EP2811043B1 - Extrudat d'alliage d'aluminium à haute résistance présentant une excellente résistance à la corrosion, ductilité, et une trempabilité et son procédé de production - Google Patents

Extrudat d'alliage d'aluminium à haute résistance présentant une excellente résistance à la corrosion, ductilité, et une trempabilité et son procédé de production Download PDF

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Publication number
EP2811043B1
EP2811043B1 EP13742883.5A EP13742883A EP2811043B1 EP 2811043 B1 EP2811043 B1 EP 2811043B1 EP 13742883 A EP13742883 A EP 13742883A EP 2811043 B1 EP2811043 B1 EP 2811043B1
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Prior art keywords
aluminum alloy
mass
extruded shape
content
ductility
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German (de)
English (en)
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EP2811043A4 (fr
EP2811043A1 (fr
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Karin Shibata
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Aisin Keikinzoku Co Ltd
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Aisin Keikinzoku Co Ltd
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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
    • C22F1/047—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
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/02—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
    • 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
    • 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
    • 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 present invention relates to an extruded shape produced using an Al-Mg-Si-based aluminum alloy.
  • An automotive structural material is required to exhibit high strength, high bendability, and high corrosion resistance, and a JIS 7000 series aluminum alloy (Al-Zn-Mg-based aluminum alloy) and a JIS 6000 series aluminum alloy (Al-Mg-Si-based aluminum alloy) have attracted attention.
  • a 7000 series aluminum alloy naturally age hardening alloy
  • a 7000 series aluminum alloy shows a decrease in corrosion resistance under a stress environment.
  • a 6000 series aluminum alloy has been considered to be a promising heat-treatable alloy that does not undergo natural age hardening, and exhibits excellent corrosion resistance.
  • An extruded shape formed of a known high-strength 6000 series aluminum alloy exhibits high tensile strength, but exhibits insufficient elongation, and easily produces cracks during bending.
  • water-cooling press quenching is performed immediately after extrusion.
  • the water-cooling press quenching treatment has an advantage in that properties similar to those obtained by solution/quenching treatment that reheats the extruded alloy after extrusion can be obtained.
  • a difference in cooling rate occurs between each cross-sectional area due to the cross-sectional shape of the extruded shape, the difference in thickness, and the like, the extruded shape shows a non-uniform temperature distribution during cooling, and strain occurs. Therefore, the dimensional accuracy deteriorates, and it is difficult to reduce the thickness of the cross-sectional profile.
  • the degree of freedom of the cross-sectional shape decreases as a result of preventing occurrence of such strain.
  • the water-cooling press quenching treatment has another disadvantage in that an increase in cost occurs as compared with an air-cooling quenching treatment.
  • the air-cooling quenching treatment has an advantage in that cost can be reduced as compared with the water-cooling press quenching treatment.
  • the cooling rate is limited, high strength may not be obtained depending on the alloy composition, and a deterioration in ductility may occur although high strength can be obtained.
  • Patent Document 1 discloses an aluminum alloy extruded shape that exhibits excellent axial crush properties and corrosion resistance, and includes 0.4 to 0.8% of Mg, 0.3 to 0.9% of Si, 0.05% or less of Cu, and 0.095% or less of Mn, Cr, Zr in total, wherein the number of Mg 2 Si moieties having a length of 3 ⁇ m in the extrusion direction is 50 or more per mm 2 .
  • the alloy composition disclosed in Patent Document 1 provides excellent corrosion resistance, but achieves a proof stress of only about 220 MPa (i.e., cannot sufficiently contribute to a reduction in weight of the product). Since a water-cooling press quenching treatment is normally used in Patent Document 1, it is considered that the extrusion productivity is low.
  • Patent Document 2 discloses an aluminum alloy extruded shape that exhibits excellent hardenability and axial crush properties, and includes 0.45 to 0.75% of Mg, 0.45 to 0.80 of Si, 0.1 to 0.4% of excess Si, 0.15 to 0.40% of Mn, and 0 to 0.1 % of Cr, wherein Mn and Cr compounds are finely dispersed. Patent Document 2 achieves good productivity by utilizing an air-cooling press quenching treatment. However, the aluminum alloy extruded shape disclosed in Patent Document 2 has a proof stress of only about 220 MPa.
  • An object of the invention is to provide an Al-Mg-Si-based high-strength aluminum alloy extruded shape that exhibits excellent corrosion resistance and ductility, and exhibits excellent hardenability during extrusion (i.e., ensures high productivity), and a method for producing the same.
  • a high-strength aluminum alloy extruded shape that exhibits excellent corrosion resistance, ductility, and hardenability
  • the aluminum alloy extruded shape including 0.65 to 0.90 mass% of Mg, 0.60 to 0.90 mass% of Si, 0.20 to 0.40 mass% of Cu, 0.20 to 0.40 mass% of Fe, 0.10 to 0.20 mass% of Mn, and 0.005 to 0.1 mass% of Ti, with the balance being Al and unavoidable impurities, the aluminum alloy extruded shape having a stoichiometric Mg 2 Si content of 1.0 to 1.3 mass%, an excess Si content relative to stoichiometric Mg 2 Si of 0.10 to 0.30 mass%, and a total content of Fe and Mn of 0.35 mass% or more.
  • the unit “mass%” may be hereinafter referred to as "%".
  • the extruded shape is obtained by extruding an aluminum alloy having the above composition, cooling the extruded aluminum alloy at an average cooling rate of 100°C/min or less immediately after the extrusion, and subjecting the cooled aluminum alloy to artificial aging.
  • the average cooling rate is 100°C/min or less, it suffices to air-cool the aluminum alloy using a fan immediately after the extrusion instead of water-cooling the aluminum alloy, and press quenching by air-cooling can be implemented.
  • a cooling rate of 50 to 100°C/min can be achieved by cooling the extruded shape extruded from an extrusion press using a fan.
  • the extruded shape thus produced has a structure in which crystal grains having an aspect ratio of 4.0 or more have an average crystal grain size of 80 ⁇ m or less, and has a 0.2% proof stress ( ⁇ ) of 280 MPa or more.
  • spect ratio refers to the ratio (L 1 /L 2 ) of the length L 1 of the crystal grains of the recrystallized structure in the extrusion direction to the length L 2 of the crystal grains in the direction orthogonal to the extrusion direction.
  • average crystal grain size refers to the average diameter of circles respectively circumscribed to the crystal grains.
  • the extruded shape according to one aspect of the invention has an impact strength determined by a Charpy impact test of 20 J/cm 2 or more.
  • Mg and Si contribute to an improvement in the strength of the extruded shape through formation of Mg 2 Si precipitates.
  • the upper limit of the Mg content is set to 0.90%, and the upper limit of the Si content is set to 0.90%.
  • the Mg 2 Si content is set to 1.0 to 1.3% in order to obtain a 0.2% proof stress of 280 MPa or more while taking account of extrudability.
  • the excess Si content relative to stoichiometric Mg 2 Si is set to 0.10 to 0.30%.
  • Cu contributes to solid solution hardening, and ensures elongation when the Cu content is within a given range.
  • the Cu content is set to 0.2 to 0.4%.
  • One aspect of the invention is characterized in that the Fe content is set to 0.20 to 0.40%.
  • Fe refines the crystal grains of the extruded metal structure, and improves ductility.
  • Mn affects quench sensitivity during air-cooling using a fan immediately after extrusion.
  • the inventor of the invention conducted extensive studies, and found that Mn does not significantly affect quench sensitivity during air-cooling using a fan when the Mn content is 0.20% or less.
  • the inventor also found that, when the Mn content is 0.10 to 0.20%, a recrystallized structure that extends in the extrusion direction is obtained in which propagation of cracks is suppressed as compared with a spherical recrystallized structure, and the crystal grains have a small average crystal grain size.
  • the total content of Fe and Mn is set to 0.35% or more.
  • Ti refines the crystal grains when casting a billet subjected to extrusion.
  • the Ti content is preferably 0.005 to 0.10%.
  • the Ti content exceeds 0.10%, coarse intermetallic compounds may be easily produced, and may not disappear during extrusion. As a result, the strength of the extruded shape may decrease.
  • Additional components e.g., Cr, Zr, and Zn
  • additional components e.g., Cr, Zr, and Zn
  • the proof stress can be improved while ensuring extrudability by setting the stoichiometric Mg 2 Si content to 1.00 to 1.30%, and setting the excess Si content relative to stoichiometric Mg 2 Si to 0.10 to 0.30%. It is possible to achieve high strength and high ductility by press quenching via air-cooling in case that the Fe content is set to 0.20 to 0.40%, and the Mn content is set to 0.10 to 0.20% so that "Fe+Mn ⁇ 0.35 mass%" is satisfied.
  • Billets that differ in chemical composition were cast, extruded, and evaluated as described below.
  • a molten metal including the alloy components shown in FIG. 1 was prepared, and cast at a casting speed 60 mm/min or more to obtain a cylindrical billet having a diameter of 8 inches.
  • FIG. 2 shows the subsequent production conditions.
  • the cast billet was homogenized at 565 to 595°C for 2 to 6 hours (see “HOMO conditions").
  • FIG. 2 shows the extrusion speed and the cooling rate.
  • the cooling rate was set to 50 to 100°C/min in order to achieve press quenching by air-cooling using a fan. Note that the cooling rate was set to 200°C/min in Comparative Example 5.
  • the extruded shape was cooled to room temperature, and subjected to artificial aging at 185 to 200°C for 3 to 3.5 hours (see “Heat treatment conditions").
  • FIG. 3 shows the property evaluation results for the extruded shape thus produced.
  • FIG. 4 shows a photograph of the metal structure of Comparative Example 1 (see “RELATED-ART ALLOY”), and a photograph of the metal structure of Example 1 (see “INVENTIVE ALLOY”).
  • Corrosion resistance The stress corrosion cracking resistance (SCC resistance) was evaluated.
  • a No. 1 specimen was prepared in accordance with JIS H 8711, and subjected to the following cycle test in a state in which a stress equal to 100% of the 0.2% proof stress was applied.
  • a cycle (3.5% NaCl aqueous solution, 25°C, 10 min ⁇ air-drying (25°C, 40% (humidity), 50 min)) is repeated 720 times, and a case where no cracks were observed was evaluated as acceptable.
  • Impact strength A JIS V-notch No. 4 tensile test specimen was prepared from the extruded shape in accordance with JIS Z 2242. The impact strength was measured using a Charpy impact tester compliant to the JIS standard.
  • the target impact strength was set to 20 J/cm 2 or more.
  • the extruded shapes of Examples 1 to 10 had a flat recrystallized metal structure (microstructure) in which crystal grains having an aspect ratio of 4.0 or more had an average crystal grain size of 80 ⁇ m or less.
  • the extruded shapes of Examples 1 to 10 had a proof stress of 280 MPa or more (i.e., exhibited high strength), and had an elongation (ductility) of 8% or more.
  • the extruded shapes of Examples 1 to 10 had a Charpy impact strength of 20 J/cm 2 or more.
  • Comparative Example 14 had low proof stress, low elongation, and low impact strength since the excess Si content and the total content of Fe and Mn were low.
  • the aluminum alloy extruded shape according to the embodiments of the invention exhibits excellent corrosion resistance, ductility, and hardenability, the aluminum alloy extruded shape may be widely used as structural materials for vehicles, machines, and the like.

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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)
  • Extrusion Of Metal (AREA)

Claims (5)

  1. Profilé extrudé d'alliage d'aluminium à haute résistance qui présente une résistance à la corrosion, une ductilité et une trempabilité excellentes, le profilé extrudé d'alliage d'aluminium comprenant de 0,65 à 0,90 % en masse de Mg, de 0,60 à 0,90 % en masse de Si, de 0,20 à 0,40 % en masse de Cu, de 0,20 à 0,40 % en masse de Fe, de 0,10 à 0,20 % en masse de Mn, et de 0,005 à 0,1 % en masse de Ti, et le reste consistant en Al et en inévitables impuretés, le profilé extrudé d'alliage d'aluminium ayant une teneur en Mg2Si stoechiométrique de 1,0 à 1,3 % en masse, une teneur en Si en excès par rapport au Mg2Si stoechiométrique de 0,10 à 0,30 % en masse, et une teneur globale en Fe et Mn de 0,35 % en masse ou davantage.
  2. Profilé extrudé d'alliage d'aluminium à haute résistance tel que défini dans la revendication 1, dans lequel les grains de cristaux du profilé extrudé d'alliage d'aluminium ayant un rapport d'aspect de 4,0 ou davantage et ont une taille de grain de cristal moyenne de 80 µm ou moins.
  3. Profilé extrudé d'alliage d'aluminium à haute résistance tel que défini dans la revendication 1 ou 2, dans lequel le profilé extrudé d'alliage d'aluminium a une limite d'élasticité de 280 MPa ou davantage.
  4. Profilé extrudé d'alliage d'aluminium à haute résistance tel que défini dans la revendication 1 ou 2, dans lequel le profilé extrudé d'alliage d'aluminium a une résistance aux chocs déterminée par un essai de résilience de Charpy de 20 J/cm2 ou davantage.
  5. Procédé de production d'un profilé extrudé d'alliage d'aluminium à haute résistance qui présente une résistance à la corrosion, une ductilité et une trempabilité excellentes, le procédé consistant à extruder un alliage d'aluminium, à refroidir l'alliage d'aluminium extrudé à une vitesse de refroidissement moyenne de 100 °C / minute ou moins immédiatement après l'extrusion, et à soumettre l'alliage d'aluminium refroidi à un vieillissement artificiel, l'alliage d'aluminium comprenant de 0,65 à 0,90 % en masse de Mg, de 0,60 à 0,90 % en masse de Si, de 0,20 à 0,40 % en masse de Cu, de 0,20 à 0,40 % en masse de Fe, de 0,10 à 0,20 % en masse de Mn, et de 0,005 à 0,1 % en masse de Ti, et le reste consistant en Al et en inévitables impuretés, l'alliage d'aluminium ayant une teneur en Mg2Si stoechiométrique de 1,0 à 1,3 % en masse, une teneur en Si en excès par rapport au Mg2Si stoechiométrique de 0,10 à 0,30 % en masse, et une teneur globale en Fe et Mn de 0,35 % en masse ou davantage.
EP13742883.5A 2012-01-31 2013-01-30 Extrudat d'alliage d'aluminium à haute résistance présentant une excellente résistance à la corrosion, ductilité, et une trempabilité et son procédé de production Active EP2811043B1 (fr)

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JP2012018486 2012-01-31
PCT/JP2013/052002 WO2013115227A1 (fr) 2012-01-31 2013-01-30 Extrudat d'alliage d'aluminium à haute résistance présentant une excellente résistance à la corrosion, ductilité, et une trempabilité et son procédé de production

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EP2811043A1 EP2811043A1 (fr) 2014-12-10
EP2811043A4 EP2811043A4 (fr) 2015-11-18
EP2811043B1 true EP2811043B1 (fr) 2016-07-27

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US (1) US20140166165A1 (fr)
EP (1) EP2811043B1 (fr)
JP (1) JP6000988B2 (fr)
CN (1) CN103781927B (fr)
WO (1) WO2013115227A1 (fr)

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JP6644376B2 (ja) * 2014-02-28 2020-02-12 アイシン軽金属株式会社 成形性に優れた高強度アルミニウム合金押出材の製造方法
JP6612029B2 (ja) * 2015-01-28 2019-11-27 アイシン軽金属株式会社 耐衝撃性に優れる高強度アルミニウム合金押出材及びその製造方法
JP2016222958A (ja) * 2015-05-28 2016-12-28 株式会社神戸製鋼所 高強度アルミニウム合金板
CN105238970B (zh) * 2015-11-18 2016-12-28 全椒县志宏机电设备设计有限公司 一种高强度高延展性的铝合金
WO2019089736A1 (fr) 2017-10-31 2019-05-09 Arconic Inc. Alliages d'aluminium améliorés et leurs procédés de production
EP3737527A4 (fr) 2018-01-12 2021-10-20 Accuride Corporation Alliages d'aluminium destinés à des applications telles que des roues et procédés de fabrication
CN109778030B (zh) * 2019-03-19 2022-03-04 苏州铭恒金属科技有限公司 一种新的铝合金材料及其制备
CN113597478A (zh) * 2021-03-31 2021-11-02 三菱铝株式会社 表面品质优异的高强度铝合金挤压材料

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"International Alloy Designations and Chemical Composition Limits for Wrought Aluminum and Wrought Aluminum Alloys", REGISTRATION RECORD SERIES TEAL SHEETS, 2009, XP055441563
DR. MURAT TIRYAKIOGLU ET AL.: "Quench Sensitivity of Aluminum Alloys", March 1999 (1999-03-01), pages 1 - 10, XP055375639
KATHARINA STROBEL ET AL.: "Relating Quench Sensitivity to Microstructure in 6000 Series Aluminium Alloys", MATERIALS TRANSACTIONS, vol. 52, no. 5, 2011, pages 914 - 919, XP055441583
MALCOLM J. COUPER: "Selecting the Optimum Mg and Si Content for 6xxx Series Extrusion Alloys", PROCEEDINGS OF THE 12TH INTERNATIONAL CONFERENCE ON ALUMINIUM ALLOYS, 5 September 2010 (2010-09-05), Yokohama, Japan, pages 149 - 154, XP055375633
NICK PARSON ET AL.: "Control of Grain Structure in Al-Mg-Si Extrusions", PROCEEDINGS OF THE EIGHTH INTERNATIONAL ALUMINUM EXTRUSION TECHNOLOGY SEMINAR EXPLORING INNOVATIONS, 18 May 2004 (2004-05-18), Orlando, Florida, pages 11 - 22, XP055441590

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EP2811043A4 (fr) 2015-11-18
JP6000988B2 (ja) 2016-10-05
JPWO2013115227A1 (ja) 2015-05-11
CN103781927A (zh) 2014-05-07
EP2811043A1 (fr) 2014-12-10
CN103781927B (zh) 2017-02-08
WO2013115227A1 (fr) 2013-08-08
US20140166165A1 (en) 2014-06-19

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