ageing treatment refers to T6, T76, T74, T73 or T77 ageing treatment.
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| CN105886976A (en) * | 2016-04-21 | 2016-08-24 | 湖南人文科技学院 | Heat mechanical treatment technology for improving comprehensive performance of aluminum alloy |
| CN110453163A (en) * | 2019-08-16 | 2019-11-15 | 中国航发北京航空材料研究院 | A method of 7000 line aluminium alloy super large-scale forging part height are improved to performance |
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| CN114717492A (en) * | 2022-04-02 | 2022-07-08 | 南通雨奇金属制品有限公司 | Heat treatment method for deformation of high-strength and high-toughness aluminum alloy |
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| CN115386695A (en) * | 2022-08-30 | 2022-11-25 | 河钢股份有限公司 | Rolling and heat treatment method of 30Ni15Cr2Ti2Al alloy |
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