EP3765647B1 - Verfahren zur herstellung eines blechprodukts aus almgsi-legierung - Google Patents

Verfahren zur herstellung eines blechprodukts aus almgsi-legierung Download PDF

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EP3765647B1
EP3765647B1 EP19705361.4A EP19705361A EP3765647B1 EP 3765647 B1 EP3765647 B1 EP 3765647B1 EP 19705361 A EP19705361 A EP 19705361A EP 3765647 B1 EP3765647 B1 EP 3765647B1
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temperature
sheet
ageing
preferred
aluminium alloy
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EP3765647A1 (de
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Mehdi LALPOOR
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Aleris Aluminum Duffell BVBA
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Aleris Aluminum Duffell BVBA
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/05—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions

Definitions

  • the invention relates to a method of manufacturing an AA6000-series aluminium alloy sheet product, which is particularly suitable for use in the production of automotive body parts, and to an aluminium alloy sheet product of the AA6000-series, produced by this method.
  • US 2016/0348225 A1 discloses a method of preparing a AA6000-series aluminium alloy sheet product, which includes solution heat treating and then quenching the AA6000-series aluminium alloy sheet product, followed by exposure of the sheet product to a temperature range of 30-60°C for 0.2-300 seconds. Afterwards, the sheet product is coiled and then placed in an ambient environment. By this method, the AA6000-series aluminium alloy sheet product may realise more consistent strength and ductility.
  • EP 0 805 879 B1 discloses a process of producing an aluminium alloy sheet material, which comprises subjecting hot-or cold-rolled aluminium alloy sheets to solution heat treatment followed by quenching and, before substantial age-hardening has taken place, subjecting the alloy sheet material to one or more subsequent heat treatments involving heating the material to a peak temperature in the range of 100-300°C, preferably 130-270°C, holding the material at the peak temperature for a period of time less than about 1min, and cooling the alloy from the peak temperature to a temperature of 85°C or less.
  • US 2016/0222491 A1 discloses an AA6000-series aluminium alloy sheet product with good bendability, which is produced by solution heat treatment, followed by quenching. After quenching, the sheet is subjected to pre-aging within 1hr.
  • the pre-aging treatment consists of holding the sheet at 60-120°C for ten hours to 40 hours.
  • CN 107254646 discloses a heat treatment method for 6000 aluminium series alloys including solution heat treatment and quenching to 40-60°C, soaking for 5-20 min, and then rapidly heating to 100-120°C, and holding at this temperature for 2-5 min.
  • EP 2 110 235 A1 discloses an aluminium alloy sheet product with improved hemming performance suitable for use for an automotive body and a method of forming an aluminum alloy sheet product comprising casting a body of an aluminium alloy, working said body to produce a sheet, solution heat treating said sheet, and pre-ageing and naturally ageing said sheet.
  • WO 96/38598 discloses a method of producing an aluminium article comprising the steps of providing a stock including an aluminium alloy, hot working the stock, solution heat treating at a temperature from 900 to 1100 °F for 2.0 seconds to about 30 minutes, rapid quenching, cooling to room temperature, holding at room temperature for not more than 24 hours and reheating to a temperature ranging from 150 to 360 °F for 24 hours to 2.0 minutes.
  • US 2008/0178973 A1 discloses a method for producing an aluminium alloy sheet with excellent bendability and paint bake hardenability, comprising homogenizing an ingot at 450 °C or more, cooling the ingot to a temperature less than 350 °C, hot-rolling the ingot, cold-rolling the hot-rolled product and a solution heat treatment at 450 °C and more, and quenching.
  • CN105441740A discloses a method for manufacturing an aluminium alloy sheet comprising melting the alloy, homogenizing the ingot at 500-580 °C, cooling to a hot-rolling temperature, hot-rolling the ingot, cold rolling and annealing to obtain a cold sheet, solution heat treatment at 500-560 °C and pre-aging at 60-100 °C.
  • JP2007031819A discloses an aluminum alloy with excellent bendability and rough-skin prevention property by performing sequentially a first cold-rolling and middle solution formation, a second cold-rolling and last solution formation and a preliminary backup aging, and performing said second cold rolling by 15 to 30 % of the last cold-rolled rate.
  • the pre-aging treatments known from the prior art mostly have the objective of stabilizing the paint-bake response, i.e. the increase in yield strength induced by a paint bake cycle.
  • the prior art has focused merely on the paint-bake response, without paying attention also to the bending behaviour and related hemming performance of the pre-aged sheet product.
  • all aluminium alloy designations and temper designations refer to the designations by the Aluminum Association as published e.g. in " International Alloy Designations and Chemical Composition Limits for Rolled Aluminum and Rolled Aluminum Alloys” in January 2018 .
  • sheet or “sheet product” refers to a rolled product having up to 4.0 mm in thickness.
  • up to 0.15% Zn may include an alloy having no Zn.
  • the yield strength after a paint-bake simulation consisting of 2% pre-strain and holding at 185°C for 20min is significantly stabilized by using a higher pre-aging temperature than was normally applied in the industrial scale process, namely by using a pre-aging temperature in the range of 65-110°C, preferably 80-110°C, more preferably 85 to 105°C, wherein the most effective range was found to be between 90-100°C.
  • the T4P temper here refers to a material that has been solution heat treated and quenched and then subjected to a pre-ageing treatment and then natural aged to provide said T4P temper.
  • the natural ageing occurs as a result of storing at ambient (room) temperature, typically for about 72 hours up to 6 months, until forming or shaping into an automotive body panel, in particular into a three-dimensional automotive panel.
  • the T64 temper here refers to a T4P temper material that has been deformed in tension by 2% pre-strain followed by a 20 minutes treatment at 185°C to represent the forming plus paint curing treatment typically experienced by automotive panels.
  • the difference in strength between T64 and T4P is often referred to as the paint-bake response.
  • the pre-aging temperature of the invention is particularly advantageous because it leads to the formation of a particular type of nano-clusters, named C2-clusters, which enhance the formation of the ⁇ "-phase during the paint-bake treatment, and therefore increase the paint bake response.
  • C2-clusters a particular type of nano-clusters
  • the precipitation of the ⁇ "-phase is believed to be responsible for the strengthening of the subject aluminium alloy sheet during paint-baking.
  • These advantageous C2 clusters form between 60-130°C. Therefore, pre-ageing temperatures in this range are advantageous.
  • a Si-rich cluster named C1-cluster is formed, which appears detrimental to the paint-bake response, since it does not dissolve at the paint-bake temperature.
  • 60°C ⁇ T ⁇ 80°C is the overlapping range where both C1 and C2 clusters form (T stands for temperature), and this range needs to be treated with care. Therefore, longer pre-ageing times might be necessary when pre-ageing within this temperature range (i.e. at 65°C to 80°C) to achieve an effective pre-ageing treatment and a good paint bake response.
  • the pre-ageing temperatures in the range 80-110°C appear to require shorter soak times (e.g. less than 60 min. or even less than 45min.), which is advantageous in an industrial context. Owing to the formation of detrimental Si-rich C1 clusters in the range 30°C ⁇ T ⁇ 60°C, it appears advantageous to avoid short stay of the material at such temperatures.
  • the pre-aging time is limited to 20-70 min according to the invention, preferably 25 to 60min.
  • a preferred lower limit is about 25 min, and more preferably about 30 min, and most preferably about 35 min.
  • a preferred upper-limit is 60 min., more preferably 55 min., and most preferably 45 min.
  • the higher pre-aging temperature may lead to a deterioration in hemming performance.
  • it has been found that it is advantageous to cool the sheet product from the pre-aging temperature at a relatively high cooling rate of more than 3°C/h.
  • the sheet product is directly coiled after the pre-aging step and placed in an ambient environment. If on an industrial-scale a coil of aluminium alloy sheet, which weighs up to about 10t, is left to cool down in natural air cooling, the cooling rate will be very slow, e.g. around or even below 1°C/h, as is disclosed for example in patent document US 2016/0047021 A1 .
  • water cooling is used after the pre-aging treatment, which results in cooling rates of >50°C/h, preferably in a range of 60-150°C/h, more preferred in a range of 80-120°C/h, most preferred in a range of 90-110°C/h.
  • a possible reason for the advantage of using a forced cooling after pre-aging rather than natural cooling, is that the detrimental temperature zone between 30-60°C, in which the C1 clusters form, is passed through relatively quickly, avoiding long dwell times in this temperature range.
  • the sheet product is cooled from the pre-aging temperature with the above-described cooling rate down to below 35°C, preferably to below 30°C or to ambient temperature. Thereby, holding of the sheet product in the temperature range where C1 clusters form is avoided.
  • the cooling time from pre-aging temperature should be less than 20h, preferably less than 10h, more preferred less than 5h. Such shorter cooling time will also result in an improvement in the hemming performance in the T4P condition after natural aging for a significant amount of time.
  • the hemming performance in T4P condition may be further improved by modifying also the quenching step after solution heat treatment, namely by pursuing the quench/cooling of the sheet to below 45°C, preferably to below 35°C, more preferred to below 30°C and most preferred to ambient temperature or room temperature.
  • the quench/cooling of the sheet to below 45°C, preferably to below 35°C, more preferred to below 30°C and most preferred to ambient temperature or room temperature.
  • CAL continuous annealing line
  • the quench rate has no significant influence on mechanical properties as long as the exit temperature of the quenching operation is sufficiently low, namely below 45°C, preferably below 35°C. Also here, this may be related to the formation of adverse C1 clusters in the temperature range of 30-80°C, which is significantly reduced by quenching down to below 45°C. It has been found that using such extended quenching has a positive effect on the hemming behaviour in T4P after natural aging for 6 months.
  • quenching from solution heat treatment temperature is done by water-quenching, which allows cooling to the desired low temperatures.
  • the method steps (b) to (d) are preferably performed on a continuous annealing line ("CAL"), i.e. the rolled aluminium alloy is provided in the coiled state, and is passed through the CAL.
  • CAL continuous annealing line
  • the sequential steps of solution heat treatment, quenching and pre-aging are performed not batch-wise but in-line in a continuous processing line.
  • the sheet product is coiled after passing the continuous annealing line, and wherein the cooling step of the aluminium sheet is thus performed in the coiled state.
  • the pre-aging step is preferably started within 30 minutes, more preferably within 20 minutes after quenching, more preferred after 15 minutes and most preferred within 5-12 minutes following the quenching step.
  • the aluminium alloy sheet is passed through the continuous annealing line at a line speed of up to 120 m/min, wherein the higher line speeds are preferred, preferably in a range of 50 to 100 m/min, more preferably 50 to 90 m/min, as experiments have shown that better hemming performance in combination with good bake response can be realized at relative high line speeds.
  • the reason may be the reduced natural aging time between quenching and pre-aging.
  • the method according to the invention guarantees the properties at both extreme speed limits.
  • solution heat treatment is performed at a temperature in a range of 510°C to 580°C, preferably 520-565°C, more preferred about 530°C to 560°C, wherein a solution heat treatment temperature of about 550 ⁇ 5°C is most preferred.
  • a relatively high solution heat treatment temperature has been found useful, since it leads to a more complete solid dissolution of elemental excess Si as well as Mg 2 Si, and this will result in the good hardening response of the aluminium alloy during paint-baking.
  • the AlSiMg- or AlMgSiCu-alloy can be provided as an ingot or slab for fabrication into rolling feedstock using casting techniques regular in the art for cast products, e.g. DC-casting, EMC-casting, and preferably having an ingot thickness in a range of about 220 mm or more, e.g. 400 mm, 500 mm or 600 mm.
  • thin gauge slabs resulting from continuous casting e.g. belt casters or roll casters, also may be used, and having a thickness of up to about 40 mm.
  • the thick as-cast ingot is commonly scalped to remove segregation zones near the cast surface of the ingot.
  • the cast ingots are subjected to a homogenization treatment by heating the ingot to a temperature of above 540°C, but at a temperature lower than the solidus temperature of the subject alloy; maintaining the ingot at this temperature for at least about 4 hours, and preferably for at least about 10 hours.
  • the ingots are hot-rolled and subsequently cold-rolled.
  • the rolled sheet has a final thickness of usually 0.5 to 4.0 mm, and preferably in a range of 0.7 mm to 2.0 mm, for example a thickness of about 1.0 mm or about 1.2 mm.
  • the cold-rolled band or sheet is then further processed according to the method of this invention.
  • the provided rolled aluminium alloy sheet product comprising an AA6000-series has a chemical composition closely associated with the known AA6016 or AA6016A series, or modifications thereof.
  • the rolled aluminium sheet may comprise a single layer of the AA6000-series alloy.
  • the rolled aluminium sheet may comprise several layers. At least one layer is made of an aluminium alloy of the AA6000-series, and preferably having the following composition, in weight %: Si 0.75 -1.5, preferably 0.9-1.4, most preferred 1.0-1.30, Mg 0.2-0.8, preferably 0.25-0.7, most preferred 0.4 -0.60, Fe ⁇ 0.5, preferably ⁇ 0.35, most preferred 0.10 -0.3, Mn ⁇ 0.25, preferably 0.03-0.20, most preferred 0.03-0.15, Cu ⁇ 0.40, preferably ⁇ 0.25, more preferably ⁇ 0.20, Cr up to 0.10, Zn up to 0.25, Ti up to 0.10, balance aluminium and impurities, each max 0.05%, in total max. 0.15 %.
  • the sheet product according to the invention preferably has a Si content of at least 0.75%, preferably 0.8%, preferably at least 0.9%, and most preferred at least 1.0%.
  • a preferred upper limit for the Si content is 1.4%, more preferred 1.30%.
  • the Mg content should be at least 0.2%, preferably at least 0.25% and more preferred at least 0.4%, in order to provide sufficient strength to the sheet product after the paint-bake cycle.
  • a preferred upper-limit for the Mg-content is 0.7%, and more preferably 0.60%.
  • the amount of iron (Fe) is carefully controlled in order to provide an improved hemming performance compared to aluminium alloys with higher Fe levels, and having otherwise the same composition.
  • the Fe content in the alloy sheet product is preferably ⁇ 0.35%, more preferred ⁇ 0.3% and most preferred 0.10-0.3%.
  • Cu can be purposively present in the sheet product to a level of ⁇ 0.40, but preferably should not exceed 0.25 in order to maintain a good corrosion performance.
  • Cu is present up to 0.20%, more preferred up to 0.15%.
  • Cu is purposefully added to be present in a range of 0.05-0.20%, preferably 0.05-0.17%. It appears that Cu is affecting the precipitation sequence of the hardening Mg 2 Si phase, leading to a favourable stabilisation of the pre-aging properties and a higher paint-bake response.
  • Mn is added to the alloy sheet product for grain size control to improve the formability of the sheet product.
  • the Mn level should be present in a range of up to 0.25%, preferably up to 0.20%, and more preferably in a range of 0.01% to 0.15%.
  • a preferred lower-limit for the Mn content is about 0.03%, and more preferably about 0.05%.
  • Cr can be present up to 0.10%. Cr is preferentially avoided in the sheet product as it may prevent full recrystallization of the sheet product. Preferably it is tolerated up to 0.04%, and is preferably less than 0.03%, and more preferably less than 0.02%.
  • the sheet product generally includes not greater than 0.03% V and not greater than 0.03% Zr.
  • the sheet product includes V only up to 0.02%.
  • the sheet product includes Zr only up to 0.02%.
  • Zn may optionally be included in the alloy, and in an amount up to about 0.25%. Zinc may be present in scrap, and its removal may be costly.
  • the alloy includes not greater than 0.10% Zn, and in a preferred embodiment the alloy includes not greater than 0.05% Zn.
  • Ti can be added to the sheet product amongst others for grain refiner purposes during casting of the alloy ingots.
  • the addition of Ti should not exceed 0.10%, and preferably it should not exceed about 0.05%.
  • a preferred lower limit for the Ti addition is about 0.008%, and can be added as a sole element or with either boron or carbon as known in the art serving as a casting aid, for grain size control.
  • Unavoidable impurities may be present up to 0.05% each, and in total up to 0.25%, preferably up to 0.15%, and the balance being aluminium.
  • the provided rolled aluminium alloy sheet comprising an AA6000-series alloy has a composition consisting of: Si 0.75 -1.5, preferably 0.9-1.4, most preferred 1.0-1.30, Mg 0.2-0.8, preferably 0.25-0.7, most preferred 0.4 -0.60, Fe ⁇ 0.5, preferably ⁇ 0.35, most preferred 0.10 -0.3, Mn ⁇ 0.25, preferably 0.03-0.20, most preferred 0.03-0.15, Cu ⁇ 0.40, preferably ⁇ 0.25, more preferably ⁇ 0.20, Cr up to 0.10, Zn up to 0.25, Ti up to 0.10, balance aluminium and impurities, each max 0.05%, in total max. 0.15 %.
  • the alloy may have preferred narrower compositional ranges as herein described and claimed.
  • the invention is also directed to an aluminium alloy sheet product, particularly suitable for use in the production of automotive body parts, and which has been manufactured by the herein described and claimed method according to the invention or one of its embodiment.
  • Such sheet product has been found to have a hemming performance of 3 or more, preferably 3 1 ⁇ 2 or more after six months of natural aging, which corresponds to the T4P temper. Once this 6 months naturally aged sheet has been subjected to a simulated paint-baking cycle of 2% pre-strain and heating at 185°C for 20 minutes, it exhibits a paint bake response of 80 MPa or more, preferably of 85 MPa or more.
  • the aluminium alloy sheet product produced according to the invention has excellent forming, and in particular hemming properties after extended natural aging for more than two months and therefore can easily be processed by or for an automobile manufacturer into an automotive body part by means of forming (e.g. by deep-drawing, pressing, or stamping).
  • the product of the invention can advantageously be used as an automotive panel, ideally an outer panel, with guaranteed paint-bake response, hemming and bending performance for 6 months after CAL-treatment, pre-ageing and natural ageing.
  • Figure 1 illustrates an embodiment of the processing steps used in the manufacturing of AA6000-series aluminium alloys to produce automotive body sheets according to the invention.
  • ingots are cast using DC or EMC casting.
  • the alloy is preferably of the AA6016-series, although the invention may also find use for e.g. AA6014, AA6081, AA6451, or AA6005A-type of alloys.
  • the cast ingots are subject to scalping and a usual homogenization treatment in step 4.
  • the homogenized ingot is hot-rolled in step 6, and the hot-rolled plate is passed to the cold-rolling mill.
  • a first cold-rolling step 8 is followed by an intermediate annealing step 10 and afterwards, a second and final cold rolling step 12 is performed.
  • the sheet is in the form of a band having a thickness of e.g. 0.5-4.0 mm, typically 0.8-1.5mm.
  • the rolled aluminium alloy sheet provided to the solution heat-treatment and pre-aging treatment according to this invention will usually be made of one monolithic layer, but the invention is equally applicable to multi-layered sheet products, wherein one or all of the layers are of the AA6000-series.
  • the rolled aluminium sheet is typically supplied to a continuous annealing line ("CAL").
  • CAL continuous annealing line
  • the steps of solution heat treatment and quenching to below 35°C are performed in step 14.
  • the quenched sheet product is subjected to levelling and in useful embodiments also to etching and passivation in step 16.
  • the sheet product is heated to the pre-aged temperature in step 18, preferably coiled at pre-aging temperature, soaked at the pre-aging temperature for the prescribed pre-aging time, and subjected to a controlled cooling step resulting in a cooling rate of >3°C/h in step 18.
  • Fig. 2 shows a temperature profile of a continuous annealing line according to an embodiment of the invention.
  • the rolled sheet product is heated up to preferably above 540°C in the solution heat treatment step.
  • Such high temperature is advantageous as it results in the highest possible rate of dissolution of Mg 2 Si and Si.
  • the shaded area 24 between 400-540°C shows the temperature range in which Si is dissolved in solid solution. In the range 22 between 400-480°C Mg 2 Si is dissolved. In the temperature range between 300-400°C, which is dotted and marked with 26, Mg 2 Si and Si are dissolved in the cold-rolled material. It follows that above 540°C, the dissolution of Mg 2 Si and Si is complete.
  • the material is held at the SHT-temperature for a short time, e.g. for less than 1 minutes, preferably less than 30 seconds, and quenched 28 preferably by water quenching, in this illustrative example to below 30°C.
  • the quenching rate is as usual in the art, namely about 200-400°C/s.
  • Fig.2 The advantage of quenching to below 45°C and more preferably to below 35°C or even below 30°C is illustrated in Fig.2 by the various zones 38-46, in which the C1 and C2 clusters form: in the temperature range 46 between 30-80°C, the C1 clusters tend to form, which are detrimental to the paint bake response, since they delay precipitation ⁇ "-phase. This effect is believed to be strongest in the middle of this range, between about 45°C and 60°C. Hence, this temperature range may be called the "unsafe zone". Accordingly, it is advantageous to quench to below 45°C in step 28.
  • the C2 clusters form In the temperature range 44 above 60°C up to 130°C, the C2 clusters form, which have been shown to have a positive effect on the properties of the sheet after natural aging, including paint-bake response (PBR). Accordingly, the zone 44 between 80-130°C, in which only C2 clusters form, is designated as "safe zone", and is a useful temperature range for the pre-ageing treatment.
  • the zone 40 between 60-80°C is characterised by the formation of both C1 and C2 clusters, and therefore may still be used with advantageous effects for pre-ageing. At these comparatively low temperatures, longer soak times are preferred according to the invention, e.g. around 40 min or 50 min to 70 min.
  • the sheet product After quenching, the sheet product is held at ambient temperature 30 for less than 30 minutes, while additional process steps such as levelling, etching and/or passivation are performed. These process steps typically take place at a temperature of e.g. between 20-30°C. After completion of these steps, and as soon as feasible after quenching, the sheet product is heated to the pre-aging temperature, in this case between 80-110°C in step 32. The sheet product is held there in step 34 for a pre-aging time of 20 min or more, however, preferably less than 70 min, wherein the holding at pre-aging temperature may take place in the uncoiled or already coiled state. After the soaking time at pre-aging temperature, the sheet, usually the coiled sheet, is subjected to forced convection cooling 36 to ambient temperature, resulting in a cooling rate of 3-150°C/h, and a cooling time of 20 hours or less.
  • additional process steps such as levelling, etching and/or passivation are performed. These process steps typically take place at
  • the provided sheet product consisted of an aluminium alloy having the following composition: Si 1.1% Mg 0.4% Fe 0.25% Mn 0.11% Cu 0.08% Ti 0.02% Cr 0.02%, balance impurities and aluminium.
  • Table 1 Processing parameters of sample coils Coil Sample Process parameters SHT Quench PAT PA-time Cooling rate (°C) type (°C) (min) (°C/h) Coil #1 C1 (comp.) 550 Standard 60 60 1-1.5 Coil #2 C2 (comp.) 540 Standard 95 60 1-1.5 Coil #3 S1 (inv.) 550 Standard 96 30 100 S2 (inv.) 550 Extended 96 30 100 Coil #4 S3 (inv.) 550 Extended 93 45 3,2 Coil #5 S4 (inv.) 550 Extended 100 30 3,8 Table 2: Mechanical properties of samples Sample Mechanical properties Re-T4P (25 d) Re-T4P (6 m) Re-T64 (25 d) Re-T64 (6 m) PBR drop of Re T64 in 5 m Hem.-L T4P (6 m) (MPa) (MPa) (MPa) (MPa) (MPa) C1 (comp.) 115 125 226 202 77 24 2 C
  • the solution heat treatment temperature was 540°C for comparison sample C2 and otherwise 550°C.
  • the quench type is either standard or extended, wherein standard relates to the standard quenching procedure wherein the quench exit temperature is above 60°C.
  • the extended quench type relates to an embodiment of the inventive quenching step with an exit temperature after quenching of below 30°C. After quenching, the usual passivation step was performed.
  • PAT stands for pre-aging temperature
  • PA-time for the holding time at PAT.
  • the cooling rate stands for the cooling rate from the pre-ageing temperature after the PA-time.
  • coils #4 and #5 and coiled sheet product samples S3 and S4 which were cooled at a cooling rate of 3.2°C/h and 3.8°C/h, respectively, were cooled in a forced convection cooling chamber, whereas coil #3 and samples S1 and S2 having a cooling rate of about 100°C/h were cooled by water spraying.
  • the mechanical properties of the materials are listed in Table 2.
  • the yield strength Re was always measured in the transverse direction and is given in T4 temper after the pre-aging treatment followed by 25 days of natural aging (25d), and 6 months of natural aging (6m).
  • the hemming performance in L-direction (rolling direction) was measured also in T4P condition after 6 months of natural aging.
  • the hemming performance was tested via a flat hemming test, by bending the samples 180° with a bending radius of 0.0mm as described in ASTM Norm E290-97-A and followed by a visual assessment.
  • the samples were subjected to a simulated paint-bake cycle, which consisted of 2% stretch and soaking at 185°C for 20min, resulting in a T64 temper.
  • the tensile tests in T64 temper were done in transverse direction and the increase in Re during the paint-bake cycle is given as the paint-bake response (PBR).
  • Coil #1 with sample C1 represents a sheet product produced with the normal state-of-the-art processing conditions, including a standard quench and a pre-aging treatment at 60°C for 60 minutes, followed by the usual natural convection cooling in the coiled state, and which results in a slow cooling rate of 1-1.5°C/h.
  • the C1 sample has a low Re-T6 and low paint-bake response.
  • the Re-T6 drops significantly by 24MPa during the 6 months aging.
  • the hemming performance at 2 is not acceptable.
  • Coil #3 and sample S1 were processed according to the invention, with a standard quench and a cooling rate of 100°C after pre-ageing.
  • the pre-ageing treatment was done at 96°C for 30 minutes.
  • the hemming performance is significantly improved to 31 ⁇ 4 in comparison with sample C2, while the PBR is even higher at 87 MPa.
  • the drop of Re-T64 in the 5 months between the two measurements (Re-T64 (25d) and Re-T64 (6 m)) is negligible at 1 MPa.
  • this process results in an excellent stability in mechanical properties, in particular of the PBR, in combination with a very good hemming performance in T4P condition after significant natural ageing.
  • Sample S2 of the same coil was processed in the same way as sample S1, with the exception that an extended quench was used. As can be seen in Table 2, this leads to a further improvement of the hemming performance in T4P condition from 31 ⁇ 4 to 31 ⁇ 2.
  • sample S3 and S4 demonstrate that forced convection cooling is adequate to achieve a cooling rate after pre-ageing which is sufficient to realize the advantages of the invention.
  • sample C2 shows that natural cooling, however, will not produce satisfactory results, as the cooling rate after pre-ageing is too low.
  • raising the pre-ageing temperature from 60°C to above 65°C to 110°C, preferably to 80-110°C, while adjusting the PA-time is shown to improve the stability of the mechanical properties during natural ageing, in a particular Re-T64 and PBR.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Claims (11)

  1. Verfahren zur Herstellung eines Blecherzeugnisses aus einer AlMgSi-Legierung, das insbesondere zur Verwendung bei der Herstellung von Kraftfahrzeugkarosserieteilen geeignet ist, wobei das Verfahren die folgenden Schritte umfasst:
    (a) Bereitstellen eines gewalzten Aluminiumlegierungsblechs, das eine Legierung der Serie AA 6000 umfasst;
    (b) Lösungsglühen des gewalzten Aluminiumlegierungsblechs;
    (c) Abschrecken des Blechs;
    (d) Vorhärten des abgeschreckten Blechs, indem es einer Wärmebehandlung bei einer Vorhärtungstemperatur im Bereich von 65°C bis 110°C für eine Vorhärtungszeit im Bereich von 20 Minuten bis 70 Minuten unterzogen wird;
    (e) Abkühlen des vorgehärteten Blechs von der Vorhärtungstemperatur mit einer Abkühlungsgeschwindigkeit von mehr als 3 °C/Std.
  2. Verfahren nach Anspruch 1, wobei die Abkühlung des vorgelagerten Blechs durch erzwungene Konvektionskühlung erfolgt.
  3. Verfahren nach einem der vorhergehenden Ansprüche, wobei zumindest die Verfahrensschritte des Lösungsglühens, des Abschreckens und des Erwärmens auf die Vorhärtungstemperatur durchgeführt werden, während das gewalzte Aluminiumlegierungsblech durch eine Durchlaufglühanlage geführt wird.
  4. Verfahren nach einem der vorhergehenden Ansprüche, wobei das Aluminiumlegierungsblech nach dem Erhitzen auf die Vorhärtungstemperatur aufgerollt wird und der Wärmebehandlungsschritt bei Vorhärtungstemperatur für die Vorhärtungszeit und der Abkühlungsschritt (e) an dem aufgerollten Blechprodukt durchgeführt werden.
  5. Verfahren nach einem der vorhergehenden Ansprüche, wobei die Vorhärtungszeit 25 bis 60 Minuten, vorzugsweise 30 bis 55 Minuten, besonders bevorzugt 35 bis 45 Minuten beträgt.
  6. Verfahren nach einem der vorhergehenden Ansprüche, wobei die Vorhärtungstemperatur 80°C bis 110°C, bevorzugter 85°C bis 105°C und am meisten bevorzugt 90°C bis 100°C beträgt.
  7. Verfahren nach einem der vorhergehenden Ansprüche, bei dem das vorgehärtete Blech von der Vorhärtungstemperatur auf unter 35°C mit einer Abkühlungsgeschwindigkeit von mehr als 3°C/Std abgekühlt wird.
  8. Verfahren nach einem der vorhergehenden Ansprüche, wobei das Lösungsglühen bei einer Temperatur von 510°C bis 580°C, vorzugsweise 520°C bis 565°C, besonders bevorzugt 540 bis 560°C, durchgeführt wird.
  9. Verfahren nach einem der vorhergehenden Ansprüche, wobei das Abschrecken nach dem Lösungsglühen auf eine Temperatur von unter 45°C, vorzugsweise unter 35°C, besonders bevorzugt unter 30°C, am meisten bevorzugt auf Raumtemperatur durchgeführt wird.
  10. Verfahren nach einem der vorangehenden Ansprüche, bei dem die Vorhärtungsbehandlung innerhalb von 20 Minuten, vorzugsweise innerhalb von 15 Minuten, nach dem Abschrecken begonnen wird.
  11. Verfahren nach einem der vorhergehenden Ansprüche, wobei das gewalzte Aluminiumlegierungsblech mindestens eine Schicht aus einer Aluminiumlegierung mit der folgenden Zusammensetzung in Gew.-% aufweist: Si 0,75 - 1,5 Mg 0,2 - 0,8 Fe < 0,5 Mn < 0,25 Cu < 0,40 Cr bis zu 0,10 Zn bis zu 0,25 Ti bis zu 0,10
    Rest Aluminium und Verunreinigungen, jeweils höchstens 0,05 %, insgesamt weniger als 0,15 Gew.-%.
EP19705361.4A 2018-03-15 2019-02-19 Verfahren zur herstellung eines blechprodukts aus almgsi-legierung Active EP3765647B1 (de)

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CN112626385B (zh) * 2020-11-04 2022-08-16 佛山科学技术学院 一种高塑性快速时效响应的铝合金及其制备方法和应用
CN113528900B (zh) * 2021-07-20 2022-05-27 中铝瑞闽股份有限公司 一种短流程高导电6系铝合金板带材及其制备方法

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