CN104894442A - Aluminum alloy sheet material for vehicles and preparation method thereof - Google Patents
Aluminum alloy sheet material for vehicles and preparation method thereof Download PDFInfo
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Abstract
The invention discloses an aluminum alloy sheet material for vehicles and a preparation method thereof. The aluminum alloy sheet material comprises 4.5-5.5wt% of Mg, 0.15-0.35wt% of Mn, 0.10-0.30wt% of Fe, less than or equal to 0.15wt% of Si, less than or equal to 0.10wt% of Ti, less than or equal to 0.10wt% of Cu, less than or equal to 0.10wt% of Zn, less than or equal to 0.10wt% of Cr and the balance Al and unavoidable impurities. The preparation method orderly comprises material blending, melting casting, uniformization, hot rolling deformation, primary cold rolling deformation, intermediate annealing, secondary cold rolling deformation and complete annealing. Through the design and optimization of alloy components and preparation processes, the 5XXX-series aluminum alloy sheet material with high formability and a low cost is prepared by the existing conventional plate and strip production line.
Description
Technical field
The invention belongs to technical field of aluminum alloy technology, particularly relate to a kind of Aluminum alloy plate for vehicle material and preparation method thereof.
Background technology
Along with continuing to increase of Global Auto recoverable amount, energy consumption, environmental pollution and safety problem have become the three large severe problems that Global Auto industry faces, thus force Automobile Enterprises to be greatly developed and advance automotive light weight technology technology.The core of automotive light weight technology technology is being controlled cost with under the prerequisite of guaranteed performance, alleviates automotive dead weight to reduce energy consumption, to improve the fuel economy of automobile, reduce environmental pollution.Therefore, along with the quickening of automotive light weight technology process in recent years, aluminium alloy is high, corrosion-resistant with its light weight, specific tenacity, good, the easy surface colour of shock resistance, good formability, and highly to reclaim again, a series of good characteristic such as reproducibility, be acknowledged as the ideal material of automotive light weight technology, be also more and more used widely in automotive light weight technology process.
Body of a motor car weight accounts for 30 ~ 40% of vehicle complete vehicle weight, and vehicle body loss of weight can bring significant effects of energy saving and emission reduction, and therefore, the aluminum lightweight of body of a motor car receives much concern always, becomes the core of countries in the world Automobile Enterprises lightweight work.The main coating member of body of a motor car can be assembled by aluminum alloy plate materials punching press, as parts such as engine shield, luggage-boot lid, car door, covering for roofs, floor, thermal baffles.But find in actual application, bonnet inner panel, boot-lid inner panel, inner plate of car door and other body of a motor car inner panel position shapes are extremely complicated, require higher to the forming property of aluminum alloy plate materials.Therefore, in typical aluminum alloy for vehicle body plate 2XXX, 5XXX and 6XXX system alloy, 5XXX line aluminium alloy is high because of forming property indexs such as itself n and r value, elongation after fracture, plate member in the body of a motor car being highly suitable for having a high requirement to forming property.
No matter be aluminium alloy automobile plate exploitation Europe comparatively early, beautiful, Deng developed country, still the China of flourish aluminium alloy automobile plate in recent years, for the alloy designs of 5XXX line aluminium alloy auto sheet, process exploitation, and forming property optimization, large quantity research has been carried out in surface quality improvement etc., as patent EP0594509B1, EP0569006B1, US4081294A, US5518558A, US6342112B1, JP4-147936A, JP4-327430A, CN101880803A, and the patent such as CN102220729A, develop 5052, 5754, 5083, the O state 5XXX line aluminium alloy auto sheet such as 5182 and KS5030, wherein 5182-O state aluminum alloy plate materials is widely used because it has the good combination of intensity and high deep punching capability.
But, in order to improve the forming property of 5XXX line aluminium alloy sheet material further, mostly Fe and Si foreign matter content is controlled at lower level (< 0.1 wt%), and adopt the methods such as advanced continous way anneling production line, greatly increase material cost and equipment investment cost.Meanwhile, part of production design is unreasonable, and as homogenizing adopts the system of 460 ~ 480 DEG C/16 ~ 24h, production energy consumption is large, cost is high, inefficiency.Therefore, under current automobile aluminium sheet price is the pressure of steel plate 4 ~ 6 times, Automobile Enterprises is badly in need of the 5XXX line aluminium alloy automobile board of a kind of high formability, low cost, complex-shaped to meet motor car engine inner cover, luggage inner cap, inner plate of car door, other body of a motor car inner panels etc., aluminium alloy plate shaping property is required to the demand of higher parts.
Summary of the invention
Object of the present invention is exactly for prior art Problems existing, provides a kind of novel automobile aluminium alloy and preparation method thereof possessing high formability energy, lower production cost.
Above-mentioned purpose is realized by following proposal:
A kind of Aluminum alloy plate for vehicle material, it is characterized in that, the chemical composition of described sheet alloy and mass percentage content thereof are: Mg:4.5 ~ 5.5 wt%, Mn:0.15 ~ 0.35 wt%, Fe:0.10 ~ 0.30 wt%, Si≤0.15 wt%, Ti≤0.10 wt%, Cu≤0.10 wt%, Zn≤0.10 wt%, Cr≤0.10 wt%, surplus is Al and inevitable impurity.
Preferably, Mg, Mn and Fe content range is respectively: Mg:4.5 ~ 5.0 wt%, Mn:0.15 ~ 0.25 wt%, Fe:0.15 ~ 0.25 wt%.
Prepare a method for above-mentioned Aluminum alloy plate for vehicle material, described preparation method comprises the following steps successively: the distortion of batching, melting and casting, homogenizing, hot rolling deformation, once cold rolling, process annealing, secondary cold-rolling distortion, Full Annealing.
Preferably, in described melting and casting step, adopt Cl
2carry out furnace refining with Ar mixed gas and SNIF carries out degassing processing, control Na≤3 ppm in ingot casting, Ca≤5 ppm, H
2≤ 0.15 ml/100g Al.
Preferably, ingot casting heating rate 15 ~ 40 DEG C/h of described uniformization step, homogenization temperature 500 ~ 550 DEG C, soaking time 1 ~ 6 h, stove is chilled to hot rolling start rolling temperature 470 ~ 490 DEG C, is incubated 2 h.
Preferably, described hot rolling deformation step adopts 1+4 hot continuous rolling production line to carry out the hot rolling of sheet material, thickness of slab 20 ~ 30 mm in the middle of hot roughing, and the thickness connecting finish rolling sheet material through 4 heat is 4 ~ 6 mm, sheet material coiling temperature 320 ~ 360 DEG C
Preferably, in described intermediate annealing step, coiled material temperature rise rate 15 ~ 40 DEG C/h, intermediate anneal temperature 310 ~ 340 DEG C, annealing time 1 ~ 4 h, air cooling.
Preferably, in described secondary cold-rolling deforming step, the coiled material after process annealing air cooling, through secondary cold-rolling distortion finish rolling to finished product thickness, is out of shape total cold processing ratio by process annealing by secondary cold-rolling and controls between 25 ~ 65%.
Preferably, in described Full Annealing step, to the Full Annealing thermal treatment of coiled material, coiled material heating-cooling speed 15 ~ 40 DEG C/h, Full Annealing temperature 320 ~ 360 DEG C, annealing time 1 ~ 4 h, air cooling.
Preferably, it is characterized in that, the hot step of described Full Annealing adopts industrial Horizental annealer to carry out the Full Annealing thermal treatment of coiled material.
The substantive distinguishing features that technical solution of the present invention is outstanding: by Composition Design and optimization, Fe, Si impurity content of conventional 5182 alloys is adjusted, particularly control and optimize the content of Fe and Mn element, make full use of the interaction of impurity F e element and microalloying Mn element, in conjunction with the ingot homogenization thermal treatment process optimized, to regulate and control impurity F e and microalloy Mn element forms larger, the subglobose Al of size in Homogenization Process
6(FeMn) disperse phase particle.Make full use of larger, the subsphaeroidal Al of size that this kind of soaking regulation and control are separated out
6(FeMn) particle excitation induction Recrystallization nucleation effect (PSN) of disperse phase, promote the generation of recrystallize in 5XXX cold rolled sheet Full Annealing process, thus in the annealing furnace of conventional strip production line, realize rolling Full Annealing process, and ensure the shaft-like such as the recrystallized structure after Full Annealing is even, be, substantially increase the forming property of sheet material.
The 5XXX system alloy that the present invention proposes is to the requirement (< 0.1 wt%) of Fe, Si impurity content control overflow lower than other high shaping prods, particularly Fe constituent content controls at 0.15 ~ 0.25 wt%, greatly can improve the employing of reclaiming aluminium scrap, significantly reduce material cost.Adopt the uniform heating process of 500 ~ 550 DEG C/1 ~ 6 h regulation and control Fe and Mn element in Homogenization Process, form larger, the subsphaeroidal Al of size
6(FeMn) disperse phase, is not only conducive to the regulation and control of follow-up sheet material recrystallized structure, and the equal thermal system of other 460 ~ 480 DEG C/16 ~ 24h is relatively energy-conservation and production efficiency is high.Therefore, the present invention, by the design and optimization of alloying constituent, preparation technology, existing conventional strip production line prepares high formability, has the low cost 5XXX line aluminium alloy sheet material of price advantage, have boundless industrialization prospect.
Accompanying drawing explanation
Fig. 1 is the Technology Roadmap of Aluminum alloy plate for vehicle material of the present invention and preparation method thereof;
Fig. 2-7 is Al after the different Homogenization Treatments of alloy cast ingot
6(FeMn) disperse phase metallographic observation results;
Fig. 8-9 is elongation after fracture and Erichsen number performance test results after the different Full Annealing process of alloy cold-reduced sheet;
Figure 10-15 is metallographic structure observationss of O state sheet material under alloy different technology conditions.
Embodiment
The technological line of Aluminum alloy plate for vehicle material of the present invention and preparation method thereof as shown in Figure 1, comprises main production flow process and key process parameter, does supplementary and explanation further below in conjunction with specific embodiments to the present invention.
The electrolytic aluminum water that starting material adopt enterprise self-produced respectively, the one-level solid waste of 30%, Al-16.5%Si master alloy, Fe agent, Cu agent, Mn agent, pure Mg ingot etc.Concrete fusion-casting process be reinforcing body material (burner hearth design temperature 1050 DEG C) → add aluminium water → solid materialization flat after skim → (temperature of skimming 711 DEG C) → sampling analysis → add alloy (adding alloy temperature 736 DEG C) → induction stirring 20min → magnesium ingot of skimming → add (adding magnesium temperature 754 DEG C) → induction stirring 30min → sampling analysis (probe temperature 740 DEG C) skims after → composition is suitable → converter (converter temperature 744 DEG C) → refining (refining temperature 733 DEG C, refining time 2h, N
2-Cl
2mixed gas) → leave standstill → Wagstaff casting system carries out DC casting.
In castingprocesses, at SNIF(Spinning Nozzle lnert Flotation, rotate nozzle rare gas element and to swim method) add Al-5Ti-0.2B in front chute, be used for crystal grain thinning, the speed of feed of titanium boron wire is: V=127 ~ 148 cm/min, passes into Cl at SNIF degasifying device
2-Ar
2mixed gas carries out degassing processing to melt, and casting temp is 680 ~ 690 DEG C, casting speed 60 mm/min.In order to improve the quality of melt further, foudry line adopts CFF screen plate filter the slag in melt, CFF screen plate adopts twin-stage (40ppi/50ppi) to filter.By above founding and corresponding measure, guarantee Na≤3 ppm in ingot casting, Ca≤5 ppm, H
2≤ 0.15 ml/100g Al, improves the processing characteristics of sheet material and the mechanical property of product.
According to the alloying constituent carried out an invention, adopt the identical founding melting and casting ingot casting of 6 batches, concrete ingot casting information, comprise ingot casting lot number, alloying constituent in table 1, dimensions is that 5000 ~ 9000 mm(are long) × 1860 mm(are wide) × 620 mm(are thick), wherein ingot casting 4F171 is as reference comparative example, and be conventional 5182 alloys, 1E298 ~ 1E302 alloy is embodiment of the present invention alloying constituent.
Table 1 carries out an invention alloy casting batch number, alloying constituent
The alloy cast ingot that carries out an invention carries out sawing milling face, sawing ingot casting head sizes 100 mm, tail dimension 300 mm; Milling ingot casting surface size 15 mm, side dimension 10 mm.After implementing ingot casting sawing milling face, put into pushing type heating furnace and carry out different Homogenization Treatments respectively, then 1+4 hot continuous rolling unit is adopted carry out hot rolling deformation to 4 ~ 6 mm to ingot casting, exporting coiling temperatures through 4 passage hot continuous rollings is 320 ~ 360 DEG C, to guarantee that realizing sheet material fully completes recrystallization annealing.Single chassis 6 roller CVC cold-rolling mill is adopted to carry out cold roller and deformed to different required thickness.Process annealing and Full Annealing adopt conventional Horizental annealer to carry out coil annealing.Meanwhile, the alloy component production technique that carries out an invention by experiment room implements suitability for industrialized production after carrying out parameter formulation, as homogenization process, secondary cold-rolling are out of shape total cold processing ratio, Full Annealing technique.
Bruker Elemental A1140 direct-reading spectrometer is adopted to carry out the composition detection of alloy.Adopt ZEISS Imager M2m type opticmicroscope, WDW-100B type universal testing machine carries out structure and properties analysis to sheet material dead annealed after homogenizing ingot casting, secondary cold-rolling, provides foundation for optimizing corresponding technique.Mechanics properties testing adopts standard GB/T 228.1-2010, and disproportional P12 tension specimen, and forming property detects according to standard GB/T 5027-2007 and GB/T 5028-2008.
The performance test results of table 2 embodiment of the present invention Full Annealing state sheet material
Concrete embodiment is as follows:
Embodiment 1
Reference example alloy cast ingot 4F171 and alloy cast ingot 1E298 of the present invention, sawing cuts the laboratory exploration that ingot casting thickness direction 1/4 place ingot casting sample carries out homogenization process after leaving out the beginning and the end, air circulating oven is adopted to carry out even process heat process, temperature rise rate is 15 ~ 40 DEG C/h, shrend after soaking insulation.Adopt opticmicroscope, under same etching condition, to the Al after equal thermal treatment
6(FeMn) disperse phase carries out structure observation.The equal thermal system of 4F171 ingot casting sample is 480 DEG C/2h and 480 DEG C/24h, and its metallographic structure photo is respectively Fig. 2 and Fig. 3.And the equal thermal system of 1E298 ingot casting sample is 480 DEG C/2h, 530 DEG C/2h, 530 DEG C/4h and 530 DEG C/8h, its Al
6(FeMn) disperse phase metallographic structure observations respectively as shown in figs. 4-7.
Embodiment 2
Adopt alloy cast ingot 1E298 of the present invention, utilize pushing type heating furnace to carry out Homogenization Treatments behind sawing milling face, treatment process is: differential heating, ingot casting heating rate 15 ~ 40 DEG C/h, homogenization temperature 530 DEG C, after being incubated 2 h, stove is chilled to hot rolling start rolling temperature 470 ~ 490 DEG C, is incubated the direct hot rolling of 2 h, 1+4 hot continuous rolling production line is adopted to carry out the hot rolling of sheet material, hot roughing is to middle thickness of slab 28 mm, and the thickness connecting finish rolling sheet material through 4 heat is 5.5 mm, sheet material coiling temperature 339 ~ 350 DEG C.Thickness 0.8 mm is deformed into through single chassis 6 roller CVC rolled by cold rolling machine after hot rolled coil is cooled to room temperature.Air circulating oven is adopted to carry out Full Annealing Process Exploration, treatment process is: heating-cooling speed 30 DEG C/h, Full Annealing temperature is respectively 300 ~ 320 ~ 340 ~ 360 ~ 380 DEG C, annealing time 2 h, carry out elongation after fracture, Sven-Gan Eriksson Erichsen number Performance Detection to the sheet material after Full Annealing, its result respectively as shown in Figure 8 and Figure 9.
Embodiment 3
Reference example alloy cast ingot 4F171, pushing type heating furnace is utilized to carry out Homogenization Treatments behind sawing milling face, treatment process is: differential heating, ingot casting heating rate 15 ~ 40 DEG C/h, homogenization temperature 480 DEG C, direct hot rolling after being incubated 2 h, 1+4 hot continuous rolling production line is adopted to carry out the hot rolling of sheet material, hot roughing is to middle thickness of slab 28 mm, and the thickness connecting finish rolling sheet material through 4 heat is 6.0 mm, sheet material coiling temperature 337 ~ 349 DEG C.Thickness 0.8 mm is deformed into through single chassis 6 roller CVC rolled by cold rolling machine after hot rolled coil is cooled to room temperature.Conventional Horizental annealer is adopted to carry out Full Annealing, treatment process is: coiled material heating-cooling speed 15 ~ 40 DEG C/h, Full Annealing temperature 330 DEG C, annealing time 2 h, carries out metallographic structure observation (details are shown in Figure 10) and Performance Detection (details are in table 2) to sheet material after annealing.
Embodiment 4
Alloy cast ingot 1E298 of the present invention, utilize pushing type heating furnace to carry out Homogenization Treatments behind sawing milling face, treatment process is: differential heating, ingot casting heating rate 15 ~ 40 DEG C/h, homogenization temperature 530 DEG C, after being incubated 2 h, stove is chilled to hot rolling start rolling temperature 470 ~ 490 DEG C, is incubated the direct hot rolling of 2 h, 1+4 hot continuous rolling production line is adopted to carry out the hot rolling of sheet material, hot roughing is to middle thickness of slab 28 mm, and the thickness connecting finish rolling sheet material through 4 heat is 5.5 mm, sheet material coiling temperature 339 ~ 350 DEG C.Thickness 0.8 mm is deformed into through single chassis 6 roller CVC rolled by cold rolling machine after hot rolled coil is cooled to room temperature.The conventional Horizental annealer of industry is adopted to carry out Full Annealing, treatment process is: coiled material heating-cooling speed 15 ~ 40 DEG C/h, Full Annealing temperature 330 DEG C, annealing time 2 h, carries out metallographic structure observation (details are shown in Figure 11) and Performance Detection (details are in table 2) to sheet material after annealing.
Embodiment 5
Alloy cast ingot 1E298 of the present invention, utilize pushing type heating furnace to carry out Homogenization Treatments behind sawing milling face, treatment process is: differential heating, ingot casting heating rate 15 ~ 40 DEG C/h, homogenization temperature 530 DEG C, after being incubated 2 h, stove is chilled to hot rolling start rolling temperature 470 ~ 490 DEG C, is incubated the direct hot rolling of 2 h, 1+4 hot continuous rolling production line is adopted to carry out the hot rolling of sheet material, hot roughing is to middle thickness of slab 28 mm, and the thickness connecting finish rolling sheet material through 4 heat is 5.5 mm, sheet material coiling temperature 339 ~ 350 DEG C.Be rolled into through once cold rolling distortion after hot rolled coil cooling: 0.9 mm, 1.1 mm, 1.5 mm, 2.5 mm different thickness, be out of shape total cold processing ratio with secondary cold-rolling after controlling process annealing and be respectively: 10%, 25%, 45%, 65%.Then adopt the conventional Horizental annealer of industry to carry out process annealing, treatment process is: coiled material heating-cooling speed 15 ~ 40 DEG C/h, intermediate anneal temperature 310 ~ 340 DEG C, annealing time 1 ~ 4 h, air cooling.Thickness 0.8 mm is deformed into through single chassis 6 roller CVC rolled by cold rolling machine after process annealing volume is cooled to room temperature.The conventional Horizental annealer of industry is adopted to carry out Full Annealing, treatment process is: coiled material heating-cooling speed 15 ~ 40 DEG C/h, Full Annealing temperature 330 DEG C, annealing time 2 h, carries out metallographic structure observation (details are shown in Figure 12 ~ 15) and Performance Detection (details are in table 2) to sheet material after annealing.
Embodiment 6
Alloy cast ingot 1E299 of the present invention, utilize pushing type heating furnace to carry out Homogenization Treatments behind sawing milling face, treatment process is: differential heating, ingot casting heating rate 15 ~ 40 DEG C/h, homogenization temperature 530 DEG C, after being incubated 2 h, stove is chilled to hot rolling start rolling temperature 470 ~ 490 DEG C, is incubated the direct hot rolling of 2 h, 1+4 hot continuous rolling production line is adopted to carry out the hot rolling of sheet material, hot roughing is to middle thickness of slab 28 mm, and the thickness connecting finish rolling sheet material through 4 heat is 5.5 mm, sheet material coiling temperature 339 ~ 350 DEG C.Be rolled into 1.5 mm through once cold rolling distortion after hot rolled coil cooling, after process annealing, total cold processing ratio of secondary cold-rolling distortion is 45%.Then adopt the conventional Horizental annealer of industry to carry out process annealing, treatment process is: coiled material heating-cooling speed 15 ~ 40 DEG C/h, intermediate anneal temperature 310 ~ 340 DEG C, annealing time 1 ~ 4 h, air cooling.Thickness 0.8 mm is deformed into through single chassis 6 roller CVC rolled by cold rolling machine after process annealing volume is cooled to room temperature.Adopt the conventional Horizental annealer of industry to carry out Full Annealing, treatment process is: coiled material heating-cooling speed 15 ~ 40 DEG C/h, Full Annealing temperature 330 DEG C, annealing time 2 h, carries out Performance Detection (details are in table 2) to sheet material after annealing.
Embodiment 7
Alloy cast ingot 1E300 of the present invention, utilize pushing type heating furnace to carry out Homogenization Treatments behind sawing milling face, treatment process is: differential heating, ingot casting heating rate 15 ~ 40 DEG C/h, homogenization temperature 530 DEG C, after being incubated 2 h, stove is chilled to hot rolling start rolling temperature 470 ~ 490 DEG C, is incubated the direct hot rolling of 2 h, 1+4 hot continuous rolling production line is adopted to carry out the hot rolling of sheet material, hot roughing is to middle thickness of slab 28 mm, and the thickness connecting finish rolling sheet material through 4 heat is 5.5 mm, sheet material coiling temperature 339 ~ 350 DEG C.Be rolled into 1.5 mm through once cold rolling distortion after hot rolled coil cooling, after process annealing, total cold processing ratio of secondary cold-rolling distortion is 45%.Then adopt the conventional Horizental annealer of industry to carry out process annealing, treatment process is: coiled material heating-cooling speed 15 ~ 40 DEG C/h, intermediate anneal temperature 310 ~ 340 DEG C, annealing time 1 ~ 4 h, air cooling.Thickness 0.8 mm is deformed into through single chassis 6 roller CVC rolled by cold rolling machine after process annealing volume is cooled to room temperature.Adopt the conventional Horizental annealer of industry to carry out Full Annealing, treatment process is: coiled material heating-cooling speed 15 ~ 40 DEG C/h, Full Annealing temperature 330 DEG C, annealing time 2 h, carries out Performance Detection (details are in table 2) to sheet material after annealing.
Embodiment 8
Alloy cast ingot 1E301 of the present invention, utilize pushing type heating furnace to carry out Homogenization Treatments behind sawing milling face, treatment process is: differential heating, ingot casting heating rate 15 ~ 40 DEG C/h, homogenization temperature 530 DEG C, after being incubated 2 h, stove is chilled to hot rolling start rolling temperature 470 ~ 490 DEG C, is incubated the direct hot rolling of 2 h, 1+4 hot continuous rolling production line is adopted to carry out the hot rolling of sheet material, hot roughing is to middle thickness of slab 28 mm, and the thickness connecting finish rolling sheet material through 4 heat is 5.5 mm, sheet material coiling temperature 339 ~ 350 DEG C.Be rolled into 1.5 mm through once cold rolling distortion after hot rolled coil cooling, after process annealing, total cold processing ratio of secondary cold-rolling distortion is 45%.Then adopt the conventional Horizental annealer of industry to carry out process annealing, treatment process is: coiled material heating-cooling speed 15 ~ 40 DEG C/h, intermediate anneal temperature 310 ~ 340 DEG C, annealing time 1 ~ 4 h, air cooling.Thickness 0.8 mm is deformed into through single chassis 6 roller CVC rolled by cold rolling machine after process annealing volume is cooled to room temperature.Adopt the conventional Horizental annealer of industry to carry out Full Annealing, treatment process is: coiled material heating-cooling speed 15 ~ 40 DEG C/h, Full Annealing temperature 330 DEG C, annealing time 2 h, carries out Performance Detection (details are in table 2) to sheet material after annealing.
Embodiment 9
Alloy cast ingot 1E302 of the present invention, utilize pushing type heating furnace to carry out Homogenization Treatments behind sawing milling face, treatment process is: differential heating, ingot casting heating rate 15 ~ 40 DEG C/h, homogenization temperature 530 DEG C, after being incubated 2 h, stove is chilled to hot rolling start rolling temperature 470 ~ 490 DEG C, is incubated the direct hot rolling of 2 h, 1+4 hot continuous rolling production line is adopted to carry out the hot rolling of sheet material, hot roughing is to middle thickness of slab 28 mm, and the thickness connecting finish rolling sheet material through 4 heat is 5.5 mm, sheet material coiling temperature 339 ~ 350 DEG C.Be rolled into 1.5 mm through once cold rolling distortion after hot rolled coil cooling, after process annealing, total cold processing ratio of secondary cold-rolling distortion is 45%.Then adopt traditional industrial Horizental annealer to carry out process annealing, treatment process is: coiled material heating-cooling speed 15 ~ 40 DEG C/h, intermediate anneal temperature 310 ~ 340 DEG C, annealing time 1 ~ 4 h, air cooling.Thickness 0.8 mm is deformed into through single chassis 6 roller CVC rolled by cold rolling machine after process annealing volume is cooled to room temperature.Adopt the conventional Horizental annealer of industry to carry out Full Annealing, treatment process is: coiled material heating-cooling speed 15 ~ 40 DEG C/h, Full Annealing temperature 330 DEG C, annealing time 2 h, carries out Performance Detection (details are in table 2) to sheet material after annealing.
Owing to inevitably there is macrosegregation and the microsegregation of ingot casting in DC castingprocesses, the large size slab ingot of normal production, 1/4 layer of its thickness direction is the segregation region of alloying element, be enrichment of element and compound aggregation zone, therefore choose thickness 1/4 place and carry out homogenization process Institutional.Meanwhile, alloying constituent, ingot structure and equal thermal system are to the Al in 5XXX system alloy cast ingot tissue
6(FeMn) disperse phase has important impact, in conjunction with industrial production practical situation, has carried out heterogeneity regulate and control mutually system disperse educt with equal thermal system according to embodiment 1.Fabric analysis result as can be seen from Fig. 2: conventional 5182 alloys define the precipitated phase (see figure 2) of a large amount of small and dispersed after the equal thermal treatment of 480 DEG C/2h, this kind of high-density, small size, the recrystallize of subglobose disperse phase to sheet material play obvious restraining effect, thus still remain part rolling feature after causing sheet material to be annealed, crystal grain prolongs and rolls to elongation (see figure 10), thus causes performance to there is anisotropy (see table 2 embodiment 3).If prolongation soaking time, the disperse educt phase (see figure 3) of a large amount of lath-shaped will be formed, the hardness of this disperse phase is high, be difficult to, by subsequent hot rolled, cold rolling processing fragmentation, also will significantly worsen the forming property of sheet material by Structure Inheritance, therefore, 460 ~ 480 DEG C/16 ~ 24h in most enterprise application can be found out, not only energy consumption is high, and production efficiency is low, and reduces the forming property of sheet material.
But alloying constituent of the present invention is on conventional 5182 alloy bases, formation disperse phase element of Fe and Mn are optimized, thus after causing the equal thermal treatment of 480 DEG C/2h, the disperse phase density of formation significantly reduces, but size still less (see figure 4).In order to improve the size of disperse phase further, have employed the high-temperature homogenization thermal treatment of 530 DEG C, when homogenization time is 2h, define size larger, subglobose disperse educt phase (see figure 5), this kind of large size, subglobose disperse educt will induce Recrystallization nucleation effect (PSN) by particle excitation mutually, promote the generation of recrystallize in cold rolled sheet Full Annealing process, rolling Full Annealing process is realized in the conventional annealing furnace of strip production line, and ensure that the recrystallized structure after Full Annealing is even, the shaft-like (see Figure 11) such as be, substantially increase the elongation after fracture (see table 2 embodiment 4) of sheet material, thus significantly improve the forming property of sheet material.But along with the prolongation of homogenization time, define a small amount of large size when 4h, lath-shaped precipitated phase, equal performance large size when particularly reaching 8h, lath-shaped precipitated phase.The precipitated phase of this large size, lath-shaped, by reducing the forming property of sheet material, should control its content as far as possible.Therefore, when adopting high-temperature homogenization thermal treatment, need the complex optimum by temperature and time, to form large size, subglobose disperse phase, corresponding homogenization temperature scope is 500 ~ 550 DEG C, and homogenization time controls at 1 ~ 6h.
Full Annealing technique is the vital technique of 5XXX automobile board, to the important of sheet material final finished O state structure and properties, the present invention is in alloying constituent optimization and adjustment, homogenization process optimization and formulate on basis, further Full Annealing technique is optimized by embodiment 2, to improve the forming property of sheet material.As can be seen from Fig. 8 and Fig. 9, Full Annealing temperature carries out 300 ~ 320 ~ 340 ~ 360 ~ 380 DEG C respectively, after annealing time 2 h process, after first rising all has appearred in the elongation after fracture of characterization board shaping property, Sven-Gan Eriksson Erichsen number by rule, in general, Full Annealing temperature is more excellent within the scope of 320 ~ 360 DEG C, and annealing time controls to be advisable at 1 ~ 4h, time, too short slab material recrystallize was insufficient, time oversize easy generation abnormal grain growth and cause uneven microstructure.
There is obvious flow lines problem in 5XXX system alloy, " a series of step or spination deformation bands " that during sheet deformation, surface occurs, causes plate surface alligatoring, have a strong impact on the appearance quality of sheet material mostly.But as 5XXX line aluminium alloy auto sheet, due to higher to plate surface specification of quality, need to control effectively to flow lines.The present invention is on the basis of alloying constituent optimization and adjustment, homogenization process optimization and formulation, Full Annealing process optimization, 3 and 4 find in conjunction with the embodiments, the non-process annealing of sheet material, during cold rolling reduction >=85%, Full Annealing state sheet material grain structure is too tiny, at about 15 μm (see Figure 10 and Figure 11), intensity is too high, and there is obvious anisotropy in performance, particularly the unit elongation in 0 ° of direction is lower, with 45 ° and 90 ° of differences larger etc., forming property is low, there is obvious flow lines defect.Therefore, introduce process annealing by embodiment 5, regulation and control cold processing ratio, to regulate and control Full Annealing state grain structure, to improve sheet material forming performance and surface quality.
As can be seen from the metallographic structure analysis of Figure 12 ~ 15, be increased to 65% along with cold processing ratio by 10%, the recrystal grain tissue change of sheet material is obvious, refine to 10 μm gradually by thick 200 μm.Find in conjunction with the analysis of corresponding performance and surface quality (see table 2 embodiment 5): when total cold processing ratio of secondary cold-rolling distortion is 10% time, when grain-size is excessive, at about 200 μm, material not only intensity is low, and the unit elongation of all directions is also low, only have about 20%, and there is serious tangerine hull constitution in the rear surface that stretches; Along with cold processing ratio be increased to 25% time, intensity improves not obvious, but elongation after fracture adds about 4%, but overall unit elongation is still relatively low, and buckling phenomena is also played without obvious orange peel in surface; And under 45% cold processing ratio condition, grain structure size is about about 20 μm, excellent surface quality, and the yield strength of sheet material reaches about 130MPa, and elongation after fracture is minimum reaches 26.5%, comprehensive plasticity reaches 27%, and the difference < 2%, n of all directions
5>=0.30, r
10>=0.70, △ r≤0.10, yield tensile ratio < 0.50, has the comprehensive matching of high formability energy and great surface quality; But along with the further increase of cold processing ratio, yield strength>=135MPa, particularly elongation after fracture strengthens in the difference of all directions, the unit elongation in 0 ° of direction is lower, and 45 ° and 90 ° of unit elongation risings, comprehensive plasticity declines, and forming property is deteriorated, and easily appearance is significantly out of shape vestige.Therefore, within the scope of Full Annealing temperature 320 ~ 360 DEG C, the cold rolling general working rate before Full Annealing should control between 25 ~ 65%.
Meanwhile, 6 ~ 9 can find out in conjunction with the embodiments, the yield strength≤135MPa of 5XXX line aluminium alloy sheet material of the present invention, yield tensile ratio < 0.50, n
5>=0.30, r
10>=0.70, △ r≤0.10, with elongation after fracture>=26% rolled to being 0 °, 45 ° and 90 ° direction, and its difference < 2%, there is the matched well of high formability and surface quality.
In sum, the present invention is on conventional 5182 alloy bases, control and optimize the content of Fe and Mn element, particularly Fe is controlled at 0.15 ~ 0.25 wt%, significantly lower than the control overflow (< 0.1 wt%) of other producer's high formability energy sheet materials, while ensure that sheet alloy high formability energy, control cost.Meanwhile, in conjunction with the complex optimum and the control that adopt high-temperature homogenization 500 ~ 550 DEG C/1 ~ 6h to regulate and control disperse phase and cold processing ratio and Full Annealing technique, conventional strip production line is prepared the 5XXX line aluminium alloy sheet material of high formability, low cost.Under current automotive light weight technology overall background, 5XXX sheet material of the present invention is highly suitable for manufacturing motor car engine inner cover, luggage inner cap, inner plate of car door, other inner panels of automobile and other complex-shaped component products stamping formabilily being had to high requirement by cold stamping, the demand of Automobile Enterprises to height shaping, low cost 5XXX sheet material can be met, there is good economic benefit and wide application prospect.
Although illustrate and described example of the present invention, for the ordinary skill in the art, be appreciated that and can carry out multiple change, amendment, replacement and modification to these embodiments without departing from the principles and spirit of the present invention, scope of the present invention is by claims and equivalency thereof.
Claims (10)
1. an Aluminum alloy plate for vehicle material, it is characterized in that, the chemical composition of described sheet alloy and mass percentage content thereof are: Mg:4.5 ~ 5.5 wt%, Mn:0.15 ~ 0.35 wt%, Fe:0.10 ~ 0.30 wt%, Si≤0.15 wt%, Ti≤0.10 wt%, Cu≤0.10 wt%, Zn≤0.10 wt%, Cr≤0.10 wt%, surplus is Al and inevitable impurity.
2. Aluminum alloy plate for vehicle material according to claim 1, is characterized in that, Mg, Mn and Fe content range is respectively: Mg:4.5 ~ 5.0 wt%, Mn:0.15 ~ 0.25 wt%, Fe:0.15 ~ 0.25 wt%.
3. a preparation method for the Aluminum alloy plate for vehicle material as described in claim 1 and 2, described preparation method comprises the following steps successively: the distortion of batching, melting and casting, homogenizing, hot rolling deformation, once cold rolling, process annealing, secondary cold-rolling distortion, Full Annealing.
4. preparation method according to claim 3, is characterized in that, in described melting and casting step, adopts Cl
2carry out furnace refining with Ar mixed gas and SNIF carries out degassing processing, control Na≤3 ppm in ingot casting, Ca≤5 ppm, H
2≤ 0.15 ml/100g Al.
5. preparation method according to claim 4, is characterized in that, ingot casting heating rate 15 ~ 40 DEG C/h of described uniformization step, homogenization temperature 500 ~ 550 DEG C, and soaking time 1 ~ 6 h, stove is chilled to hot rolling start rolling temperature 470 ~ 490 DEG C, is incubated 2 h.
6. preparation method according to claim 5, it is characterized in that, described hot rolling deformation step adopts 1+4 hot continuous rolling production line to carry out the hot rolling of sheet material, thickness of slab 20 ~ 30 mm in the middle of hot roughing, the thickness connecting finish rolling sheet material through 4 heat is 4 ~ 6 mm, sheet material coiling temperature 320 ~ 360 DEG C.
7. preparation method according to claim 6, is characterized in that, in described intermediate annealing step, and coiled material temperature rise rate 15 ~ 40 DEG C/h, intermediate anneal temperature 310 ~ 340 DEG C, annealing time 1 ~ 4 h, air cooling.
8. preparation method according to claim 7, it is characterized in that, in described secondary cold-rolling deforming step, the coiled material after process annealing air cooling, through secondary cold-rolling distortion finish rolling to finished product thickness, by process annealing, secondary cold-rolling is out of shape total cold processing ratio and controls between 25 ~ 65%.
9. preparation method according to claim 8, is characterized in that, in described Full Annealing step, to the Full Annealing thermal treatment of coiled material, and coiled material heating-cooling speed 15 ~ 40 DEG C/h, Full Annealing temperature 320 ~ 360 DEG C, annealing time 1 ~ 4 h, air cooling.
10. preparation method according to claim 9, is characterized in that, the hot step of described Full Annealing adopts industrial Horizental annealer to carry out the Full Annealing thermal treatment of coiled material.
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Application publication date: 20150909 |