EP3314031B1 - Hochfestes und gut umformbares almg-band sowie verfahren zu seiner herstellung - Google Patents

Hochfestes und gut umformbares almg-band sowie verfahren zu seiner herstellung Download PDF

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Publication number
EP3314031B1
EP3314031B1 EP16732581.0A EP16732581A EP3314031B1 EP 3314031 B1 EP3314031 B1 EP 3314031B1 EP 16732581 A EP16732581 A EP 16732581A EP 3314031 B1 EP3314031 B1 EP 3314031B1
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Prior art keywords
aluminium alloy
alloy strip
rolling
aluminum alloy
strip
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EP16732581.0A
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German (de)
English (en)
French (fr)
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EP3314031A1 (de
Inventor
Olaf Engler
Henk-Jan Brinkman
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Speira GmbH
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Hydro Aluminium Rolled Products GmbH
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
    • 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.
  • the highly stressed vehicle components were preferably made of aluminum sheets consisting of a curable 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.
  • This complicated manufacturing path leads to higher production costs, in particular due to the logistical effort for processing the plates in the state T4 and the hot aging of the plates to reach the state T6.
  • components of non-hardenable aluminum alloys of the type AA5XXX have been produced by forming soft annealed aluminum alloy sheets.
  • 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.
  • ⁇ -Al 5 Mg 3 phases separate out along the grain boundaries, which are called ⁇ -particles and can be selectively dissolved in the presence of a corrosive medium.
  • This also applies to the components of a motor vehicle, in particular the components of the so-called "body-in-white" of the motor vehicle, which are usually subjected to a cathodic dip coating (KTL) and then dried in a baking process. Sensitization to intergranular corrosion can already be caused by this baking process in conventional aluminum alloy strips.
  • KTL cathodic dip coating
  • the susceptibility to intergranular corrosion is usually tested in a 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 standard test according to 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.
  • ASTM G67 the mass loss for materials which are not resistant to intergranular corrosion is more than 15 mg / cm 2 .
  • 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 simultaneously high strength values , in particular yield strength R p0,2 and tensile strength R m . Unwanted hardening and precipitation effects of Si are reduced by limiting the Si content to a maximum of 0.4% by weight. In order not to adversely affect the properties of the aluminum alloy, the Fe content should be limited to a maximum of 0.5 wt .-%.
  • 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.
  • the manganese content must be limited, since otherwise the forming properties of the re-annealed aluminum alloy strips are adversely affected.
  • too high Mn contents at the last intermediate annealing lead to mean grain diameters of less than 20 ⁇ m.
  • the Mn content should be 0.1% by weight to 0.4% by weight. Chromium, even in the smallest amounts, already causes the forming properties, for example the uniform elongation A g or the fracture contraction Z, to decrease, so that the forming properties are impaired.
  • the chromium content is to be limited to values of less than 0.05 wt .-%, preferably less than 0.01 wt .-%.
  • 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 of the aluminum alloy strip is according to the invention only 10% to 45%, since the degree of rolling before the last intermediate annealing decisively influences the formation of the grain structure during recrystallization during the intermediate annealing.
  • the intermediate annealing makes it possible to provide a recrystallized microstructure for the last cold rolling step, which is carried out with a rolling degree of 30% to 60% of final thickness.
  • the final rolling degree makes it possible, unlike soft annealed variants, to continuously increase the yield strength of the aluminum alloy strip to be produced by work hardening to the desired application, for example to a yield strength of more than 190 MPa after the subsequent final annealing.
  • the final annealing of the aluminum alloy strip in the coil at metal temperatures of 190 ° C to 250 ° C for at least 0.5 hours results in that the forming properties, in particular the uniform elongation A g and the Brucheinschnürung Z are improved by the recovery process in the structure of the aluminum alloy strip.
  • the production method can thus be used to provide an aluminum alloy strip which, on the one hand, can be shaped well, for example into a vehicle component, and on the other hand also provides high yield strengths in the unformed regions.
  • the produced aluminum alloy strip is at the same time also resistant to intergranular corrosion and, due to the simple production route, less expensive than previously used AA6XXX alloy strips.
  • the degree of rolling is limited to 20% to 30% in the case of cold rolling before the last intermediate annealing, larger grain diameters are provided in the aluminum alloy strip after the last intermediate annealing, thus improving the resistance to intergranular corrosion in the re-annealed aluminum alloy strip.
  • 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 ., the fracture constriction Z are adversely affected.
  • the method according to the invention makes it possible to provide aluminum alloy strips and sheets for conversion to vehicle components, for example body-in-white (BIW) components.
  • the temperature during the annealing of the aluminum alloy strip is 220 ° C to 240 ° C.
  • the forming capability of the aluminum alloy strip is increased by recovery processes with an increase in the uniform elongation A g and the Brucheinschnürung Z process reliable.
  • the high annealing temperatures of 220 ° C. to 240 ° C.
  • the above object is achieved by a cold-rolled and re-annealed aluminum alloy strip or sheet produced by the method of the invention consisting of an aluminum alloy having the following alloying components: 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 % . Residual Al and unavoidable impurities, individually max.0,05%, in total max.
  • the aluminum alloy ribbon a yield strength R p0.2 of more than 190 MPa, a uniform elongation A g of at least 14%, a fracture constriction Z of more than 50% and in the corrosion test according to ASTM G67 after a previous sensitization annealing for 17 h at 130 ° C has a mass loss of less than 15 mg / cm 2 .
  • an aluminum alloy strip or sheet having the above-mentioned aluminum alloy composition having a yield strength of more than 190 MPa, a uniform elongation A g of at least 14%, and a fracture waist Z of more than 50% while resisting the corrosion test according to ASTM G67 with a mass loss of less than 15 mg / cm 2 after a previous sensitization annealing for 17 h at 130 ° C for non-hardenable aluminum alloy tapes open up further applications previously reserved for aluminum alloy tapes of hardenable materials, in particular AA6xxx aluminum alloys.
  • Yield strengths Rp0.2 of greater than 190 MPa to 300 MPa with a uniform elongation of 14% to 18% and a breakage entanglement Z of more than 50% to 70% for given aluminum oxide composition are expected Corrosion resistance can be achieved.
  • the embodiments set forth below show inventive aluminum alloy strips or sheets with yield strengths R p0.2 of more than 190 MPa and up to 270 MPa while maintaining a good forming behavior due to a uniform expansion of A g up to 16.6% and a Brucheinschnürung Z from to to 62% with existing resistance to intergranular corrosion.
  • the yield strength values are opposite to the values obtained for the uniform elongation A g and the fracture constriction Z.
  • the Mg content of the aluminum alloy strip or sheet is 4.2% by weight to 6% by weight, preferably 4.2% by weight to 5.2% by weight Aluminum alloy strip or sheet with maximum yield strengths after the last cold rolling.
  • the manganese content is limited to 0.1 wt% to 0.3 wt% according to another aspect of the aluminum alloy strip or sheet, good and good strength can be attained despite the positive influence of manganese on the strength and corrosion resistance of the aluminum alloy strip or sheet Forming properties, ie high values for uniform expansion A g and the Brucheinschnürung Z can be achieved with high process reliability.
  • mean grain diameters of more than 20 ⁇ m can be set reliably, which positively influence 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 alloying ingredients: Si ⁇ 0.2 weight , - % . Fe ⁇ 0.35 weight , - % or Zn ⁇ 0.01 weight , - % . Negative effects of said alloying components on the properties of the aluminum alloy strip or sheet can be excluded.
  • the aluminum alloy strip or sheet according to the present embodiment allows a significantly increased field of application due to the greatly improved yield strengths compared to the previously annealed, soft annealed variants.
  • 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.
  • FIG. 1 shows first in a schematic representation of the method steps of an embodiment for producing an aluminum strip on an aluminum alloy according to the present invention.
  • step 1 a billet of aluminum alloy having the following alloy contents is cast: 3.6 weight , - % ⁇ mg ⁇ 6 weight , - % . Si ⁇ 0.4 weight , - % . Fe ⁇ 0.5 weight , - % . Cu ⁇ 0.15 weight , - % . 0.1 weight , - % ⁇ Mn ⁇ 0.4 weight , - % . Cr ⁇ 0.05 weight , - % . Zn ⁇ 0.20 weight , - % . Ti ⁇ 0.20 weight , - % .
  • Residual Al and unavoidable impurities individually max.0.05 wt .-%, in total max. 0.15% by weight.
  • 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 microns can be achieved.
  • Carrying out the last intermediate annealing of the cold-rolled aluminum alloy strip at 300 ° C. to 500 ° C.
  • step 6 provides for the final cold rolling step 6 a recrystallized structure with particle sizes of more than 20 ⁇ m. If necessary, steps 4 and 5 can be repeated to obtain thinner sheet thicknesses of final thickness if required.
  • step 6 work hardening is introduced into the recrystallized structure at a rolling degree of 30% to 60% of the final thickness, 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 uniform dimension A g and the Brucheinschnürung Z again assume higher values and a good forming behavior is set.
  • the increase in yield strength R p0.2 achieved during the last cold rolling remains at least partly due to the temperature selection after the annealing, so that an aluminum alloy strip with a yield strength of more than 190 MPa can be made available.
  • the produced aluminum alloy strip and sheets produced therefrom may also be subjected to complex forming processes.
  • additional step 8 are cut from the aluminum alloy strip sheets, which are then converted into forming processes to form 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 high forming capacity of the strips or sheets from which they are made.
  • BIW components made from an aluminum alloy also require correspondingly low sheet thicknesses, which requires high strengths and yield strengths of the aluminum alloy strips or sheets used.
  • the 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. If vehicle components, in particular BIW components, are therefore produced from an aluminum alloy strip according to the invention, they can be made available at lower cost than previous components made of AA6XXX materials.
  • FIGS. 2a) and 2b schematically show areas of application of the aluminum alloy strip produced according to the invention in the form of a wide variety of metal sheets according to a vehicle structure FIG. 2a ) or, for example, a schematically illustrated inner part of a vehicle door according to FIG. 2b ). Due to the good corrosion behavior of the aluminum alloy strips according to the present invention, further application possibilities for the non-curable, ie naturally hard, aluminum alloy strips and sheets according to the invention open up in the motor vehicle.
  • Roll bars were cast from various aluminum alloy compositions, subjected to homogenization at 480 ° C to 550 ° C for at least 0.5 hour, hot rolled at 280 ° C to 500 ° C into hot strip, and then subjected to varying conditions in cold rolling before and after a final intermediate annealing.
  • Table 1 shows a total of seven different alloy compositions. In the twelve experiments, in addition to the seven different alloys, different parameters were used for cold rolling before and after the last intermediate annealing. Until the completion of the hot strip, the test strips produced did not differ, apart from different hot strip thicknesses and different aluminum alloys. Table 1 Alloy components [% by weight] Experiment No.
  • the hot strips made of various aluminum alloys were then cold rolled according to the specifications in Table 2 in the cold rolling before the last intermediate annealing and after the intermediate annealing.
  • the 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 ao, which are approximately between 0.7 mm and 1.7 mm.
  • Comparative Examples Nos. 1 and 6 have excessive degrees of finish before intermediate annealing, whereas Comparative Example No. 3 has too low a final rolling degree after intermediate annealing.
  • the mean grain size ie the average grain diameter
  • 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.
  • Comparative Examples 1 and 2 clearly show the influence of the alloy composition on the results with regard to formability.
  • 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 which are less than 50%, indicating a deteriorated forming performance.
  • the Brucheinschnürung Z represents namely the property of the material, in large transformations over a cross-sectional reduction material for 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.
  • 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 over final rolling degrees after intermediate annealing of 31% to 60%, the yield strength R p0.2 can be increased to values up to 211 MPa without significant sacrifice in the range of characteristics important for forming how to draw the uniform strain A g or Z.
  • Comparative Example No. 6 which has an identical aluminum alloy as Examples 3, 4, 5 and 8, the effect of adjusting the average grain diameter by limiting the degree of rolling in cold rolling before the last intermediate annealing can be very clearly recognized.
  • the intermediate annealing produces a relatively fine grain having an average diameter or a mean grain size of 13 ⁇ m, which adversely affects the corrosion properties. Comparative Example No. 6 is classified as not resistant to intergranular corrosion.
  • the embodiments according to the invention show that the yield strength R p0.2 can be 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 p0.2 .
  • 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.
  • the corrosion resistance of these embodiments is significantly better than the smaller grain diameter and lower Mg content embodiment No. 9.
  • the preferred process route over the inventive limitations of the cold rolling degrees before the last intermediate annealing has a significant influence on the end product of the annealed strip.
  • the embodiments of the present invention show that an aluminum alloy ribbon having yield strengths, elongation values and corrosion resistance against intergranular corrosion, which is particularly well suited for use in high-stress vehicle components, can be manufactured inexpensively due to the use of a non-hardenable aluminum alloy can be.

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  • Engineering & Computer Science (AREA)
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EP16732581.0A 2015-06-25 2016-06-23 Hochfestes und gut umformbares almg-band sowie verfahren zu seiner herstellung Active EP3314031B1 (de)

Applications Claiming Priority (2)

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EP15173888 2015-06-25
PCT/EP2016/064530 WO2016207274A1 (de) 2015-06-25 2016-06-23 Hochfestes und gut umformbares almg-band sowie verfahren zu seiner herstellung

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EP3314031A1 EP3314031A1 (de) 2018-05-02
EP3314031B1 true EP3314031B1 (de) 2018-11-07

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

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RU2749101C1 (ru) * 2020-08-07 2021-06-04 Федеральное государственное бюджетное учреждение науки Самарский федеральный исследовательский центр Российской академии наук (СамНЦ РАН) СПОСОБ ХОЛОДНОЙ МНОГОПРОХОДНОЙ ПРОКАТКИ ТОНКИХ ЛЕНТ ИЗ АЛЮМИНИЕВЫХ СПЛАВОВ Al-Mg
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JP2024534911A (ja) * 2021-09-03 2024-09-26 スペイラ ゲゼルシャフト ミット ベシュレンクテル ハフツング 成形のために最適化されたアルミニウム合金ストリップおよび製造のための方法
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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KR20180016608A (ko) 2018-02-14
CN107787376A (zh) 2018-03-09
ES2700140T3 (es) 2019-02-14
CA2990303C (en) 2019-12-17
RU2685295C1 (ru) 2019-04-17
KR101911037B1 (ko) 2018-10-23
JP2018524468A (ja) 2018-08-30
CA2990303A1 (en) 2016-12-29
WO2016207274A1 (de) 2016-12-29
JP6481052B2 (ja) 2019-03-13
US20180112297A1 (en) 2018-04-26
US11352686B2 (en) 2022-06-07
EP3314031A1 (de) 2018-05-02

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