CA2882614C - Highly formable and intercrystalline corrosion-resistant almg strip - Google Patents
Highly formable and intercrystalline corrosion-resistant almg strip Download PDFInfo
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- CA2882614C CA2882614C CA2882614A CA2882614A CA2882614C CA 2882614 C CA2882614 C CA 2882614C CA 2882614 A CA2882614 A CA 2882614A CA 2882614 A CA2882614 A CA 2882614A CA 2882614 C CA2882614 C CA 2882614C
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- 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
- C22C21/04—Modified aluminium-silicon alloys
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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
- C22F1/047—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 magnesium as the next major constituent
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- 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
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- 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
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- 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
Abstract
The invention relates to a cold-rolled aluminium alloy strip made of an AlMg aluminium alloy as well as a method for producing the same. Furthermore, corresponding components made from said aluminium alloy strips are also proposed. The problem for the invention of providing a single-layer aluminium alloy strip that is sufficiently resistant to intercrystalline corrosion and is nevertheless very formable so that even large-area deep-drawn parts, e.g. interior parts of motor vehicle doors, can be made with sufficient strength, is solved by an aluminium alloy strip made of an AlMg aluminium alloy which has the following alloying components: Si <= 0.2 wt.%, Fe <= 0.35 wt.%, Cu <= 0.15 wt.%, 0.2 wt.% <= Mn <= 0.35 wt.%, 4.1 wt.% <= Mg <= 4.5 wt.%, Cr <= 0.1 wt.%, Zn <= 0.25 wt.%, Ti <= 0.1 wt.%, the remainder being Al and inevitable impurities, amounting to a maximum of 0.05 wt.% individually and a maximum of 0.15 wt.% in total, wherein the aluminium alloy strip has a recrystallized microstructure, the average grain size of the microstructure ranges from 15 µm to 30 µm, preferably from 15 µm to 25 µm, and the final soft annealing of the aluminium alloy strip is performed in a continuous furnace.
Description
STRIP
The invention relates to a cold-rolled aluminium alloy strip composed of an AlMg aluminium alloy and a method for the production thereof. Furthermore, corresponding components produced from the aluminium alloy strips will be proposed.
Aluminium-magnesium-(A1Mg+alloys of the AA 5xxx type are used in the form of sheets or plates or strips for the construction of welded or joined structures in ship, automotive and aircraft construction. They are characterised by high strength which increases as the magnesium content rises. AlMg-alloys of the AA 5xxx type with Mg contents of more than 3%, in particular more than 4%, have an increasing tendency towards intercrystalline corrosion, when exposed to high temperatures. At temperatures of 70 - 200 C, 13-A15Mg3 phases precipitate along the grain boundaries, which are referred to as 13-particles and in the presence of a corrosive medium can be selectively dissolved. The result of this is that the AA 5182-type aluminium alloy (Al 4.5% Mg 0.4% Mn) having very good strength properties and very good formability in particular cannot be used in heat-stressed areas, where the presence of a corrosive medium such as water in the form of moisture must be contended with. This concerns in particular the components of a motor vehicle which normally undergo cathode dip painting (CDP) and are then dried in a stoving process, as already due to this stoving process, normal aluminium alloy strips can become susceptible to intercrystalline corrosion. Furthermore, for use in the automotive sector, forming during the manufacture of a component and subsequent operational stressing of the component must be taken into consideration.
The susceptibility to intercrystalline corrosion is normally checked in a standard test (NAMLT
test) according to ASTM G67, during which the specimens are exposed to nitric acid and the mass loss due to the intercrystalline corrosion is measured. According to ASTM
G67, the mass loss of materials which are not resistant to intercrystalline corrosion, is more than 15 mg/cm2.
The invention relates to a cold-rolled aluminium alloy strip composed of an AlMg aluminium alloy and a method for the production thereof. Furthermore, corresponding components produced from the aluminium alloy strips will be proposed.
Aluminium-magnesium-(A1Mg+alloys of the AA 5xxx type are used in the form of sheets or plates or strips for the construction of welded or joined structures in ship, automotive and aircraft construction. They are characterised by high strength which increases as the magnesium content rises. AlMg-alloys of the AA 5xxx type with Mg contents of more than 3%, in particular more than 4%, have an increasing tendency towards intercrystalline corrosion, when exposed to high temperatures. At temperatures of 70 - 200 C, 13-A15Mg3 phases precipitate along the grain boundaries, which are referred to as 13-particles and in the presence of a corrosive medium can be selectively dissolved. The result of this is that the AA 5182-type aluminium alloy (Al 4.5% Mg 0.4% Mn) having very good strength properties and very good formability in particular cannot be used in heat-stressed areas, where the presence of a corrosive medium such as water in the form of moisture must be contended with. This concerns in particular the components of a motor vehicle which normally undergo cathode dip painting (CDP) and are then dried in a stoving process, as already due to this stoving process, normal aluminium alloy strips can become susceptible to intercrystalline corrosion. Furthermore, for use in the automotive sector, forming during the manufacture of a component and subsequent operational stressing of the component must be taken into consideration.
The susceptibility to intercrystalline corrosion is normally checked in a standard test (NAMLT
test) according to ASTM G67, during which the specimens are exposed to nitric acid and the mass loss due to the intercrystalline corrosion is measured. According to ASTM
G67, the mass loss of materials which are not resistant to intercrystalline corrosion, is more than 15 mg/cm2.
- 2 -Sheet metal for the automotive industry, e.g. for internal door parts, must have very good formability. Here, the requirements are essentially determined by the stiffness of the component concerned, with the strength of the material playing only a subordinate role.
The components often undergo multi-stage forming processes, such as for example doors with integrated window frame areas.
So, apart from the corrosion properties, the formability of the AlMg aluminium alloy also has a major influence on the usage possibilities for this material. For example, the materials known so far have meant that it is not possible for the side walls of a motor vehicle to be deep-drawn from a single sheet, making not only reconstruction of the side wall but also additional process steps for providing the side wall of a motor vehicle necessary.
The forming behaviour can, for example, be measured in a stretch drawing trial by an Erichsen m cupping test (DIN EN ISO 20482), in which a test piece is pushed against the sheet, resulting in cold forming. During the cold forming, the force and the force displacement of the test piece are measured, until a load drop occurs, caused by the formation of a crack. The SZ32 stretch drawing measurements quoted in the application were performed with a punch head diameter of 32 mm and a die diameter of 35.4 mm with the help of a TeflonTm deep-drawing film to reduce friction. Further measurements of the deep drawability were performed using the so-called plane-strain-cupping test using a Nakajima geometry according to DIN EN ISO 12004 with a punch diameter of 100 mm. For this, specimens with a specific geometry underwent drawing tests until a crack appeared, with the depth until cracking being used as a measure of the formability of the material.
From JP 2011-052290 A, an aluminium alloy strip for can lids is known, which is preferably load-resistant despite its small thickness. Here, the strip has a recrystallized microstructure.
Further, from EP 2 302 087 A1, a chassis part is known made from an aluminium composite material, which has aluminium alloy layers as outer layers. Due to the alloying constituents, the
The components often undergo multi-stage forming processes, such as for example doors with integrated window frame areas.
So, apart from the corrosion properties, the formability of the AlMg aluminium alloy also has a major influence on the usage possibilities for this material. For example, the materials known so far have meant that it is not possible for the side walls of a motor vehicle to be deep-drawn from a single sheet, making not only reconstruction of the side wall but also additional process steps for providing the side wall of a motor vehicle necessary.
The forming behaviour can, for example, be measured in a stretch drawing trial by an Erichsen m cupping test (DIN EN ISO 20482), in which a test piece is pushed against the sheet, resulting in cold forming. During the cold forming, the force and the force displacement of the test piece are measured, until a load drop occurs, caused by the formation of a crack. The SZ32 stretch drawing measurements quoted in the application were performed with a punch head diameter of 32 mm and a die diameter of 35.4 mm with the help of a TeflonTm deep-drawing film to reduce friction. Further measurements of the deep drawability were performed using the so-called plane-strain-cupping test using a Nakajima geometry according to DIN EN ISO 12004 with a punch diameter of 100 mm. For this, specimens with a specific geometry underwent drawing tests until a crack appeared, with the depth until cracking being used as a measure of the formability of the material.
From JP 2011-052290 A, an aluminium alloy strip for can lids is known, which is preferably load-resistant despite its small thickness. Here, the strip has a recrystallized microstructure.
Further, from EP 2 302 087 A1, a chassis part is known made from an aluminium composite material, which has aluminium alloy layers as outer layers. Due to the alloying constituents, the
- 3 -Al composite material is characterized by excellent strength values with a high corrosion resistance at low weight.
Composite material solutions composed of AA5xxx aluminium alloys with a high Mg content and outer aluminium alloy layers to protect against corrosion, however, have the disadvantages that manufacture is complex and additionally at joining points where the aluminium composite material joins to other parts, for example at cutting edges, drill-holes and breakouts, there is furthermore an increased danger of corrosion.
The present invention is therefore concerned with single-layer aluminium materials. On this basis, the object of the invention is to provide a single-layer aluminium alloy strip, having sufficient resistance to intercrystalline corrosion but nevertheless having good formability, so that large-area, deep-drawn parts, such as interior parts of motor vehicles doors, with sufficient strength can be provided. Furthermore, a method will be indicated with which single-layer aluminium alloy strips can be produced. Finally, components produced from the aluminium alloy strips according to the invention will be indicated.
According to a first teaching of the present invention, the object indicatedl is achieved by a cold-rolled aluminium alloy strip composed of an AlMg aluminium alloy, wherein the aluminium alloy has the following alloying elements:
Si 5_ 0.2 wt.%.
Fe 0.35 wt.%, Cu 0.15 wt.%, 0.2 wt.% Mn 0.35 wt.%,
Composite material solutions composed of AA5xxx aluminium alloys with a high Mg content and outer aluminium alloy layers to protect against corrosion, however, have the disadvantages that manufacture is complex and additionally at joining points where the aluminium composite material joins to other parts, for example at cutting edges, drill-holes and breakouts, there is furthermore an increased danger of corrosion.
The present invention is therefore concerned with single-layer aluminium materials. On this basis, the object of the invention is to provide a single-layer aluminium alloy strip, having sufficient resistance to intercrystalline corrosion but nevertheless having good formability, so that large-area, deep-drawn parts, such as interior parts of motor vehicles doors, with sufficient strength can be provided. Furthermore, a method will be indicated with which single-layer aluminium alloy strips can be produced. Finally, components produced from the aluminium alloy strips according to the invention will be indicated.
According to a first teaching of the present invention, the object indicatedl is achieved by a cold-rolled aluminium alloy strip composed of an AlMg aluminium alloy, wherein the aluminium alloy has the following alloying elements:
Si 5_ 0.2 wt.%.
Fe 0.35 wt.%, Cu 0.15 wt.%, 0.2 wt.% Mn 0.35 wt.%,
4.1 wt.% Mg 4.5 wt.%, Cr 0.1 wt.%, Zn 0.25 wt.%, Ti < 0.1 wt.%, the remainder being Al and inevitable impurities, amounting to a maximum of 0.05 wt.%
individually and a maximum of 0.15 wt.% in total, wherein the aluminium alloy strip has a recrystallized microstructure, the average grain size of the structure ranges from 15 um to 30 um, preferably from 15 urn to 25 pm and the final soft annealing of the aluminium alloy strip is carried out in a continuous furnace.
It has been found that within the specification of the AA5182-type aluminium alloy, there is a specific, narrow, alloying range which offers sufficient resistance to intercrystalline corrosion and at the same time, by taking into account certain constraints, such as for example the average grain size and the type of final soft annealing, results in an exceptional forming behaviour. In particular, the combination of the average grain size with the claimed alloying elements of the aluminium alloy of the aluminium alloy strip means that degrees of formability can be achieved allowing the production of large-area design, deep-drawn sheet aluminium products with sufficient strength. In particular it has been found that the use of a continuous furnace rather than the normal coil annealing performed in a chamber furnace provides a further significant increase in formability.
According to a first configuration of the aluminium alloy strip, the aluminium alloy also has one or more of the following restrictions to the contents of alloying elements:
0.03 wt.% Si 5_ 0.10 wt.%, Cu 5_ 0.1% preferably 0.04% Cu 0.08%, Cr 0.05 wt.%, Zn 0.05 wt.%,
individually and a maximum of 0.15 wt.% in total, wherein the aluminium alloy strip has a recrystallized microstructure, the average grain size of the structure ranges from 15 um to 30 um, preferably from 15 urn to 25 pm and the final soft annealing of the aluminium alloy strip is carried out in a continuous furnace.
It has been found that within the specification of the AA5182-type aluminium alloy, there is a specific, narrow, alloying range which offers sufficient resistance to intercrystalline corrosion and at the same time, by taking into account certain constraints, such as for example the average grain size and the type of final soft annealing, results in an exceptional forming behaviour. In particular, the combination of the average grain size with the claimed alloying elements of the aluminium alloy of the aluminium alloy strip means that degrees of formability can be achieved allowing the production of large-area design, deep-drawn sheet aluminium products with sufficient strength. In particular it has been found that the use of a continuous furnace rather than the normal coil annealing performed in a chamber furnace provides a further significant increase in formability.
According to a first configuration of the aluminium alloy strip, the aluminium alloy also has one or more of the following restrictions to the contents of alloying elements:
0.03 wt.% Si 5_ 0.10 wt.%, Cu 5_ 0.1% preferably 0.04% Cu 0.08%, Cr 0.05 wt.%, Zn 0.05 wt.%,
-5-0.01 wt.% Ti 5_ 0.05 wt.%
Restricting the alloying content for copper to a maximum of 0.1 wt.% leads to an improvement in the corrosion resistance of the aluminium alloy strip. A Cu content of 0.04 wt.% to 0.08 wt.%
ensures that the copper contributes to an increase in strength, but that nevertheless the corrosion resistance is not reduced too sharply. Silicon, chromium, zinc and titanium contents higher than the values indicated lead to a worsening of the formability of the aluminium alloy. The amount of silicon present in the alloy of 0.03 to 0.1 wt.%, in combination with the iron and manganese components in the stated quantities, in particular leads to relatively evenly distributed, compact particles of the quaternary a-Al(Fe,Mn)Si-phase, increasing the strength of the aluminium alloy, without negatively influencing other properties such as the formability or corrosion behaviour.
Titanium is normally added during continuous casting of the aluminium alloy as a grain refiner, for example in the form of titanium boride wire or rods. Therefore in a further embodiment the aluminium alloy has a Ti content of at least 0.01 wt.%.
A further improvement in the corrosion behaviour and the formability of the aluminium alloy strip can be achieved by the aluminium alloy also having one or more of the following restrictions to the contents of alloying elements:
Cr 0.02 wt.%, Zn 5. 0.02 wt.%
It has been found that chromium in contents below the contamination threshold of 0.05 wt.%
significantly influences the formability of the aluminium alloy strip and therefore should be contained in the smallest possible proportions in the aluminium alloy of the aluminium alloy strip according to the invention. The zinc content is set at below the contamination threshold of 0.05 wt.%, in order not to impair the general corrosion behaviour of the aluminium alloy strip.
It has furthermore been found that iron within the values permitted according to the AA5182-type aluminium alloy in conjunction with silicon and manganese contents as described above has
Restricting the alloying content for copper to a maximum of 0.1 wt.% leads to an improvement in the corrosion resistance of the aluminium alloy strip. A Cu content of 0.04 wt.% to 0.08 wt.%
ensures that the copper contributes to an increase in strength, but that nevertheless the corrosion resistance is not reduced too sharply. Silicon, chromium, zinc and titanium contents higher than the values indicated lead to a worsening of the formability of the aluminium alloy. The amount of silicon present in the alloy of 0.03 to 0.1 wt.%, in combination with the iron and manganese components in the stated quantities, in particular leads to relatively evenly distributed, compact particles of the quaternary a-Al(Fe,Mn)Si-phase, increasing the strength of the aluminium alloy, without negatively influencing other properties such as the formability or corrosion behaviour.
Titanium is normally added during continuous casting of the aluminium alloy as a grain refiner, for example in the form of titanium boride wire or rods. Therefore in a further embodiment the aluminium alloy has a Ti content of at least 0.01 wt.%.
A further improvement in the corrosion behaviour and the formability of the aluminium alloy strip can be achieved by the aluminium alloy also having one or more of the following restrictions to the contents of alloying elements:
Cr 0.02 wt.%, Zn 5. 0.02 wt.%
It has been found that chromium in contents below the contamination threshold of 0.05 wt.%
significantly influences the formability of the aluminium alloy strip and therefore should be contained in the smallest possible proportions in the aluminium alloy of the aluminium alloy strip according to the invention. The zinc content is set at below the contamination threshold of 0.05 wt.%, in order not to impair the general corrosion behaviour of the aluminium alloy strip.
It has furthermore been found that iron within the values permitted according to the AA5182-type aluminium alloy in conjunction with silicon and manganese contents as described above has
- 6 -an effect on the formability. In combination with silicon and manganese, iron contributes to the thermal stability of the aluminium alloy strip, so that preferably the Fe-content of the aluminium alloy strip according to a next configuration is 0.1 wt.% to 0.25 wt.% or 0.10 wt.% to 0.20 wt.%.
The same also applies to the Mn content of a further configuration of the aluminium alloy strip, which should preferably be limited to 0.20 wt.% to 0.30 wt.%, in order to achieve optimum formability of the aluminium alloy strip.
An especially good compromise between the provision of high strength properties, good corrosion resistance to intercrystalline corrosion and improved forming properties can be achieved according to a further configuration of the aluminium alloy strip with an Mg content of 4.2 wt.% to 4.4 wt.%.
In order to provide the strength properties necessary for the areas of application, the aluminium alloy strip according to a next embodiment has a thickness of 0.5 mm to 4 mm.
The thickness is preferably 1 mm to 2.5 mm, since most of the areas of application of the aluminium alloy strip fall within this range.
Finally, in the automotive sector the aluminium alloy strip according to the invention allows areas of application wherein the altuninium alloy strip in the soft state has a yield point R0.2 of at least 110 MPa and a tensile strength R,,, of at least 255 M Pa. It has been found that aluminium alloy strips with such yield points and tensile strengths especially are particularly well-suited for use in the automotive sector.
According to a second teaching of the present invention the object shown above is achieved by a method for producing an aluminium alloy strip according to the embodiments described above, wherein the method comprises the following process steps:
- casting a rolling ingot preferably in the DC continuous casting process;
- homogenisation of the rolling ingot at 480 C to 550 C for at least 0.5 hours;
- hot rolling of the rolling ingot at a temperature of 280 C to 500 C;
The same also applies to the Mn content of a further configuration of the aluminium alloy strip, which should preferably be limited to 0.20 wt.% to 0.30 wt.%, in order to achieve optimum formability of the aluminium alloy strip.
An especially good compromise between the provision of high strength properties, good corrosion resistance to intercrystalline corrosion and improved forming properties can be achieved according to a further configuration of the aluminium alloy strip with an Mg content of 4.2 wt.% to 4.4 wt.%.
In order to provide the strength properties necessary for the areas of application, the aluminium alloy strip according to a next embodiment has a thickness of 0.5 mm to 4 mm.
The thickness is preferably 1 mm to 2.5 mm, since most of the areas of application of the aluminium alloy strip fall within this range.
Finally, in the automotive sector the aluminium alloy strip according to the invention allows areas of application wherein the altuninium alloy strip in the soft state has a yield point R0.2 of at least 110 MPa and a tensile strength R,,, of at least 255 M Pa. It has been found that aluminium alloy strips with such yield points and tensile strengths especially are particularly well-suited for use in the automotive sector.
According to a second teaching of the present invention the object shown above is achieved by a method for producing an aluminium alloy strip according to the embodiments described above, wherein the method comprises the following process steps:
- casting a rolling ingot preferably in the DC continuous casting process;
- homogenisation of the rolling ingot at 480 C to 550 C for at least 0.5 hours;
- hot rolling of the rolling ingot at a temperature of 280 C to 500 C;
-7-- cold rolling of the aluminium alloy strip to the final thickness with a degree of rolling of 40% to 70% or 50% to 60%; and - soft annealing of the finished rolled aluminium alloy strip at 300 C to 500 C in a continuous furnace.
It has been found that with the indicated parameters in conjunction with the stated aluminium alloying components an aluminium alloy strip with average grain sizes of 15 lam ¨ 30 lam can be produced, having sufficient resistance to intercrystalline corrosion, providing sufficient strength properties and also having very good forming properties, so that large-area, deep-drawn sheet metal parts can be produced. Homogenisation of the rolling ingot ensures a homogenous structure and a homogenous distribution of the alloying elements in the hot rolling ingots to be rolled. The hot rolling at temperatures of 280 C - 500 C allows recrystallization throughout during hot rolling, wherein the hot rolling typically is performed up to a thickness of 2.8 mm - 8 mm. The final cold-rolling step is restricted to a degree of rolling of 40% to 70% or 50% to 60%, in both cases in order to ensure recrystallization throughout the aluminium alloy strip during soft annealing. The higher the degree of rolling of the aluminium alloy strip, the lower the average grain sizes become, wherein it has been found that above a 70% degree of rolling in the final soft annealing an average grain size can result that is too low. At a degree of rolling below 40%
during soft annealing the average grain sizes are on the other hand too large, so that despite the resistance to intercrystalline corrosion increasing, the formability is nevertheless reduced. Soft annealing of the finish-rolled aluminium alloy strip takes place in a continuous furnace, which will normally have a heat-up rate of 1 - 10 C/second and so unlike a chamber furnace, in which an entire coil is heated, because of the rapid heating will have a marked effect on the later properties of the structure of the aluminium alloy strip. In particular, it has been possible to establish that during soft annealing in the continuous furnace an improved formability of the strip compared to variants annealed in the chamber furnace is achieved.
Alternatively, according to a further embodiment of the method, the aluminium alloy strip can also be produced with an intermediate annealing. According to this alternative variant after hot rolling alternatively the following process steps are performed:
It has been found that with the indicated parameters in conjunction with the stated aluminium alloying components an aluminium alloy strip with average grain sizes of 15 lam ¨ 30 lam can be produced, having sufficient resistance to intercrystalline corrosion, providing sufficient strength properties and also having very good forming properties, so that large-area, deep-drawn sheet metal parts can be produced. Homogenisation of the rolling ingot ensures a homogenous structure and a homogenous distribution of the alloying elements in the hot rolling ingots to be rolled. The hot rolling at temperatures of 280 C - 500 C allows recrystallization throughout during hot rolling, wherein the hot rolling typically is performed up to a thickness of 2.8 mm - 8 mm. The final cold-rolling step is restricted to a degree of rolling of 40% to 70% or 50% to 60%, in both cases in order to ensure recrystallization throughout the aluminium alloy strip during soft annealing. The higher the degree of rolling of the aluminium alloy strip, the lower the average grain sizes become, wherein it has been found that above a 70% degree of rolling in the final soft annealing an average grain size can result that is too low. At a degree of rolling below 40%
during soft annealing the average grain sizes are on the other hand too large, so that despite the resistance to intercrystalline corrosion increasing, the formability is nevertheless reduced. Soft annealing of the finish-rolled aluminium alloy strip takes place in a continuous furnace, which will normally have a heat-up rate of 1 - 10 C/second and so unlike a chamber furnace, in which an entire coil is heated, because of the rapid heating will have a marked effect on the later properties of the structure of the aluminium alloy strip. In particular, it has been possible to establish that during soft annealing in the continuous furnace an improved formability of the strip compared to variants annealed in the chamber furnace is achieved.
Alternatively, according to a further embodiment of the method, the aluminium alloy strip can also be produced with an intermediate annealing. According to this alternative variant after hot rolling alternatively the following process steps are performed:
-8--cold rolling of the hot-rolled aluminium alloy strip to an intermediate thickness which is determined in such a way that the final degree of cold rolling to the final thickness is 40%
to 70% or 50% to 60%;
- intermediate annealing of the aluminium alloy strip at 300 C to 500 C;
- cold rolling of the aluminium alloy strip to the final thickness with a degree of rolling of 40% to 70% or 50% to 60%;
- soft annealing of the finish-rolled aluminium alloy strip at 300 C to 500 C in a continuous furnace.
The intermediate annealing of the aluminium alloy strip can take place both in the chamber furnace and in the continuous furnace. An effect on formability could not be determined. The decisive factors here are the degree of rolling achieved in cold rolling to the final thickness and if the soft annealing of the strip takes place in the continuous furnace. This determines the formability and corrosion resistance in conjunction with the alloying composition, irrespective of the type of intermediate annealing.
In order to prevent a further change in the microstructural state in the coiled condition following soft annealing, the aluminium alloy strip according to a further configuration of the method is cooled after soft annealing to a maximum temperature of 100 C, preferably a maximum of 70 C
and then coiled.
As already stated above, the intermediate annealing can be carried out in a further configuration of the method in a batch furnace or in a continuous furnace.
If the aluminium alloy strip is cold-rolled to a final thickness of 0.5 mm - 4 mm, preferably to a final thickness of 1 mm ¨ 2.5 mm, this provides the typical areas of application, in particular automotive construction, with sheet metal with very good formability, and which can be deep=
-drawn with large surface areas and at the same time provide high strength properties together with sufficient corrosion resistance to intercrystalline corrosion.
to 70% or 50% to 60%;
- intermediate annealing of the aluminium alloy strip at 300 C to 500 C;
- cold rolling of the aluminium alloy strip to the final thickness with a degree of rolling of 40% to 70% or 50% to 60%;
- soft annealing of the finish-rolled aluminium alloy strip at 300 C to 500 C in a continuous furnace.
The intermediate annealing of the aluminium alloy strip can take place both in the chamber furnace and in the continuous furnace. An effect on formability could not be determined. The decisive factors here are the degree of rolling achieved in cold rolling to the final thickness and if the soft annealing of the strip takes place in the continuous furnace. This determines the formability and corrosion resistance in conjunction with the alloying composition, irrespective of the type of intermediate annealing.
In order to prevent a further change in the microstructural state in the coiled condition following soft annealing, the aluminium alloy strip according to a further configuration of the method is cooled after soft annealing to a maximum temperature of 100 C, preferably a maximum of 70 C
and then coiled.
As already stated above, the intermediate annealing can be carried out in a further configuration of the method in a batch furnace or in a continuous furnace.
If the aluminium alloy strip is cold-rolled to a final thickness of 0.5 mm - 4 mm, preferably to a final thickness of 1 mm ¨ 2.5 mm, this provides the typical areas of application, in particular automotive construction, with sheet metal with very good formability, and which can be deep=
-drawn with large surface areas and at the same time provide high strength properties together with sufficient corrosion resistance to intercrystalline corrosion.
- 9 -The soft annealing is preferably performed in the continuous furnace at a metal temperature of 350 C - 550 C, preferably at 400 C - 450 C for 10 seconds to 5 minutes, preferably 20 seconds to 1 minute. This allows the cold rolled strip to recrystallize sufficiently thoroughly and the corresponding properties with regard to the very good formability and the average grain size to be achieved reliably and economically.
Finally, the object indicated above is achieved by a component for a motor vehicle, composed of the aluminium alloy strip according to the invention. The components are characterised in that, as already stated, they can be deep-drawn with a large surface area and therefore for example large-area components for automotive construction can be provided.
Furthermore, because of the strength properties provided these also have the necessary stiffness and the corrosion resistance required for use in automotive construction.
It is conceivable, for example, for the component according to a further configuration to be a motor vehicle body part or body accessory, which apart from being subject to high strength requirements is also heat-stressed. Preferably, the body-in-white parts such as an internal door part or an internal tailgate part, are made from the aluminium alloy strip according to the invention.
The invention is explained in more detail below with the help of the drawing.
The drawing shows as follows:
Fig. 1 a schematic flow diagram of an embodiment of the production method of the aluminium alloy strip;
Fig. 2a a top view of the specimen geometry for the plane-strain cupping test according to DIN EN ISO 12004;
Fig. 2b a side-view of the schematic test set-up for the plane-strain cupping test according to DIN EN ISO 12004;
-Fig. 3 a sectional view of the test setup for the SZ32 stretch drawing measurements in the Erichsen cupping test according to DIN EN ISO 20482; and Fig. 4 a typical embodiment of a large-area, deep-drawn sheet metal part according to the present invention.
Fig. 1 shows the sequence of embodiments for the production of aluminium strips. The flow diagram of Fig. 1 is a schematic representation of the various process steps of the production process of the aluminium alloy strip according to the invention.
In step 1, a rolling ingot of an AlMg aluminium alloy with the following alloying elements is cast, for example in DC continuous casting:
Si 0.2 wt.%, Fe 0.35 wt.%, Cu 0.15 wt.%, 0.2 wt.% Mn 0.35 wt.%
4.1 wt.% Mg 4.5 wt.%, Cr 0.1 wt.%, Zn 0.25 wt.%, Ti 0.1 wt.%, the remainder being Al and inevitable impurities, amounting to a maximum of 0.05 wt.%
individually and a maximum of 0.15 wt.% in total.
Then the rolling ingot in process step 2 undergoes homogenisation, which can be performed in one or more stages. During homogenisation, temperatures of the rolling ingot of 480 to 550 C
are reached for at least 0.5 hours. In process step 3 the rolling ingot is then hot rolled, wherein typically temperatures of 280 C to 500 C are reached. The final thicknesses of the hot-rolled strip are for example 2.8 to 8 mm. The hot-rolled strip thickness can be selected such that after hot rolling only a single cold rolling step 4 takes place, in which the hot-rolled strip, with a degree of rolling of 40% to 70%, preferably 50% to 60%, has its thickness reduced to the final thickness.
Then the aluminium alloy strip that has been cold-rolled to its final thickness undergoes soft annealing. According to the invention the soft annealing is performed in a continuous furnace. In the embodiments shown in Table 1, the second route was applied with an intermediate annealing.
For this, the hot-rolled strip after hot rolling according to process step 3 is passed for cold rolling 4a, in which the aluminium alloy strip is cold rolled to an intermediate thickness, which is determined in such a way that the final degree of cold rolling to the final thickness is 40% to 70% or 50% to 60%. In a subsequent intermediate annealing the aluminium alloy strip preferably recrystallizes throughout. The intermediate annealing was carried out in the embodiments either in the continuous furnace at 400 C to 450 C or in the chamber furnace at 330 C
to 380 C.
The intermediate annealing is shown in Fig. 1 by process step 4b. In process step 4c according to Fig. 1 the intermediately-annealed aluminium alloy strip is finally passed for cold rolling to the final thickness, wherein the degree of rolling in process step 4c is between 40% and 70%, preferably between 50% and 60%. Then the aluminium alloy strip is again converted to the soft state by soft annealing in step 5, wherein according to the invention the soft annealing is carried out in the continuous furnace at 400 C to 450 C. The annealings of the comparative examples in table 4 were carried out in the chamber furnace (KO) at 330 C to 380 C. During the various trials, apart from the different aluminium alloys various degrees of rolling after the intermediate annealing were set. The values for the degree of rolling after the intermediate annealing are likewise shown in Tables 1 and 4. The average grain size of the soft-annealed aluminium alloy strip was also measured. To this end, longitudinal sections were anodised according to the Barker method and then measured under the microscope according to ASTM E1382 and the average grain size determined from the average grain diameter.
The aluminium alloy strips manufactured in this way had their mechanical characteristics determined, in particular the yield point R0.2, the tensile strength Rm, the uniform elongation Ag and the elongation at rupture Agomm, Tables 2, 5. Apart from the mechanical characteristics of the aluminium alloy strips measured according to EN 1 0002- 1 or ISO 6892 in addition the average grain sizes according to ASTM E1382 in p.m are given. Furthermore, the corrosion resistance to intercrystalline corrosion in accordance with ASTM G67 was measured, and in fact without additional heat treatment in the initial state (at Oh). In order to simulate use in a motor vehicle, the aluminium alloy strips, prior to the corrosion test, furthermore underwent various heat treatments. A first heat treatment consisted of storage of the aluminium strips for 20 minutes at 185 C, in order to model the CDP cycle.
In a further series of measurements the aluminium alloy strips were also stored for 200 hours or 500 hours at 80 C and then underwent the corrosion test. Since the forming of aluminium alloy strips or sheets can also affect the corrosion resistance, the aluminium alloy strips were stretched in a further trial by approximately 15%, and underwent heat treatment or storage at raised temperature and then a test for intercrystalline corrosion according to ASTM
G67, during which the mass loss was measured.
Table 1 gives the alloying contents of a total of four different aluminium alloys, which fall within the specification of the AA5182-type aluminium alloy. The reference alloy is constituted by the material used to date and is shown in comparison to variants 1, 2 and 3. Table 1 also contains details of the type of final annealing, the final degree of rolling and the measured average grain size (grain size diameter) in p.m. Variants 1 and 2 differ here merely in terms of final degree of rolling, which leads to the formation of a different grain size. Thus variant 2 differs from variant I irrespective of the almost identical alloying elements essentially in terms of the final degree of rolling of 57% at identical continuous furnace conditions. The result was that variant 2 had an average grain size of 18 p.m compared to 33 [tm for variant I. The strips in Table 1 were heated in the continuous furnace for 20 seconds to I minute to a temperature of 400 C to 450 C, then cooled and coiled at less than 100 C. The specimens taken were then, as indicated in Table 2, measured according to the corresponding DIN EN ISO
standards.
It is clear from Table 2 that variant 1 in terms of the yield point does not reliably reach the value of 110 MPa and in the diagonal measurement, identified by the D symbol, has a value of less than 110 MPa. The measurement in the direction of rolling L and transversally to the direction of rolling Q showed, however, that variant 1 actually reached a yield point R0.2 of 110 MPa. The reference and variants 2 and 3 were significantly above this lower limit for the yield point. The embodiment according to the invention in variant 2 reliably achieved the yield point value of 110 M Pa in all tensile directions. It is clear to see that variant 3 with the highest Mg content of 4.95 wt.% achieves the highest yield point and tensile strength figures. It can also be seen that the different degree of rolling between variants 1 and 2 not only markedly influences the grain size, but in particular raises the yield point to a value of significantly higher than 110 MPa.
In particular the alloy according to the invention in variant 2 has a lower anisotropy compared to the reference, reflected in lower values of the planar anisotropy Ar. Here, the planar anisotropy Ar is defined as 1/2*(11 +4)-2 rD), wherein 4,, 4) and rD correspond to the r-values in the longitudinal, traversal and/or diagonal direction. Here, the average r-value 7, calculated from 1/4*(4 +4)+2rD), does not differ significantly from that of the reference material.
Table 3 gives the measured values recorded in relation to the resistance to intercrystalline corrosion. It can be seen that variant 2 according to the invention in terms of the measured values of the reference, in particular in respect of the long-time stressing, has comparable values both in the stretched state and in the unstretched state. Here variant 2 and the reference are almost identical. Variant 3, which despite the having the highest yield point values and tensile strength values, nevertheless in the corrosion test demonstrated that an excessive Mg content results in an excessive mass loss, in particular in the long-time tests, which apart from a short temperature cycle of 20 minutes at 185 C also include long-time stressing of 200 hours at 80 C.
With regard to the measured values in Table 3 regarding the formability it can be seen that in particular variant 2 was superior in terms of the stretch forming properties in the SZ32 cupping test and in the plane-strain cupping test to the reference alloy. The clear improvement in forming behaviour of the aluminium alloy strip according to variant 2 compared to the reference aluminium alloy strip shows that even with a reduced Mg content comparable yield point values and tensile strength vales could be achieved with the reference alloy, without major losses in resistance to intercrystalline corrosion. This was demonstrated in particular by the mass loss measurement performed according to ASTM G67 in the NAML test. Significantly, with variant 2 an improvement in the deep drawing behaviour in the Erichsen cupping test by 7% and in the plane-strain cupping tests by approximately 10% was found, demonstrating the additional forming potential of the aluminium alloy strip according to the invention.
This additional forming potential can be used to produce deep-drawn, large-area sheet metal parts, for example internal door parts of a motor car.
A brief explanation of the test setup for the "SZ32 cupping" test according to DIN EN ISO
20482 and the plane-strain cupping test with Nakajima geometry according to DIN EN ISO
12004 is provided below.
Fig. 2a shows the geometry of test piece 201. From a circular sheet metal cut-out the tapered test piece 201 is cut such that the web 204 has a width of 100 mm and the radii 202 at the waisted parts are 20 mm. Dimension 203, which is 100 mm, represents the diameter of the punch. Fig. 2b shows the test piece 201 clamped between two holders 205, 206. The test piece 201, which was placed on a mount 208 and via the holders 205, 206 pushed against the support, is pulled with a punch 207, having a semi-circular tip with a radius of 100 mm, in the direction of the arrow. The holders also have entry radii R of 5 or 10 mm on their side facing the mount 208. The force with which the cupping test is performed is measured during the forming and a sudden drop in load, signalling the formation of a crack, leads to the measurement of the corresponding punching depth.
The "SZ32 cupping" test according to Erichsen has a similar setup, but no waisted test pieces are used, however. Ilere, a test piece 309 is simply held between a holder 310 and a support 311 and drawn with a punch 312 until likewise a drop is measured in the load of the drawing force. Then, again, the corresponding position of the punch is measured. The opening of the dies in Fig. 3 was 35.4 mm and the punch diameter 32 mm, meaning that the punch radius was 16 mm.
A Teflon deep-drawing film was also used to reduce friction in the SZ32 deep-drawing test.
In Tables 4 and 5, further embodiments and comparative examples were created and measured according to their mechanical characteristics and their resistance to intercrystalline corrosion. It can be seen that the combination of using the continuous furnace and a specifically selected grain size of 15 pm - 30 p.m, preferably of 151.tm - 25 p.m results in a good compromise between corrosion resistance and mechanical measured values. Thus, for example, the embodiments according to the invention Nos. 3, 4, 7 and 11 have a satisfactory resistance to intercrystalline corrosion and also exhibit the mechanical measured values R0.2 and R,õ
necessary for use in the automotive sector, so that these are ideal for the provision of large-area, deep-drawn components.
Fig. 4 shows as an example a corresponding body-in-white part in the form of an interior part of a door, which by using the aluminium alloy strip of the present invention can be produced from a single deep-drawn sheet. Here, the sheet thickness is preferably 1.0 ¨ 2.5 mm.
Furthermore, other parts of a motor vehicle are conceivable in sheet metal shell construction, such as the interior parts of tailgates, bonnets, and components in the vehicle structure, which are subject to stringent requirements in terms of formability and intercrystalline corrosion.
'I
Table 1 Material Si Fe Cu Mn Mg Cr Zn Ti Impurities Final Final degree of Grain lwt.%1 annealing rolling(cold sizelu rolling) ml min 0.20 4.0 Individually max.
. AA 5182 max. 0.20 0.35 0.15 0.50 5.0 0.10 0.25 0.10 0.05 in total max.
0.15 , Reference 0.07 0.24 0.036 0.3 4.570.005 0.007 0.016 0.05 0.15 BDLO
Var. 1 0.06 0.16 0.004 0.27 4.37 0.008 0.002 0.013 0.05 0.15 BDLO
Var. 2 0.06 0.16 0.004 0.27 4.38 0.008 0.003 0.013 0.05 0.15 BDLO
Var. 3 0.05 0.17 0.023 0.26 4.95 0.008 0.003- 0.026 0.05 0.15 BDLO
Table 2 Test piece Pos. Rol Rm Ag Ag Ason,õ,A80,,m(Hand Z- n-value r- Ar F
(elong) ) value value _ N/mm N/mm % % % % %
Ref. L 137 284 21.3 20.7 24.5 25.2 69 0.316 0.827. 0.197 0.754 - T 133 276 22.i 21.4 25.2 25.8 72 0.306 0.704 D 133 277 21.9 21.6 25.5 26.3 71 0.305 0.779 Var.1 L 110 262 21.2 21.9 k 25.9 26.4 71 0.335 0.668 - 0.779 0.363 T 107 256 24.7 23.0 27.7 28.7 72 0.338 0.870 D 1 1 1 259 22.0 21.2 24.6 25.7 65 0.332 0.708 Var.2 L 128 266 23.2 22.7 26.8 27.7 67 0.332 0.724 0.035 0.693 T 127 261 23.1 22.2 26.2 27.0 67 0.332 0.685 D 128 262 23.9 22.5 26.5 27.6 66 0.333 0.681 Var.3 L 141 29024.1 23.5 28.4 29.1 70 0.335 0.697 -0.12 0.710 T 140 286 22.6 - 23.4 27.6 27.8 68 0.336 0.740 _ .
- D 141 286 22.6 23.3 27.1 27.7 65 0.335 0.663 DIN EN ISO 6892-1:2009 DIN EN ISO
DIN EN ISO 10113:2009 10275:2009 Table 3 IK-mass losses Formability SZ32 cupping Plane-strain Variant Not 20 min. 20 min 17h 15% 15%stretched cupping thermall 185 C 185 C plus 130 C stretched 20 20 min. [mm]
y treated 200 h 80 C min. 185 C 185 C plus [mm]
200h 80 C
Limit 2.0 4.0 35.0 50.0 15.0 45.0 Reference 1.2 2.1 29.8 48.8 10.4 42.1 14.2 27.9 Var. 1.2 1.7 10.4 21.3 4.4 12.9 14.5 30.3 1(comp.) Var. 2 1.2 2.4 33.7 42.2 13.5 40.1 14.6 30.7 (inv.) 1.3 5.3 41.7 55.0 30.4 53.5 14.6 31.6 Var. 3 (comp.) ]
, Table 4 Alloy Degree Final Gra No of anneali in Si Fe Cu Mn Mg Cr Zn Ti size rolling ng 1Ftnal 1%1 1 III 46 KO 16 0.0 0.2 0.04 0.3 4.5 0.00 0.00 0.01 3 II 57 BOLO 18 0.0 0.1 0.00 0.2 4.3 0.00 0.00 0.01 _ 4 I 45 BOLO 18 0.0 0.1 0.00 0.2 4.1 0.00 0.00 0.02 6 I 45 KO 21 0.0 0.1 0.00 0.2 4.1 0.00 0.00 0.02 7 III 30 BOLO 22 0.0 0.2 0.04 0.3 4.5 0.00 0.00 0.01 7 4 0 0 o 5 1 III 25 BOLO 27 0.0 0.2 0.04 0.3 4.5 0.00 0.00 0.01 1 7 4 0 0 o 5 1 I 32 BOLO 29 0.0 0.1 0.00 0.2 4.1 0.00 0.00 0.02 15 III 30 KO 30 0.0 0.2 0.04 0.3 4.5 0.00 0.00 0.01 -16 I 25 BOLO 31 0.0 0.1 0.00 0.2 4.1 0.00 0.00 0.02 1 II _ 21 BOLO 33 0.0- 0.1 0.00 0.2 4.3 0.00 0.00 0.01 -20 I 20 BOLO 34 0.0 0.1 0.00 0.2 4.1 0.00 0.00 0.02 '1 Table 5 IK-mass loss, IK-mass loss, 15% Mechanical characteristics, soft unstretched** stretched ** state _ 20 Min. 20Min. 20 Min.
No Start 20 min. 185 C
185 C 20 Min. 185 C Result (Oh) 185 ( 185 C R02 Rm Ag A)on,.
+ 200 h + 500 h +200h =
1 III 15.4 ' 16.6 25.7 26.9 18.8 33.6 135 279 20.7 25.2 Comparison 3 11 1.2 2.4 33.7 36.7 13.5 40.1 128 262 23.9 26.5 Invention 4 1 1.3 ' 1.9 17.8 22.2 1.6 20.1 -117 258 22.8 25.3 Invention 6 1 8.2 10.8 18.6 22.1 9.6 20.7 106 250 23.8 26.7 Comparison 7 III 1.1 1.7 18.0 24.5 3.3 25.1 119 276 20.3 24.9 Invention 11 III 1.1 1.6 14.3 17.7 2.8 19.8 116 275 20.2 24.4 Invention 13 1 1.1 1.2 13.3 16.7 2.1 17.4 104 251 22.2 24.8 Comparison _ 15 III 2.8 3.0 7.9 10.9 6.4 18.0 125 281 19.5 23.6 Comparison 16 l' 1.1 1.3 10.8 13.1 1.9 14.2 103 252 21.6 26.1 Comparison 18 11 1.2 1.7 10.4 12.5 4.4 12.9 109 259 22.0 24.6 Comparison 20 1 1.1 1.2 8.3 11.1 1.7 12.4 101 251 20.8 25.1 Comparison ,
Finally, the object indicated above is achieved by a component for a motor vehicle, composed of the aluminium alloy strip according to the invention. The components are characterised in that, as already stated, they can be deep-drawn with a large surface area and therefore for example large-area components for automotive construction can be provided.
Furthermore, because of the strength properties provided these also have the necessary stiffness and the corrosion resistance required for use in automotive construction.
It is conceivable, for example, for the component according to a further configuration to be a motor vehicle body part or body accessory, which apart from being subject to high strength requirements is also heat-stressed. Preferably, the body-in-white parts such as an internal door part or an internal tailgate part, are made from the aluminium alloy strip according to the invention.
The invention is explained in more detail below with the help of the drawing.
The drawing shows as follows:
Fig. 1 a schematic flow diagram of an embodiment of the production method of the aluminium alloy strip;
Fig. 2a a top view of the specimen geometry for the plane-strain cupping test according to DIN EN ISO 12004;
Fig. 2b a side-view of the schematic test set-up for the plane-strain cupping test according to DIN EN ISO 12004;
-Fig. 3 a sectional view of the test setup for the SZ32 stretch drawing measurements in the Erichsen cupping test according to DIN EN ISO 20482; and Fig. 4 a typical embodiment of a large-area, deep-drawn sheet metal part according to the present invention.
Fig. 1 shows the sequence of embodiments for the production of aluminium strips. The flow diagram of Fig. 1 is a schematic representation of the various process steps of the production process of the aluminium alloy strip according to the invention.
In step 1, a rolling ingot of an AlMg aluminium alloy with the following alloying elements is cast, for example in DC continuous casting:
Si 0.2 wt.%, Fe 0.35 wt.%, Cu 0.15 wt.%, 0.2 wt.% Mn 0.35 wt.%
4.1 wt.% Mg 4.5 wt.%, Cr 0.1 wt.%, Zn 0.25 wt.%, Ti 0.1 wt.%, the remainder being Al and inevitable impurities, amounting to a maximum of 0.05 wt.%
individually and a maximum of 0.15 wt.% in total.
Then the rolling ingot in process step 2 undergoes homogenisation, which can be performed in one or more stages. During homogenisation, temperatures of the rolling ingot of 480 to 550 C
are reached for at least 0.5 hours. In process step 3 the rolling ingot is then hot rolled, wherein typically temperatures of 280 C to 500 C are reached. The final thicknesses of the hot-rolled strip are for example 2.8 to 8 mm. The hot-rolled strip thickness can be selected such that after hot rolling only a single cold rolling step 4 takes place, in which the hot-rolled strip, with a degree of rolling of 40% to 70%, preferably 50% to 60%, has its thickness reduced to the final thickness.
Then the aluminium alloy strip that has been cold-rolled to its final thickness undergoes soft annealing. According to the invention the soft annealing is performed in a continuous furnace. In the embodiments shown in Table 1, the second route was applied with an intermediate annealing.
For this, the hot-rolled strip after hot rolling according to process step 3 is passed for cold rolling 4a, in which the aluminium alloy strip is cold rolled to an intermediate thickness, which is determined in such a way that the final degree of cold rolling to the final thickness is 40% to 70% or 50% to 60%. In a subsequent intermediate annealing the aluminium alloy strip preferably recrystallizes throughout. The intermediate annealing was carried out in the embodiments either in the continuous furnace at 400 C to 450 C or in the chamber furnace at 330 C
to 380 C.
The intermediate annealing is shown in Fig. 1 by process step 4b. In process step 4c according to Fig. 1 the intermediately-annealed aluminium alloy strip is finally passed for cold rolling to the final thickness, wherein the degree of rolling in process step 4c is between 40% and 70%, preferably between 50% and 60%. Then the aluminium alloy strip is again converted to the soft state by soft annealing in step 5, wherein according to the invention the soft annealing is carried out in the continuous furnace at 400 C to 450 C. The annealings of the comparative examples in table 4 were carried out in the chamber furnace (KO) at 330 C to 380 C. During the various trials, apart from the different aluminium alloys various degrees of rolling after the intermediate annealing were set. The values for the degree of rolling after the intermediate annealing are likewise shown in Tables 1 and 4. The average grain size of the soft-annealed aluminium alloy strip was also measured. To this end, longitudinal sections were anodised according to the Barker method and then measured under the microscope according to ASTM E1382 and the average grain size determined from the average grain diameter.
The aluminium alloy strips manufactured in this way had their mechanical characteristics determined, in particular the yield point R0.2, the tensile strength Rm, the uniform elongation Ag and the elongation at rupture Agomm, Tables 2, 5. Apart from the mechanical characteristics of the aluminium alloy strips measured according to EN 1 0002- 1 or ISO 6892 in addition the average grain sizes according to ASTM E1382 in p.m are given. Furthermore, the corrosion resistance to intercrystalline corrosion in accordance with ASTM G67 was measured, and in fact without additional heat treatment in the initial state (at Oh). In order to simulate use in a motor vehicle, the aluminium alloy strips, prior to the corrosion test, furthermore underwent various heat treatments. A first heat treatment consisted of storage of the aluminium strips for 20 minutes at 185 C, in order to model the CDP cycle.
In a further series of measurements the aluminium alloy strips were also stored for 200 hours or 500 hours at 80 C and then underwent the corrosion test. Since the forming of aluminium alloy strips or sheets can also affect the corrosion resistance, the aluminium alloy strips were stretched in a further trial by approximately 15%, and underwent heat treatment or storage at raised temperature and then a test for intercrystalline corrosion according to ASTM
G67, during which the mass loss was measured.
Table 1 gives the alloying contents of a total of four different aluminium alloys, which fall within the specification of the AA5182-type aluminium alloy. The reference alloy is constituted by the material used to date and is shown in comparison to variants 1, 2 and 3. Table 1 also contains details of the type of final annealing, the final degree of rolling and the measured average grain size (grain size diameter) in p.m. Variants 1 and 2 differ here merely in terms of final degree of rolling, which leads to the formation of a different grain size. Thus variant 2 differs from variant I irrespective of the almost identical alloying elements essentially in terms of the final degree of rolling of 57% at identical continuous furnace conditions. The result was that variant 2 had an average grain size of 18 p.m compared to 33 [tm for variant I. The strips in Table 1 were heated in the continuous furnace for 20 seconds to I minute to a temperature of 400 C to 450 C, then cooled and coiled at less than 100 C. The specimens taken were then, as indicated in Table 2, measured according to the corresponding DIN EN ISO
standards.
It is clear from Table 2 that variant 1 in terms of the yield point does not reliably reach the value of 110 MPa and in the diagonal measurement, identified by the D symbol, has a value of less than 110 MPa. The measurement in the direction of rolling L and transversally to the direction of rolling Q showed, however, that variant 1 actually reached a yield point R0.2 of 110 MPa. The reference and variants 2 and 3 were significantly above this lower limit for the yield point. The embodiment according to the invention in variant 2 reliably achieved the yield point value of 110 M Pa in all tensile directions. It is clear to see that variant 3 with the highest Mg content of 4.95 wt.% achieves the highest yield point and tensile strength figures. It can also be seen that the different degree of rolling between variants 1 and 2 not only markedly influences the grain size, but in particular raises the yield point to a value of significantly higher than 110 MPa.
In particular the alloy according to the invention in variant 2 has a lower anisotropy compared to the reference, reflected in lower values of the planar anisotropy Ar. Here, the planar anisotropy Ar is defined as 1/2*(11 +4)-2 rD), wherein 4,, 4) and rD correspond to the r-values in the longitudinal, traversal and/or diagonal direction. Here, the average r-value 7, calculated from 1/4*(4 +4)+2rD), does not differ significantly from that of the reference material.
Table 3 gives the measured values recorded in relation to the resistance to intercrystalline corrosion. It can be seen that variant 2 according to the invention in terms of the measured values of the reference, in particular in respect of the long-time stressing, has comparable values both in the stretched state and in the unstretched state. Here variant 2 and the reference are almost identical. Variant 3, which despite the having the highest yield point values and tensile strength values, nevertheless in the corrosion test demonstrated that an excessive Mg content results in an excessive mass loss, in particular in the long-time tests, which apart from a short temperature cycle of 20 minutes at 185 C also include long-time stressing of 200 hours at 80 C.
With regard to the measured values in Table 3 regarding the formability it can be seen that in particular variant 2 was superior in terms of the stretch forming properties in the SZ32 cupping test and in the plane-strain cupping test to the reference alloy. The clear improvement in forming behaviour of the aluminium alloy strip according to variant 2 compared to the reference aluminium alloy strip shows that even with a reduced Mg content comparable yield point values and tensile strength vales could be achieved with the reference alloy, without major losses in resistance to intercrystalline corrosion. This was demonstrated in particular by the mass loss measurement performed according to ASTM G67 in the NAML test. Significantly, with variant 2 an improvement in the deep drawing behaviour in the Erichsen cupping test by 7% and in the plane-strain cupping tests by approximately 10% was found, demonstrating the additional forming potential of the aluminium alloy strip according to the invention.
This additional forming potential can be used to produce deep-drawn, large-area sheet metal parts, for example internal door parts of a motor car.
A brief explanation of the test setup for the "SZ32 cupping" test according to DIN EN ISO
20482 and the plane-strain cupping test with Nakajima geometry according to DIN EN ISO
12004 is provided below.
Fig. 2a shows the geometry of test piece 201. From a circular sheet metal cut-out the tapered test piece 201 is cut such that the web 204 has a width of 100 mm and the radii 202 at the waisted parts are 20 mm. Dimension 203, which is 100 mm, represents the diameter of the punch. Fig. 2b shows the test piece 201 clamped between two holders 205, 206. The test piece 201, which was placed on a mount 208 and via the holders 205, 206 pushed against the support, is pulled with a punch 207, having a semi-circular tip with a radius of 100 mm, in the direction of the arrow. The holders also have entry radii R of 5 or 10 mm on their side facing the mount 208. The force with which the cupping test is performed is measured during the forming and a sudden drop in load, signalling the formation of a crack, leads to the measurement of the corresponding punching depth.
The "SZ32 cupping" test according to Erichsen has a similar setup, but no waisted test pieces are used, however. Ilere, a test piece 309 is simply held between a holder 310 and a support 311 and drawn with a punch 312 until likewise a drop is measured in the load of the drawing force. Then, again, the corresponding position of the punch is measured. The opening of the dies in Fig. 3 was 35.4 mm and the punch diameter 32 mm, meaning that the punch radius was 16 mm.
A Teflon deep-drawing film was also used to reduce friction in the SZ32 deep-drawing test.
In Tables 4 and 5, further embodiments and comparative examples were created and measured according to their mechanical characteristics and their resistance to intercrystalline corrosion. It can be seen that the combination of using the continuous furnace and a specifically selected grain size of 15 pm - 30 p.m, preferably of 151.tm - 25 p.m results in a good compromise between corrosion resistance and mechanical measured values. Thus, for example, the embodiments according to the invention Nos. 3, 4, 7 and 11 have a satisfactory resistance to intercrystalline corrosion and also exhibit the mechanical measured values R0.2 and R,õ
necessary for use in the automotive sector, so that these are ideal for the provision of large-area, deep-drawn components.
Fig. 4 shows as an example a corresponding body-in-white part in the form of an interior part of a door, which by using the aluminium alloy strip of the present invention can be produced from a single deep-drawn sheet. Here, the sheet thickness is preferably 1.0 ¨ 2.5 mm.
Furthermore, other parts of a motor vehicle are conceivable in sheet metal shell construction, such as the interior parts of tailgates, bonnets, and components in the vehicle structure, which are subject to stringent requirements in terms of formability and intercrystalline corrosion.
'I
Table 1 Material Si Fe Cu Mn Mg Cr Zn Ti Impurities Final Final degree of Grain lwt.%1 annealing rolling(cold sizelu rolling) ml min 0.20 4.0 Individually max.
. AA 5182 max. 0.20 0.35 0.15 0.50 5.0 0.10 0.25 0.10 0.05 in total max.
0.15 , Reference 0.07 0.24 0.036 0.3 4.570.005 0.007 0.016 0.05 0.15 BDLO
Var. 1 0.06 0.16 0.004 0.27 4.37 0.008 0.002 0.013 0.05 0.15 BDLO
Var. 2 0.06 0.16 0.004 0.27 4.38 0.008 0.003 0.013 0.05 0.15 BDLO
Var. 3 0.05 0.17 0.023 0.26 4.95 0.008 0.003- 0.026 0.05 0.15 BDLO
Table 2 Test piece Pos. Rol Rm Ag Ag Ason,õ,A80,,m(Hand Z- n-value r- Ar F
(elong) ) value value _ N/mm N/mm % % % % %
Ref. L 137 284 21.3 20.7 24.5 25.2 69 0.316 0.827. 0.197 0.754 - T 133 276 22.i 21.4 25.2 25.8 72 0.306 0.704 D 133 277 21.9 21.6 25.5 26.3 71 0.305 0.779 Var.1 L 110 262 21.2 21.9 k 25.9 26.4 71 0.335 0.668 - 0.779 0.363 T 107 256 24.7 23.0 27.7 28.7 72 0.338 0.870 D 1 1 1 259 22.0 21.2 24.6 25.7 65 0.332 0.708 Var.2 L 128 266 23.2 22.7 26.8 27.7 67 0.332 0.724 0.035 0.693 T 127 261 23.1 22.2 26.2 27.0 67 0.332 0.685 D 128 262 23.9 22.5 26.5 27.6 66 0.333 0.681 Var.3 L 141 29024.1 23.5 28.4 29.1 70 0.335 0.697 -0.12 0.710 T 140 286 22.6 - 23.4 27.6 27.8 68 0.336 0.740 _ .
- D 141 286 22.6 23.3 27.1 27.7 65 0.335 0.663 DIN EN ISO 6892-1:2009 DIN EN ISO
DIN EN ISO 10113:2009 10275:2009 Table 3 IK-mass losses Formability SZ32 cupping Plane-strain Variant Not 20 min. 20 min 17h 15% 15%stretched cupping thermall 185 C 185 C plus 130 C stretched 20 20 min. [mm]
y treated 200 h 80 C min. 185 C 185 C plus [mm]
200h 80 C
Limit 2.0 4.0 35.0 50.0 15.0 45.0 Reference 1.2 2.1 29.8 48.8 10.4 42.1 14.2 27.9 Var. 1.2 1.7 10.4 21.3 4.4 12.9 14.5 30.3 1(comp.) Var. 2 1.2 2.4 33.7 42.2 13.5 40.1 14.6 30.7 (inv.) 1.3 5.3 41.7 55.0 30.4 53.5 14.6 31.6 Var. 3 (comp.) ]
, Table 4 Alloy Degree Final Gra No of anneali in Si Fe Cu Mn Mg Cr Zn Ti size rolling ng 1Ftnal 1%1 1 III 46 KO 16 0.0 0.2 0.04 0.3 4.5 0.00 0.00 0.01 3 II 57 BOLO 18 0.0 0.1 0.00 0.2 4.3 0.00 0.00 0.01 _ 4 I 45 BOLO 18 0.0 0.1 0.00 0.2 4.1 0.00 0.00 0.02 6 I 45 KO 21 0.0 0.1 0.00 0.2 4.1 0.00 0.00 0.02 7 III 30 BOLO 22 0.0 0.2 0.04 0.3 4.5 0.00 0.00 0.01 7 4 0 0 o 5 1 III 25 BOLO 27 0.0 0.2 0.04 0.3 4.5 0.00 0.00 0.01 1 7 4 0 0 o 5 1 I 32 BOLO 29 0.0 0.1 0.00 0.2 4.1 0.00 0.00 0.02 15 III 30 KO 30 0.0 0.2 0.04 0.3 4.5 0.00 0.00 0.01 -16 I 25 BOLO 31 0.0 0.1 0.00 0.2 4.1 0.00 0.00 0.02 1 II _ 21 BOLO 33 0.0- 0.1 0.00 0.2 4.3 0.00 0.00 0.01 -20 I 20 BOLO 34 0.0 0.1 0.00 0.2 4.1 0.00 0.00 0.02 '1 Table 5 IK-mass loss, IK-mass loss, 15% Mechanical characteristics, soft unstretched** stretched ** state _ 20 Min. 20Min. 20 Min.
No Start 20 min. 185 C
185 C 20 Min. 185 C Result (Oh) 185 ( 185 C R02 Rm Ag A)on,.
+ 200 h + 500 h +200h =
1 III 15.4 ' 16.6 25.7 26.9 18.8 33.6 135 279 20.7 25.2 Comparison 3 11 1.2 2.4 33.7 36.7 13.5 40.1 128 262 23.9 26.5 Invention 4 1 1.3 ' 1.9 17.8 22.2 1.6 20.1 -117 258 22.8 25.3 Invention 6 1 8.2 10.8 18.6 22.1 9.6 20.7 106 250 23.8 26.7 Comparison 7 III 1.1 1.7 18.0 24.5 3.3 25.1 119 276 20.3 24.9 Invention 11 III 1.1 1.6 14.3 17.7 2.8 19.8 116 275 20.2 24.4 Invention 13 1 1.1 1.2 13.3 16.7 2.1 17.4 104 251 22.2 24.8 Comparison _ 15 III 2.8 3.0 7.9 10.9 6.4 18.0 125 281 19.5 23.6 Comparison 16 l' 1.1 1.3 10.8 13.1 1.9 14.2 103 252 21.6 26.1 Comparison 18 11 1.2 1.7 10.4 12.5 4.4 12.9 109 259 22.0 24.6 Comparison 20 1 1.1 1.2 8.3 11.1 1.7 12.4 101 251 20.8 25.1 Comparison ,
Claims (20)
1. A cold-rolled aluminium alloy strip composed of an AlMg aluminium alloy, wherein the aluminium alloy has the following alloying elements:
Si <= 0.2 wt.%, Fe <= 0.35 wt.%, Cu <= 0.15 wt.%, 0.2 wt.% <= Mn <= 0.35 wt.%, 4.1 wt.% <= Mg <= 4.5 wt.%, Cr <= 0.1 wt.%, Zn <= 0.25 wt.%, and Ti <= 0.1 wt.%, the remainder being Al and inevitable impurities, amounting to a maximum of 0.05 wt.%
individually and to a maximum of 0.15 wt.% in total, wherein the aluminium alloy strip has a recrystallized microstructure, the grain size of the microstructure ranges from 15 µm to 25 µm and the final soft annealing or the aluminium alloy strip is performed in a continuous furnace.
Si <= 0.2 wt.%, Fe <= 0.35 wt.%, Cu <= 0.15 wt.%, 0.2 wt.% <= Mn <= 0.35 wt.%, 4.1 wt.% <= Mg <= 4.5 wt.%, Cr <= 0.1 wt.%, Zn <= 0.25 wt.%, and Ti <= 0.1 wt.%, the remainder being Al and inevitable impurities, amounting to a maximum of 0.05 wt.%
individually and to a maximum of 0.15 wt.% in total, wherein the aluminium alloy strip has a recrystallized microstructure, the grain size of the microstructure ranges from 15 µm to 25 µm and the final soft annealing or the aluminium alloy strip is performed in a continuous furnace.
2. The aluminium alloy strip according to claim 1, wherein the aluminium alloy also has one or more restriction to the contents of alloying elements selected from the group consisting of:
0.03 wt.% Si <= 0.10 wt.%, Cu <= 0.1, Cr <= 0.05 wt.%, Zn <= 0.05 wt.%, and 0.01 wt.% <= Ti <= 0.05 wt.%.
0.03 wt.% Si <= 0.10 wt.%, Cu <= 0.1, Cr <= 0.05 wt.%, Zn <= 0.05 wt.%, and 0.01 wt.% <= Ti <= 0.05 wt.%.
3. The aluminium alloy strip according to claim 1 or 2, wherein the aluminium alloy also has one or more restriction to the contents of alloying elements selected from the group consisting of:
Cr <= 0.02 wt.%, and Zn <= 0.02 wt.%.
Cr <= 0.02 wt.%, and Zn <= 0.02 wt.%.
4. The aluminium alloy strip according to any one of claims 1 to 3, wherein the Fe content is 0.10 wt.% to 0.25 wt.%.
5. The aluminium alloy strip according to any one of claims 1 to 3, wherein the Fe content is 0.10 wt.% to 0.2 wt.%.
6. The aluminium alloy strip according to any one of claims 1 to 4, wherein the Mn content is 0.20 wt.% to 0.30 wt.%.
7. The aluminium alloy strip according to any one of claims 1 to 6, wherein the Mg content is 4.2 wt.% to 4.4 wt.%.
8. The aluminium alloy strip according to any one of claims 1 to 7, wherein the aluminium alloy strip has a thickness of 0.5 mm to 4 mm.
9. The aluminium alloy strip according to any one of claims 1 to 8, wherein the aluminium alloy strip in the soft state has a yield point R p0.2 of at least 110 MPa and a tensile strength R m of at least 255 MPa.
10. A method for producing an aluminium alloy strip according to any one of claims 1 to 9, comprising the following process steps:
- casting a rolling ingot;
- homogenisation of the rolling ingot at 480°C to 550°C for at least 0.5 hours;
- hot rolling of the rolling ingot at a temperature of 280°C to 500°C;
- cold rolling of the aluminium alloy strip to the final thickness with a degree of rolling of 40% to 70%; and - soft annealing of the finished-rolled aluminium alloy strip at 300°C to 500°C in a continuous furnace.
- casting a rolling ingot;
- homogenisation of the rolling ingot at 480°C to 550°C for at least 0.5 hours;
- hot rolling of the rolling ingot at a temperature of 280°C to 500°C;
- cold rolling of the aluminium alloy strip to the final thickness with a degree of rolling of 40% to 70%; and - soft annealing of the finished-rolled aluminium alloy strip at 300°C to 500°C in a continuous furnace.
11. The method of claim 10, wherein the step of cold rolling comprises cold rolling of the aluminium alloy strip to the final thickness with a degree of rolling of 50%
to 60%.
to 60%.
12. The method according to claim 10, wherein after hot rolling alternatively the following process steps are performed:
- cold rolling of the hot-rolled aluminium alloy strip to an intermediate thickness which is determined in such a way that the final degree of cold rolling to the final thickness is 40%
to 70%;
- intermediate annealing of the aluminium alloy strip at 300°C to 500°C;
- cold rolling of the aluminium alloy strip to the final thickness with a degree of rolling of 40% to 70%; and - soft annealing of the finish-rolled aluminium alloy strip at 300°C
- 500°C in a continuous furnace.
- cold rolling of the hot-rolled aluminium alloy strip to an intermediate thickness which is determined in such a way that the final degree of cold rolling to the final thickness is 40%
to 70%;
- intermediate annealing of the aluminium alloy strip at 300°C to 500°C;
- cold rolling of the aluminium alloy strip to the final thickness with a degree of rolling of 40% to 70%; and - soft annealing of the finish-rolled aluminium alloy strip at 300°C
- 500°C in a continuous furnace.
13. The method of claim 12, wherein the step of cold rolling of the hot-rolled aluminium alloy strip comprises cold rolling of the hot-rolled aluminium alloy strip to an intermediate thickness which is determined in such a way that the final degree of cold rolling to the final thickness is 50% to 60%.
14. The method of claim 12 or 13, wherein the step of cold rolling of the aluminium alloy strip comprises cold rolling of the aluminium alloy strip to the final thickness with a degree of rolling of 50% to 60%.
15. The method according to any one of claims 12 to 14, wherein the intermediate annealing is performed in a batch furnace or in a continuous furnace.
16. The method according to any one of claims 10 to 15, wherein the aluminium alloy strip after soft annealing is cooled to a maximum temperature of 100°C and then coiled.
17. The method according to any one of claims 10 to 16, wherein the aluminium alloy strip is cold rolled to a final thickness of 0.5 mm to 4 mm.
18. The method according to any one of claims 10 to 17, wherein the soft annealing is performed in the continuous furnace at a metal temperature of 350°C to 550°C for 10 seconds to minutes.
19. A component for a motor vehicle, composed of the aluminium alloy strip according to any one of claims 1 to 9.
20. The component according to claim 19, wherein the component is a body part or a body accessory of a motor vehicle.
Applications Claiming Priority (5)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| EP12181356.2 | 2012-08-22 | ||
| EP12181356 | 2012-08-22 | ||
| EP2013064736 | 2013-07-11 | ||
| EPPCT/EP2013/064736 | 2013-07-11 | ||
| PCT/EP2013/067487 WO2014029856A1 (en) | 2012-08-22 | 2013-08-22 | Highly malleable and igc-resistant almg strip |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CA2882614A1 CA2882614A1 (en) | 2014-02-27 |
| CA2882614C true CA2882614C (en) | 2018-01-02 |
Family
ID=49084999
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA2882614A Expired - Fee Related CA2882614C (en) | 2012-08-22 | 2013-08-22 | Highly formable and intercrystalline corrosion-resistant almg strip |
Country Status (9)
| Country | Link |
|---|---|
| US (1) | US20150159250A1 (en) |
| EP (1) | EP2888383B1 (en) |
| JP (1) | JP5923665B2 (en) |
| KR (1) | KR101709289B1 (en) |
| CN (1) | CN104937120B (en) |
| CA (1) | CA2882614C (en) |
| ES (1) | ES2569945T3 (en) |
| RU (1) | RU2608931C2 (en) |
| WO (1) | WO2014029856A1 (en) |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2015027037A1 (en) * | 2013-08-21 | 2015-02-26 | Taheri Mitra Lenore | Annealing process |
| ES2961820T3 (en) * | 2015-06-05 | 2024-03-14 | Novelis Inc | An automobile body part comprising an aluminum alloy and a method of producing the automobile body part |
| EP3314031B1 (en) * | 2015-06-25 | 2018-11-07 | Hydro Aluminium Rolled Products GmbH | High strength and easily reformable almg tape and method for producing the same |
| EP3589772B1 (en) * | 2017-02-28 | 2023-04-05 | Tata Steel IJmuiden B.V. | Method for producing a hot-formed coated steel product |
| WO2020182506A1 (en) | 2019-03-08 | 2020-09-17 | Aleris Aluminum Duffel Bvba | Method of manufacturing a 5xxx-series sheet product |
| CN113186413A (en) * | 2021-04-29 | 2021-07-30 | 郑州明泰实业有限公司 | Preparation method of 5083-O-state battery case side plate for new energy automobile |
| WO2023031334A1 (en) | 2021-09-03 | 2023-03-09 | Speira Gmbh | Aluminium alloy strip optimised for forming, and method for manufacturing same |
Family Cites Families (16)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4151013A (en) | 1975-10-22 | 1979-04-24 | Reynolds Metals Company | Aluminum-magnesium alloys sheet exhibiting improved properties for forming and method aspects of producing such sheet |
| JP2671121B2 (en) | 1986-03-10 | 1997-10-29 | スカイアルミニウム 株式会社 | Rolled aluminum alloy sheet for forming, which has excellent elongation, bendability, and overhanging property, and method for producing the same |
| JPH0668146B2 (en) | 1986-09-09 | 1994-08-31 | スカイアルミニウム株式会社 | Method for manufacturing rolled aluminum alloy plate |
| EP0681034A1 (en) | 1994-05-06 | 1995-11-08 | The Furukawa Electric Co., Ltd. | A method of manufacturing an aluminum alloy sheet for body panel and the alloy sheet manufactured thereby |
| FR2740144B1 (en) * | 1995-10-18 | 1997-11-21 | Pechiney Rhenalu | ALMG ALLOY FOR WELDED CONSTRUCTS WITH IMPROVED MECHANICAL CHARACTERISTICS |
| NL1003453C2 (en) | 1996-06-28 | 1998-01-07 | Hoogovens Aluminium Nv | AA5000 type aluminum sheet and a method for its manufacture. |
| DE69808738T2 (en) * | 1997-03-07 | 2003-06-26 | Alcan Int Ltd | METHOD FOR PRODUCING AN ALUMINUM SHEET |
| DE10231437B4 (en) * | 2001-08-10 | 2019-08-22 | Corus Aluminium N.V. | Process for producing an aluminum wrought alloy product |
| RU2230131C1 (en) * | 2002-09-20 | 2004-06-10 | Региональный общественный фонд содействия защите интеллектуальной собственности | Alloy of the system of aluminum-magnesium-manganese and items made out of the alloy |
| PT1466992E (en) * | 2003-04-08 | 2007-09-12 | Hydro Aluminium Deutschland | A flat rolled semi-finished product from an aluminium alloy |
| JP4534573B2 (en) * | 2004-04-23 | 2010-09-01 | 日本軽金属株式会社 | Al-Mg alloy plate excellent in high-temperature high-speed formability and manufacturing method thereof |
| RU2280705C2 (en) * | 2004-09-15 | 2006-07-27 | Открытое акционерное общество "Каменск-Уральский металлургический завод" | Aluminum-based alloy and articles made from this alloy |
| EP1852251A1 (en) * | 2006-05-02 | 2007-11-07 | Aleris Aluminum Duffel BVBA | Aluminium composite sheet material |
| JP2008202134A (en) * | 2007-02-22 | 2008-09-04 | Kobe Steel Ltd | Aluminum alloy hot rolled sheet having excellent press formability |
| JP5432642B2 (en) * | 2009-09-03 | 2014-03-05 | 株式会社Ｕａｃｊ | Aluminum alloy plate for can end and manufacturing method thereof. |
| ES2392131T3 (en) * | 2009-09-15 | 2012-12-04 | Hydro Aluminium Rolled Products Gmbh | AL composite material translation mechanism part |
-
2013
- 2013-08-22 CA CA2882614A patent/CA2882614C/en not_active Expired - Fee Related
- 2013-08-22 EP EP13756053.8A patent/EP2888383B1/en not_active Revoked
- 2013-08-22 KR KR1020157007194A patent/KR101709289B1/en active IP Right Grant
- 2013-08-22 CN CN201380044183.0A patent/CN104937120B/en not_active Expired - Fee Related
- 2013-08-22 JP JP2015527926A patent/JP5923665B2/en active Active
- 2013-08-22 WO PCT/EP2013/067487 patent/WO2014029856A1/en active Application Filing
- 2013-08-22 ES ES13756053.8T patent/ES2569945T3/en active Active
- 2013-08-22 RU RU2015110021A patent/RU2608931C2/en not_active IP Right Cessation
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2015
- 2015-02-18 US US14/624,793 patent/US20150159250A1/en not_active Abandoned
Also Published As
| Publication number | Publication date |
|---|---|
| KR101709289B1 (en) | 2017-02-22 |
| ES2569945T3 (en) | 2016-05-13 |
| US20150159250A1 (en) | 2015-06-11 |
| EP2888383A1 (en) | 2015-07-01 |
| JP2015532679A (en) | 2015-11-12 |
| CN104937120B (en) | 2017-11-17 |
| CN104937120A (en) | 2015-09-23 |
| JP5923665B2 (en) | 2016-05-24 |
| RU2608931C2 (en) | 2017-01-26 |
| RU2015110021A (en) | 2016-10-20 |
| CA2882614A1 (en) | 2014-02-27 |
| EP2888383B1 (en) | 2016-03-30 |
| KR20150076151A (en) | 2015-07-06 |
| WO2014029856A1 (en) | 2014-02-27 |
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