WO2023187019A1 - Procédé de production d'une tôle ou d'une bande métallique, et tôle ou bande métallique produite au moyen de ce procédé - Google Patents

Procédé de production d'une tôle ou d'une bande métallique, et tôle ou bande métallique produite au moyen de ce procédé Download PDF

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Publication number
WO2023187019A1
WO2023187019A1 PCT/EP2023/058212 EP2023058212W WO2023187019A1 WO 2023187019 A1 WO2023187019 A1 WO 2023187019A1 EP 2023058212 W EP2023058212 W EP 2023058212W WO 2023187019 A1 WO2023187019 A1 WO 2023187019A1
Authority
WO
WIPO (PCT)
Prior art keywords
strip
sheet
rolling
hot
final
Prior art date
Application number
PCT/EP2023/058212
Other languages
German (de)
English (en)
Inventor
Peter J. Uggowitzer
Anita Gründlinger
Josef Berneder
Original Assignee
Amag Rolling Gmbh
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Amag Rolling Gmbh filed Critical Amag Rolling Gmbh
Publication of WO2023187019A1 publication Critical patent/WO2023187019A1/fr

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/047—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with magnesium as the next major constituent
    • 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
    • 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

Definitions

  • the invention relates to a method for producing a sheet or strip and a sheet or strip produced therewith.
  • optical scattering centers for example foreign phases in the oxide layer, must be reduced so that the directed light reflection responsible for the degree of gloss can take place unimpaired. This is particularly true for scattering centers whose size is comparable to or larger than the wavelength of visible light (400 to 750 nm).
  • EP3011067B1 proposes to reduce fine Mg2Si precipitates that arise during the manufacturing process by means of intermediate annealing followed by cooling during cold rolling. This intermediate annealing takes place between the solvus temperature of the precipitates and the melting temperature of the aluminum alloy.
  • the invention has therefore set itself the task of changing the method of the type described at the beginning in such a way that both the degree of gloss and its durability are further improved in the case of a sheet or strip made of a 5xxx aluminum alloy.
  • the invention solves the problem set with regard to the method through the features of claim 1.
  • Mg-containing precipitates can be acted upon before cold rolling.
  • quenching takes place to a temperature below the precipitation temperature of Mg-containing precipitates.
  • quenching takes place with an average cooling rate of at least 10 °C/s, for example at least 50 °C/s.
  • the grains of the aluminum matrix are significantly stretched, resulting in higher corrosion resistance due to increased path length for intergranular Corrosion leads - this in turn can have a positive effect on the stability of the gloss level.
  • the intermediate annealing in combination with the comparatively high degree of cold rolling results in an improved and more stable level of gloss or improved corrosion resistance on the sheet or strip.
  • this is provided in several stitches and may optionally include a pickling step as an intermediate step between these stitches.
  • the method according to the invention includes a final annealing of the cold-rolled sheet or strip with a second holding temperature ⁇ recrystallization temperature of the aluminum alloy.
  • the cold-rolled structure is now finally annealed and is in a non-recrystallized state.
  • the grain structure is elongated in the rolling direction.
  • the condition of the sheet or strip produced with it is, for example, H2X.
  • the first holding temperature is preferably in the range from >400 °C to ⁇ 600 °C, so that essentially all Mg-containing precipitates are dissolved in the aluminum alloy. This can be achieved in particular if the first holding temperature of the intermediate annealing is in the range from 450 °C to 560 °C.
  • the intermediate annealing has a first holding time in the range of > 2 s (seconds) to 6 min (minutes).
  • this range of the first holding time can, among other things, prevent the formation of coarse grain due to excessive grain growth and thus orange peel when forming or bending the sheet or strip.
  • the second holding temperature i.e. the holding temperature of the final annealing
  • the second holding temperature is, for example, in the range below the recrystallization temperature of the aluminum.
  • the Defect density or dislocation density in the aluminum matrix introduced by cold rolling is reduced primarily through recovery processes while avoiding new grain formation. This makes it possible to set the required mechanical characteristics while maintaining the elongated grain structure created during cold rolling and increasing corrosion resistance. This is particularly the case when the second holding temperature is in the range from 200 to 280 °C, preferably in the range from 200 °C to 250 °C.
  • the extent of the reduction in the defect density introduced by cold rolling depends on the level of the thermal load introduced by the final annealing, for example, in addition to the second holding temperature, also on the second holding time, i.e. the holding time of the final annealing.
  • the second holding time > 6 hours and/or ⁇ 30 hours should be selected.
  • the second holding time is in the range from 8 to 24 hours (hours).
  • the final annealing of the sheet or strip takes place under inert gas, for example, this can prevent magnesium from reacting with oxygen from the environment and thus prevent the surface from becoming cloudy.
  • the gloss level of the sheet or strip can thus be further increased and/or produced more reproducibly.
  • the hot rolling is carried out with a hot rolling ratio of 95% or higher from the initial thickness to the final hot strip thickness.
  • a sufficiently high level of work hardening can subsequently be available to ensure an elongated grain and to fragment Fe-containing phases.
  • the level of gloss as well as the corrosion resistance and thus the stability of the level of gloss can be further improved.
  • a sufficiently high hot strip thickness for the possibility of a comparatively high degree of deformation during cold rolling can be achieved, for example, if the sheet or strip is reduced to a final hot strip thickness in the range of 5 to 12 mm, for example from 6 to 12 mm, or in particular from 6 to 10 mm, is hot rolled.
  • the sheet or strip is preferably rolled in rolling passes with decreasing roll roughness of the rolls for each rolling pass. This means, for example, that the surface roughness of the strip or sheet can be further reduced, which, according to the prior art, also has a positive effect on the shine of the untreated aluminum surface.
  • the sheet or strip is cold-rolled to a final thickness in the range of 0.5 to 1.5 mm (millimeters), in particular to 0.8 to 1.3 mm.
  • This thickness range is particularly suitable for applications in decorative components whose geometric design requires high degrees of deformation and small bending radii.
  • Hot rolling can be further facilitated if, for example, the rolling billets are kept at a heating temperature of > 400 ° C for at least one hour before hot rolling.
  • the heating temperature is in the range from 400 °C to 470 °C.
  • a heating temperature of 400 °C is a minimum temperature at which hot rolling should take place, as recrystallization processes are enabled at this temperature and a reduction in ingot thickness can be facilitated. Because the heating temperature is ⁇ 470 °C, a coarsening of phases in the temperature range close to the melting temperature of the aluminum alloy is essentially prevented.
  • the sheet or strip is made of an aluminum alloy of type EN AW-5xxx with a cold-rolled structure which has a grain structure that is elongated in the rolling direction and has grains whose grain aspect ratio is AI t > 10, measured according to ASTM E112-13.
  • AI t li ⁇ /l >15.
  • the sheet (often called metal sheet) or strip (often called metal strip) produced by the method according to the invention can have an increased degree of gloss and increased durability with its cold-rolled and final annealed structure.
  • the structure in the H2X state is preferably not recrystallized and therefore does not have any recrystallized components. This is ensured, for example, by the final annealing of the cold-rolled sheet or strip with a second holding temperature ⁇ the recrystallization temperature of the aluminum alloy. This means that the cold-rolled structure is retained with the grain structure elongated in the rolling direction.
  • the surface of the strip or sheet preferably has a gloss level of > 50 Gil, measured according to ⁇ NORM EN ISO 7668 at an angle of 20° and transverse to the rolling direction. Preferably this value is > 55 Gil.
  • a measuring device called “micro-TRI-gloss S” from BYK-Gardner GmbH can be used for this measurement.
  • the sheet or strip preferably has a shiny or a shiny and anodized surface layer, the surface of the strip or sheet having a gloss level of > 60 Gil, measured according to ⁇ NORM EN ISO 7668 at an angle of 20° and transverse to the rolling direction.
  • the aluminum alloy of the strip or sheet preferably has from 0.50 to 1.1% by weight of magnesium (Mg), from 0.01 to 0.30% by weight of silicon (Si), from 0.01 to 0.7 % by weight of iron (Fe) and the remainder aluminum as well as impurities that are unavoidable due to production, each with a maximum of 0.05% by weight and a maximum of 0.15% by weight in total.
  • the aluminum alloy can also be used individually or in combination
  • the tapes A, B, C, D are of type EN AW-5xxx with the following chemical composition in wt.%: Mg: 0.8%, Si: 0.03%, Fe: 0.03% and the balance Aluminum and impurities that are unavoidable due to production, each with a maximum of 0.05% by weight and a maximum of 0.15% by weight in total.
  • Production sequence A The tape A according to the invention was subjected to the following process steps in the order mentioned: a. heating the aluminum alloy rolling billet to a temperature of 420 ° C for 9 hours; b. Hot rolling the rolling billet in several hot rolling passes into a hot rolled strip with a hot rolling degree of 98% to a final hot strip thickness of 8 mm; c. Intermediate annealing of the hot-rolled strip in a strip passing furnace with a first holding temperature of 480 ° C (> solvus temperature of Mg-containing precipitates) with a holding time of 3 min. d. Quenching the intermediate annealed strip with water to a temperature ⁇ 100 °C with a cooling rate of 50 °C/sec.
  • Manufacturing sequence B The tape B according to the invention was subjected to the following process steps in the order mentioned: a. Heating the aluminum alloy rolling billet to a temperature of 420 ° C for 9 hours. b. Hot rolling of the rolling billet in several hot rolling passes to a hot rolled strip with a hot rolling degree of 98% to a final hot strip thickness of 8 mm. c. Intermediate annealing of the hot-rolled strip in a strip passing furnace with a first holding temperature of 480 ° C (> solvus temperature of Mg-containing precipitates) with a holding time of 3 min. d.
  • Manufacturing sequence C The tape C not according to the invention was manufactured in the following process steps: a. Heating the aluminum alloy rolling billet at a heating temperature of 420 ° C for 9 hours. b. Hot rolling of the rolling billet in several hot rolling passes to a hot rolled strip with a hot rolling degree of 98% to a final hot strip thickness of 9 mm. c. Cold rolling the quenched strip in several passes with a pickling step as an intermediate step, with decreasing roll roughness and with a cold rolling degree of 87% to a final thickness of 1.2 mm d. Final annealing of the cold-rolled strip with a second holding temperature of 245 ° C in a coil furnace with a second holding time of 12 h. e. Cooling of the finally annealed strip to room temperature in still air.
  • Manufacturing sequence D The tape D not according to the invention was manufactured in the following process steps: a. Heating the aluminum alloy rolling billet at a temperature of 420 ° C for 9 hours. b. Hot rolling of the rolling billet in several hot rolling passes to a hot rolled strip with a hot rolling degree of 98% to a final hot strip thickness of 9 mm. c. Cold rolling the quenched strip in several cold rolling passes with a pickling step as an intermediate step and with a cold rolling degree of 82% to a material thickness of 1.6 mm. d.
  • the strips A and B which follow the hot rolling according to the invention and are annealed in the strip furnace, have a gloss level that is up to 10 Gil higher than the strips C and D. This is the case both for the untreated strip and for the surface-treated, namely brightened ( chemical or electrolytic) and then anodized, band the case.
  • the soluble Mg-containing phases can be influenced by implementing intermediate annealing before cold rolling according to the invention.
  • intermediate annealing before cold rolling according to the invention.
  • the production sequences A, B and C were cold rolled with decreasing roll roughness in order to reduce the surface roughness.
  • a comparison of the production sequences A, B shows higher gloss levels for sheet A than is the case for sheet B, where a rougher roller was used.
  • the gloss levels of the sheet B according to the invention are significantly higher than the sheets C and D not according to the invention, of which, for example, sheet C was also cold-rolled with a decreasing roll roughness.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Metal Rolling (AREA)

Abstract

L'invention concerne un procédé de production d'une tôle ou d'une bande métallique ainsi qu'une tôle ou une bande métallique produite au moyen de ce procédé. Selon l'invention, pour un niveau de brillance comparativement élevé et une résistance comparativement élevée, la tôle ou la bande métallique, constituée d'un alliage d'aluminium du type EN AW-5xxx, présente une jonction laminée à froid avec une structure de grain s'étendant dans la direction de laminage et avec des grains ayant un rapport d'aspect de grain AIt = ̅ll ( 0°)/ ̅ll (90 °) ≥ 10, en particulier ≥ 15, mesuré selon la norme ASTM E112-13.
PCT/EP2023/058212 2022-03-29 2023-03-29 Procédé de production d'une tôle ou d'une bande métallique, et tôle ou bande métallique produite au moyen de ce procédé WO2023187019A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
EP22165279.5A EP4253585A1 (fr) 2022-03-29 2022-03-29 Procédé de fabrication d'une tôle ou d'une bande et tôle ou bande ainsi fabriquée
EP22165279.5 2022-03-29

Publications (1)

Publication Number Publication Date
WO2023187019A1 true WO2023187019A1 (fr) 2023-10-05

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Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/EP2023/058212 WO2023187019A1 (fr) 2022-03-29 2023-03-29 Procédé de production d'une tôle ou d'une bande métallique, et tôle ou bande métallique produite au moyen de ce procédé

Country Status (2)

Country Link
EP (1) EP4253585A1 (fr)
WO (1) WO2023187019A1 (fr)

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2018011069A1 (fr) * 2016-07-13 2018-01-18 Constellium Neuf-Brisach Ébauches en alliage d'aluminium avec recuit éclair local
EP3011067B1 (fr) 2013-06-17 2018-10-24 Constellium Rolled Products Singen GmbH & Co.KG Jonc enjoliveur de véhicule automobile en alliage aluminium-magnésium.
CN113106307A (zh) * 2021-03-04 2021-07-13 中铝材料应用研究院有限公司 一种镜面铝合金板带材及其制备方法

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3011067B1 (fr) 2013-06-17 2018-10-24 Constellium Rolled Products Singen GmbH & Co.KG Jonc enjoliveur de véhicule automobile en alliage aluminium-magnésium.
WO2018011069A1 (fr) * 2016-07-13 2018-01-18 Constellium Neuf-Brisach Ébauches en alliage d'aluminium avec recuit éclair local
CN113106307A (zh) * 2021-03-04 2021-07-13 中铝材料应用研究院有限公司 一种镜面铝合金板带材及其制备方法

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
ARNAUD WECK ET AL: "Mechanical properties of the aluminum roll-bond laminate AA5005AA5083AA5005", MATERIALS SCIENCE, ELSEVIER, AMSTERDAM, NL, vol. 528, no. 19, 14 April 2011 (2011-04-14), pages 6186 - 6193, XP028227901, ISSN: 0921-5093, [retrieved on 20110422], DOI: 10.1016/J.MSEA.2011.04.037 *
ENGLER OLAF: "Texture and anisotropy in the Al-Mg alloy AA 5005 - Part I: Texture evolution during rolling and recrystallization", MATERIALS SCIENCE, vol. 618, 24 August 2014 (2014-08-24), AMSTERDAM, NL, pages 654 - 662, XP055958588, ISSN: 0921-5093, DOI: 10.1016/j.msea.2014.08.037 *

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Publication number Publication date
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