PT2570509E - Production method for almgsi-aluminium strip - Google Patents

Description

ΕΡ2570509Β1

DESCRIPTION PROCESS OF PRODUCTION OF ONE. The invention relates to a process for the production of a band of an AlMgSi alloy in which a rolled ingot of an AlMgSi alloy is melted, the rolled ingot is subjected to homogenization, the rolled ingot placed at rolling temperature is hot rolled, then optionally cold rolled to the final thickness, the rolled strip being prepared, annealed in solution and tempered. In addition, the invention relates to advantageous uses of a suitably fabricated aluminum band of AlMgSi.

Especially in the automotive industry but also in other application areas, for example in the construction of aircraft or railway vehicles, aluminum alloy plates are required, which are characterized not only by particularly high mechanical characteristics but also exhibit very good deformation behavior and allow a high degree of deformation. In the automotive industry are typical applications the bodywork and chassis parts. In the case of visible painted components such as externally visible body panels, it is added that the deformation of the materials must take place in such a way that the surface after painting is not affected by errors such as flow lines or Roping, . This is particularly important, for example, in the use of aluminum alloy sheets for the production of motor hoods and other parts of a motor vehicle's body. The choice of materials in terms of an aluminum alloy is however limited. In particular AlMgSi alloys whose main constituents of the alloy are magnesium and silicon, exhibit relatively high εΡ 2570509Β1 strength in the T6 condition also with equally good deformation behavior in the T4 condition as well as excellent corrosion resistance. AlMgSi alloys are the types of AA6XXX alloys, for example the type of alloy AA6016, AA6014, AA6181, AA6060 and AA6111. Normally aluminum strips are fabricated from an AlMgSi alloy by casting a rolled ingot, homogenizing the rolled ingot, hot rolling the rolled ingot and cold rolling the hot strip. Homogenization of the rolled ingot is carried out at a temperature of 380 to 580 ° C for more than one hour. By annealing for final solubilisation at typical temperatures of 500 ° C to 570 ° C followed by quenching and quenching process treated in solution at room temperature for at least three days, the strips can be supplied in the T4 condition. Condition T6 is defined after the quenching process through artificial aging at temperatures between 100 ° C and 220 ° C. The problem is that there are hot rolled aluminum strips of AlMgSi alloys, coarse precipitations of Mg 2 Si, which in the subsequent cold rolling are broken and reduced due to the high degree of plastic deformation. Hot strips of an AlMgSi alloy are generally produced in thicknesses of 3 mm to 12 mm and supplied to a cold rolling with a high degree of plastic deformation. Since the temperature range at which the AlMgSi phases form in conventional hot rolling is passed very slowly, these phases form coarsely. The temperature range for the formation of the above-mentioned phases is dependent on the alloy. However, it is in the range of 230 ° C to 550 ° C, thus in the range of hot rolling temperatures. It has been experimentally shown that these coarse phases negatively affect the elongation of the final product in the hot band. This means that the deformation behavior of AlMgSi alloys aluminum bands could not until now be fully exploited.

In European patent application EP 2 270 249 AI published by the applicant, it has been proposed that the AlMgSi alloy band exhibits a maximum temperature of 130 ° C immediately after the exit of the last pass from the hot rolling, being wound with this or lower temperature. Through the quenching process of the hot rolled strip with this process, aluminum strips in the T4 condition could be fabricated, which have an elongation at break of A80 greater than 30% or a uniform Ag elongation of more than 25%. In addition, very high values were obtained for the elongation at break in the T6 condition. However, it has been found that this temperature range at the outlet of the last pass of the hot rolling leads to problems in the smoothness of the hot strip, so that the subsequent manufacturing steps have been disturbed. In addition, the predetermined cooling rate could only be achieved at reduced production rates. From this condition of the art, the present invention aims to provide an improved process for the production of an aluminum band of an AlMgSi alloy, with which the AlMgSi aluminum bands can be reliably fabricated with a very high deformation behavior good in condition T4.

According to a first teaching of the present invention, the stated aim for a process is achieved by the hot strip, immediately after the exit of the last hot rolling pass, having a temperature in excess of 130øC, preferably 135øC up to a maximum of 3Â ° F 2570509Â · 250Â ° C, preferably 135Â ° C at a maximum of 230Â ° C and the hot strip is wound at this temperature.

Contrary to the known process with particularly low winding temperatures it has surprisingly been found that the mechanical properties, relative to the uniform elongation Ag determined for the deformation behavior despite the altered winding temperatures, do not change or change only slightly. The AlMgSi alloy strips manufactured according to the invention in condition T4 furthermore exhibit a uniform elongation of more than 25% in the tensile test according to DIN EN. In addition, they have shown very good hardenability in condition T6, as is known from the applicant's provisional declaration. However the production process can be significantly stabilized and a higher production rate is obtained.

According to an advantageous embodiment of the process according to the invention, this cooling process takes place within the last two hot rolling passes, i.e., cooling above 130øC, preferably 135øC to 250ø ° C, more preferably 135 ° C to 230 ° C takes place within a few seconds, at the most within five minutes. It has been found that with this approach, high values of uniform elongation at the conventional limits of strength or elongation at the T4 condition and the improved hardness at the T6 condition can be achieved in a particularly reliable manner.

According to a further embodiment of the process according to the invention a reliable quenching of the hot strip is achieved by the hot strip 4 ΕΡ 2570509Β1 being quenched at the outlet temperature using at least one plate cooler and the same rolling pass to hot emulsion. A plate cooler consists of a set of coolant injectors or lubricants, which spray a rolling emulsion on the aluminum strip. The plate cooler may be present in a hot rolling mill to cool to the rolling temperature hot rolled strips prior to hot rolling and to achieve higher production speeds.

If, prior to the start of the cooling process, the hot strip temperature, which takes place preferably within the last two rolling passes, is at least 400øC, preferably 470øC at 490øC, is achieved in accordance with a further embodiment of the process, that particularly small precipitations of Mg 2 Si are present in the hot tempered band since a large part of the magnesium and silicon alloy components are present at these dissolved state temperatures in the aluminum matrix. This favorable condition of the hot band is almost " frozen " by the quenching process.

According to another embodiment of the process, the hot strip temperature is after the penultimate rolling pass, from 290 ° C to 310 ° C. It has been found that these temperatures allow both sufficient cooling of the precipitations and, on the other hand, the last rolling pass can be performed simultaneously without problems.

If the hot strip at the outlet directly after the last hot rolling pass has a temperature of 200 ° C to 230 ° C, an optimum process speed can be achieved without deteriorating the properties of the produced aluminum strip. The thickness of the prepared hot strip is from 3 mm to 12 mm, preferably from 5 mm to 8 mm, so that conventional cold rolled cold rolling can be used.

Preferably the aluminum alloy used is ΑΑβχχχ, preferably AA6014, AA6016, AA6060, AA6111 or AA6181 alloy. All types of ΑΑβχχχ alloys mean that they exhibit a particularly good deformation behavior characterized by high elongation values in the T4 condition, as well as high strength and permanent elongation limit in the T6 application condition, for example after an artificial aging at 205 ° C / 30 min.

According to another embodiment of the process according to the invention, the laminated aluminum strip is subjected to a heat treatment, the aluminum strip after annealing for solubilization and quenching is heated to more than 100 ° C and then at a temperature in excess of 55øC, preferably more than 85øC, rolled up and aged. This embodiment of the process enables that after quench treated in solution, and through a short heating phase with low temperatures, to adjust the condition T6 in the web or plate, in which the sheets or strips molded in components are applied in the use . These fast setting aluminum strips are thereby heated at temperatures of about 185 ° C for only 20 min. to reach the highest elastic limits in the T6 condition.

In fact the elongation at break values A80 of the 6 Å 2525509 1 aluminum strip produced according to the process according to this embodiment in the T 4 condition are slightly below 29%. The aluminum strip produced according to the present invention continues to be characterized however after natural or artificial precipitation in the T4 condition by a very good uniform Ag elongation of greater than 25%. Under the uniform elongation Ag is meant the maximum elongation of the sample, in which in the tensile test there is no constriction of the sample. The sample is also uniformly elongated in the zone of uniform elongation. The value for uniform stretching was so far in similar materials up to 22% to 23%. Uniform elongation significantly influences deformation behavior since it determines the degree of maximum deformation of the material used in practice. Accordingly, an aluminum strip having very good deformation properties can be provided with the process according to the invention, which can also be transferred to the T6 condition by accelerated artificial aging (185 ° C / 20 min).

An aluminum alloy of type AA6016 has the following alloying components in percent by weight: â € ƒâ € ƒâ € ƒâ € ƒâ € ƒâ € ƒâ € ƒâ € ƒ0.25%

Fe £ 0.5%

Cu & 0.2%

Mn & 0.2%,

Cr < 0.1%,

Zn &lt; 0.1%,

Ti &lt; 0.1% and AI remainder as well as unavoidable impurities in the maximum total of 0.15%, individually at most 0.05%.

At magnesium contents of less than 0.25 in weight percent the strength of the aluminum strip, which is intended for structural applications, is too low, and on the other hand the deformation capacity deteriorates with magnesium contents higher than 0.6 in percent by weight. Silicon is in interaction with magnesium mainly responsible for the hardenability of the aluminum alloy and thus also for the high strength which can be obtained in the case of application for example after firing the lacquer. In silicon contents of less than 1.0 percent by weight, the hardening capacity of the aluminum strip is reduced, so that in the case of application only reduced strength can be provided. Si contents greater than 1.5 percent by weight do not improve the bond hardening behavior. The Fe content should be limited to a maximum of 0.5% by weight in order to avoid coarse precipitation. Limiting the copper content to 8 ÅΡ 2570509Β1 a maximum of 0.2 percent by weight leads above all to improved corrosion resistance of the aluminum alloy in the specific application. The manganese content of less than 0.2 weight percent reduces the tendency for the formation of coarse manganese precipitation. Although chromium provides a fine structure, it should be limited to 0.1 percent by weight, so as to also avoid gross precipitations. The presence of manganese, however, improves the weldability by reducing the cracking tendency or sensitivity to the quenching process of the aluminum strip according to the invention. A reduction of the zinc content to a maximum of 0.1 weight percent particularly improves the corrosion resistance of the aluminum alloy or sheet prepared in the respective application. However titanium provides a grain refining during casting but should be limited to a maximum of 0.1 weight percent to ensure good flowability of the aluminum alloy.

An aluminum alloy of type AA6060 has the following alloying components in weight percent: 0.35% &lt; Mg &lt; 0.6%, 0.3% &lt; Si S 0.6%, 0.1% &lt; Fe £ 0.3%

Ca &lt; 0.1 I,

Mn &lt; 0.1%

Cr £ 0.05%,

Zn = 0.10%

Ti &lt; 0.1% 9 ΕΡ 2570509Β1 and AI moiety as well as unavoidable impurities in the maximum total of 0.15%, individually at most 0.05%. The combination of exactly predetermined magnesium content with a reduced Si content compared to the first embodiment and restrictedly specified Fe content results in an aluminum alloy which can be prevented by the process according to the invention, particularly the formation of Mg 2 Si precipitations after hot rolling, so that a sheet with improved elongation and high elongation limits can be provided in comparison with conventionally produced sheets. The small maximum limits of the Cu, Mn and Cr alloy components additionally increase the effect of the process according to the invention. With regard to the effects of the Zn and Ti ceiling, see the embodiments of the first embodiment of the aluminum alloy.

An aluminum alloy of the AA6014 type has the following alloying components in percent by weight: â € ‡ â € ‡ â € ‡ â € ‡ â € ‡ â € ‡ â € ‡ â € ‡ â € ‡ â € ‡ â € ‡ If &lt; 0.6%,

Fe < 0.35%

Cu < 0.25%, 0.05% Mn S 0.20%, Cr £ 0.20 I,

Sn S 0.10%, 0.05% SV ≤ 0.20%, Ti <0.1% and the AI moiety as well as unavoidable impurities in the maximum total of 0.15%, individually at most 0.05% .

An aluminum alloy of type AA6181 has the following alloying components in percent by weight: 0.6 * S Hg S 1.0%, 0.8% &lt; If &lt; 1.2%,

Fe &lt; 0.45%

Cu < 0.10%, 11 ΕΡ 2570509Β1 Μη 0.15%, Cr < 0.10%, 2æ 0 0.20%, ΤΙ < 0.1% and AI rest as well as unavoidable impurities in the maximum total of 0.15%, individually at most 0.05%.

An aluminum alloy of the AA6111 type has the following alloying components in percent by weight: 0-5% a Mg = 1.0 I, O ,? If £ 1.1%

Fe to 0.40% 0.50% Cu Cu 0.90%, 0.15% &lt; Mn 0.45%,

Cr < 0.10%

Zn = 0.15%

Ti &lt; 0.1% and AI rest as well as unavoidable impurities in the maximum total of 0.15%, individually at most 0.05%. The AA6111 alloy basically shows, because of the high copper content, higher strength values under the condition of 12 ΕΡ2570509Β1 T6 use, but should be considered as susceptible to corrosion.

All the aluminum alloys shown are specifically adapted, in their alloy components, for different applications. As already mentioned, the bands of these aluminum alloys, which were produced using the process according to the invention, exhibit particularly high values of uniform elongation in the T4 condition coupled to a particularly strong increase of the elongation limits eg after aging artificial at 205 ° C / 30 min. This also applies to aluminum strips subjected to a heat treatment at the T4 condition after annealing for solubilization.

Due to the excellent combination of good deformation ability in the T4 condition, high corrosion resistance as well as high values for the elongation limits Rp0.2 in the application condition (condition T6) the above described object is achieved according to a second teaching of the present invention by the use of an AlMgSi alloy web produced in a method according to the invention for a component, chassis part or part of the structure and structure plate in the automotive, aeronautical or railway vehicle construction, in particular as a component, part of the chassis, external or internal plate in the automotive construction, preferably as a body-building element. Above all visible body parts, eg engine hoods, mudguards, etc., as well as external casing parts of a rail vehicle or aircraft benefit from high Rp0.2 elongation limits with good surface properties, even after a deformation with a high degree of deformation. 13 ΕΡ 2570509Β1

Therefore, a fast-setting AlMgSi alloy web having excellent plastic deformation properties can be provided through an aluminum alloy strip produced in accordance with the invention, which is subjected after its production to an annealing for solubilization followed by a heat treatment. In the condition T4 has, as already indicated, a uniform Ag elongation of more than 25%, for example with an elongation limit Rp0.2 of 80 to 140 MPa. With this variant there can be provided a fast hardening and simultaneously easily deformable alMgSi alloy web. Artificial aging to obtain the T6 condition can take place at 185 ° C for 20 minutes to achieve the necessary increase in the elongation limit.

An aluminum alloy web produced in accordance with the invention has in a further embodiment a uniform Ag elongation of more than 25% in the rolling direction, transverse to the rolling direction and diagonal to the rolling direction, that more isotropic deformation capacity is possible.

Preferably the aluminum strips produced in accordance with the invention have a thickness of 0.5 mm to 12 mm. Aluminum strips with thicknesses of 0.5 mm to 2 mm are preferably used for body parts, for example in the automotive industry, while aluminum strips with thicknesses of more than 2 to 4.5 mm are chassis parts in the automotive industry. The individual components can be manufactured in cold rolled strip with a thickness of up to 6 mm. In addition, aluminum strips with thicknesses up to 12 mm can also be used in specific applications. These very thick aluminum strips are usually provided only by hot rolling εΡ 2570509Β¹. The invention will be described in detail below, by way of example embodiments in conjunction with the drawing. The drawing shows in the single figure 1 a schematic flow diagram of an exemplary embodiment of the process according to the invention for the production of a band of an aluminum alloy MgSi with steps a) Production and homogenization of the rolled ingot, b) Hot rolling, c) Cold rolling, and d) Annealing for solubilization with quenching process.

First, a rolled ingot 1 of an aluminum alloy having the following alloying components in percent by weight is poured: 0.25 1 to Mg < 0.6%, 1.0% Si Si < 1.5 I,

Fe < 0.50%,

Cu < 0.20%,

Mn 0.20%, Cr £ 0.10, Zn < 0.20%, Ti < 0.15 I and AI moiety as well as unavoidable impurities in the maximum total of 0.15%, individually at most 0.05%. The rolled ingot produced in this way is homogenized at a homogenization temperature of about 550 ° C for 8 hours in a furnace 2, so that the alloyed components of the alloy are particularly evenly distributed in the rolled ingot, Fig. over there).

In figure 1b) it is shown how the laminated ingot 1 is reversely heat-laminated through the hot-rolling mill 3 in the exemplary embodiment of the process according to the invention, the laminated billet 1 having a temperature 400 ° C and 550 ° C during hot rolling. In this exemplary embodiment, after leaving the hot mill 3 and before the penultimate hot mill pass the hot mill 4 preferably has a temperature of at least 400øC, preferably 470øC at 490øC . Preferably, the hot strip tempering process 4 takes place at this hot strip temperature using a plate cooler 5 and the hot rolling mill working cylinders 3. Preferably the hot strip is cooled here to a temperature from 290 ° C to 310 ° C prior to the last hot rolling pass. To this end the plate cooler 5 only schematically sprays the hot strip 4 with cooling roll emulsion and is responsible for accelerated cooling of the hot strip 4 to the last mentioned temperatures. The working rolls of the hot rolling mill 3 are emulsified and further cool hot strip 4 in the last hot rolling pass. After the last rolling pass the hot strip 4 presents at the outlet of the plate cooler 5 'in the present example embodiment, a temperature of 200 ° C to 230 ° C, and then is wound at this temperature on a receiving spool 6. 16 ΕΡ 2570509Β1

Since the hot strip 4 immediately after the last hot rolling pass has a temperature of more than 135 ° C to 250 ° C, preferably 200 ° C to 230 ° C or optionally is conducted at the temperatures referred to in the two the last hot rolling passes using the plate cooler 5 and the working rolls of the hot rolling mill 3, the hot strip 4 presents, despite the high rolling temperature, a frozen condition for the crystalline structure leading to the elongation properties uniform Ag very good, of more than 25% in the T4 condition. Due to the higher winding temperature one can process faster and better. The hot strip having a thickness of 3 to 12 mm, preferably 5 to 8 mm is wound onto the receiving spool 6. As already described, the rolling temperature in the present embodiment is preferably 135 ° C to 250 ° C.

In the process according to the invention in the coiled hot strip 4, no coarse Mg 2 Si can be formed or only a few coarse Mg 2 Si precipitations can be formed. The hot strip 4 has a very favorable crystal state for further processing and can be unwound from the unwinding spool 7, for example supplied to a cold mill 9 and rewound onto a take up spool 8, Figure 1c). The resulting cold rolled strip 11 is wound. Then subjected to annealing for solubilization at temperatures of 520 ° C to 570 ° C and a tempering process 10, figure 1d). It is unwound from the coil 12 again, annealed in a solution and tempered in a furnace 10 and wound again on a coil 13. The aluminum strip can then be supplied after a natural aging at room temperature in the condition T4 with a capacity of 17 ÅΡ2570509Β1 maximum deformation . Alternatively (not shown) the aluminum strip 11 may be separated into individual sheets, which are provided after natural aging in condition T4.

In the case of larger aluminum band thicknesses, for example in the case of landing gear applications or components such as for example brake anchor plates, the parts annealing can alternatively be performed and the sheets are then passed through a process of tempering.

In condition T6 the aluminum band or the aluminum plate is subjected to an artificial aging at 100 ° C to 220 ° C to obtain maximum values for the permanent stretching limits. For example, an artificial aging can be performed at 205 ° C / 30 min.

The aluminum strips produced in accordance with the illustrated example of embodiment have after cold rolling, for example a thickness of 0.5 to 4.5 mm. Band thicknesses of 0.5 to 2 mm are commonly used for bodywork applications or band thicknesses from 2.0 mm to 4.5 mm for chassis parts in the automotive industry. In both fields of application the improved uniform stretching values are advantageously decisive in the production of the components, since strong sheet deformations are performed, although high strength is required in the condition of use (T6) of the final product.

The compositions of the alloys of aluminum alloys from which conventional aluminum strips or according to the invention are produced are shown in Table 1. In addition to the presented contents of alloy components the 18 ΕΡ 2570509Β1 aluminum bands contain as residual aluminum part and impurities, individually a maximum of 0.05 percent by weight and a maximum of 0.15 percent by weight.

Table 1

Bands Si% total Fe% wt Cu% wt% Mn wt% Mg wt% Cr wt% Zn wt% Ti wt% 251 1.3 0.19 - 0.06 0.3 - 0.01 0, 02 252 1.3 0.19 - 0.06 0.3 - 0.01 0.02 491-1 1.39 0.18 0.002 0.062 0.30 0.0006 0.01 0.0158 491-11 1.40 0.18 0.002 0.063 0.31 0.0006 0.0104 0.0147

Bands (samples) 251 and 252 were produced by a process according to the invention, wherein the hot strip in the last two hot rolling passes was cooled, and wound, from about 470øC to 490øC to 135 ° C to 250 ° C using a plate cooler as well as hot rolling. In Table 2 the measured values of these bands are marked with &quot; Inv. &Quot;. Then a cold rolling to a final thickness of 0.865 mm was performed.

Bands (samples) 491-1 and 491-11 were produced with conventional hot rolling and cold rolling and marked with &quot; Conv &quot;.

The results of the mechanical properties shown in Table 2 clearly show the difference in the Ach values of uniform elongation achievable. 19 ΕΡ 2570509Β1

Table 2

Bands T4 T6 205 ° C / 30 Min. (MPa) (MPa) (MPa) (%) (MPa) (MPa) (MPa) (%) (MPa) 251 L Inv 0.865 93 207 26, 3 30.4 251 Q Inv 0.865 86 203 26.4 29.0 193 249 12.4 107 251 D Inv 0.865 87 203 27.0 30.0 252 L Inv 0.865 93 206 26.1 31.5 252 Q Inv. 0.865 88 205 26.6 29.0 185 244 12.2 97 252 D Inv 0.865 87 202 27.3 31.1 491- -1 Conv. 1, 09 92 202 23.1 27.8 180 235 10.7 88 491- 11 Conv. 1, 04 88 196 23.0 27.4 179 232 11.2 91

To obtain condition T4 the bands were subjected to an annealing for solubilization followed by the quenching process and subsequent natural aging for eight days at room temperature. Condition T6 was achieved by artificial aging following natural aging at 205 ° C for 30 minutes.

The samples marked with L were cut in the direction of rolling, the samples marked Q in the cross-roll direction and the samples marked D in the diagonal direction in the rolling direction. Samples 491-1 and 491-11 were measured respectively transversely to the rolling direction.

It has been found that the advantageous structure which has been created by the process according to the invention in the bands 251 and 252 provides with an identical elongation limit Rp0.2 and resistance Rm a significant increase of the uniform Ag elongation. from 23.0% to 26.6% crosswise to the rolling direction in the bands produced according to the invention in 20 Å 2525509 1 compared to the conventionally produced bands. The structure created with the process according to the invention leads to a particularly advantageous combination of a uniform Ag elongation of greater than 25% at very high values for the elongation limit Rp0.2 from 80 to 140 MPa. In the T6 condition the elongation limit Rp0.2 increases to at least 185 MPa, and the uniform Ag elongation still remains at more than 12%. The hardenability with an ARp0.2 of 97 or 107 MPa is still very good in the bands produced according to the invention.

In the condition Τβ the increase of the uniform Ag elongation can almost be conserved, when compared with bands produced conventionally.

The elongation at break values Ag and A80, the limit values of elongation Rp0.2 and the values of tensile strength Rm in the tables were measured according to DIN EN. 21 ΕΡ 2570509Β1

DOCUMENTS REFERRED TO IN THE DESCRIPTION

This list of documents referred to by the author of the present patent application has been prepared solely for the reader's information. It is not an integral part of the European patent document. Notwithstanding careful preparation, the IEP assumes no responsibility for any errors or omissions.

Patent documents referred to in the specification • EP 2270249 AI [0004]

Lisbon, April 21, 2014 22

Claims (9)

A process for the production of a web of AlMgSi alloy in which a rolled ingot of an AlMgSi alloy is melted, the rolled ingot is subjected to homogenization, the rolled ingot placed at the rolling temperature is hot rolled , and then optionally cold rolled to the final thickness, the prepared rolled strip being annealed in a solution and tempered, characterized in that the hot strip immediately after the exit of the last hot rolling pass has a temperature in excess of 130 ° C to 250 ° C, preferably up to 230 ° C and the hot strip is wound at this temperature. A process according to claim 1, characterized in that the hot strip is quenched at the outlet temperature using at least one plate cooler and the own emulsion hot rolling pass. Process according to claim 1 or 2, characterized in that before the start of the cooling process the temperature of the hot strip during hot rolling is greater than 400øC. A process as claimed in any one of claims 1 to 3, characterized in that the temperature of the hot strip after the penultimate rolling pass is greater than 250 ° C. Process according to any one of claims 1 to 4, characterized in that the temperature of the hot strip after the last rolling pass prior to rolling is 200 ° C to 230 ° C. 1 ΕΡ 2570509Β1 Process according to any one of claims 1 to 5, characterized in that the thickness of the prepared hot strip is from 3 to 12 mm, preferably 5 to 8 mm. Process according to any of claims 1 to 6, characterized in that the aluminum alloy is of the ΑΑβχχχ, preferably AA6014, AA6016, AA6060, AA6111 or AA 6181 type alloy. Process according to any one of claims 1 to 7, characterized in that the prepared laminated aluminum strip is subjected to a heat treatment in which the aluminum strip after annealing for solubilization and tempering process is heated to more than 100 ° C and then at a temperature above 55øC, preferably more than 85øC, rolled up and aged. Use of an aluminum strip produced with a process according to any of claims 1 to 8 for a component, chassis part or part of the structure or sheet in the automotive, aeronautical or railway vehicle construction, in particular as component, chassis, external or internal plate in the automotive construction, preferably as a body-building element. Lisbon, April 21, 2014 2