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EP3314031A1 - Bande almg à haute résistance aisément façonnable et procédé de production de celle-ci - Google Patents

Bande almg à haute résistance aisément façonnable et procédé de production de celle-ci

Info

Publication number
EP3314031A1
EP3314031A1 EP16732581.0A EP16732581A EP3314031A1 EP 3314031 A1 EP3314031 A1 EP 3314031A1 EP 16732581 A EP16732581 A EP 16732581A EP 3314031 A1 EP3314031 A1 EP 3314031A1
Authority
EP
European Patent Office
Prior art keywords
aluminum alloy
strip
rolling
alloy strip
weight
Prior art date
Legal status (The legal status 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 status listed.)
Granted
Application number
EP16732581.0A
Other languages
German (de)
English (en)
Other versions
EP3314031B1 (fr
Inventor
Olaf Engler
Henk-Jan Brinkman
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Speira GmbH
Original Assignee
Hydro Aluminium Rolled Products 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 Hydro Aluminium Rolled Products GmbH filed Critical Hydro Aluminium Rolled Products GmbH
Publication of EP3314031A1 publication Critical patent/EP3314031A1/fr
Application granted granted Critical
Publication of EP3314031B1 publication Critical patent/EP3314031B1/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • 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
    • 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

Definitions

  • the invention relates to a method for producing an aluminum strip or sheet from an aluminum alloy and an aluminum alloy strip or sheet and its use.
  • Aluminum alloy sheets are playing an increasing role as compared to
  • Aluminum sheets made of a hardenable Al-Mg-Si alloy of class AA6XXX Aluminum alloy sheets of this class are used in the solution-treated state T4 and then subjected to a heat aging to achieve a higher ultimate strength in the state T6.
  • AlMg alloys of the type AA 5xxx with Mg contents of more than 3% by weight, in particular more than 4% by weight, are increasingly prone to intercrystalline corrosion, for example when exposed to elevated temperatures.
  • ⁇ -AlsMg3 phases precipitate along the grain boundaries, which are referred to as ⁇ -particles and can be selectively dissolved in the presence of a corrosive medium.
  • Standard test according to ASTM G67 in which the samples are exposed to nitric acid and the mass loss of the aluminum sheet is measured.
  • ASTM G67 Standard test according to ASTM G67, in which the samples are exposed to nitric acid and the mass loss of the aluminum sheet is measured.
  • ASTM G67 a corresponding heat load of the components in the application is simulated by a prior sensitization annealing at temperatures of 130 ° C. for 17 hours.
  • the mass loss for materials which are not resistant to intergranular corrosion is more than 15 mg / cm 2 .
  • the production of an intercrystalline corrosion resistant
  • WO 2014/029853 Al Although the aluminum alloy sheets disclosed herein have a good tensile strength R m and excellent values for the uniform elongation A g with good resistance to intergranular corrosion. However, the values for the yield strength R p0 , 2, which is a measure of the resistance of the sheet to plastic deformation, are too low to significantly reduce the yield
  • Aluminum alloy sheets are from the cited German Offenlegungsschrift not known.
  • information on specific mechanical properties of a work hardened and Weggeglühten aluminum alloy strip in said German patent application are not disclosed.
  • the object of the present invention is to propose an aluminum alloy strip or sheet made of a hardenable aluminum alloy which, in addition to a high weight saving potential in the motor vehicle, can be produced inexpensively.
  • the aforementioned object solves a method for producing an aluminum strip or sheet from a
  • Aluminum alloy strip at 300 ° C to 500 ° C, such that the cold-rolled aluminum alloy strip has a recrystallized structure after the intermediate annealing,
  • Metal temperature is 190 - 250 ° C for at least 0.5 h.
  • sheets can then be tinned from the aluminum alloy strip.
  • the magnesium content of the aluminum alloy to be used according to the invention is from 3.6% by weight to 6% by weight, preferably from 4.2% by weight to 6% by weight, particularly preferably from 4.2% by weight to 5 , 2 wt .-% contributes to the fact that the aluminum alloy with good forming properties at the same time high
  • Strength values in particular yield strength R p0 , 2 and tensile strength R m achieved. Unwanted hardening and precipitation effects of Si are reduced by limiting the Si content to a maximum of 0.4% by weight.
  • the Fe content should be limited to a maximum of 0.5% by weight. This also applies to the copper content, which should be limited to a maximum of 0.15 wt .-%.
  • Manganese leads to an increase in strength and also to an improvement in the resistance to intergranular corrosion. However, the manganese content must be limited because otherwise the forming properties of the annealed
  • Forming properties such as the uniform strain A g or the
  • Fractional contraction Z decrease, so that the forming properties are deteriorated. Furthermore, Cr also leads to small grain sizes after the intermediate annealing.
  • the chromium content should be limited to values of less than 0.05% by weight, preferably less than 0.01% by weight.
  • Zr which, since it usually has to be added, is not listed here in detail.
  • Zinc could have a negative effect on the corrosion resistance of the aluminum alloy strip and should therefore be limited to a maximum of 0.2% by weight.
  • Titanium is commonly added in continuous casting of the aluminum alloy as a grain refining agent, for example in the form of Ti-boride wire or rods.
  • too high Ti contents in turn have a negative effect on the forming properties, so that a limitation of the Ti content to a maximum of 0.20 wt .-% is desired.
  • a roll bar for hot rolling By casting and homogenizing the rolling ingot at 480 ° C to 550 ° C for at least 0.5 hours, a roll bar for hot rolling can be provided which has a very homogeneous distribution of the alloy components.
  • a homogeneous recrystallized hot strip is provided by hot rolling in a temperature range of 280 ° C to 500 ° C.
  • the degree of rolling during cold rolling is
  • Aluminum alloy strip according to the invention only 10% to 45%, since the Abwalzgrad before the last intermediate annealing the emergence of the grain structure
  • the intermediate annealing allows the provision of a recrystallized microstructure for the last one
  • Cold rolling step which is carried out with a degree of rolling of 30% to 60% of final thickness.
  • the final rolling degree allows, in contrast to
  • Aluminum alloy strip by work hardening to the desired application, for example, to a yield strength of more than 190 MPa after the
  • Aluminum alloy tape can be provided, on the one hand good, for example, can be converted to a vehicle component and on the other hand provides high yield strengths in the non-formed areas.
  • the produced aluminum alloy strip is at the same time also resistant to intercrystalline
  • the degree of rolling is limited to 20% to 30%, larger grain diameters are provided in the aluminum alloy strip after the last intermediate annealing and thus the resistance to
  • the yield strength R p0 , 2 can be set to values above 200 MPa, without the forming properties, for example, the uniform elongation A g or .
  • Providing aluminum alloy tapes and sheets for conversion to vehicle components such as body-in-white (BIW) components.
  • vehicle components such as body-in-white (BIW) components.
  • the aluminum alloy strip when the aluminum alloy strip is cold rolled to a thickness of 0.5 mm to 5.0 mm, preferably to 1.0 mm to 3.0 mm final thickness, moldings may be produced from a non-hardenable aluminum alloy for vehicle components, which cost
  • the temperature during the annealing of the aluminum alloy strip is 220 ° C to 240 ° C.
  • Aluminum alloy strip produced components in case of any thermal stress during operation.
  • the above object is achieved by a cold-rolled and re-annealed aluminum alloy strip or sheet, which is preferably made by the method of the invention, consisting of an aluminum alloy with the following
  • Aluminum Alloy Composition Yield Strings Rp0.2 of greater than 190 MPa to 300 MPa with a uniform elongation of 14% to 18% and a
  • the Mg content of the aluminum alloy strip or sheet may be 4.2% by weight to 6% by weight, preferably 4.2% by weight to 5.2% by weight
  • Aluminum alloy ribbon or sheet limited to 0.1 wt .-% to 0.3 wt .-%, so can despite the positive influence of manganese on the strength and
  • Corrosion resistance of aluminum alloy strip or sheet at the same time good forming properties, ie high values for uniform elongation A g and the
  • Grain diameter of more than 20 ⁇ be set reliably, which positively affect the corrosion resistance of the aluminum alloy strip or sheet.
  • the chromium content negatively affects the properties of the aluminum alloy even at very low concentrations with respect to the forming behavior and limits the grain size after the last intermediate annealing so that, according to another embodiment of the aluminum alloy strip or sheet, the chromium content is reduced to less is limited as 0.01 wt .-%. This also applies analogously to zirconium and scandium which, if at all, are only present in traces in the aluminum alloy.
  • the aluminum alloy strip or sheet has one or more of the following limitations on the proportions of
  • Aluminum alloy strip or sheet the aluminum alloy strip has one or more of the following characteristics:
  • the aluminum alloy strip can be manufactured by adjusting the specific properties of yield strength, uniform elongation, fracture constriction and behavior in the corrosion test in addition to the different fields of application. For example, a higher yield strength of more than 200 MPa can reduce the final thicknesses of the aluminum alloy strip and thus a allow further reduction of the weight of the molding produced therefrom, for example a vehicle component.
  • the increase in the uniform expansion to at least 15% or the increase in the Brucheinschnürung Z to at least 55% means that the aluminum alloy strip or sheet according to the invention can be used in complex forming processes and, for example, complex shaped moldings can be produced with a few forming steps.
  • Corrosion test according to ASTM G67 in turn leads to increased safety against failure due to intercrystalline corrosion of a molded part produced from the aluminum alloy strip.
  • Aluminum alloy strip or sheet according to the present embodiment a significantly increased field of application due to the greatly improved
  • the above object is also achieved by the use of an aluminum alloy strip or sheet according to the invention for the production of structural parts or vehicle components, in particular BIW components of a motor vehicle, since the aluminum alloy strips according to the invention allow the production of molded parts for the corresponding use, which undergo very high degrees of deformation At the same time, however, they can provide high yield strengths for reducing the material thickness of the aluminum alloy strip or sheet and nevertheless have a very good corrosion behavior in the corrosion test according to ASTM G67.
  • the invention will be explained in more detail with reference to embodiments in conjunction with the drawings.
  • the drawing shows in Fig. 1 in a schematic representation of the method steps of an embodiment of the method for producing an aluminum alloy strip and
  • FIG. 1 initially shows the method steps of a schematic representation
  • step 1 a
  • Rolling bar consisting of an aluminum alloy with the following
  • the ingot is homogenized for a period of at least 0.5 h according to step 2.
  • This is followed by the Hot rolling the rolling ingot in step 3 at a temperature of 280 ° C to 500 ° C to a hot strip.
  • the limitation of Abwalzgrads to 10% to 45% causes in the subsequent intermediate annealing according to step 5 by recrystallization a mean grain size of more than 20 ⁇ can be achieved.
  • the implementation of the last intermediate annealing of the cold-rolled aluminum alloy strip at 300 ° C to 500 ° C provides for the final cold rolling step 6, a recrystallized structure with grain sizes of more than 20 ⁇ available. Steps 4 and 5 can possibly
  • step 6 the cold rolling according to step 6 at a degree of rolling of 30% to 60% of the final thickness, cold work hardening is introduced into the recrystallized structure, which leads to an increase in the yield strength R p0 , 2 .
  • step 7 the cold-rolled structure is subjected to a recovery, so that in particular the
  • the manufactured uniform elongation A g of more than 14% and values for the fracture waist Z of more than 50% the manufactured
  • BIW components are often converted into shaped parts, for example to vehicle components of the "body-in-white" of a motor vehicle, so-called BIW components.
  • BIW components often have complex geometries and therefore require a high degree of reshapability of the belts or belts Sheets from which they are made
  • BIW components made of an aluminum alloy also require correspondingly low sheet thicknesses, which is high
  • Aluminum alloy strips according to the invention and the sheets produced therefrom fulfill this requirement as well as the necessary corrosion resistance, as experiments show.
  • Be vehicle components, in particular BIW components therefore from an inventive
  • FIG. 2a) and 2b) show schematically areas of application of the invention
  • Corrosion behavior of the aluminum alloy strips according to the present invention opens up further applications for the
  • Table 1 shows a total of seven different ones
  • Experiments 1, 2 and 9 included aluminum alloys whose Mg, Mn or Cr content are outside the range according to the invention.
  • the Mg content is too small and the contents of Mn and Cr are too large. Too high values for Cr and slightly increased values for Mn also include Comparative Example No. 2.
  • Comparative Example No. 9 in turn has clearly too large values for Mn and Cr. The hot strips made of different aluminum alloys were then cold rolled before the last one according to the specifications in Table 2
  • Annealing temperature was 240 ° C in all experiments. The annealing was carried out in the coil, wherein the metal temperature of the annealing temperature was maintained for a period of at least 0.5 h.
  • Table 2 also indicates the final thicknesses a 0 , which are approximately between 0.7 mm and 1.7 mm. In Table 2, the Abwalzgrade which are outside the range of the invention, underlined. Comparative Examples Nos. 1 and 6 have excessive degrees of finish before intermediate annealing, whereas Comparative Example No. 3 has too low final rolling degree after intermediate annealing.
  • the mean grain size ie the average grain diameter, was measured. For this purpose, samples were taken from the tapes and anodized longitudinal blanks according to the Barker method. Under the microscope, the samples were measured according to ASTM E1382 and the mean grain size determined by the mean grain diameter.
  • Table 3 also shows the mass loss values in a corrosion test according to ASTM G67 (NAMLT), in which the samples were previously subjected to a simulated thermal stress for 17 hours at 130 ° C.
  • NAMLT ASTM G67
  • Comparative Example No. 1 which has a markedly increased Mn content, for example, the uniform elongation A g decreases to 10.6%. Also, the too low Mg content of Comparative Example No. 1 counteracts large elongation values.
  • Comparative Example No. 2 having an increased Cr content at a slightly excessive Mn content shows fracture necking values Z that are less than 50%, indicating a deteriorated forming performance.
  • Fracture necking Z represents precisely the property of the material, in the case of large deformations via a cross-sectional reduction material for the forming to provide without tearing. Due to the higher Mn contents or Cr contents, the average particle size of 10 or 15 ⁇ m has no negative influence on the corrosion properties of these samples. Comparing Comparative Example No. 3 with the invention
  • Exemplary embodiment No. 4 makes it clear that the yield point R p0 , 2 can be set via the adjustment of the degree of rolling during final rolling after the intermediate annealing .
  • Embodiments Nos. 4, 5 and 8 show that about
  • the yield strength R p o, 2 can be increased to values up to 211 MPa without causing significant losses in the area of the characteristic values for the transformation, such as the uniform elongation A g or Z.
  • Aluminum alloy as Examples 3, 4, 5 and 8 can be very clearly recognized the influence of the adjustment of the average grain diameter by limiting the degree of rolling during cold rolling before the last intermediate annealing.
  • the intermediate annealing produces a relatively fine grain having an average diameter or an average grain size of 13 ⁇ m, which produces the
  • Comparative Example No. 6 is classified as not resistant to intergranular corrosion.
  • the embodiments according to the invention show that the yield strength R p o, 2 are increased to values of up to 270 MPa by using degrees of rolling in final cold rolling of 40% to 60%.
  • the higher Mg content of up to 5.2 wt .-% in the embodiment no. 12 contributes to the significant increase in the yield strength R p o, 2 at.
  • a comparison of the embodiments of the invention No. 9, 10 and 11 shows that the corrosion resistance depends strongly on the choice of Abwalzgrades before the last intermediate annealing and thus from the mean grain diameter or the average grain size.
  • the Mg content is increased over Embodiment No. 9, which in principle may lead to inferior corrosion resistance to intergranular corrosion.
  • Aluminum alloy strip can be provided which
  • Vehicle components is particularly well suited and can be produced inexpensively due to the use of non-hardenable aluminum alloy.

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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 fabrication d'une bande ou d'une tôle en alliage d'aluminium, ainsi qu'une bande en alliage d'aluminium et son utilisation. Le but de l'invention est de proposer un procédé de production d'une bande en alliage d'aluminium, à partir d'un alliage d'aluminium non durcissable, qui permet de produire de manière simple des pièces façonnées pour composants de véhicules, en particulier pour composants BIW, et de faire en outre des économies de poids. Ce but est atteint par un procédé de production d'une bande en alliage d'aluminium avec les constituants d'alliage suivants en pourcentage en poids : 3,6 % ≤ Mg ≤ 6 %, Si ≤ 0,4 %, Fe ≤ 0,5 %, Cu ≤ 0,15, 0,1 % ≤ Mn ≤ 0,4 %, Cr < 0,05 %, Zn ≤ 0,20 %, Ti ≤ 0,20 %, le reste étant Al et des impuretés inévitables, dissous à raison de 0,05 % maximum chacun, au total 0,15 % maximum. Le procédé comprend les étapes suivantes consistant à : - couler un lingot de laminage constitué dudit alliage d'aluminium, - homogénéiser le lingot de laminage à une température allant de 480 °C à 550 °C pendant au moins 0,5 h, - laminer à chaud le lingot de laminage à une température allant de 280 °C à 500 °C pour former une bande à chaud, - laminer à froid la bande d'alliage d'aluminium après le laminage à chaud avec un degré de laminage de 10 % à 45 % avant un dernier recuit intermédiaire, - effectuer au moins un dernier recuit intermédiaire de la bande en alliage d'aluminium laminée à froid à une température allant de 300 °C à 500 °C de sorte que la bande en alliage d'aluminium laminée à froid a une structure recristallisée après le recuit intermédiaire, - laminer à froid la bande en alliage d'aluminium recuite avec un degré de laminage de 30 % à 60 % à une épaisseur finale, et - recuire à nouveau la bande en alliage d'aluminium dans l'enroulement à l'épaisseur finale. La température du métal est de 190 à 250 °C pendant au moins 0,5 h.
EP16732581.0A 2015-06-25 2016-06-23 Bande almg facilement déformable et très résistante et son procédé de fabrication Active EP3314031B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
EP15173888 2015-06-25
PCT/EP2016/064530 WO2016207274A1 (fr) 2015-06-25 2016-06-23 Bande almg à haute résistance aisément façonnable et procédé de production de celle-ci

Publications (2)

Publication Number Publication Date
EP3314031A1 true EP3314031A1 (fr) 2018-05-02
EP3314031B1 EP3314031B1 (fr) 2018-11-07

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Country Status (9)

Country Link
US (1) US11352686B2 (fr)
EP (1) EP3314031B1 (fr)
JP (1) JP6481052B2 (fr)
KR (1) KR101911037B1 (fr)
CN (1) CN107787376A (fr)
CA (1) CA2990303C (fr)
ES (1) ES2700140T3 (fr)
RU (1) RU2685295C1 (fr)
WO (1) WO2016207274A1 (fr)

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FR3085968B1 (fr) 2018-09-13 2022-08-12 Constellium Issoire PRODUIT EN ALLIAGE AlMgMn A TENUE A LA CORROSION AMELIOREE
CN109321790B (zh) * 2018-12-06 2020-10-02 中铝瑞闽股份有限公司 一种土司盒用铝基材及其制备方法
EP3690076A1 (fr) * 2019-01-30 2020-08-05 Amag Rolling GmbH Procédé de fabrication d'une tôle ou d'une bande d'un alliage d'aluminium ainsi que tôle, bande ou pièce moulée fabriqués selon ledit procédé
FR3093960B1 (fr) 2019-03-19 2021-03-19 Constellium Neuf Brisach Partie basse de caisson de batteries pour véhicules électriques
EP3741875A1 (fr) * 2019-05-24 2020-11-25 Constellium Rolled Products Singen GmbH & Co.KG Produit de feuille en alliage d'aluminium ayant un aspect de surface amélioré
CN110343919A (zh) * 2019-07-18 2019-10-18 哈尔滨理工大学 一种质量轻硬度大强度高的铝合金及其制备方法
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CN111647774A (zh) * 2020-02-17 2020-09-11 海德鲁挤压解决方案股份有限公司 生产耐腐蚀和耐高温材料的方法
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CN112442617B (zh) * 2020-11-11 2022-04-19 宁波吉顺汽车配件有限公司 一种汽车气门嘴变形铝合金、制备方法及应用
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CA3207291A1 (fr) * 2021-03-12 2022-09-15 Novelis Inc. Variantes d'alliage d'aluminium 5xxx a haute resistance et leurs procedes de preparation
CN113403506A (zh) * 2021-06-21 2021-09-17 安徽标兵实业有限公司 一种8系铝合金带材制备电池盖板用防爆片、翻转片方法
CN117897511B (zh) * 2021-09-03 2025-07-11 斯佩拉有限公司 变形优化的铝合金带材及制造方法
CN113862533B (zh) * 2021-09-30 2022-06-28 中国航发北京航空材料研究院 一种铝合金及其制备方法
CN113981282A (zh) * 2021-10-28 2022-01-28 中铝西南铝板带有限公司 一种液晶背光模组背板用铝合金带材及其制备方法和应用
CN114438381B (zh) * 2022-01-13 2023-03-24 河南泰鸿新材料有限公司 一种高强、高韧、耐腐蚀的铝合金板及其制备方法
CN114480928A (zh) * 2022-01-28 2022-05-13 全良金属(苏州)有限公司 一种电子产品用高强铝板及其制造方法
CN114457265B (zh) * 2022-01-28 2023-06-02 河南明晟新材料科技有限公司 一种高强度高疲劳性能6系铝合金、气瓶及其制备方法
CN115369293B (zh) * 2022-04-08 2023-08-18 中铝瑞闽股份有限公司 一种高强度阳极氧化用Al-Mg系铝板带及其制备方法
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CN116904785B (zh) * 2023-09-13 2023-12-01 湖南卓创精材科技股份有限公司 一种铝镁合金镜面材料、制备方法和应用
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CN107810284A (zh) * 2015-06-05 2018-03-16 诺维尔里斯公司 高强度5xxx铝合金以及其制造方法

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US11352686B2 (en) 2022-06-07
EP3314031B1 (fr) 2018-11-07
JP2018524468A (ja) 2018-08-30
RU2685295C1 (ru) 2019-04-17
ES2700140T3 (es) 2019-02-14
KR20180016608A (ko) 2018-02-14
CA2990303A1 (fr) 2016-12-29
WO2016207274A1 (fr) 2016-12-29
CA2990303C (fr) 2019-12-17
US20180112297A1 (en) 2018-04-26
JP6481052B2 (ja) 2019-03-13
KR101911037B1 (ko) 2018-10-23
CN107787376A (zh) 2018-03-09

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