US20150152535A2 - Method for manufacturing AlMgSi aluminium strip - Google Patents

Method for manufacturing AlMgSi aluminium strip Download PDF

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Publication number
US20150152535A2
US20150152535A2 US14/205,645 US201414205645A US2015152535A2 US 20150152535 A2 US20150152535 A2 US 20150152535A2 US 201414205645 A US201414205645 A US 201414205645A US 2015152535 A2 US2015152535 A2 US 2015152535A2
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Prior art keywords
strip
hot
temperature
rolling
aluminium
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US14/205,645
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US20140190595A1 (en
Inventor
Werner Kehl
Dietmar Schroder
Henk-Jan Brinkman
Natalie Horster
Kai-Friedrich Karhausen
Eike Brunger
Thomas Wirtz
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Speira GmbH
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Hydro Aluminium Rolled Products GmbH
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Application filed by Hydro Aluminium Rolled Products GmbH filed Critical Hydro Aluminium Rolled Products GmbH
Publication of US20140190595A1 publication Critical patent/US20140190595A1/en
Assigned to HYDRO ALUMINIUM ROLLED PRODUCTS GMBH reassignment HYDRO ALUMINIUM ROLLED PRODUCTS GMBH ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: KARHAUSEN, KAI-FRIEDRICH, BRINKMAN, HENK-JAN, Brünger, Eike, KEHL, WERNER, WIRTZ, THOMAS, Hörster, Natalie, Schröder, Dietmar
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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
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • C22C21/04—Modified aluminium-silicon alloys
    • 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 manufacturing a strip from an AlMgSi alloy, in which a rolling ingot is cast from an AlMgSi alloy, the rolling ingot undergoes homogenization, the rolling ingot which has been brought to rolling temperature is hot rolled then optionally cold rolled to final thickness and the finished strip is solution annealed and quenched. Furthermore, the invention relates to advantageous uses of an AlMgSi aluminium strip which has been manufactured accordingly.
  • metal sheets of aluminium alloys are required which are not only distinguished by particularly high strength values, but at the same time have a very good formability and enable high degrees of deforming.
  • typical application fields are the bodywork and chassis components.
  • visible painted components for example, metal bodywork sheets which can be seen from the outside, additionally the forming of the materials has to be carried out in such a manner that the surface is not impaired by defects such as flow figures or roping after the painting.
  • This is particularly important, for example, for the use of aluminium alloy metal sheets for producing bonnets and other bodywork components of an automotive vehicle.
  • it choice of material is restricted with respect to the aluminium alloy.
  • AlMgSi alloys the main alloy constituents of which are magnesium and silicon, have relatively high strengths in the state T6 with, at the same time, good forming behaviour in the state T4 and excellent corrosion resistance.
  • AlMgSi alloys are the alloy types AA6XXX, for example, the alloy type AA6016, AA6014, AA6181, AA6060 and AA6111.
  • aluminium strips are produced from an AlMgSi alloy by means of casting a rolling ingot, homogenising the rolling ingot, hot rolling the rolling ingot and cold rolling the hot strip. The homogenisation of the rolling ingot is carried out at a temperature from 380 to 580° C. for more than one hour.
  • the strips can be delivered in the state T4.
  • the state T6 is set after the quenching by means of artificial ageing at temperatures between 100° C. and 220° C.
  • Hot strips of an AlMgSi alloy are usually produced in thicknesses from 3 mm to 12 mm and supplied to a cold-rolling operation with high degrees of forming. Since the temperature range in which the AlMgSi phases are formed is passed through very slowly during conventional hot rolling, these phases are formed in a very coarse manner.
  • the temperature range for forming the above-mentioned phases is alloy dependent. However, it is between 230° C. and 550° C., that is to say, in the range of the hot-rolling temperatures. It could be proven experimentally that these coarse phases in the hot strip have a negative influence on the elongation of the end product. This means that the formability of aluminium strips from AlMgSi alloys could previously not be fully exploited.
  • the AlMgSi alloy strip directly after leaving the last hot rolling pass, has a temperature of a maximum of 130° C. and is coiled at this or a lower temperature. Owing to the quenching of the hot strip with this method, aluminium strips in the state T4 were able to be produced, which in the state T4 has an elongation at break of A80 of more than 30% or a uniform elongation A g of more than 25%. Furthermore, very high values for the elongation at break in the state T6 were also produced.
  • an object of the present invention is to provide an improved method for manufacturing an aluminium strip from an AlMgSi alloy, by means of which method AlMgSi aluminium strips with very good formability in the state T4 may be produced in an operationally reliable manner.
  • the object set out for a method is achieved in that, immediately after being discharged from the last hot rolling pass, the hot strip is at a temperature of more than 130° C. to 250° C., preferably to 230° C. and the hot strip is coiled at this temperature.
  • this cooling process is carried out within the last two hot-rolling passes, that is to say, the cooling to more than 130° C., preferably from 135° C. to 250° C., preferably from 135° C. to 230° C., is carried out within seconds, at the most within 5 minutes. It has been found that, in this method, the increased uniform elongation values with usual strength and yield point values in the state T4 and the improved hardenability in the state T6 are achieved in a particularly operationally reliable manner.
  • operationally reliable cooling of the hot strip is achieved in that the hot strip is quenched to the outlet temperature using at least one plate cooler and the hot rolling pass itself, loaded with emulsion.
  • a plate cooler comprises an arrangement of cooling or lubrication nozzles which spray a rolling emulsion onto the aluminium strip.
  • the plate cooler may be present in a hot rolling installation in order to cool rolled hot strips to rolling temperature before hot rolling and in order to be able to achieve higher production speeds.
  • the temperature of the hot strip before the start of the cooling process which preferably takes place within the last two rolling passes, is at least 400° C., preferably from 470° C. to 490° C.
  • This advantageous state of the hot strip is practically “frozen” by the quenching operation.
  • the temperature of the hot strip after the penultimate rolling pass is from 290° C. to 310° C. It has been found both that these temperatures enable sufficient freezing of the precipitations and, on the other hand, at the same time, the last rolling pass can be carried out without any problems.
  • the rolled hot strip has, immediately after being discharged from the final hot rolling pass, a temperature of from 200° C. to 230° C., an optimum process speed can be achieved during hot rolling, without the properties of the aluminium strip produced being impaired.
  • the thickness of the prepared hot strip is from 3 mm to 12 mm, preferably from 5 mm to 8 mm, so that conventional cold rolling mills can be used for the cold rolling operation.
  • the aluminium alloy used is preferably of the alloy type AA6xxx, preferably AA6014, AA6016, AA6060, AA6111 or AA6181. All the alloy types AA6xxx have the common feature that they have particularly good formability, characterised by high elongation values in the state T4 and high strengths or yield points in the state for use T6, for example, after artificial ageing at 205° C./30 minutes.
  • the finished, rolled aluminium strip undergoes a heat treatment, in which the aluminium strip is heated to more than 100° C. after solution annealing and quenching and then coiled and aged at a temperature of more than 55° C., preferably more than 85° C.
  • This embodiment of the method enables, after the natural ageing, by means of a shorter heating phase at lower temperatures the state T6 to be set in the strip or the metal sheet, in which the metal sheets or strips formed to components are used in the application.
  • these rapidly hardening aluminium strips are heated only to temperatures of approximately 185° C. for only 20 minutes in order to achieve the higher yield point values in the state T6.
  • the elongation at break values A 80 of the aluminium strips produced by means of this embodiment of the method according to the invention in the state T4 are slightly below 29%.
  • the aluminium strip produced according to the invention is further distinguished after the ageing in the state T4 by a very good uniform elongation A g of more than 25%.
  • the term uniform elongation A g is intended to be understood to refer to the maximum elongation of the sample, at which no necking of the sample can be identified during the tensile test.
  • the sample is thus expanded in a uniform manner in the region of the uniform elongation.
  • the value for the uniform elongation for similar materials was previously at a maximum of 22% to 23%.
  • an aluminium strip having very good forming properties can be provided, and can also be converted into the state T6 by means of an accelerated artificial ageing operation (185° C./20 min).
  • An aluminium alloy of the type AA6016 has the following alloy constituents in percent by weight:
  • the manganese content of less than 0.2% by weight reduces the tendency for the formation of relatively coarse manganese precipitations.
  • chromium ensures a fine microstructure, it is intended to be limited to 0.1% by weight in order to also prevent coarse precipitations.
  • the presence of manganese in contrast improved the weldability by reducing the tendency for cracking or susceptibility to quenching of the aluminium strip according to the invention.
  • titanium ensures grain refinement during the casting operation, but is intended to be limited to a maximum of 0.1% by weight in order to ensure good castability of the aluminium alloy.
  • An aluminium alloy of the type AA6060 has the following alloy constituents in percentage by weight:
  • the combination of a precisely predetermined magnesium content with an Si content which is reduced in comparison with the first embodiment and narrowly specified Fe content produces an aluminium alloy in which the formation of Mg 2 Si precipitations after hot rolling with the method according to the invention can be prevented particularly well so that a metal sheet having improved elongation and high yield points in comparison with conventionally produced metal sheets can be provided.
  • the lower upper limits of the alloy constituents Cu, Mn and Cr additionally increase the effect of the method according to the invention. With respect to the effects of the upper limit of Zn and Ti, reference may be made to the statements relating to the first embodiment of the aluminium alloy.
  • An aluminium alloy of the type AA6014 has the following alloy constituents in percentage by weight:
  • An aluminium alloy of the type AA6181 has the following alloy constituents in percentage by weight:
  • An aluminium alloy of the type AA6111 has the following alloy constituents in percentage by weight:
  • aluminium alloys set out are adapted specifically in terms of their alloy constituents to different applications.
  • strips of these aluminium alloys, which have been produced using the method according to the invention have particularly good uniform elongation values in the state T4 paired with a particularly evident increase of the yield point, for example, after artificial ageing at 205° C./30 min.
  • the object set out above is achieved according to a second teaching of the present invention by the use of an AlMgSi alloy strip produced by the method according to the invention for a component, chassis or structural part or panel in automotive, aircraft or railway vehicle engineering, in particular as component, chassis part, external or internal panel in automotive engineering, preferably as a bodywork component.
  • visible bodywork components for example, bonnets, mudguards, etc.
  • outer skin components of a railway vehicle or aircraft benefit from the high yield points Rp0.2 with good surface properties even after a forming with high degrees of deformation.
  • a rapidly hardening AlMgSi alloy strip having excellent formability can therefore be provided by an aluminium alloy strip which has been produced according to the invention and which has been subjected to a solution annealing with subsequent heat treatment after the production thereof.
  • the state T4 has a uniform elongation A g of more than 25%, for example, with an yield point Rp0.2 of from 80 to 140 MPa.
  • the artificial ageing in order to achieve the state T6 can be carried out at 185° C. for 20 minutes in order to achieve the required increase of the yield point.
  • an aluminium alloy strip which has been produced according to the invention has a uniform elongation A g of more than 25% in the rolling direction, transversely relative to the rolling direction and diagonally relative to the rolling direction so that a particularly isotropic formability is enabled.
  • the aluminium strips produced according to the invention have a thickness from 0.5 mm to 12 mm.
  • Aluminium strips having thicknesses from 0.5 mm to 2 mm are preferably used for bodywork components, for example, in automotive vehicle construction, whilst aluminium strips having larger thicknesses from 2 to 4.5 mm are used, for example, in chassis components for automotive vehicle construction.
  • Individual components can also be produced in a cold strip with a thickness of up to 6 mm.
  • aluminium strips with thicknesses of up to 12 mm can also be used. These aluminium strips with a very large thickness are conventionally provided only by means of hot rolling.
  • FIG. 1 shows in the single FIG. 1 a schematic flow chart of an embodiment of the method according to the invention for manufacturing a strip from an MgSi aluminium alloy having the steps of a) producing and homogenising the rolling ingot, b) hot rolling, c) cold rolling and d) solution annealing with quenching.
  • a rolling ingot 1 is first cast from an aluminium alloy with the following alloy constituents in percentage by weight:
  • the rolling ingot produced in this manner is homogenised at a homogenisation temperature of approximately 550° C. for 8 hours in a furnace 2 so that the alloy constituents which have been added by means of alloying are present in the rolling ingot in a state distributed in a particularly homogeneous manner, FIG. 1 a ).
  • FIG. 1 b illustrates how the rolling ingot 1 in the present embodiment of the method according to the invention is hot rolled in a reversing manner by means of a hot rolling mill 3 , the rolling ingot 1 having a temperature of from 400 to 550° C. during the hot rolling operation.
  • 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., preferably from 470° C. to 490° C.
  • the quenching of the hot strip 4 is carried out using a plate cooler 5 and the operating rollers of the hot rolling mill 3 .
  • the hot strip is in this instance cooled to a temperature of from 290° C.
  • the plate cooler 5 illustrated only schematically, sprays the hot strip 4 with cooling rolling emulsion and ensures accelerated cooling of the hot strip 4 to the last-mentioned temperatures.
  • the operating rollers of the hot rolling mill 3 are also loaded with emulsion and further cool the hot strip 4 during the last hot rolling pass.
  • the hot strip 4 has at the output of the plate cooler 5 ′ in the present embodiment a temperature from 200° C. to 230° C. and is subsequently coiled at this temperature by means of the recoiler 6 .
  • the hot strip 4 directly at the outlet of the last hot-rolling pass has a temperature of more than 135° C. to 250° C., preferably from 200° C. to 230° C., or optionally in the last two hot rolling passes, using the plate cooler 5 and the operating rollers of the hot rolling mill 3 , is brought to the temperatures mentioned, in spite of the increased winding temperature, the hot strip 4 has a frozen crystalline microstructural state which leads to very good uniform elongation properties A g of more than 25% in the state T4. Nonetheless, owing to the higher coiling temperature, it can be processed more rapidly and advantageously.
  • the hot strip having a thickness from 3 to 12 mm, preferably from 5 to 8 mm is coiled via the recoiler 6 .
  • the coiling temperature in the present embodiment is preferably from 135° C. to 250° C.
  • the hot strip 4 has a very favourable crystalline state for further processing and can be decoiled from the decoiler 7 , supplied, for example, to a cold rolling mill 9 and recoiled on a recoiler 8 , FIG. 1 c ).
  • the resulting cold rolled strip 11 is coiled. Subsequently, it is supplied to a solution annealing operation at temperatures from 520° C. to 570° C. and a quenching operation 10 , FIG. 1 d ). To this end, it is decoiled again from the coil 12 , solution annealed in a furnace 10 and quenched, and again coiled to a coil 13 . After natural ageing at ambient temperature in the state T4, the aluminium strip can then be supplied with maximum formability. Alternatively (not illustrated), the aluminium strip 11 can be separated into individual sheets, which are present in the state T4 after natural ageing.
  • piece annealing operations can also alternatively be carried out and the metal sheets can be subsequently quenched.
  • the aluminium strip or the aluminium sheet is brought into the state T6 by means of artificial ageing at from 100° C. to 220° C. in order to achieve maximum values for the yield point.
  • artificial ageing can also be carried out at 205° C./30 min.
  • the aluminium strips produced in accordance with the embodiment illustrated have after the cold rolling, for example, a thickness of from 0.5 to 4.5 mm.
  • Strip thicknesses from 0.5 to 2 mm are conventionally used for bodywork applications or strip thicknesses of from 2.0 mm to 4.5 mm for chassis components in automotive vehicle construction.
  • the improved uniform elongation values are a decisive advantage in the production of components since in most cases significant deformations of the metal sheets are carried out and nonetheless great strengths are required in the state for use (T6) of the end product.
  • Table 1 sets out the alloy constituents of aluminium alloys from which aluminium strips are produced in a conventional manner or according to the invention.
  • the aluminium strips contain as remainder aluminium and impurities, individually at a maximum of 0.05% by weight and in total a maximum of 0.15% by weight.
  • the strips (samples) 251 and 252 were produced using a method according to the invention in which the hot strip was cooled and coiled within the last two hot rolling passes from approximately 470° C. to 490° C. to from 135° C. to 250° C. using a plate cooler and the hot rollers themselves. In Table 2, the measurement values of these strips are designated “Inv.”. Subsequently, a cold rolling operation was carried out to a final thickness of 0.865 mm.
  • the strips (samples) 491-1 and 491-11 were produced using a conventional hot rolling and cold rolling operation and designated “Cony.”.
  • the strips were subjected to a solution-annealing operation with subsequent quenching and subsequent natural ageing for eight days at ambient temperature.
  • the T6 state was achieved by means of artificial ageing which followed the natural ageing at 205° C. for 30 minutes.
  • the samples designated L were cut out in the rolling direction, the samples designated Q transversely relative to the rolling direction and the samples designated D diagonally with respect to the rolling direction.
  • the samples 491-1 and 491-11 were each measured transversely relative to the rolling direction.
  • the advantageous microstructure which was adjusted in the strips 251 and 252 by means of the method according to the invention, with an identical yield point Rp0.2 and strength Rm, enables a substantial increase of the uniform elongation A g .
  • the uniform elongation A g increased from 23.0% to a maximum of 26.6% transversely relative to the rolling direction in the strips produced according to the invention in comparison with the conventionally produced strips.
  • the microstructure configured with the method according to the invention leads to the particularly advantageous combination of high uniform elongation A g of more than 25% with very high values for the yield point Rp0.2 from 80 to 140 MPa.
  • the yield point Rp0.2 increases up to at least 185 MPa, the uniform elongation A g further remaining at more than 12%.
  • the hardenability with a ⁇ Rp0.2 of 97 or 107 MPa is furthermore very good in the strips produced according to the invention.
US14/205,645 2011-09-15 2014-03-12 Method for manufacturing AlMgSi aluminium strip Abandoned US20150152535A2 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
EP11181519.7 2011-09-15
EP11181519.7A EP2570509B1 (de) 2011-09-15 2011-09-15 Herstellverfahren für AlMgSi-Aluminiumband
PCT/EP2012/068005 WO2013037919A1 (de) 2011-09-15 2012-09-13 HERSTELLVERFAHREN FÜR AlMgSi-ALUMINIUMBAND

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US20150152535A2 true US20150152535A2 (en) 2015-06-04

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US (1) US20150152535A2 (ja)
EP (1) EP2570509B1 (ja)
JP (1) JP5699255B2 (ja)
KR (2) KR101974624B1 (ja)
CN (1) CN103842550B (ja)
CA (1) CA2848457C (ja)
ES (1) ES2459307T3 (ja)
PT (1) PT2570509E (ja)
RU (1) RU2576976C2 (ja)
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EP4190932A1 (en) * 2021-12-01 2023-06-07 Constellium Bowling Green LLC 6xxx series aluminium alloy sheets, plates or blanks with improved formabilty

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DE102013221710A1 (de) 2013-10-25 2015-04-30 Sms Siemag Aktiengesellschaft Aluminium-Warmbandwalzstraße und Verfahren zum Warmwalzen eines Aluminium-Warmbandes
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MX2018008367A (es) 2016-01-08 2018-12-10 Arconic Inc Nuevas aleaciones de aluminio 6xxx, y metodos para su fabricacion.
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KR20140057666A (ko) 2014-05-13
US20140190595A1 (en) 2014-07-10
KR20150126975A (ko) 2015-11-13
PT2570509E (pt) 2014-04-30
ES2459307T3 (es) 2014-05-08
JP5699255B2 (ja) 2015-04-08
RU2014114792A (ru) 2015-10-20
CN103842550B (zh) 2017-05-03
JP2014532114A (ja) 2014-12-04
WO2013037919A1 (de) 2013-03-21
RU2576976C2 (ru) 2016-03-10
CN103842550A (zh) 2014-06-04
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EP2570509A1 (de) 2013-03-20
CA2848457C (en) 2016-10-04

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