EP2449145B1 - AlMgSi-sheet for applications with high shaping requirements - Google Patents
AlMgSi-sheet for applications with high shaping requirements Download PDFInfo
- Publication number
- EP2449145B1 EP2449145B1 EP10723562.4A EP10723562A EP2449145B1 EP 2449145 B1 EP2449145 B1 EP 2449145B1 EP 10723562 A EP10723562 A EP 10723562A EP 2449145 B1 EP2449145 B1 EP 2449145B1
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- EP
- European Patent Office
- Prior art keywords
- strip
- hot
- aluminium strip
- rolling
- alloy
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- Revoked
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- 238000007493 shaping process Methods 0.000 title 1
- 229910052782 aluminium Inorganic materials 0.000 claims description 84
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 84
- 229910045601 alloy Inorganic materials 0.000 claims description 43
- 239000000956 alloy Substances 0.000 claims description 43
- 238000000034 method Methods 0.000 claims description 38
- 238000005098 hot rolling Methods 0.000 claims description 31
- 238000005096 rolling process Methods 0.000 claims description 24
- 229910000838 Al alloy Inorganic materials 0.000 claims description 22
- 230000032683 aging Effects 0.000 claims description 22
- 238000004519 manufacturing process Methods 0.000 claims description 17
- 238000010438 heat treatment Methods 0.000 claims description 13
- 230000008569 process Effects 0.000 claims description 10
- 229910052751 metal Inorganic materials 0.000 claims description 9
- 239000002184 metal Substances 0.000 claims description 9
- 238000001816 cooling Methods 0.000 claims description 8
- 239000000839 emulsion Substances 0.000 claims description 5
- 238000000265 homogenisation Methods 0.000 claims description 5
- 239000004411 aluminium Substances 0.000 claims 17
- 239000011777 magnesium Substances 0.000 description 22
- 239000011572 manganese Substances 0.000 description 20
- 239000010949 copper Substances 0.000 description 19
- 239000011651 chromium Substances 0.000 description 18
- 238000010791 quenching Methods 0.000 description 18
- 239000010936 titanium Substances 0.000 description 18
- 239000011701 zinc Substances 0.000 description 18
- 230000000171 quenching effect Effects 0.000 description 17
- 238000005097 cold rolling Methods 0.000 description 11
- 239000012535 impurity Substances 0.000 description 8
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 6
- 238000000137 annealing Methods 0.000 description 6
- 229910052749 magnesium Inorganic materials 0.000 description 6
- 239000002244 precipitate Substances 0.000 description 6
- 229910019018 Mg 2 Si Inorganic materials 0.000 description 5
- 239000000470 constituent Substances 0.000 description 5
- 238000005260 corrosion Methods 0.000 description 5
- 230000007797 corrosion Effects 0.000 description 5
- 230000008901 benefit Effects 0.000 description 4
- 229910052748 manganese Inorganic materials 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 3
- 229910017639 MgSi Inorganic materials 0.000 description 3
- 238000005275 alloying Methods 0.000 description 3
- 238000005266 casting Methods 0.000 description 3
- 229910052802 copper Inorganic materials 0.000 description 3
- 238000005259 measurement Methods 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 229910052710 silicon Inorganic materials 0.000 description 3
- 239000010703 silicon Substances 0.000 description 3
- 238000003878 thermal aging Methods 0.000 description 3
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 2
- 239000007795 chemical reaction product Substances 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
- 238000010276 construction Methods 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 229910052719 titanium Inorganic materials 0.000 description 2
- 229910052725 zinc Inorganic materials 0.000 description 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 239000002826 coolant Substances 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000003379 elimination reaction Methods 0.000 description 1
- 230000029142 excretion Effects 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 230000003993 interaction Effects 0.000 description 1
- 239000000314 lubricant Substances 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000010422 painting Methods 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 230000035945 sensitivity Effects 0.000 description 1
- 239000007921 spray Substances 0.000 description 1
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- 239000000725 suspension Substances 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
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Images
Classifications
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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
- C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
- B22D21/002—Castings of light metals
- B22D21/007—Castings of light metals with low melting point, e.g. Al 659 degrees C, Mg 650 degrees C
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D7/00—Casting ingots, e.g. from ferrous metals
- B22D7/005—Casting ingots, e.g. from ferrous metals from non-ferrous metals
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/62—Quenching devices
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
- C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/05—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions
Definitions
- the invention relates to a method for producing a strip from an AlMgSi alloy, in which an ingot of AlMgSi alloy is cast, the roll ingot is subjected to homogenization, the roll bar rolled to rolling temperature is hot rolled and then optionally cold rolled to final thickness. Moreover, the invention relates to an aluminum strip of an AlMgSi alloy and its advantageous use.
- AlMgSi alloys whose main alloying constituents are magnesium and silicon have relatively high strengths while at the same time having good forming behavior and excellent corrosion resistance.
- AlMgSi alloys are the alloy types AA6XXX, for example, the alloy types AA6016, AA6014, AA6181, AA6060 and AA6111.
- Aluminum tapes of AlMgSi alloy are produced by casting a roll bar, homogenizing the roll bar, hot rolling the roll bar, and cold rolling the hot strip. The homogenisation of the rolling ingot takes place at a temperature of 380 to 580 ° C for more than one hour.
- the tapes can be delivered in condition T4.
- the state T6 is set after quenching by thermal aging at temperatures between 100 ° C and 220 ° C.
- a method for producing a strip of AlMgSi alloy which is characterized by improved forming properties, is known from the prior art US 4,808,247 known. According to this method, first a ingot of AlMgSi alloy is cast and then subjected to homogenization at a temperature between 450 and 580 ° C. To provide the desired thickness of the strip, the ingot is hot and cold rolled. After a final solution anneal, the Al tape is cold-aged for two weeks at room temperature. An aluminum strip produced by this process has a yield strength of 15 kg / mm 2 (147 MPa).
- the EP 1 533 394 A1 relates to a component of an automobile body of two sheet metal parts each made of an AlMgSi alloy.
- the process for producing these sheets comprises the following steps: vertical continuous casting, homogenizing annealing, hot and cold rolling of the strips to a thickness of 1.2 mm.
- the tapes produced in this way have a yield strength Rp0.2 of 80 to 140 MPa; at the same time, the value of the breaking elongation A 80 is clearly below 30%.
- a solution annealed aluminum strip of alloy AA6016 is known, the method of making this strip comprising various warming and cooling steps.
- An aluminum tape made according to this method has a general yield strength ("YS") of 117 MPa and a general elongation at break (“EL”) of 32%.
- the problem is that coarse Mg 2 Si precipitates are present in hot-rolled aluminum strips of AlMgSi alloys, which are broken and reduced in the subsequent cold rolling by high degrees of deformation.
- Hot strips of AlMgSi alloy are usually produced in thicknesses of 3 mm to 12 mm and fed to a cold rolling with high degrees of deformation. Since the temperature range in which the AlMgSi phases form, is traversed very slowly during conventional hot rolling, these phases form very coarse. The temperature range for forming the above phases is depending on the alloy but is between 550 ° C and 230 ° C. It was experimentally proven that these coarse phases in the hot strip negatively influence the elongation of the end product. This means that the forming behavior of Aluminum strips of AlMgSi alloys could not be fully exploited.
- the present invention is therefore based on the object to provide a method for producing an aluminum strip of an AlMgSi alloy and an aluminum strip available, which has a higher elongation in the state T4 and thus allows higher degrees of deformation in the production of structural components.
- the present invention is based on the object to propose advantageous uses of a sheet produced from the aluminum strip according to the invention.
- the above-indicated object for a method for producing a strip of an AlMgSi alloy is achieved in that the hot strip immediately at the outlet from the last hot roll pass a maximum temperature of 130 ° C, preferably a maximum temperature 100 ° C and the hot strip is wound at this or a lower temperature.
- the size of the Mg 2 Si precipitates in a hot strip of an AlMgSi alloy can be significantly reduced by quenching, ie by accelerated cooling. Due to the rapid cooling from a hot strip temperature between 230 ° C and 550 ° C to a maximum of 130 ° C, preferably at most 100 ° C at the outlet of the last hot roll pass, the microstructure state of the hot strip frozen, so that coarse excretions can no longer form. The resulting aluminum strip, after solution heat treatment and final thickness quenching, exhibits significantly improved elongation at conventional T4 strengths and equal or even improved T6 cure. This combination of properties has not yet been achieved for strips of AlMgSi alloys.
- this cooling process takes place within the last two hot rolling passes, i. cooling to 130 ° C and less takes place within seconds, within a maximum of five minutes. It has been shown that in this procedure, the increased elongation values at the usual strength or expansion limits in the condition T4 and the improved hardenability in the condition T6 are achieved particularly reliably.
- a particularly economical realization of the method is achieved by quenching the hot strip itself to coiling temperature using at least one sinker cooler and the hot rolling passes applied with emulsion.
- a board cooler consists of an array of coolant or lubricant nozzles which spray a rolling emulsion onto the aluminum strip.
- the sinker cooler is often present in a hot rolling mill to cool rolled hot strip to roll temperature before hot rolling and to set the coiling temperature. The method according to the invention can thus be used on conventional systems without special ancillary equipment.
- the hot rolling temperature is above the recrystallization temperature of a metal, that is, above 230 ° C for aluminum.
- the coiling temperature at 130 ° C but significantly below these process conditions.
- the hot rolling temperature of the hot strip prior to the penultimate hot rolling pass at least 230 ° C, preferably above 400 ° C is achieved according to a next embodiment of the method that particularly small Mg 2 Si precipitates are present in the quenched hot strip, since the largest proportion of alloying components Magnesium and silicon are present at these temperatures in the dissolved state in the aluminum matrix.
- This advantageous state of the hot strip is quasi “frozen” by quenching.
- the thickness of the finished hot strip is 3 mm to 12 mm, preferably 3.5 mm to 8 mm, so that conventional cold rolling stands for cold rolling can be used.
- the alloy AA6xxx alloy used for the process of the invention is preferably of the type AA6014, AA6016, AA6060, AA6111 or AA6181. All alloy types AA6xxx have in common that they have a particularly good forming behavior characterized by high elongation values in the state T4 and very high strength or yield strength in use state T6, for example, after a heat aging at 205 ° C / 30 min.
- the finished rolled aluminum strip is subjected to a heat treatment, wherein the aluminum strip is heated to more than 100 ° C and then wound at a temperature of more than 55 ° C, preferably more than 85 ° C and paged.
- This embodiment of the method after cold aging by a shorter heating phase at lower temperatures, allows to set the state T6 in the aluminum strip or sheet in which the sheet-formed or strip-formed components are used in the application.
- these fast-curing aluminum strips are heated to temperatures of about 185 ° C. for only 20 minutes in order to achieve the higher yielding limits in state T6.
- the elongation at break values A 80 of the aluminum strips produced with this embodiment of the method according to the invention are slightly below 29%.
- the aluminum strip produced according to the invention is still characterized by a very good uniform elongation A g of more than 25% after aging in state T4.
- Equal expansion A g is the maximum elongation of the sample at which no constriction of the sample is observed during the tensile test. The sample is thus stretched evenly in the region of the uniform expansion.
- the uniform elongation significantly influences the forming behavior, since this determines the maximum degree of deformation of the material used in practice.
- an aluminum strip with very good forming properties can be made available with the process according to the invention, which can also be converted into the state T6 via accelerated thermal aging (185 ° C./120 min.).
- the manganese content of less than 0.2% by weight reduces the tendency to form coarser manganese precipitates.
- chromium ensures a fine microstructure, it should be limited to 0.1% by weight in order to avoid coarse precipitation.
- the presence of manganese improved the weldability by reducing the tendency to crack or quenching sensitivity of the aluminum strip according to the invention.
- a reduction of the zinc content to a maximum of 0.1% by weight improves in particular the corrosion resistance of the aluminum alloy or of the finished sheet in the respective application.
- titanium provides grain refining during casting, but should be limited to a maximum of 0.1% by weight to ensure good castability of the aluminum alloy.
- the combination of a precisely predetermined magnesium content with a reduced Si content and narrowly specified Fe content in comparison to the first embodiment results in an aluminum alloy in which the formation of Mg 2 Si precipitates after hot rolling can be prevented particularly well by the method according to the invention, so that a sheet with improved elongation and high yield strengths can be provided compared to conventionally produced sheets.
- the lower upper limits of the alloy components Cu, Mn and Cr additionally reinforce the effect of the method according to the invention. With regard to the effects of the upper limit of Zn and Ti, reference is made to the comments on the first embodiment of the aluminum alloy.
- All the aluminum alloys shown are specifically adapted to different applications in their alloy components.
- tapes made of these aluminum alloys which were produced using the method according to the invention, exhibit particularly high elongation values in state T4, coupled with a particularly pronounced increase in the yield strength, for example after heat aging at 205 ° C./30 min. This also applies to the aluminum strips subjected to a heat treatment after solution treatment in the condition T4.
- the above object is achieved by an aluminum strip with the features of claim 7.
- the delivery state T4 is usually achieved by a solution treatment with quenching and subsequent storage at room temperature for at least three days, since then the properties of the solution-annealed Sheets or ribbons are stable.
- the combination of breaking elongation A 80 and yield strength Rp0.2 of the aluminum strip according to the invention has not been achieved with previously known AlMgSi alloys.
- the aluminum strip according to the invention therefore permits maximum degrees of deformation due to the high elongation values with maximum values for the yield strength Rp0.2 in the finished sheet metal or component.
- Particularly advantageous forming properties are achieved by an embodiment of the MgSi aluminum strip according to the invention in that in addition the uniform elongation A g is more than 25%.
- the uniform expansion significantly determines the maximum degree of deformation of the aluminum strip or the sheet produced therefrom in the manufacture of components, since uncontrolled constrictions during manufacture must be avoided.
- the aluminum strip according to the invention has a particularly high forming reserve with respect to constrictions and can therefore be converted to components with greater process reliability.
- the aluminum strip according to the invention preferably has a yield strength Rp0.2 of greater than 185 MPa at an elongation A 80 of at least 15% in the condition T6, that is to say in the use or application state. These values were measured in the aluminum tapes according to the invention in the condition T6, which have undergone a heat aging at 205 ° C / 30 min. After a solution heat treatment and quenching (state T4). Due to the high yield strengths in state T6 with very good elongation values in state T4, the aluminum strip according to the invention is particularly well suited for use in motor vehicle construction, for example.
- the increase in the yield strength from state T4 to state T6 is particularly high in the case of the aluminum strip according to the invention.
- the aluminum strip according to the invention can therefore be formed very well in the condition T4 and then be put into a high-strength use state (state T6) by heat aging.
- state T6 high-strength use state
- a fast-hardening AlMgSi aluminum strip with excellent forming properties is provided with an aluminum strip according to claim 11.
- the aluminum strip according to the invention produced according to claim 11 is subjected to a solution annealing with subsequent heat treatment after its preparation and has in the state T4 an equal dimension A g of more than 25% at a yield strength Rp0.2 of 80 to 140 MPa.
- this variant makes it possible to provide a rapidly-hardenable and, at the same time, very easily transformable MgSi aluminum strip.
- the thermal aging to reach state T6 can be 185 ° C for 20 min. To achieve the required elongation increases.
- the aluminum strip has a uniform elongation A g of more than 25% in the rolling direction, transversely to the rolling direction and diagonally to the rolling direction, a particularly isotropic forming capability can be made possible.
- the aluminum strips 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 bands with larger thicknesses of 2 to 4.5 mm, for example, find in chassis parts in automotive applications.
- Individual components can also be manufactured in a cold-rolled strip with a thickness of up to 6 mm.
- aluminum strips with thicknesses of up to 12 mm can be used. These very thick aluminum strips are usually provided only by hot rolling.
- the aluminum strip according to the invention is of the alloy type AA6014, AA6016, AA6060, AA6111 or AA6181. With regard to the advantages of these aluminum alloys, reference is made to the comments on the method according to the invention.
- the above object according to a third teaching of the present invention by the use of a sheet produced from an aluminum strip according to the invention as a component, suspension or structural part and sheet metal in automotive, aircraft or rail vehicle, in particular as a component, chassis part, outer or inner panel in the automotive industry, preferably as a body component solved.
- visible body parts, such as hoods, fenders, etc., as well as outer skin parts of a rail vehicle or aircraft benefit from the high yield strengths Rp0.2 with good surface properties even after forming with high degrees of deformation.
- FIG. 1 a schematic flow diagram of an embodiment of the inventive method for producing a strip of a MgSi aluminum alloy with the steps of a) producing and homogenizing the rolling ingot, b) hot rolling, c) cold rolling and d) with solution treatment with quenching.
- the ingot produced in this way is homogenized in a furnace 2 for 8 hours at a homogenization temperature of about 550 ° C., so that the alloyed components alloyed in are present in a particularly homogeneous distribution in the rolling ingot.
- Fig. 1a The ingot produced in this way is homogenized in a furnace 2 for 8 hours at a homogenization temperature of about 550 ° C., so that the alloyed components alloyed in are present in a particularly homogeneous distribution in the rolling ingot.
- Fig. 1a The ingot produced in this way is homogenized in a furnace 2 for 8 hours at a homogenization temperature of about 550 ° C.
- the hot strip 4 after leaving the hot rolling mill 3 and before the penultimate hot rolling pass, the hot strip 4 preferably has a temperature of at least 400 ° C.
- the work rolls of the hot rolling stand 3 are subjected to emulsion and cool the hot strip 4 further down. After the last rolling pass, the hot strip 4 at the outlet of the sinker cooler 5 'in the present embodiment, only a temperature of 95 ° C and will then be wound on the take-up reel 6.
- the hot strip 4 has a temperature of at most 130 ° C or at most 100 ° C immediately at the outlet of the last hot rolling pass or optionally in the last two hot rolling passes using the sinker 5 and the work rolls of the hot rolling mill 3 to a temperature below Is brought to 130 ° C or below 100 ° C, the hot strip 4 has a frozen crystal structure state, since no additional energy in the form of heat for subsequent elimination processes for Available.
- the hot strip with a thickness of 3 to 12 mm, preferably 3.5 to 8 mm is wound on the take-up reel 6.
- the coiling temperature in the present embodiment is less than 95 ° C.
- the hot strip 4 has a very favorable for further processing crystal state and can be unwound from the unwinding reel 7, for example, fed to a cold rolling mill 9 and rewound on a take-up reel 8, Fig. 1c ).
- the resulting cold-rolled strip 11 is wound up. Subsequently, it is supplied to a solution annealing and quenching 10, Fig. 1d ). For this purpose, it is again unwound from the coil 12, solution-annealed in an oven 10 and quenched again wound into a coil 13.
- the aluminum strip can then be delivered after a cold aging at room temperature in the state T4 with maximum formability. Alternatively (not shown), the aluminum strip 11 can be singulated into individual sheets, which are present after a cold aging in the state T4.
- the aluminum strip or the aluminum sheet is brought by cold aging at 100 ° C to 220 ° C in order to achieve maximum values for the yield strength. For example, a hot aging at 205 ° C / 30 min. Performed.
- the aluminum strips produced according to the illustrated embodiment have a thickness of 0.5 to 4.5 mm after cold rolling.
- Tape thicknesses of 0.5 to 2 mm are commonly used for body applications or tape thicknesses of 2.0 mm to 4.5 mm for chassis parts in the automotive industry.
- the improved elongation values in the manufacture of the components are of decisive advantage, since in most cases strong deformation of the sheets is carried out and nevertheless high strengths in the operating condition (T6) of the end product are required.
- Table 1 shows the alloy compositions of aluminum alloys from which aluminum tapes have been produced conventionally or according to the invention.
- the aluminum strips contain aluminum and impurities as a residual proportion, individually not more than 0.05% by weight and in total not more than 0.15% by weight.
- the tapes (samples) 409 and 410 were made by a process according to the invention in which the hot strip was cooled and wound up within the last two hot rolling passes from about 400 ° C to 95 ° C using a sinker cooler and the hot rolls themselves. Table 2 shows the measured values of these bands as "Inv.” characterized. Subsequently, a cold rolling to a final thickness of 1.04 mm.
- the tapes (samples) 491-1 and 491-11 were made with conventional hot rolling and cold rolling and with a "conv.” characterized.
- Table 2 bands T4 T6 205 ° C / 30 min. Thickness (mm) Rp0.2 (MPa) R m (MPa) A g (%) A 80 (%) Rp0.2 (MPa) R m (MPa) A 80 (%) ⁇ Rp0, 2 (MPa) 409 Inv. 1.04 100 220 26.3 31.3 187 251 16.2 87 410 Inv. 1.04 98 217 25.6 30.3 195 256 15.5 97 491-1 Conv. 1.04 92 202 23.1 27.8 180 235 14.7 88 491-11 Conv. 1.04 88 196 23.0 27.4 179 232 14.3 91
- the strips were subjected to solution annealing with subsequent quenching and subsequent cold aging at room temperature.
- the T6 state was achieved by hot aging at 205 ° C for 30 minutes.
- This structure leads to the particularly advantageous combination of high elongation at break A 80 of at least 30% and at least 30% at very high values for the yield strength Rp0.2 of 80 to 140 MPa.
- the yield strength can increase to over 185 MPa, with the elongation A 80 still remaining at more than 15%.
- the curability with a ⁇ Rp0.2 of 87 and 97 MPa shows that the embodiments according to the invention, despite the increased elongation values of more than 15%, achieve a very good increase in the yield strength in the warm-aged state T6 during a heat aging at 205 ° C./30 min ,
- the A and B tapes were wound to 95 ° C using the quenching process of the present invention within the last two hot rolling passes and then cold rolled to a final thickness of 1.0 mm and 3.0 mm, respectively.
- the strips A and B were solution-annealed and cold-aged after quenching.
- Table 4 shows the composition of tape 342 which was treated with the additional heat treatment after solution heat treatment and quenching.
- Table 4 tape Si% by weight Fe% by weight Cu% by weight Mn% by weight Mg% by weight Cr% by weight Zn% by weight Ti% by weight P342 1.3 0.17 0.00 0.06 0.3 ⁇ 0.0005 ⁇ 0.001 0.02
- the heat treatment led to the fact that the elongation at break properties deteriorated because the elongation at break A 80 was now below 30%.
- the uniform elongation of the aluminum strip P342 remained unchanged compared to the non-heat treated variants at more than 25%, as Table 5 shows.
- the uniform strain is a very important factor in the transformation of the aluminum strip into a component, since an improved uniform elongation allows higher degrees of deformation and thus either a reliable production or fewer forming steps.
- Table 5 shows various measurements. On the one hand, three measurements were performed at the beginning of the tape P342-BA and at the end of the tape P342-BE. In the column “Condition” it is stated that the band was in the condition T4, ie solution-annealed and quenched, after a cold aging at room temperature of 8 days. The strips from the beginning of the strip and the end of the strip were cut out and measured in the longitudinal direction (L) in the rolling direction, transverse to the rolling direction (Q) and diagonally (D) to the rolling direction.
- the condition T6 could be reached after 20 min.
- Typical values measured in state T6 were for the yield strength at more than 140 MPa after hot aging or more than 165 MPa after a hot aging and subsequent stretching by 2%.
- the aluminum strip produced according to the invention which has additionally been subjected to a heat treatment, therefore combines two important properties. It can be in the state T4 due to the high uniformity very good strain forming and achieved at the same time after a hot aging at 185 ° C for 20 min. The desired strength.
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Description
Die Erfindung betrifft ein Verfahren zur Herstellung eines Bandes aus einer AlMgSi-Legierung, bei welchem ein Walzbarren aus einer AlMgSi-Legierung gegossen wird, der Walzbarren einer Homogenisierung unterzogen wird, der auf Walztemperatur gebrachte Walzbarren warmgewalzt wird und anschließend optional auf Enddicke kaltgewalzt wird. Darüber hinaus betrifft die Erfindung ein Aluminiumband aus einer AlMgSi-Legierung sowie dessen vorteilhafte Verwendung.The invention relates to a method for producing a strip from an AlMgSi alloy, in which an ingot of AlMgSi alloy is cast, the roll ingot is subjected to homogenization, the roll bar rolled to rolling temperature is hot rolled and then optionally cold rolled to final thickness. Moreover, the invention relates to an aluminum strip of an AlMgSi alloy and its advantageous use.
Vor allem im Kraftfahrzeugbau aber auch in anderen Anwendungsgebieten, beispielsweise dem Flugzeugbau oder Schienenfahrzeugbau werden Bleche aus Aluminiumlegierungen benötigt, welche sich nicht nur durch besonders hohe Festigkeitswerte auszeichnen, sondern gleichzeitig ein sehr gutes Umformverhalten aufweisen und hohe Umformgrade ermöglichen. Im Kraftfahrzeugbau sind typische Anwendungsgebiete die Karosserie und Fahrwerkteile. Bei sichtbaren, lackierten Bauteilen, beispielsweise außen sichtbaren Karosserieblechen, kommt hinzu, dass das Umformen der Werkstoffe so erfolgen muss, dass die Oberfläche nach der Lackierung nicht durch Fehler wie Fließfiguren oder Zugrilligkeit (Roping) beeinträchtigt ist. Dies ist beispielsweise für die Verwendung von Aluminiumlegierungsblechen zur Herstellung von Motorhauben und anderen Karosseriebauteilen eines Kraftfahrzeuges besonders wichtig. Es schränkt die Werkstoffwahl hinsichtlich der Aluminiumlegierung allerdings ein. Insbesondere AlMgSi-Legierungen, deren Hauptlegierungsbestandteile Magnesium und Silizium sind, weisen relativ hohe Festigkeiten auf bei gleichzeitig gutem Umformverhalten sowie hervorragender Korrosionsbeständigkeit. AlMgSi-Legierungen sind die Legierungstypen AA6XXX, beispielsweise der Legierungstyp AA6016, AA6014, AA6181, AA6060 und AA6111. Üblicherweise werden Aluminiumbänder aus einer AlMgSi-Legierung durch Gießen eines Walzbarrens, Homogenisieren des Walzbarrens, Warmwalzen des Walzbarrens und Kaltwalzen des Warmbandes hergestellt. Die Homogenisierung des Walzbarrens erfolgt bei einer Temperatur von 380 bis 580 °C für mehr als eine Stunde. Durch ein abschließendes Lösungsglühen mit nachfolgendem Abschrecken und Kaltauslagern etwa bei Raumtemperatur für mindestens drei Tage können die Bänder im Zustand T4 ausgeliefert werden. Der Zustand T6 wird nach dem Abschrecken durch eine Warmauslagerung bei Temperaturen zwischen 100 °C und 220 °C eingestellt.Above all, in the automotive industry but also in other applications, such as aircraft or rail vehicle sheet metal from aluminum alloys are needed, which are not only characterized by particularly high strength values, but also have a very good forming behavior and allow high degrees of deformation. In automotive engineering typical applications are the body and chassis parts. In the case of visible, painted components, for example exterior body panels, it is necessary that the forming of the materials must be carried out in such a way that the surface after painting is not impaired by defects such as flow patterns or roping. This is particularly important, for example, for the use of aluminum alloy sheets for the production of engine hoods and other body parts of a motor vehicle. However, it restricts the choice of material with regard to the aluminum alloy. In particular AlMgSi alloys, whose main alloying constituents are magnesium and silicon have relatively high strengths while at the same time having good forming behavior and excellent corrosion resistance. AlMgSi alloys are the alloy types AA6XXX, for example, the alloy types AA6016, AA6014, AA6181, AA6060 and AA6111. Conventionally, aluminum tapes of AlMgSi alloy are produced by casting a roll bar, homogenizing the roll bar, hot rolling the roll bar, and cold rolling the hot strip. The homogenisation of the rolling ingot takes place at a temperature of 380 to 580 ° C for more than one hour. By a final solution annealing with subsequent quenching and cold aging at about room temperature for at least three days, the tapes can be delivered in condition T4. The state T6 is set after quenching by thermal aging at temperatures between 100 ° C and 220 ° C.
Ein Verfahren zur Herstellung eines Bandes aus einer AlMgSi-Legierung, das sich durch verbesserte Umformeigenschaften auszeichnet, ist aus dem Stand der Technik der
Die
Aus der
Schließlich offenbart auch die
Problematisch ist, dass in warmgewalzten Aluminiumbändern aus AlMgSi-Legierungen grobe Mg2Si-Ausscheidungen vorliegen, welche im anschließenden Kaltwalzen durch hohe Umformgrade gebrochen und verkleinert werden. Warmbänder einer AlMgSi-Legierung werden in der Regel in Dicken von 3 mm bis 12 mm hergestellt und einem Kaltwalzen mit hohen Umformgraden zugeführt. Da der Temperaturbereich in dem sich die AlMgSi-Phasen bilden, beim konventionellen Warmwalzen sehr langsam durchlaufen wird, bilden sich diese Phasen sehr grob aus. Der Temperaturbereich zur Bildung der obengenannten Phasen ist legierungsabhängig aber liegt zwischen 550°C und 230°C. Es konnte experimentell nachgewiesen werden, dass diese groben Phasen im Warmband die Dehnung des Endprodukts negativ beeinflussen. Das bedeutet, dass das Umformverhalten von Aluminiumbändern aus AlMgSi-Legierungen bisher nicht vollständig ausgeschöpft werden konnte.The problem is that coarse Mg 2 Si precipitates are present in hot-rolled aluminum strips of AlMgSi alloys, which are broken and reduced in the subsequent cold rolling by high degrees of deformation. Hot strips of AlMgSi alloy are usually produced in thicknesses of 3 mm to 12 mm and fed to a cold rolling with high degrees of deformation. Since the temperature range in which the AlMgSi phases form, is traversed very slowly during conventional hot rolling, these phases form very coarse. The temperature range for forming the above phases is depending on the alloy but is between 550 ° C and 230 ° C. It was experimentally proven that these coarse phases in the hot strip negatively influence the elongation of the end product. This means that the forming behavior of Aluminum strips of AlMgSi alloys could not be fully exploited.
Der vorliegenden Erfindung liegt daher die Aufgabe zu Grunde, ein Verfahren zur Herstellung eines Aluminiumbandes aus einer AlMgSi-Legierung sowie ein Aluminiumband zur Verfügung zu stellen, welches im Zustand T4 eine höhere Dehnung aufweist und insofern höhere Umformgrade bei der Herstellung von beispielsweise Strukturbauteilen ermöglicht. Darüber hinaus liegt der vorliegenden Erfindung die Aufgabe zu Grunde, vorteilhafte Verwendungen eines aus dem erfindungsgemäßen Aluminiumband hergestellten Blechs vorzuschlagen.The present invention is therefore based on the object to provide a method for producing an aluminum strip of an AlMgSi alloy and an aluminum strip available, which has a higher elongation in the state T4 and thus allows higher degrees of deformation in the production of structural components. In addition, the present invention is based on the object to propose advantageous uses of a sheet produced from the aluminum strip according to the invention.
Die genannte Aufgabe wird durch ein Verfahren nach Anspruch 1, ein Aluminiumband nach Anspruch 7 und 11 sowie eine Verwendung nach Anspruch 14 gelöst.The above object is achieved by a method according to claim 1, an aluminum strip according to
Gemäß einer ersten Lehre der vorliegenden Erfindung wird die oben aufgezeigte Aufgabe für ein Verfahren zur Herstellung eines Bandes aus einer AlMgSi-Legierung dadurch gelöst, dass das Warmband unmittelbar am Auslauf aus dem letzten Warmwalzstich eine Temperatur von maximal 130 °C, vorzugsweise eine Temperatur von maximal 100 °C aufweist und das Warmband mit dieser oder einer geringeren Temperatur aufgewickelt wird.According to a first teaching of the present invention, the above-indicated object for a method for producing a strip of an AlMgSi alloy is achieved in that the hot strip immediately at the outlet from the last hot roll pass a maximum temperature of 130 ° C, preferably a maximum temperature 100 ° C and the hot strip is wound at this or a lower temperature.
Es hat sich gezeigt, dass die Größe der Mg2Si-Ausscheidungen in einem Warmband einer AlMgSi-Legierung durch ein Abschrecken, d.h. durch eine beschleunigte Abkühlung, deutlich verringert werden kann. Durch das schnelle Abkühlen von einer Warmbandtemperatur zwischen 230 °C und 550 °C auf maximal 130 °C, vorzugsweise maximal 100 °C am Auslauf des letzten Warmwalzstichs wird der Gefügezustand des Warmbandes eingefroren, so dass sich grobe Ausscheidungen nicht mehr bilden können. Das resultierende Aluminiumband weist nach einem Lösungsglühen und Abschrecken an Enddicke eine deutlich verbesserte Dehnung bei üblichen Festigkeiten im Zustand T4 auf und eine gleiche oder sogar verbesserte Aushärtbarkeit zum Zustand T6. Diese Eigenschaftskombination ist bei Bändern aus AlMgSi-Legierungen bisher nicht erreicht worden.It has been found that the size of the Mg 2 Si precipitates in a hot strip of an AlMgSi alloy can be significantly reduced by quenching, ie by accelerated cooling. Due to the rapid cooling from a hot strip temperature between 230 ° C and 550 ° C to a maximum of 130 ° C, preferably at most 100 ° C at the outlet of the last hot roll pass, the microstructure state of the hot strip frozen, so that coarse excretions can no longer form. The resulting aluminum strip, after solution heat treatment and final thickness quenching, exhibits significantly improved elongation at conventional T4 strengths and equal or even improved T6 cure. This combination of properties has not yet been achieved for strips of AlMgSi alloys.
Gemäß einer vorteilhaften Ausführungsform des erfindungsgemäßen Verfahrens erfolgt dieser Abkühlvorgang innerhalb der letzten beiden Warmwalzstiche, d.h. die Abkühlung auf 130 °C und weniger erfolgt innerhalb von Sekunden, maximal innerhalb von fünf Minuten. Es hat sich gezeigt, dass bei dieser Vorgehensweise die erhöhten Dehnungswerte bei üblichen Festigkeits- bzw. Dehngrenzwerten im Zustand T4 und die verbesserte Aushärtbarkeit im Zustand T6 besonders prozesssicher erreicht werden.According to an advantageous embodiment of the method according to the invention, this cooling process takes place within the last two hot rolling passes, i. cooling to 130 ° C and less takes place within seconds, within a maximum of five minutes. It has been shown that in this procedure, the increased elongation values at the usual strength or expansion limits in the condition T4 and the improved hardenability in the condition T6 are achieved particularly reliably.
Gemäß einer ersten Ausgestaltung des erfindungsgemäßen Verfahrens wird eine besonders wirtschaftliche Realisierung des Verfahrens dadurch erzielt, dass das Warmband unter Verwendung von mindestens einem Platinenkühler und der mit Emulsion beaufschlagten Warmwalzstiche selbst auf Aufwickeltemperatur abgeschreckt wird. Ein Platinenkühler besteht aus einer Anordnung von Kühl- bzw. Schmiermitteldüsen, welche eine Walzemulsion auf das Aluminiumband sprühen. Der Platinenkühler ist häufig in einem Warmwalzwerk vorhanden, um gewalzte Warmbänder vor dem Warmwalzen auf Walztemperatur zu kühlen und die Aufwickeltemperatur einzustellen. Das erfindungsgemäße Verfahren kann somit auf konventionellen Anlagen ohne spezielle Zusatzeinrichtungen zum Einsatz gebracht werden.According to a first embodiment of the method according to the invention, a particularly economical realization of the method is achieved by quenching the hot strip itself to coiling temperature using at least one sinker cooler and the hot rolling passes applied with emulsion. A board cooler consists of an array of coolant or lubricant nozzles which spray a rolling emulsion onto the aluminum strip. The sinker cooler is often present in a hot rolling mill to cool rolled hot strip to roll temperature before hot rolling and to set the coiling temperature. The method according to the invention can thus be used on conventional systems without special ancillary equipment.
Per Definition liegt die Warmwalztemperatur oberhalb der Rekristallisationstemperatur eines Metalls, also bei Aluminium oberhalb ca. 230 °C. Entsprechend der Lehre der vorliegenden Erfindung liegt die Aufwickeltemperatur mit 130 °C aber deutlich unterhalb dieser prozessüblichen Bedingungen.By definition, the hot rolling temperature is above the recrystallization temperature of a metal, that is, above 230 ° C for aluminum. According to the teachings of the present invention, the coiling temperature at 130 ° C but significantly below these process conditions.
Beträgt die Warmwalztemperatur des Warmbandes vor dem vorletzten Warmwalzstich mindestens 230 °C, vorzugsweise über 400 °C, wird gemäß einer nächsten Ausgestaltung des erfindungsgemäßen Verfahrens erreicht, dass besonders kleine Mg2Si-Ausscheidungen im abgeschreckten Warmband vorhanden sind, da der größte Anteil der Legierungsbestandteile Magnesium und Silizium bei diesen Temperaturen im gelösten Zustand in der Aluminiummatrix vorliegen. Dieser vorteilhafte Zustand des Warmbandes wird durch das Abschrecken quasi "eingefroren".If the hot rolling temperature of the hot strip prior to the penultimate hot rolling pass at least 230 ° C, preferably above 400 ° C, is achieved according to a next embodiment of the method that particularly small Mg 2 Si precipitates are present in the quenched hot strip, since the largest proportion of alloying components Magnesium and silicon are present at these temperatures in the dissolved state in the aluminum matrix. This advantageous state of the hot strip is quasi "frozen" by quenching.
Die Dicke des fertigen Warmbandes beträgt 3 mm bis 12 mm, vorzugsweise 3,5 mm bis 8 mm, so dass übliche Kaltwalzgerüste für das Kaltwalzen verwendet werden können.The thickness of the finished hot strip is 3 mm to 12 mm, preferably 3.5 mm to 8 mm, so that conventional cold rolling stands for cold rolling can be used.
Die für das erfindungsgemäße Verfahren verwendete Aluminiumlegierung vom Legierungstyp AA6xxx ist vorzugsweise vom Typ AA6014, AA6016, AA6060, AA6111 oder AA6181. Allen Legierungstypen AA6xxx ist gemein, dass sie ein besonders gutes Umformverhalten gekennzeichnet durch hohe Dehnungswerte im Zustand T4 sowie sehr hohe Festigkeiten bzw. Dehngrenzen im Einsatzzustand T6, beispielsweise nach einem Warmauslagern bei 205 °C / 30 Min. aufweisen.The alloy AA6xxx alloy used for the process of the invention is preferably of the type AA6014, AA6016, AA6060, AA6111 or AA6181. All alloy types AA6xxx have in common that they have a particularly good forming behavior characterized by high elongation values in the state T4 and very high strength or yield strength in use state T6, for example, after a heat aging at 205 ° C / 30 min.
Gemäß einer weiteren Ausgestaltung des erfindungsgemäßen Verfahrens wird das fertig gewalzte Aluminiumband einer Wärmebehandlung unterzogen, wobei das Aluminiumband auf mehr als 100 °C erwärmt wird und anschließend mit einer Temperatur von mehr als 55 °C, vorzugsweise mehr als 85 °C aufgewickelt und ausgelagert. Diese Ausführungsform des Verfahrens ermöglicht es nach der Kaltauslagerung durch eine kürzere Erwärmungsphase mit niedrigeren Temperaturen den Zustand T6 in dem Aluminiumband oder Blech einzustellen, in welchem die zu Bauteilen umgeformten Bleche oder Bänder in der Anwendung eingesetzt werden. Diese schnellaushärtende Aluminiumbänder werden hierzu auf Temperaturen von etwa 185 °C für lediglich 20 Min. erwärmt, um die höheren Streckgrenzwerte im Zustand T6 zu erreichen. Zwar liegen die Bruchdehnungswerte A80 der mit dieser Ausführungsform des erfindungsgemäßen Verfahrens hergestellten Aluminiumbänder leicht unterhalb von 29 %. Das erfindungsgemäß hergestellte Aluminiumband zeichnet sich aber nach der Auslagerung im Zustand T4 weiterhin durch eine sehr gute Gleichmaßdehnung Ag von mehr als 25 % aus. Unter der Gleichmaßdehnung Ag versteht man die maximale Dehnung der Probe, bei welcher sich beim Zugversuch keine Einschnürung der Probe zeigt. Die Probe wird im Bereich der Gleichmaßdehnung also gleichmäßig gedehnt. Der Wert für die Gleichmaßdehnung lag bisher bei ähnlichen Werkstoffen bei maximal 22 % bis 23 %. Die Gleichmaßdehnung beeinflusst maßgeblich das Umformverhalten, da diese den in der Praxis verwendeten maximalen Umformgrad des Werkstoffs bestimmt. Insofern kann mit dem erfindungsgemäßen Verfahren ein Aluminiumband mit sehr guten Umformeigenschaften zur Verfügung gestellt werden, welches auch über eine beschleunigte Warmauslagerung (185°C/120 Min.) in den Zustand T6 überführt werden kann.According to a further embodiment of the method according to the invention, the finished rolled aluminum strip is subjected to a heat treatment, wherein the aluminum strip is heated to more than 100 ° C and then wound at a temperature of more than 55 ° C, preferably more than 85 ° C and paged. This embodiment of the method, after cold aging by a shorter heating phase at lower temperatures, allows to set the state T6 in the aluminum strip or sheet in which the sheet-formed or strip-formed components are used in the application. For this purpose, these fast-curing aluminum strips are heated to temperatures of about 185 ° C. for only 20 minutes in order to achieve the higher yielding limits in state T6. Although the elongation at break values A 80 of the aluminum strips produced with this embodiment of the method according to the invention are slightly below 29%. However, the aluminum strip produced according to the invention is still characterized by a very good uniform elongation A g of more than 25% after aging in state T4. Equal expansion A g is the maximum elongation of the sample at which no constriction of the sample is observed during the tensile test. The sample is thus stretched evenly in the region of the uniform expansion. The value for the uniform elongation used to be a maximum of 22% to 23% for similar materials. The uniform elongation significantly influences the forming behavior, since this determines the maximum degree of deformation of the material used in practice. In this respect, an aluminum strip with very good forming properties can be made available with the process according to the invention, which can also be converted into the state T6 via accelerated thermal aging (185 ° C./120 min.).
Eine Aluminiumlegierung vom Typ AA6016 weist folgende Legierungsbestandteile in Gewichtsprozent auf:
- 0,25 % ≤ Mg ≤ 0,6 %,
- 1,0 % ≤ Si ≤ 1,5 %,
- Fe ≤ 0,5 %,
- Cu ≤ 0,2 %,
- Mn ≤ 0,2 %,
- Cr ≤ 0,1 %,
- Zn ≤ 0,1 %,
- Ti ≤ 0,1 %
- 0.25% ≤ Mg ≤ 0.6%,
- 1.0% ≦ Si ≦ 1.5%,
- Fe ≤ 0.5%,
- Cu ≤ 0.2%,
- Mn≤0.2%,
- Cr ≤ 0.1%,
- Zn≤0.1%,
- Ti ≤ 0.1%
Bei Magnesiumgehalten von weniger als 0,25 Gew.-% ist die Festigkeit des Aluminiumbandes, welches für Strukturanwendungen vorgesehen ist zu gering, andererseits verschlechtert sich die Umformbarkeit bei Magnesiumgehalten oberhalb von 0,6 Gew.-%. Silizium ist im Zusammenspiel mit Magnesium im Wesentlichen für die Aushärtbarkeit der Aluminiumlegierung verantwortlich und somit auch für die hohen Festigkeiten, welche im Anwendungsfall beispielsweise nach einem Lackiereinbrennen erzielt werden können. Bei Si-Gehalten von weniger als 1,0 Gew.-% ist die Aushärtbarkeit des Aluminiumbandes verringert, so dass im Anwendungsfall nur verringerte Festigkeiten bereitgestellt werden können. Si-Gehalte von mehr als 1,5 Gew.-% führen aber zu Gießproblemen im Hinblick auf die Herstellung des Walzbarrens. Der Fe-Anteil sollte auf maximal 0,5 Gew-% begrenzt werden, um grobe Ausscheidungen zu verhindern. Eine Beschränkung des Kupfergehalts auf maximal 0,2 Gew.-% führt vor allem zu einer verbesserten Korrosionsbeständigkeit der Aluminiumlegierung in der spezifischen Anwendung. Der Mangangehalt von weniger als 0,2 Gew.-% verringert die Tendenz zur Bildung von gröberen Mangangausscheidungen. Chrom sorgt zwar für ein feines Gefüge, ist aber auf 0,1 Gew.-% zu beschränken, um ebenfalls grobe Ausscheidungen zu vermeiden. Das Vorhandensein von Mangan verbesserte dagegen die Schweißbarkeit durch Verringerung der Rissneigung beziehungsweise Abschreckempfindlichkeit des erfindungsgemäßen Aluminiumbandes. Eine Reduzierung des Zink-Gehaltes auf maximal 0,1 Gew.-% verbessert insbesondere die Korrosionsbeständigkeit der Aluminiumlegierung bzw. des fertigen Blechs in der jeweiligen Anwendung. Dagegen sorgt Titan für eine Kornfeinung während des Gießens, sollte aber auf maximal 0,1 Gew.-% beschränkt werden, um eine gute Gießbarkeit der Aluminiumlegierung zu gewährleisten.At magnesium contents of less than 0.25% by weight, the strength of the aluminum strip intended for structural applications is too low, while on the other hand the workability at magnesium contents deteriorates above 0.6% by weight. Silicon, in interaction with magnesium, is essentially responsible for the hardenability of the aluminum alloy and thus also for the high strength, which can be achieved in the application example after a Lackiereinbrennen. With Si contents of less than 1.0% by weight, the hardenability of the aluminum strip is reduced, so that only reduced strengths can be provided in the application. Si contents of more than 1.5% by weight, however, lead to casting problems with regard to the production of the rolling ingot. The Fe content should be limited to a maximum of 0.5% by weight to prevent coarse precipitation. A limitation of Copper content to a maximum of 0.2 wt .-% leads above all to improved corrosion resistance of the aluminum alloy in the specific application. The manganese content of less than 0.2% by weight reduces the tendency to form coarser manganese precipitates. Although chromium ensures a fine microstructure, it should be limited to 0.1% by weight in order to avoid coarse precipitation. In contrast, the presence of manganese improved the weldability by reducing the tendency to crack or quenching sensitivity of the aluminum strip according to the invention. A reduction of the zinc content to a maximum of 0.1% by weight improves in particular the corrosion resistance of the aluminum alloy or of the finished sheet in the respective application. In contrast, titanium provides grain refining during casting, but should be limited to a maximum of 0.1% by weight to ensure good castability of the aluminum alloy.
Eine Aluminiumlegierung vom Typ AA6060 weist folgende Legierungsbestandteile in Gewichtsprozent auf:
- 0,35 % ≤ Mg ≤ 0,6 %,
- 0,3 % ≤ Si ≤ 0,6 %,
- 0,1 % ≤ Fe ≤ 0,3 %
- Cu ≤ 0,1 %,
- Mn ≤ 0,1 %,
- Cr ≤ 0,05 %,
- Zn ≤ 0,10 %,
- Ti ≤ 0,1 % und
- 0.35% ≤ Mg ≤ 0.6%,
- 0.3% ≦ Si ≦ 0.6%,
- 0.1% ≤ Fe ≤ 0.3%
- Cu ≤ 0.1%,
- Mn ≤ 0.1%,
- Cr ≤ 0.05%,
- Zn≤0.10%,
- Ti ≤ 0.1% and
Die Kombination aus genau vorgegebenem Magnesiumgehalt mit einem im Vergleich zur ersten Ausführungsform reduzierten Si-Gehalt und eng spezifiziertem Fe-Gehalt ergibt eine Aluminiumlegierung, bei welcher besonders gut die Bildung Mg2Si Ausscheidungen nach dem Warmwalzen mit dem erfindungsgemäßen Verfahren verhindert werden kann, so dass ein Blech mit einer verbesserten Dehnung und hohen Dehngrenzen im Vergleich zu konventionell hergestellten Blechen bereitgestellt werden kann. Die geringeren Obergrenzen der Legierungsbestandteile Cu, Mn und Cr verstärken den Effekt des erfindungsgemäßen Verfahrens zusätzlich. Hinsichtlich der Auswirkungen der Obergrenze von Zn und Ti wird auf die Ausführungen zur ersten Ausführungsform der Aluminiumlegierung verwiesen.The combination of a precisely predetermined magnesium content with a reduced Si content and narrowly specified Fe content in comparison to the first embodiment results in an aluminum alloy in which the formation of Mg 2 Si precipitates after hot rolling can be prevented particularly well by the method according to the invention, so that a sheet with improved elongation and high yield strengths can be provided compared to conventionally produced sheets. The lower upper limits of the alloy components Cu, Mn and Cr additionally reinforce the effect of the method according to the invention. With regard to the effects of the upper limit of Zn and Ti, reference is made to the comments on the first embodiment of the aluminum alloy.
Eine Aluminiumlegierung vom Typ AA6014 weist folgende Legierungsbestandteile in Gewichtsprozent auf:
- 0,4 % ≤ Mg ≤ 0,8 %,
- 0,3 % ≤ Si ≤ 0,6 %,
- Fe ≤ 0,35 %
- Cu ≤ 0,25 %,
- 0,05 % ≤ Mn ≤ 0,20 %,
- Cr ≤ 0,20 %,
- Zn ≤ 0,10 %,
- 0,05 % ≤ V ≤ 0,20 %,
- Ti ≤ 0,1 % und
- 0.4% ≤ Mg ≤ 0.8%,
- 0.3% ≦ Si ≦ 0.6%,
- Fe ≤ 0.35%
- Cu ≤ 0.25%,
- 0.05% ≤ Mn ≤ 0.20%,
- Cr ≤ 0.20%,
- Zn≤0.10%,
- 0.05% ≤ V ≤ 0.20%,
- Ti ≤ 0.1% and
Eine Aluminiumlegierung vom Typ AA6181 weist folgende Legierungsbestandteile in Gewichtsprozent auf:
- 0,6 % ≤ Mg ≤ 1,0 %,
- 0,8 % ≤ Si ≤ 1,2 %,
- Fe ≤ 0,45 %
- Cu ≤ 0,10 %,
- Mn ≤ 0,15 %,
- Cr ≤ 0,10 %,
- Zn ≤ 0,20 %,
- Ti ≤ 0,1 % und
- 0.6% ≤ Mg ≤ 1.0%,
- 0.8% ≦ Si ≦ 1.2%,
- Fe ≤ 0.45%
- Cu ≤ 0.10%,
- Mn ≤ 0.15%,
- Cr ≤ 0.10%,
- Zn≤0.20%,
- Ti ≤ 0.1% and
Eine Aluminiumlegierung vom Typ AA6111 weist folgende Legierungsbestandteile in Gewichtsprozent auf:
- 0,5 % ≤ Mg ≤ 1,0 %,
- 0,7 % ≤ Si ≤ 1,1 %,
- Fe ≤ 0,40 %
- 0,50 % ≤ Cu ≤ 0,90 %,
- 0,15 % ≤ Mn ≤ 0,45 %,
- Cr ≤ 0,10 %,
- Zn ≤ 0,15 %,
- Ti ≤ 0,1 % und
- 0.5% ≤ Mg ≤ 1.0%,
- 0.7% ≦ Si ≦ 1.1%,
- Fe ≤ 0.40%
- 0.50% ≤ Cu ≤ 0.90%,
- 0.15% ≤ Mn ≤ 0.45%,
- Cr ≤ 0.10%,
- Zn ≤ 0.15%,
- Ti ≤ 0.1% and
Alle aufgezeigten Aluminiumlegierungen sind spezifisch in ihren Legierungsbestandteilen auf unterschiedliche Anwendungen angepasst. Wie bereits ausgeführt, zeigen Bänder aus diese Aluminiumlegierungen, welche unter Verwendung des erfindungsgemäßen Verfahrens hergestellt wurden, besonders hohe Dehnungswerte im Zustand T4 gepaart mit einer besonders ausgeprägten Steigerung der Dehngrenze beispielsweise nach einem Warmauslagern bei 205 °C / 30 Min.. Dies gilt auch für die nach dem Lösungsglühen einer Wärmebehandlung unterzogenen Aluminiumbändern im Zustand T4.All the aluminum alloys shown are specifically adapted to different applications in their alloy components. As already stated, tapes made of these aluminum alloys, which were produced using the method according to the invention, exhibit particularly high elongation values in state T4, coupled with a particularly pronounced increase in the yield strength, for example after heat aging at 205 ° C./30 min. This also applies to the aluminum strips subjected to a heat treatment after solution treatment in the condition T4.
Gemäß einer zweiten Lehre der vorliegenden Erfindung wird die oben aufgezeigte Aufgabe durch ein Aluminiumband mit den Merkmalen des Patentanspruchs 7. Der Auslieferungszustand T4 wird üblicherweise durch ein Lösungsglühen mit Abschrecken und einer anschließenden Lagerung bei Raumtemperatur für mindestens drei Tage erreicht, da dann die Eigenschaften der lösungsgeglühten Bleche oder Bänder stabil sind. Die Kombination aus Bruchdehnung A80 und Dehngrenze Rp0,2 des erfindungsgemäßen Aluminiumbandes ist mit bisher bekannten AlMgSi-Legierungen nicht erreicht worden. Das erfindungsgemäße Aluminiumband ermöglicht daher maximale Umformgrade aufgrund der hohen Dehnungswerte mit maximalen Werten für die Dehngrenze Rp0,2 im fertigen Blech bzw. Bauteil.According to a second teaching of the present invention, the above object is achieved by an aluminum strip with the features of
Besonders vorteilhafte Umformeigenschaften erreicht eine Ausführungsform des erfindungsgemäßen MgSi-Aluminiumbands dadurch, dass zusätzlich die Gleichmaßdehnung Ag mehr als 25 % beträgt. Die Gleichmaßdehnung bestimmt maßgeblich den maximalen Umformgrad des Aluminiumbandes bzw. des daraus hergestellten Blechs bei der Herstellung von Bauteilen, da unkontrollierte Einschnürungen bei der Herstellung vermieden werden müssen. Das erfindungsgemäße Aluminiumband hat eine besonders hohe Umformreserve in Bezug auf Einschnürungen und kann deshalb prozesssicherer zu Bauteilen umgeformt werden.Particularly advantageous forming properties are achieved by an embodiment of the MgSi aluminum strip according to the invention in that in addition the uniform elongation A g is more than 25%. The uniform expansion significantly determines the maximum degree of deformation of the aluminum strip or the sheet produced therefrom in the manufacture of components, since uncontrolled constrictions during manufacture must be avoided. The aluminum strip according to the invention has a particularly high forming reserve with respect to constrictions and can therefore be converted to components with greater process reliability.
Vorzugsweise weist das erfindungsgemäße Aluminiumband im Zustand T6, also im Einsatzzustand bzw. Anwendungszustand, eine Dehngrenze Rp0,2 von mehr als 185 MPa bei einer Dehnung A80 von mindestens 15 % auf. Diese Werte wurden bei erfindungsgemäß hergestellten Aluminiumbändern im Zustand T6 gemessen, welche eine Warmauslagerung bei 205 °C/30 Min. nach einem Lösungsglühen und Abschrecken (Zustand T4) durchlaufen haben. Aufgrund der hohen Dehngrenzen im Zustand T6 bei sehr guten Dehnungswerten im Zustand T4 ist das erfindungsgemäße Aluminiumband beispielsweise für die Verwendung im Kraftfahrzeugbau besonders gut geeignet.The aluminum strip according to the invention preferably has a yield strength Rp0.2 of greater than 185 MPa at an elongation A 80 of at least 15% in the condition T6, that is to say in the use or application state. These values were measured in the aluminum tapes according to the invention in the condition T6, which have undergone a heat aging at 205 ° C / 30 min. After a solution heat treatment and quenching (state T4). Due to the high yield strengths in state T6 with very good elongation values in state T4, the aluminum strip according to the invention is particularly well suited for use in motor vehicle construction, for example.
Gemäß einer weiteren Ausführungsform der Erfindung weist das lösungsgeglühte und abgeschreckte Aluminiumband nach einer Warmauslagerung bei 205 °C / 30 Min. im Zustand T6 eine Dehngrenzendifferenz ΔRp0,2 zwischen Zustand T6 und T4 von mindestens 80 MPa auf. Die Steigerung der Dehngrenze vom Zustand T4 in den Zustand T6 ist bei dem erfindungsgemäßen Aluminiumband besonders hoch. Das erfindungsgemäße Aluminiumband kann deshalb im Zustand T4 sehr gut umgeformt und anschließend durch ein Warmauslagern in einen hochfesten Einsatzzustand (Zustand T6) versetzt werden kann. Bei den notwendigen, komplexen Formgebungen und den geforderten hohen Festigkeitswerten bzw. Dehngrenzen, beispielsweise im Kraftfahrzeugbau, ist eine gute Aushärtbarkeit für die Herstellung komplexer Bauteile von besonderem Vorteil.According to a further embodiment of the invention, the solution-annealed and quenched aluminum strip after heat aging at 205 ° C / 30 min. In the state T6, a strain limit difference ΔRp0,2 between state T6 and T4 of at least 80 MPa. The increase in the yield strength from state T4 to state T6 is particularly high in the case of the aluminum strip according to the invention. The aluminum strip according to the invention can therefore be formed very well in the condition T4 and then be put into a high-strength use state (state T6) by heat aging. With the necessary, complex shapes and the required high Strength values or expansion limits, for example in motor vehicle construction, is a good hardenability for the production of complex components of particular advantage.
Ein schnell aushärtendes AlMgSi-Aluminiumband mit hervorragenden Umformeigenschaften wird mit einem Aluminiumband gemäß Patentanspruch 11 bereitgestellt. Das erfindungsgemäß hergestellte Aluminiumband nach Patentanspruch 11 wird nach dessen Herstellung einem Lösungsglühen mit anschließender Wärmebehandlung unterzogen und weist im Zustand T4 eine Gleichmaßdehnung Ag von mehr als 25 % bei einer Dehngrenze Rp0,2 von 80 bis 140 MPa auf. Wie ausgeführt, kann mit dieser Variante ein schnellaushärtbares und zugleich sehr gut umformbares MgSi-Aluminiumband zur Verfügung gestellt werden. Die Warmauslagerung zur Erzielung des Zustandes T6 kann 185 °C für 20 Min. erfolgen, um die erforderlichen Dehngrenzsteigerungen zu erzielen.A fast-hardening AlMgSi aluminum strip with excellent forming properties is provided with an aluminum strip according to
Weist das Aluminiumband gemäß einer nächsten Ausgestaltung eine Gleichmaßdehnung Ag von mehr als 25 % in Walzrichtung, quer zur Walzrichtung und diagonal zur Walzrichtung auf, kann ein besonders isotropes Umformvermögen ermöglicht werden. Vorzugsweise weisen die Aluminiumbänder eine Dicke von 0,5 mm bis 12 mm auf. Aluminiumbänder mit Dicken von 0,5 mm bis 2 mm werden vorzugsweise für Karosserieteile beispielsweise im Kraftfahrzeugbau verwendet, während Aluminiumbänder mit größeren Dicken von 2 bis 4,5 mm beispielsweise in Fahrwerksteilen im Kraftfahrzeugbau Anwendungen finden. Einzelne Komponenten können im Kaltband auch mit einer Dicke von bis 6 mm gefertigt werden. Daneben können in spezifischen Anwendungen auch Aluminiumbänder mit Dicken von bis zu 12 mm verwendet werden. Diese Aluminiumbänder mit sehr großer Dicke werden üblicherweise nur durch Warmwalzen bereitgestellt.If, according to a next embodiment, the aluminum strip has a uniform elongation A g of more than 25% in the rolling direction, transversely to the rolling direction and diagonally to the rolling direction, a particularly isotropic forming capability can be made possible. Preferably, the aluminum strips 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 bands with larger thicknesses of 2 to 4.5 mm, for example, find in chassis parts in automotive applications. Individual components can also be manufactured in a cold-rolled strip with a thickness of up to 6 mm. In addition, in specific Applications also aluminum strips with thicknesses of up to 12 mm can be used. These very thick aluminum strips are usually provided only by hot rolling.
Das erfindungsgemäße Aluminiumband ist vom Legierungstyp AA6014, AA6016, AA6060, AA6111 oder AA6181. Hinsichtlich der Vorteile dieser Aluminiumlegierungen wird auf die Ausführungen zum erfindungsgemäßen Verfahren verwiesen.The aluminum strip according to the invention is of the alloy type AA6014, AA6016, AA6060, AA6111 or AA6181. With regard to the advantages of these aluminum alloys, reference is made to the comments on the method according to the invention.
Aufgrund der hervorragenden Kombination zwischen guter Umformbarkeit im Zustand T4, hoher Korrosionsbeständigkeit sowie hohen Werten für die Dehngrenze Rp0,2 im Einsatzzustand (Zustand T6) wird die oben aufgeführte Aufgabe gemäß einer dritten Lehre der vorliegenden Erfindung durch die Verwendung eines aus einem erfindungsgemäßen Aluminiumband hergestellten Blechs als Bauteil, Fahrwerks- oder Strukturteil und -blech im Kraftfahrzeug-, Flugzeug- oder Schienenfahrzeugbau, insbesondere als Komponente, Fahrwerksteil, Außen- oder Innenblech im Kraftfahrzeugbau, vorzugsweise als Karosseriebauelement, gelöst. Vor allem sichtbare Karosserieteile, beispielsweise Motorhauben, Kotflügel etc. sowie Außenhautteile eines Schienenfahrzeugs oder Flugzeugs profitieren von den hohen Dehngrenzen Rp0,2 bei guten Oberflächeneigenschaften auch nach einem Umformen mit hohen Umformgraden.Due to the excellent combination of good formability in the state T4, high corrosion resistance and high yield strength Rp0.2 in the use state (state T6), the above object according to a third teaching of the present invention by the use of a sheet produced from an aluminum strip according to the invention as a component, suspension or structural part and sheet metal in automotive, aircraft or rail vehicle, in particular as a component, chassis part, outer or inner panel in the automotive industry, preferably as a body component solved. Above all, visible body parts, such as hoods, fenders, etc., as well as outer skin parts of a rail vehicle or aircraft benefit from the high yield strengths Rp0.2 with good surface properties even after forming with high degrees of deformation.
Es gibt nun eine Vielzahl von Möglichkeiten das erfindungsgemäße Verfahren sowie das erfindungsgemäße Aluminiumband und die Verwendung eines daraus hergestellten Blechs auszugestalten und weiterzubilden. Hierzu wird verwiesen auf die Beschreibung von Ausführungsbeispielen in Verbindung mit der Zeichnung.There are now a variety of ways to design the method of the invention and the aluminum strip according to the invention and the use of a sheet produced therefrom and further. For this purpose is refer to the description of embodiments in conjunction with the drawings.
Die Zeichnung zeigt in der einzigen
Zunächst wird ein Walzbarren 1 aus einer Aluminiumlegierung mit den folgenden Legierungsbestandteilen in Gewichtsprozent gegossen:
- 0,35 % ≤ Mg ≤ 0,6 %,
- 0,3 % ≤ Si ≤ 0,6 %,
- 0,1 % ≤ Fe ≤ 0,3 %
- Cu ≤ 0,1 %,
- Mn ≤ 0,1 %,
- Cr ≤ 0,05 %,
- Zn ≤ 0,1 %,
- Ti ≤ 0,1 % und
- 0.35% ≤ Mg ≤ 0.6%,
- 0.3% ≦ Si ≦ 0.6%,
- 0.1% ≤ Fe ≤ 0.3%
- Cu ≤ 0.1%,
- Mn ≤ 0.1%,
- Cr ≤ 0.05%,
- Zn≤0.1%,
- Ti ≤ 0.1% and
Der so hergestellte Walzbarren wird bei einer Homogenisierungstemperatur von etwa 550 °C für 8 h in einem Ofen 2 homogenisiert, so dass die zulegierten Legierungsbestandteile besonders homogen verteilt im Walzbarren vorliegen,
In
Dadurch, dass das Warmband 4 unmittelbar am Auslauf des letzten Warmwalzstichs eine Temperatur von maximal 130 °C bzw. maximal 100 °C aufweist bzw. optional in den letzten beiden Warmwalzstichen unter Verwendung des Platinenkühlers 5 und der Arbeitswalzen des Warmwalzgerüstes 3 auf eine Temperatur unterhalb von 130 °C bzw. unter 100°C gebracht wird, weist das Warmband 4 einen eingefrorenen Kristallgefügezustand auf, da keine zusätzliche Energie in Form von Wärme für nachfolgende Ausscheidungsvorgänge zur Verfügung steht. Das Warmband mit einer Dicke von 3 bis 12 mm, vorzugsweise 3,5 bis 8 mm wird über die Aufwickelhaspel 6 aufgewickelt. Wie bereits ausgeführt, beträgt die Aufwickeltemperatur im vorliegenden Ausführungsbeispiel weniger als 95 °C.Characterized in that the
Bei dem erfindungsgemäßen Verfahren können sich in dem aufgewickelten Warmband 4 jetzt keine oder nur wenige grobe Mg2Si-Ausscheidungen bilden. Das Warmband 4 hat einen für die Weiterverarbeitung sehr günstigen Kristallzustand und kann von der Abwickelhaspel 7 abgewickelt beispielsweise einem Kaltwalzgerüst 9 zugeführt und wieder auf einer Aufwickelhaspel 8 aufgewickelt werden,
Das resultierende, kaltgewalzte Band 11 wird aufgewickelt. Anschließend wird es einem Lösungsglühen und Abschrecken 10 zugeführt,
Bei größeren Aluminiumbanddicken, beispielsweise bei Fahrwerksanwendungen oder Komponenten wie beispielsweise Bremsankerplatten können auch alternativ Stückglühungen durchgeführt werden und die Bleche anschließend abgeschreckt werden.In the case of larger aluminum strip thicknesses, for example in chassis applications or components such as brake anchor plates, it is also possible alternatively to carry out piece annealing and then to quench the metal sheets.
Im Zustand T6 wird das Aluminiumband oder das Aluminiumblech durch eine Warmauslagerung bei 100 °C bis 220 °C gebracht, um maximale Werte für die Dehngrenze zu erzielen. Beispielsweise kann eine Warmauslagerung bei 205 °C/ 30 Min. durchgeführt.In state T6, the aluminum strip or the aluminum sheet is brought by cold aging at 100 ° C to 220 ° C in order to achieve maximum values for the yield strength. For example, a hot aging at 205 ° C / 30 min. Performed.
Die gemäß dem dargestellten Ausführungsbeispiel hergestellten Aluminiumbänder weisen nach dem Kaltwalzen beispielsweise eine Dicke von 0,5 bis 4,5 mm auf. Banddicken von 0,5 bis 2 mm werden üblicherweise für Karosserieanwendungen bzw. Banddicken von 2,0 mm bis 4,5 mm für Fahrwerksteile im Kraftfahrzeugsbau verwendet. In beiden Anwendungsbereichen sind die verbesserten Dehnungswerte bei der Herstellung der Bauteile von entscheidendem Vorteil, da zumeist starke Umformungen der Bleche durchgeführt werden und trotzdem hohe Festigkeiten im Einsatzzustand (T6) des Endprodukt benötigt werden.The aluminum strips produced according to the illustrated embodiment, for example, have a thickness of 0.5 to 4.5 mm after cold rolling. Tape thicknesses of 0.5 to 2 mm are commonly used for body applications or tape thicknesses of 2.0 mm to 4.5 mm for chassis parts in the automotive industry. In both applications, the improved elongation values in the manufacture of the components are of decisive advantage, since in most cases strong deformation of the sheets is carried out and nevertheless high strengths in the operating condition (T6) of the end product are required.
In Tabelle 1 sind die Legierungszusammensetzungen von Aluminiumlegierungen angegeben, aus welchen konventionell oder erfindungsgemäß Aluminiumbänder hergestellt wurden. Neben den gezeigten Gehalten an Legierungsbestandteilen enthalten die Aluminiumbänder als Restanteil Aluminium und Verunreinigungen, einzeln maximal 0,05 Gew.-% und in Summe maximal 0,15 Gew.-%.
Die Bänder (Proben) 409 und 410 wurden mit einem erfindungsgemäßen Verfahren hergestellt, bei welchem das Warmband innerhalb der letzten beiden Warmwalzstiche von etwa 400°c auf 95 °C unter Verwendung eines Platinenkühlers sowie der Warmwalzen selbst abgekühlt und aufgewickelt wurde. In Tabelle 2 sind die Messwerte dieser Bänder mit "Inv." gekennzeichnet. Anschließend erfolgte ein Kaltwalzen auf eine Enddicke von 1,04 mm.The tapes (samples) 409 and 410 were made by a process according to the invention in which the hot strip was cooled and wound up within the last two hot rolling passes from about 400 ° C to 95 ° C using a sinker cooler and the hot rolls themselves. Table 2 shows the measured values of these bands as "Inv." characterized. Subsequently, a cold rolling to a final thickness of 1.04 mm.
Die Bänder (Proben) 491-1 und 491-11 wurden mit einem konventionellen Warmwalzen und Kaltwalzen hergestellt und mit einem "Konv." gekennzeichnet.The tapes (samples) 491-1 and 491-11 were made with conventional hot rolling and cold rolling and with a "conv." characterized.
Die in Tabelle 2 dargestellten Resultate der mechanischen Eigenschaften zeigen deutlich den Unterschied in den erzielbaren Dehnungswerten A80.
Zur Erzielung des T4-Zustands wurden die Bänder einem Lösungsglühen mit nachfolgender Abschreckung und einer anschließender Kaltauslagerung bei Raumtemperatur unterworfen. Der T6-Zustand wurde durch eine Warmauslagerung bei 205 °C für 30 Minuten erreicht.To achieve the T4 state, the strips were subjected to solution annealing with subsequent quenching and subsequent cold aging at room temperature. The T6 state was achieved by hot aging at 205 ° C for 30 minutes.
Es zeigte sich, dass das vorteilhafte Gefüge, welches über das erfindungsgemäße Verfahren in den Bänder 409 und 410 eingestellt wurde, bei gestiegener Dehngrenze Rp0,2 und Festigkeit Rm eine Steigerung der Dehnung A80 ermöglichte.It was found that the advantageous microstructure, which was set by means of the method according to the invention in bands 409 and 410, made it possible to increase the elongation A 80 with increased yield strength Rp0.2 and strength Rm.
Dieses Gefüge führt zu der besonders vorteilhaften Kombination aus hoher Bruchdehnung A80 von mindestens 30 % bzw. mindestens 30 % bei sehr hohen Werten für die Dehngrenze Rp0,2 von 80 bis 140 MPa. Im Zustand T6 kann die Dehngrenze bis auf über 185 MPa ansteigen, wobei die Dehnung A80 weiterhin bei mehr als 15 % verbleibt. Die Aushärtbarkeit mit einem ΔRp0,2 von 87 bzw. 97 MPa zeigt, dass die erfindungsgemäßen Ausführungsbeispiele trotz der erhöhten Dehnungswerte von mehr als 15 % eine sehr gute Steigerung der Dehngrenze im warmausgelagerten Zustand T6 bei einer Warmauslagerung bei 205 °C / 30 Min. erreichen.This structure leads to the particularly advantageous combination of high elongation at break A 80 of at least 30% and at least 30% at very high values for the yield strength Rp0.2 of 80 to 140 MPa. In state T6, the yield strength can increase to over 185 MPa, with the elongation A 80 still remaining at more than 15%. The curability with a ΔRp0.2 of 87 and 97 MPa shows that the embodiments according to the invention, despite the increased elongation values of more than 15%, achieve a very good increase in the yield strength in the warm-aged state T6 during a heat aging at 205 ° C./30 min ,
Auch der Vergleich der Gleichmaßdehnungen Ag der erfindungsgemäßen Bänder und der konventionellen Bänder zeigt, dass die Gleichmaßdehnung Ag mit mehr als 25 % bei den erfindungsgemäßen Bändern 409 und 410, die Werte der konventionellen Bänder, welche mit 23 % gemessen wurden, deutlich übersteigen. In der Tabelle 2 sind die Werte für die Gleichmaßdehnung quer zur Walzrichtung gemessen worden. An in der Tabelle 2 nicht dargestellten Bändern, die mit dem erfindungsgemäßen Verfahren vermessen wurden, sind Werte über 25 % für die Gleichmaßdehnung Ag auch diagonal und in Walzrichtung bestimmt worden. Diese Ergebnisse unterstreichen das außergewöhnliche Umformvermögen der erfindungsgemäßen Bänder.The comparison of the uniform elongations A g of the tapes according to the invention and the conventional tapes also shows that the uniform elongation A g of more than 25% in the tapes 409 and 410 according to the invention clearly exceeds the values of the conventional tapes measured at 23%. In Table 2, the values for the uniform elongation transverse to the rolling direction have been measured. On tapes, not shown in Table 2, which were measured by the method according to the invention, values above 25% for the uniform elongation A g have also been determined diagonally and in the rolling direction. These results underscore the exceptional formability of the tapes of the invention.
Die Bruchdehnungswerte Ag und A80, die Dehngrenzwerte Rp0,2 und die Zugfestigkeitswerte Rm in den nachfolgenden Tabellen wurden nach DIN EN gemessen.The elongation at break values A g and A 80 , the elongation limits Rp0,2 and the tensile strength values Rm in the following tables were measured according to DIN EN.
Die Messwerte konnten im Zustand T4 durch Messungen an weiteren Bändern verifiziert werden. Die Aluminiumlegierung der Bänder A und B wiesen folgende Zusammensetzung auf:
- 0,25 % ≤ Mg ≤ 0,6 %,
- 1,0 % ≤ Si ≤ 1,5 %,
- Fe ≤ 0,5 %,
- Cu ≤ 0,2 %,
- Mn ≤ 0,2 %,
- Cr ≤ 0,1 %,
- Zn ≤ 0,1 %,
- Ti ≤ 0,1 %
- 0.25% ≤ Mg ≤ 0.6%,
- 1.0% ≦ Si ≦ 1.5%,
- Fe ≤ 0.5%,
- Cu ≤ 0.2%,
- Mn≤0.2%,
- Cr ≤ 0.1%,
- Zn≤0.1%,
- Ti ≤ 0.1%
Die Bänder A und B wurden unter Verwendung des erfindungsgemäßen Verfahrens mit einem Abschrecken des Warmbandes innerhalb der letzten zwei Warmwalzstiche auf 95 °C aufgewickelt und anschließend auf eine Enddicke von 1,0 mm respektive 3,0 mm kaltgewalzt. Um den Zustand T4 zu erreichen wurden die Bänder A und B lösungsgeglüht und nach einem Abschrecken kalt ausgelagert.The A and B tapes were wound to 95 ° C using the quenching process of the present invention within the last two hot rolling passes and then cold rolled to a final thickness of 1.0 mm and 3.0 mm, respectively. In order to reach the state T4, the strips A and B were solution-annealed and cold-aged after quenching.
Folgende Messwerte konnten an beiden Bänder ermittelt werden:
Die noch einmal gesteigerten Dehnungswerte A80 zeigen die herausragende Eignung dieser Aluminiumbänder für die Herstellung von Bauteilen, bei welchen sehr hohe Umformgrade während der Herstellung im Zustand T4 mit maximalen Zugfestigkeiten Rm und Dehngrenzen Rp0,2 im Zustand T6 kombiniert werden müssen.The once again increased elongation values A 80 show the outstanding suitability of these aluminum strips for the production of components, in which very high degrees of deformation must be combined during production in state T4 with maximum tensile strengths Rm and elongation limits Rp0.2 in state T6.
Darüber hinaus wurden weitere Aluminiumbänder untersucht, welche einer zusätzlichen Wärmebehandlung, die vorzugsweise unmittelbar nach dem Fertigstellen des Produktes, beispielsweise unmittelbar nach dem Lösungsglühen und Abschrecken am Aluminiumband durchgeführt wurde. Die Aluminiumbänder wurden hierzu kurzzeitig auf über 100 °C erwärmt und anschließend mit einer Temperatur von mehr als 85 °C, vorliegend mit 88 °C aufgewickelt und kalt ausgelagert.In addition, further aluminum strips were tested, which was an additional heat treatment, which was preferably carried out immediately after the completion of the product, for example, immediately after the solution heat treatment and quenching on the aluminum strip. For this purpose, the aluminum strips were briefly heated to above 100 ° C. and then wound up at a temperature of more than 85 ° C., in the present case at 88 ° C., and cold-aged.
Tabelle 4 zeigt die Zusammensetzung des Bandes 342, welches mit der zusätzlichen Wärmebehandlung nach dem Lösungsglühen und Abschrecken behandelt wurde.
Die Wärmebehandlung, ein sogenannter Pre-Bake-Schritt, führte zwar dazu, dass die Bruchdehnungseigenschaften sich verschlechterten, da die Bruchdehnung A80 nunmehr unter 30 % betrug. Überraschender Weise blieb die Gleichmaßdehnung des Aluminiumbandes P342 unverändert gegenüber den nicht Wärme behandelten Varianten bei mehr als 25%, wie Tabelle 5 zeigt. Die Gleichmaßdehnung ist ein sehr wichtiger Faktor bei der Umformung des Aluminiumbandes zu einem Bauteil, da eine verbesserte Gleichmaßdehnung höhere Umformgrade und damit entweder eine prozesssichere Fertigung oder weniger Umformschritte ermöglicht.The heat treatment, a so-called pre-bake step, led to the fact that the elongation at break properties deteriorated because the elongation at break A 80 was now below 30%. Surprisingly, the uniform elongation of the aluminum strip P342 remained unchanged compared to the non-heat treated variants at more than 25%, as Table 5 shows. The uniform strain is a very important factor in the transformation of the aluminum strip into a component, since an improved uniform elongation allows higher degrees of deformation and thus either a reliable production or fewer forming steps.
In Tabelle 5 sind verschiedene Messwerte dargestellt. Einerseits wurden drei Messungen am Bandanfang P342-BA und am Bandende P342-BE durchgeführt. In der Spalte "Zustand" ist angegeben, dass sich das Band im Zustand T4, also lösungsgeglüht und abgeschreckt, nach einer Kaltauslagerung bei Raumtemperatur von 8 Tagen befanden. Die Bänder vom Bandanfang und Bandende wurden in Längsrichtung (L) also in Walzrichtung, quer zur Walzrichtung (Q) und diagonal (D) zur Walzrichtung ausgeschnitten und vermessen. Es zeigte sich zwar ein Abfall der Bruchdehnungswerte A80mm auf teilweise unter 30 %, die Gleichmaßdehnung Ag wurde aber in allen Richtungen mit größer als 25 % gemessen und blieb im Vergleich zur Bruchdehnung der nicht Wärme behandelten überraschenderweise konstant.
Bei einer späteren Warmauslagerung konnte der Zustand T6 nach 20 Min. bei 185 °C erreicht werden. Typische Werte gemessene im Zustand T6 lagen für die Streckgrenze bei mehr als 140 MPa nach der Warmauslagerung bzw. mehr als 165 MPa nach einer Warmauslagerung und einem anschließenden Recken um 2%. Das erfindungsgemäß hergestellte Aluminiumband, welches zusätzlich einer Wärmebehandlung unterzogen wurde, kombiniert daher zwei wichtige Eigenschaften. Es lässt sich im Zustand T4 aufgrund der hohen Gleichmaßdehnung sehr gut Umformen und erreicht gleichzeitig nach einer Warmauslagerung bei 185 °C für 20 Min. die gewünschte Festigkeit.In a later artificial aging, the condition T6 could be reached after 20 min. At 185 ° C. Typical values measured in state T6 were for the yield strength at more than 140 MPa after hot aging or more than 165 MPa after a hot aging and subsequent stretching by 2%. The aluminum strip produced according to the invention, which has additionally been subjected to a heat treatment, therefore combines two important properties. It can be in the state T4 due to the high uniformity very good strain forming and achieved at the same time after a hot aging at 185 ° C for 20 min. The desired strength.
Claims (14)
- A method for producing a strip of an AlMgSi alloy of the type AA6xxx, in which a rolling ingot is cast from an AlMgSi alloy of the type AA6xxx, the rolling ingot is subjected to homogenization, the rolling ingot, which has been brought to hot rolling temperature, is hot rolled and then optionally cold rolled to its final thickness, characterized in that immediately at the exit from the last hot rolling pass, the hot strip has a temperature of at most 130 °C, preferably a temperature of at most 100 °C, and the hot strip is coiled at this or at a lower temperature.
- The method according to claim 1,
characterized in that the hot strip is quenched to the exiting temperature using at least one plate cooler and the emulsion charged hot rolling passes themselves. - The method according to claim 1 or 2,
characterized in that the hot rolling temperature of the hot strip is at least 230 °C, preferably above 400 °C, before the cooling process during hot rolling, particularly before the penultimate hot rolling pass. - The method according to any one of claims 1 to 3,
characterized in that the thickness of the finished hot strip is 3 mm to 12 mm, preferably 3.5 mm to 8 mm. - The method according to any one of claims 1 to 4,
characterized in that the aluminium alloy is of the alloy type AA6014, AA6016, AA6060, AA6111 or AA6181. - The method as recited in any one of claims 1 to 5,
characterized in that the finish rolled aluminium strip is subjected to a heat treatment in which the aluminium strip is heated to above 100 °C and is then coiled and aged at a temperature above 55 °C, preferably above 85 °C. - An aluminium strip comprising an AlMgSi alloy of the alloy type AA6014, AA6016, AA6060, AA6111 or AA6181 produced with a method according to any one of claims 1 to 5,
characterized in that the aluminium strip in the T4 state has an elongation at fracture A80 of at least 30 % with a yield strength of Rp0.2 of from 80 to 140 MPa. - The aluminium strip according to claim 7,
characterized in that the aluminium strip in the T4 state has a uniform elongation Ag of more than 25 %. - The aluminium strip according to claim 7 or 8,
characterized in that the solution annealed and quenched aluminium strip after artificial aging at 205 °C / 30 minutes in the T6 state has a yield strength of Rp0.2 of more than 185 MPa. - The aluminium strip according to any one of claims 7 to 9,
characterized in that the solution annealed and quenched aluminium strip after artificial aging at 205°C / 30 minutes in the T6 state has a yield strength difference ΔRp0.2 between states T6 and T4 of at least 80 MPa. - A rapidly curing aluminium strip comprising an AlMgSi alloy of the alloy type AA6014, AA6016, AA6060, AA6111 or AA6181 produced with a method according to claim 6,
characterized in that the aluminium strip has a uniform elongation Ag of more than 25 % with a yield strength of Rp0.2 of 80 to 140 MPa. - The aluminium strip according to claim 11 or 8,
characterized in that the aluminium strip has a uniform elongation Ag of more than 25 % in the direction of rolling, transversely to the direction of rolling and/or diagonally to the direction of rolling. - The aluminium strip according to one any of claims 7 to 12,
characterized in that the aluminium strip has a thickness of 0.5 to 12 mm. - Use of a metal sheet produced from an aluminium strip according to any one of claims 7 to 13 as a component, chassis or structural element or as a metal sheet in automotive, aircraft or railcar engineering, particularly as a component, chassis element, exterior or interior metal sheet in automotive engineering, preferably as a bodywork structural element.
Priority Applications (1)
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EP10723562.4A EP2449145B1 (en) | 2009-06-30 | 2010-05-21 | AlMgSi-sheet for applications with high shaping requirements |
Applications Claiming Priority (3)
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EP09164221.5A EP2270249B2 (en) | 2009-06-30 | 2009-06-30 | AlMgSi-sheet for applications with high shaping requirements |
EP10723562.4A EP2449145B1 (en) | 2009-06-30 | 2010-05-21 | AlMgSi-sheet for applications with high shaping requirements |
PCT/EP2010/057071 WO2011000635A1 (en) | 2009-06-30 | 2010-05-21 | Almgsi strip for applications having high plasticity requirements |
Publications (2)
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EP2449145A1 EP2449145A1 (en) | 2012-05-09 |
EP2449145B1 true EP2449145B1 (en) | 2019-08-07 |
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EP09164221.5A Active EP2270249B2 (en) | 2009-06-30 | 2009-06-30 | AlMgSi-sheet for applications with high shaping requirements |
EP10723562.4A Revoked EP2449145B1 (en) | 2009-06-30 | 2010-05-21 | AlMgSi-sheet for applications with high shaping requirements |
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EP09164221.5A Active EP2270249B2 (en) | 2009-06-30 | 2009-06-30 | AlMgSi-sheet for applications with high shaping requirements |
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US (2) | US10047422B2 (en) |
EP (2) | EP2270249B2 (en) |
JP (1) | JP5981842B2 (en) |
KR (1) | KR101401060B1 (en) |
CN (1) | CN102498229B (en) |
CA (1) | CA2766327C (en) |
ES (2) | ES2426226T3 (en) |
RU (1) | RU2516214C2 (en) |
WO (1) | WO2011000635A1 (en) |
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EP2570257B1 (en) | 2011-09-15 | 2021-05-12 | Hydro Aluminium Rolled Products GmbH | Aluminium compound material with AIMgSi-core alloy layer |
DE102012108590A1 (en) * | 2011-10-11 | 2013-04-11 | Ksm Castings Group Gmbh | casting |
DE102013108127A1 (en) | 2012-08-23 | 2014-02-27 | Ksm Castings Group Gmbh | Al-cast alloy |
WO2014121785A1 (en) | 2013-02-06 | 2014-08-14 | Ksm Castings Group Gmbh | Aluminium casting alloy |
FR3008427B1 (en) | 2013-07-11 | 2015-08-21 | Constellium France | ALUMINUM ALLOY SHEET FOR AUTOMOBILE BODY STRUCTURE |
DE102013221710A1 (en) | 2013-10-25 | 2015-04-30 | Sms Siemag Aktiengesellschaft | Aluminum hot strip rolling mill and method for hot rolling an aluminum hot strip |
WO2018033537A2 (en) * | 2016-08-15 | 2018-02-22 | Hydro Aluminium Rolled Products Gmbh | Aluminum alloy and aluminum alloy strip for pedestrian impact protection |
US11384418B2 (en) | 2017-05-11 | 2022-07-12 | Aleris Aluminum Duffel Bvba | Method of manufacturing an Al—Si—Mg alloy rolled sheet product with excellent formability |
MX2020011512A (en) | 2018-05-15 | 2020-12-09 | Novelis Inc | F* and w temper aluminum alloy products and methods of making the same. |
PL3825428T3 (en) * | 2019-11-25 | 2023-03-20 | Amag Casting Gmbh | Die cast component and method for producing a die cast component |
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Also Published As
Publication number | Publication date |
---|---|
WO2011000635A1 (en) | 2011-01-06 |
CN102498229B (en) | 2014-03-12 |
EP2270249B2 (en) | 2020-05-27 |
US20160068939A1 (en) | 2016-03-10 |
CN102498229A (en) | 2012-06-13 |
JP2012531521A (en) | 2012-12-10 |
CA2766327C (en) | 2016-02-02 |
EP2270249A1 (en) | 2011-01-05 |
RU2516214C2 (en) | 2014-05-20 |
ES2746846T3 (en) | 2020-03-09 |
EP2270249B1 (en) | 2013-05-29 |
KR20120057607A (en) | 2012-06-05 |
CA2766327A1 (en) | 2011-01-06 |
US10612115B2 (en) | 2020-04-07 |
US20120222783A1 (en) | 2012-09-06 |
ES2426226T3 (en) | 2013-10-22 |
US10047422B2 (en) | 2018-08-14 |
EP2449145A1 (en) | 2012-05-09 |
KR101401060B1 (en) | 2014-05-29 |
RU2012102976A (en) | 2013-08-10 |
JP5981842B2 (en) | 2016-08-31 |
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