Classifications

• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
  • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
  • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
  • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
  • C21D8/0226—Hot rolling
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
  • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
  • C21D8/0236—Cold rolling
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
  • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
• • 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
  • C22C—ALLOYS
  • C22C21/00—Alloys based on aluminium
  • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
  • C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
• • 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
  • C22F1/043—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 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 the field of motor vehicle structure parts or components, also referred to as "body in white”, manufactured in particular by stamping aluminium alloy sheets, more particularly alloys in the AA6xxx series in accordance with the designation of the Aluminium Association, intended to absorb energy irreversibly at the time of an impact, and having excellent compromise between high mechanical strength and good behaviour in a crash, such as in particular impact absorbers or "crashboxes", reinforcement parts, linings, or other bodywork structure parts.
• body in white manufactured in particular by stamping aluminium alloy sheets, more particularly alloys in the AA6xxx series in accordance with the designation of the Aluminium Association, intended to absorb energy irreversibly at the time of an impact, and having excellent compromise between high mechanical strength and good behaviour in a crash, such as in particular impact absorbers or "crashboxes", reinforcement parts, linings, or other bodywork structure parts.
• the invention relates to the manufacture of such components by stamping in a solution- hardened, quenched and naturally aged temper state followed by hardening by on-part ageing and a treatment of baking the paint or "bake hardening".
• Aluminium alloys are increasingly used in automobile construction in order to reduce the weight of the vehicles and thus reduce fuel consumption and discharges of greenhouse gases.
• Aluminium alloy sheets are used in particular for manufacturing many parts of the "body in white", among which there are bodywork skin parts (or external bodywork panels) such as the front wings, roofs, bonnet, boot or door skins, and the lining parts or bodywork structure components such as for example door, bonnet, tailgate or roof linings or reinforcements, or spars, bulkheads, load-bearing floors, tunnels and front, middle and rear pillars, and finally the impact absorbers or
• bodywork skin parts or external bodywork panels
• the lining parts or bodywork structure components such as for example door, bonnet, tailgate or roof linings or reinforcements, or spars, bulkheads, load-bearing floors, tunnels and front, middle and rear pillars, and finally the impact absorbers or
• the main property remains high mechanical strength, even if it is initially designed to withstand indentation for applications of the skin type: "A yield-strength of 280 MPa is achieved after 2% pre-strain and 30 min at 177°C".
• 03006697 relates to an alloy in the AA6xxx series with 0.2% to 0.45% Cu.
• the object of the invention is to propose an alloy of the AA6013 type with a reduced Cu level, targeting 355 MPa of Rm in the T6 temper and good resistance to intergranular corrosion.
• the composition claimed is as follows: 0.8-1.3% Si, 0.2-0.45% Cu; 0.5- 1.1% Mn; 0.45-0.1% Mg.
• Structural parts for an automobile application made from a 7xxx alloy as described for example in the application EP 2581 218 are also known.
• the document EP 1702995 A1 describes a method for producing a sheet of aluminium alloy, which comprises the supply of a molten aluminium alloy having a chemical composition, as a percentage by weight, Mg: 0.30 to 1.00%, Si: 0.30 to 1.20%, Fe: 0.05 to 0.50%, Mn: 0.05 to 0.50%, Ti: 0.005 to 0.10%, optionally one or more from among Cu: 0.05 to 0.70% and Zr: 0.05 to 0.40%, and the remainder: A1 and unavoidable impurities: the casting of the molten alloy in a plate having a thickness of 5 to 15 mm by the double-strip casting method with a cooling rate at 1/4 of the thickness of the plate of 40° to 150°C/s, coiling in the form of a reel, homogenisation treatment, cooling of the resulting reel to a temperature of 250°C at least at a cooling rate of 500°C/h or more, followed by cold rolling, and then solution heat treatment.
• Mg 0.30 to
• - W02018/185425 invention relates to a method for producing a stamped component of motor vehicle bodywork or body structure from aluminium alloy comprising the steps of producing a metal sheet or strip of thickness between 1.0 and 3.5 mm in an alloy of composition (% by weight): Si: 0.60-0.85; Fe: 0.05-0.25; Cu: 0.05-0.30; Mn: 0.05-0.30; Mg: 0.50-1.00; Ti: 0.02-0.10; V: 0.00-0.10 with Ti + V 0.10.
• the invention also relates to a stamped component of motor vehicle bodywork or body structure, also called a "body in white” produced by such a method.
• US20180119261 described 6xxx series aluminum alloys with unexpected properties and novel methods of producing such aluminum alloys.
• the aluminum alloys are highly formable and exhibit high strength.
• the alloys are produced by continuous casting and can be hot rolled to a final gauge and/or a final temper.
• the alloys can be used in automotive, transportation, industrial, and electronics applications, just to name a few.
• US20180171452 disclosed high-strength, highly deformable aluminum alloys and methods of making and processing such alloys. More particularly, disclosed is a heat treatable aluminum alloy exhibiting improved mechanical strength and formability.
• the processing method includes casting, homogenizing, hot rolling, solutionizing, pre-ageing and in some cases pre straining. In some cases, the processing steps can further include cold rolling and/or heat treating.
• the invention aims to obtain an excellent compromise between formability in T4 temper and high mechanical strength as well as good behaviour of the finished component under riveting and in a crash, by proposing a method for manufacturing such components including forming in T4 temper after natural ageing at ambient temperature, followed optionally by age hardening on the formed part and baking of the paints or bake hardening.
• One problem is also to achieve a short and economically advantageous method and to improve compared to a product made of alloy AA 6111.
• An object of the invention is a method for manufacturing a rolled product for automobile bodywork or body structure, also referred to as "body in white", from an aluminium alloy, comprising the following successive steps: a.casting of an ingot with the following composition (% by weight):
• V max 0.1; inevitable elements and impurities at maximum 0.05% each, and total 0.15% maximum; remainder aluminium, b. homogenization of the ingot, c.hot rolling of the ingot, d.cold rolling into a sheet, e.solution heat treatment, quenching of the sheet, f.pre ageing of the sheet, g.natural ageing of the sheet.
• Another object of the invention is a rolled product obtainable by the method of the invention.
• Another object of the invention is a part obtainable by the method of the invention.
• Another object of the invention is the use of the part in in a car as bodywork skin parts (or external bodywork panels) such as the front wings, roofs, bonnet, boot or door skins, and the lining parts or bodywork structure components such as for example door, bonnet, tailgate or roof linings or reinforcements, or spars, bulkheads, load-bearing floors, tunnels and front, middle and rear pillars, and finally the impact absorbers or "crashboxes".
• bodywork skin parts or external bodywork panels
• the lining parts or bodywork structure components such as for example door, bonnet, tailgate or roof linings or reinforcements, or spars, bulkheads, load-bearing floors, tunnels and front, middle and rear pillars, and finally the impact absorbers or "crashboxes”.
• Figure 1 depicts the device for "three-point bending test" consisting of two rollers R, and a punch B of radius r, for carrying out the bending of the rolled product T of thickness t.
• Figure 2 depicts the rolled product T after the "three-point bending" test with the internal angle b and the external angle, the measured result of the test: is reported in the enclosed result. The maximum strength during the test procedure is also reported.
• Figure 3 depicts a specific embodiment for the method:
• a sheet is a flat rolled product of rectangular cross- section with uniform thickness between 0,20 mm and 6 mm.
• the static tensile mechanical characteristics in other words the ultimate tensile strength R m , the tensile yield strength at 0.2% elongation Rpo.2 ⁇ and the elongation at break A%, are determined by a tensile test in accordance with NF EN ISO 6892-1.
• the bending angles are determined by a three-point bending test in accordance with NF EN ISO 7438 and the procedures VDA 238-100 and VDA 239-200.
• the bendability is also measured with the norm ASTM E290-97a.
• the inventors selected a set of composition of aluminium alloys in conjunction with suitable methods which offer to car manufacturer interesting properties to produce parts.
• the subject of the invention is a method for manufacturing a rolled product for automobile bodywork or body structure, also referred to as "body in white", from aluminium alloy, comprising the following steps.
• the minimum Fe content is 0.15% and/or the maximum Fe content is 0.30%.
• the Cu maximum content of the ingot is 0.70% and/or the Cu minimum content is 0.55%. More preferably, the maximum Cu content is 0.65%. Limiting the Cu to 0.8%, 0.70% or even 0.65% is interesting for economical reason as Cu is usually more expensive than aluminium. It is also advantageous to ease recyclability of the material. It may also improve the corrosion resistance. In another embodiment however the
• Cu minimum content is 0.65 % in particular to increase strength.
• Mn 0.1 - 0.4.
• the maximum Mn content is 0.35% and / or the minimum Mn content is 0.24% or preferably 0.25%. Addition of Mn improves in particular the bending behaviour.
• Mg 0.75- 1, preferably, the minimum content of Mg is 0.80% and/or the maximum Mg content is 0.90%.
• Ti max 0.15, preferably the minimum Ti content is 0.01% and/or the maximum Ti content is 0.05%.
• the Cr is an inevitable element or an impurity.
• V max 0.1, and preferably the V is an inevitable element or an impurity.
• the casting can be made with various casting process. Continuous casting, which is usually a horizontal casting, is possible. It is also preferred to use a vertical semi continuous casting, which is also known under the name of direct chill casting.
• the vertical semi continuous casting is preferred because it more homogenous through the thickness of the sheet.
• the ingot is homogenised, hot rolled and cold rolled into a sheet.
• the sheet is solution heat treated and quenched.
• the homogenization treatment of the ingot is at a temperature from 520 to 560°C during preferably from 2 to 8 hours.
• the cold rolling rolls the rolled intermediate product into a sheet having a thickness from 1 to 4 mm.
• the sheet is then solution heat treated typically at a temperature beyond the solvus temperature of the alloy while avoiding incipient melting.
• the solution heat treatment temperature is from 530°C, preferably 540°C to 580°C during preferably from Is to 5 minutes.
• Quenching is then applied to the sheet. Water quenching is suitable with a temperature about 15 to 60°C, preferably 15°C to 40°C.
• a pre ageing is applied during preferably at least 8 hours with preferably a temperature from 50 to 120°C.
• Natural ageing is then applied. Natural ageing is defined in NF EN 12258-1 and room temperature is defined in NF EN ISO 6892-1.
• the duration of the natural ageing is from 72 hours to 6 months.
• the pre ageing step is preferably achieved by coiling of the sheet at a coiling temperature and cooling it in open air at the room temperature.
• FIG. 3 A convenient continuous annealing line device to realise the pre ageing is described by figure 3.
• the sheet 3 is uncoiled by uncoiler 1 and goes through the solutionizing furnace 4 and the quenching unit 5, then the sheet 3 enters the surface treatment machine 6, which is a very usual step for car body sheet, followed by a pre ageing oven 7 and finally coiled on the coiler 8 in open air.
• the sheet is therefore hot and the sheet is coiled on the coiler 2 at a coiling temperature in open air.
• the coiled sheet 8 is hot and is stored at ambient temperature in the plant and cools down to ambient temperature. Pre ageing occurs during this cooling. Natural ageing starts after the end the cooling of the coiled sheet 8, preferably the pre ageing duration is at least 8 hours.
• the pre ageing is obtained by coiling the sheet at a coiling temperature from 50 to 120°C, preferably from 60 to 120°C, followed by cooling the coiled sheet in open air, and its duration is 8 hours at least.
• the rolled product of the invention comprises the product obtainable with the above method from casting to natural ageing.
• the temper of the rolled product after natural ageing is T4.
• T4 temper rolled product tensile yield strength varies less than 5 MPa, preferably 3 MPa between the tensile yield strength in the transverse and 45° directions within the same rolled product.
• the same sheet is defined a rolled product made from the same ingot, same homogenization, same hot and cold rolling, same solution heat treatment, same quenching, same pre aging, same natural aging and the tensile testing samples are cut off from the rolled product as close as possible. This is a useful property for part stamping.
• the rolled product in T4 temper can be characterized in 6 others specific tempers, T8A, T8C, T8D, T6B, T6C and T8D, which estimate the material properties of the part.
• T8A, T8C and T8D tempers are achieved by applying on the T4 rolled product a 2% strain followed each by a specific heat treatment.
• T8A temper uses a bake hardening heat treatment of 20 minutes at a temperature of 180°C.
• T8C temper uses a light and short bake hardening heat treatment of 5 minutes at a temperature of 160°C.
• T8D temper uses a light and long bake hardening heat treatment of 20 minutes at a temperature of 160°C.
• the T6B, T6C and T6D tempers are achieved by applying on the T4 rolled product a specific heat treatment.
• T6B temper uses a heat treatment at a temperature of 225°C during 30 minutes.
• T6C temper uses a light and short bake hardening heat treatment of 5 minutes at a temperature of 160°C.
• T6D temper uses a light and long bake hardening heat treatment of 20 minutes at a temperature of 160°C.
• the T4 rolled product can then be formed, in particular by press stamping, in order to obtain a shape.
• the shape is aged.
• the shape may be painted and bake hardened into a part at a temperature from 150 to 190°C, and preferably from 170 to 190°C, during from 5 to 30 minutes, preferably from 15 to 30 minutes.
• An object of the invention is a part obtainable with the above method with the rolled product of the invention.
• the part can be used in a car as bodywork skin parts (or external bodywork panels) such as the front wings, roofs, bonnet, boot or door skins, and the lining parts or bodywork structure components such as for example door, bonnet, tailgate or roof linings or reinforcements, or, preferably, spars, bulkheads, load- bearing floors, tunnels and front, middle and rear pillars, and finally the impact absorbers or "crashboxes" .
• the coiling temperature is from 50°C to 95°C, 95°C being excluded, preferably from 60 to 95°C, 95°C being excluded.
• the T4 temper rolled product of this first embodiment is characterized by a tensile yield strength lower than 165MPa, which can be useful for customer formability at press stamping.
• the T6B temper rolled product of this first embodiment as described formally, has a minimum tensile yield strength of 345 MPa and preferably a minimum tensile yield strength of 350 MPa.
• a preferred composition for the method according to the first embodiment is
• Si 0.75 -1.10 and more preferably less 0.95%
• Fe max 0.4 and more preferably between 0.15% and 0.30%
• Cu 0.5 - 0.70 and preferably 0.5 - 0.65;
• V as an impurity; and the inevitable elements and impurities at maximum 0.05% each, and total 0.15% maximum and the remainder is aluminium.
• the bendability of the T4 rolled product of the first embodiment is 0.19 maximum. This is advantageous in part forming.
• a still more preferred composition of the first embodiment is Si: 0.75 -1.10 and more preferably less 0.95%;
• Fe max 0.4 and more preferably between 0.15% and 0.30%;
• Cu 0.5 - 0.70 and preferably 0.5 - 0.65;
• V as an impurity; and the inevitable elements and impurities at maximum 0.05% each, and total 0.15% maximum and the remainder is aluminium.
• the VDA angle of the T4 temper rolled product is greater than 125°.
• the bendability of the T4 rolled product is still smaller than 0.19. This can be useful in some press stamping application .
• the coiling temperature is between 70°C and 95°C.
• the T8A temper rolled product has a minimum tensile yield strength of 275 MPa.
• the T8A temper rolled product has a minimum tensile yield strength of 280 MPa with a coiling temperature between 70°C and 95°C and with a composition of
• Si 0.75 -1.10 and more preferably less 0.90%;
• Fe max 0.4 and more preferably between 0.15% and 0.30%;
• Mn 0.1 - 0.4 and more preferably less than
• Mg 0.75 - 1 and more preferably less 0.95%; Ti: 0.01 - 0.05;
• V as an impurity; and the inevitable elements and impurities at maximum 0.05% each, and total 0.15% maximum and the remainder is aluminium.
• the coiling temperature is from 95°C to 120°C and preferably from 95°C to 105°C with preferably the composition: Si: 0.75 -1.10 and more preferably less 0.90%;
• Fe max 0.4 and more preferably between 0.15% and 0.30%;
• Cu 0.5 - 0.70 and preferably 0.5 - 0.65;
• Mn 0.1 - 0.4 and preferably minimum 0.25% and preferably less than 0,35%;
• V as an impurity; and the inevitable elements and impurities at maximum 0.05% each, and total 0.15% maximum and the remainder is aluminium.
• the advantage of this second embodiment is in particular the low sensitivity of the yield strength of the part to a variation of the bake hardening treatment.
• the bake hardening conditions are dependent on the location inside the car body assembly, parts having a low sensitivity to bake hardening conditions are thus favourable because the car manufacturer has more flexibility.
• This low sensitivity can be assessed by comparing properties in T6C temper to those in T6D temper and/or properties in T8C temper to those in T8D temper which are obtained from the same T4 temper rolled product.
• the tensile yield strength of the rolled product in T8C and T8D tempers and made from the same rolled product in T4 temper differ by less than 5 MPa.
• the T8C and T8D rolled product samples differs only by the duration of the bake hardening, the temperature of which is 160°C.
• the T6C and T6D rolled product samples differs only by the duration of the bake hardening the temperature of which is 160°C.
• the tensile yield strength of the rolled product in T6C and T6D tempers and made from the same rolled product in T4 temper differ by less than 5 MPa.
• the rolled product can be heat treated with a temperature from 150 to 190°C, and preferably from 170 to 190°C, during from 5 to 30 minutes, preferably from 15 to 30 minutes.
• the yield strength of the rolled product, heat treated at a given temperature in the above temperature ranges, during any duration in the above duration ranges, varies by less than 15 MPa, preferably 10 MPa and more preferably 5 MPa.
• the 2% strained rolled product can be heat treated with a temperature from 150 to 190°C, and preferably from 170 to 190°C, during from 5 to 30 minutes, preferably from 15 to 30 minutes.
• the yield strength of the 2% strained rolled product, heat treated at a given temperature in the above temperature ranges, during any duration in the above duration ranges, varies by less than 15 MPa, preferably 10 MPa and more preferably 5 MPa.
• the T4 temper rolled product has a maximum tensile yield strength of 190 MPa.
• the T6B temper rolled product has a minimum tensile yield strength of 340 MPa.
• the T8A temper rolled product has a minimum tensile yield strength of 280 MPa, preferably of 290MPa.
• Recyclability of any alloy is an important technical and economical parameter. Reducing the range any element is useful in order to strengthen recycling process as it gives predictability of the future melt. Reducing the maximum of the addition element is also advantageous as they can be more expensive than aluminium Reducing Si content is advantageous for recycling because in many alloys, this element is not only an impurity but also detrimental to aluminium product properties. Therefore, an advantageous embodiment of the invention is to reduce the Si content to maximum of 0.95% It is also an advantageous embodiment to reduce Fe maximum to 0.30% and/or to increase the Fe minimum to 0.15%. Another advantageous embodiment is to reduce the Cu maximum to 0.70% and preferably to 0.65% and/or to increase the Cu minimum to 0.55%.
• Another advantageous embodiment is to reduce the Mn maximum content to 0.35% and more preferably to 0.30% and/or to increase its minimum content to 0.15% and more preferably to 0.25%. Another embodiment is also to reduce the Ti maximum content to 0.05% and/or to increase the minimum content to 0.01%. Another embodiment is to classify the V as an impurity with a maximum of 0.05%
• All those combinations of alloys composition and coiling temperature of the invention gives many possibilities for the car manufacturer with different forming properties.
• the car manufacturer can also optimize its processing and the design of its part.
• the shape ageing allows a high strength part but it requires a specific heat treatment of the shape ageing.
• High strength alloys are useful to lightweight part. If the part does not require high strength material, the car manufacturer can avoid the shape ageing, which is advantageous to simplify the production. Hence, the invention gives flexibility to car manufacturer.
• Table 1 summarises the chemical compositions (% by weight) of the alloys used during tests. The proportion of the others inevitable elements and impurities were lower than 0.05%, the total lower is than 0.15%, and the remainder is aluminium. Alloy G is an exemplary AA6111 alloy and alloy H is an exemplary of a modified AA6056.
• the rolling ingots of these various alloys were obtained by vertical semi-continuous casting. After scalping, these various ingots underwent homogenisation heat treatment at 540°C during about 4 hours directly followed by the hot rolling to a 5mm intermediate rolled product. The 5 mm intermediate rolled product was cold rolled to obtain sheets with a thickness of 2mm.
• the rolling steps were followed by a solution heat treatment followed by quenching.
• the solution heat treatment was at a temperature beyond the solvus temperature of the alloy while avoiding incipient melting. In this non limitating example the solutionizing temperature was 570°C.
• the solutionized sheet was then water quenched in a 20°C water.
• the sheet samples were coiled with 3 coiling temperatures of 100°C, 80°C and 60°C for a pre ageing of 8 hours followed by a natural ageing. Two natural ageing were used: 7 days and 30 days at room temperature to obtain T4 temper rolled products.
• T4 rolled products were transformed into a T8A temper with a 2% strain and then heat treatment with a typical bake hardening heat treatment of 180°C during 20 minutes. T8A samples were then characterized. The T4 rolled product were also heat treated into a T6B temper with a heat treatment of 225°C during 30 minutes. T6B samples were then characterized.
• Tests results Tensile tests at ambient temperature were carried out in accordance with NF EN ISO 6892-1 with non-proportional test pieces, with a geometry widely used for sheets, and corresponding to the type of test piece 2 in table B.l of Appendix B of said standard. These test pieces in particular have a width of 20 mm and a calibrated length of 120 mm. Tensile tests were done on rolled product in T4, T8A and T6B temper. The results obtained with a coiling temperature of 80 °C and
• the coiling temperature is an important parameter for T4 temper tensile yield strength. At 60 and 80°C it allows to limit the T4 tensile yield strength below 165 MPa which can be advantageous for car manufacturer if it is needed to maintain stamping easiness.
• Example alloys B, D, E and F have a tensile yield strength minimum of 350 MPa in T8B temper. Those example alloys have a tensile yield strength minimum of 275 MPa in T8A temper.
• the optimized range of Mn from 0.25 to 0.35% offers with the 60°C coiling temperature a very advantageous 3 points bending test with a high VDA angle which is good for formability. This is exemplified by alloy E with coiling temperature of 60°C.
• Example 2 Rolled products manufactured with alloy E, with coiling temperatures 80°C and 100°C and after 7 days of natural ageing were used for others trials. Samples at both coiling temperature were split in 2 groups: in the first group a strain of 2% was applied and the second group there was not any strain. Then a bake hardening temperature of 160°C was applied, with two different durations of 5 and 20 minutes.
• the rolling ingot were heated at 554°C during 4 hours.
• the ingot was directly hot rolled.
• the temperature of the ingot just before the start of hot rolling was 540°C.
• the thickness at the end of hot rolling was 5mm.
• the thickness at the end of cold rolling was 2mm.
• the sheet was split in three in order to solutionize at three different temperatures, 535°C, 544°C and with each a different duration above 525°C: 20s, 45s and 68s.
• the sheets were quenched in 22°C water.
• the sheets were pre aged by coiling the sheets at a temperature of 96°C and cooling in open air followed by a natural ageing at room temperature about 20°C during 3 days to obtain T4 temper rolled products.
• the T4 rolled products were transformed into a T8A temper with a 2% strain and then heat treatment with a typical bake hardening heat treatment of 180°C during 20 minutes. T8A samples were then characterized.
• T4 rolled product were also heat treated into a T6B temper with a heat treatment of 225°C during 30 minutes. T6B samples were then characterized.
• T4 temper tensile yield strength shows an anisotropy of less than 3 MPa between the tensile yield strength in the T and 45° directions within the same rolled product as it can be seen in table 8.
• Bending radius was also measured on T6B temper to check the crash behaviour of the rolled product.

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• 2019
  • 2019-12-17 EP EP19306659.4A patent/EP3839085B1/de active Active
• 2020
  • 2020-12-15 CN CN202080087196.6A patent/CN114829644A/zh active Pending
  • 2020-12-15 CA CA3162027A patent/CA3162027A1/en active Pending
  • 2020-12-15 EP EP20842558.7A patent/EP4077753A1/de active Pending
  • 2020-12-15 KR KR1020227024163A patent/KR20220113793A/ko unknown
  • 2020-12-15 JP JP2022536960A patent/JP2023506278A/ja active Pending
  • 2020-12-15 WO PCT/EP2020/086256 patent/WO2021122621A1/en unknown
  • 2020-12-15 US US17/781,682 patent/US20230008838A1/en active Pending

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