US20050095167A1 - Hot-and cold-formed aluminum alloy - Google Patents

Hot-and cold-formed aluminum alloy Download PDF

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Publication number
US20050095167A1
US20050095167A1 US10/499,755 US49975504A US2005095167A1 US 20050095167 A1 US20050095167 A1 US 20050095167A1 US 49975504 A US49975504 A US 49975504A US 2005095167 A1 US2005095167 A1 US 2005095167A1
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US
United States
Prior art keywords
component
percent
weight
semi
finished product
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.)
Abandoned
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US10/499,755
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English (en)
Inventor
Andreas Barth
Patrick Laevers
Arne Mulkers
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.)
Mercedes Benz Group AG
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DaimlerChrysler AG
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 DaimlerChrysler AG filed Critical DaimlerChrysler AG
Assigned to DAIMLERCHRYSLER AG reassignment DAIMLERCHRYSLER AG ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: BARTH, ANDREAS, LAEVERS, PATRICK, MULKERS, ARNE
Publication of US20050095167A1 publication Critical patent/US20050095167A1/en
Priority to US11/974,466 priority Critical patent/US20080078480A1/en
Assigned to DAIMLER AG reassignment DAIMLER AG CHANGE OF NAME (SEE DOCUMENT FOR DETAILS). Assignors: DAIMLERCHRYSLER AG
Abandoned legal-status Critical Current

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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
    • 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
    • C22C21/06—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
    • C22F1/05—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 a hot- and cold-workable aluminum alloy according to claim 1 , and to a method for manufacturing an aluminum component according to claim 5 , as well as to the use of an aluminum alloy according to claim 9 .
  • High-strength Cu- (for example, Al Mg Si 1 Cu 0.5) or Zn-containing, heat-treated Al semi-finished products and Al forgings do have high static strength levels, but their elongation at break is low. Therefore, in the case of a notch effect (for example, stone impact), this results in a low dynamic strength. Moreover, these alloys are susceptible to corrosion so that expensive corrosion protection is required to avoid corrosion pits having a notch effect. Since, for example, highly stressed, forged Al suspension components are always exposed to stone impact (notching) and corrosion, Cu-/Zn-containing Al materials are used in these areas only in exceptional cases. Al Mg Si 1 alloys with higher ductility or lower notch sensitivity, such as EN-AW 6082, are, in fact, corrosion-resistant because of their low Cu- and Zn-content; however, these alloys do not reach adequate strength levels.
  • Unexamined German Laid-Open Patent Applications DE-OS 2 103 614 and DE OS 2 213 136 each describe an aluminum-silicon-magnesium alloy that reacts in a recrystallization-inhibiting manner; however, these alloys have insufficient strength, and the tendency of this alloy to recrystallize is still too high for cold-formed components or components undergoing multiple forming operations. The same is true for the known alloy according to EN-AW 6082.
  • the component or semi-finished product according to the present invention is made of an aluminum alloy having the following composition: silicon 0.9-1.3, magnesium 0.7-1.2, manganese 0.5-1.0, copper less than 0.1, iron less than 0.5, chromium less than 0.25, circonium and/or hafnium 0.05-0.2.
  • certain alloying constituents are present in the following proportions: copper less than 0.05, iron 0.1-0.5, chromium 0.05-0.2, zinc less than 0.05.
  • the alloy may contain the elements zinc less than 0.2 titanium less than 0.1.
  • titanium is used for grain refinement
  • zinc may contribute to an increase in strength
  • the alloy contains unavoidable impurities that are attributable to the manufacturing process.
  • the alloy has a silicon content of between 0.9 and 1.7 percent by weight.
  • the alloying elements manganese, chromium and circonium and/or hafnium all together represent a proportion of at least 0.4 percent by weight. Preferably, the proportion of these elements is higher than 0.6 percent by weight. These elements act as recrystallization inhibitors.
  • these elements together with aluminum, form intermetallic dispersoids which anchor the grain boundaries and do not dissolve, or dissolve only to a small extent, even during further heat treatments. Because the dispersoids are anchored at their grain boundaries, the grains are prevented from growing to coarse grains, thus effectively suppressing recrystallization. Circonium- and hafnium-containing dispersoids are particularly temperature-resistant, which has an inhibiting effect on the recrystallization at high temperatures.
  • the alloy has a silicon content of from 0.9 to 1.3%. It has turned out that a lower silicon content does not lead to the required strength levels.
  • the silicon acts in combination with the magnesium in the form of precipitation hardening (heat treatment) which develops in the form of Mg2Si precipitates. Higher contents of manganese and chromium also lead to precipitation hardening and an increase in strength.
  • the ratio of silicon to manganese is preferably between 1.1:1 and 1.3:1, more preferably between 1.16:1 to 1.24:1.
  • the alloy is particularly resistant to recrystallization both during hot and cold working, and intrinsically has high strength and a low susceptibility to corrosion, nearly independently of the manufacturing process.
  • the low susceptibility to corrosion is primarily attributable to the low content of copper and zinc.
  • the cast raw material of the alloy is homogenized at temperatures between 420° C. and 540° C., preferably between 460° C. and 500° C.
  • the alloying constituents magnesium and silicon are finely distributed in the aluminum matrix and, moreover, the dispersoids form whose composition is based on circonium or hafnium, manganese, chromium and/or iron.
  • the raw material is formed into semi-finished products at a temperature between 450° C. and 560° C. (for example, by extrusion or sheet rolling) and quenched, if necessary.
  • the semi-finished products are preferably formed between 500° C. and 560° C., it being necessary to select, in each case, the highest temperature possible in order to avoid recrystallization nuclei.
  • the semi-finished products are cut apart into workpieces that are suitable for forming, and are either cold-formed once or multiple times or hot-formed into components or further semi-finished products, possibly multiple times.
  • the semi-finished products may also be machined in a suitable manner, for example, by turning or milling. Cold- or hot-forming or machining may be carried out within the scope of expert skills and may possibly include usual heat treatments.
  • the hot-forming of the semi-finished product is carried out at temperatures in the range of the usual solution treatment (between 440° C. and 560° C.).
  • the forming process in particular, during multiple forming steps, care must be taken that the workpiece temperature does not fall below the mentioned temperature, which would result in coarse precipitations in the grain structure of the component. Accordingly, the forming process replaces the step of solution treatment, which has a considerable effect on the process costs and process duration.
  • the forming temperatures according to the present invention which at the same time imply a solution treatment, are higher than the usual forming temperatures, which results in a lower work hardening and thus in less formation of recrystallization nuclei in the grain structure.
  • recrystallization is effectively suppressed, resulting in higher strength levels and, above all, in a significantly higher elongation at break in highly worked areas.
  • the workpiece is preferably quenched in water, thus freezing the grain structure.
  • the desired increase in strength occurs during the subsequent artificial aging between 160° C. und 240° C.
  • the aluminum component according to the present invention has a tensile strength of at least 400 MPa and a minimum breaking strain (A5) of 10%.
  • Components of this kind are preferably used as tension rods or other suspension components, sections, bolts, screws, or wheels.
  • the ingots are homogenized at a temperature of 480° C. for 12 hrs.
  • the round rods are quenched and cut apart into workpieces having a length of about 20 cm.
  • the tension rods are quenched in water and artificially aged at 200° C. for 4 hrs.
  • the tension rods have a tensile strength of more than 400 MPa and an elongation at break (A5) of more than 13% both in the region of a central rod and in the region of a large eye which usually has a high degree of recrystallization due to the high degree of deformation.

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  • Chemical & Material Sciences (AREA)
  • Mechanical Engineering (AREA)
  • Organic Chemistry (AREA)
  • Metallurgy (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Forging (AREA)
  • Cookers (AREA)
  • Powder Metallurgy (AREA)
  • Conductive Materials (AREA)
US10/499,755 2001-12-21 2002-12-18 Hot-and cold-formed aluminum alloy Abandoned US20050095167A1 (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
US11/974,466 US20080078480A1 (en) 2001-12-21 2007-10-12 Hot-and cold-formed aluminum alloy

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
DE10163039A DE10163039C1 (de) 2001-12-21 2001-12-21 Warm- und kaltumformbares Bauteil aus einer Aluminiumlegierung und Verfahren zu seiner Herstellung
DE10163039.5 2001-12-21
PCT/EP2002/014452 WO2003054243A1 (de) 2001-12-21 2002-12-18 Warm- und kaltumformbare aluminiumlegierung

Related Child Applications (1)

Application Number Title Priority Date Filing Date
US11/974,466 Division US20080078480A1 (en) 2001-12-21 2007-10-12 Hot-and cold-formed aluminum alloy

Publications (1)

Publication Number Publication Date
US20050095167A1 true US20050095167A1 (en) 2005-05-05

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US10/499,755 Abandoned US20050095167A1 (en) 2001-12-21 2002-12-18 Hot-and cold-formed aluminum alloy
US11/974,466 Abandoned US20080078480A1 (en) 2001-12-21 2007-10-12 Hot-and cold-formed aluminum alloy

Family Applications After (1)

Application Number Title Priority Date Filing Date
US11/974,466 Abandoned US20080078480A1 (en) 2001-12-21 2007-10-12 Hot-and cold-formed aluminum alloy

Country Status (7)

Country Link
US (2) US20050095167A1 (de)
EP (1) EP1458898B1 (de)
AT (1) ATE294252T1 (de)
AU (1) AU2002352255A1 (de)
DE (2) DE10163039C1 (de)
ES (1) ES2239261T3 (de)
WO (1) WO2003054243A1 (de)

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20100028101A1 (en) * 2008-07-30 2010-02-04 Olab S.R.L. Hot pressing process, particularly for providing metal unions for pneumatic, hydraulic and fluid-operated circuits, and metal union obtained thereby
US20150050520A1 (en) * 2011-12-02 2015-02-19 Uacj Corporation Aluminum alloy material, aluminum alloy structure, and manufacturing method for same
US10378088B2 (en) * 2015-02-10 2019-08-13 Mitsubishi Aluminum Co., Ltd. Aluminum alloy fin material and heat exchanger
EP3464659B1 (de) 2016-06-01 2020-03-11 Aleris Aluminum Duffel BVBA 6xxx-serien-aluminiumlegierungsschmiederohmaterial und verfahren zur herstellung davon
US10646914B2 (en) 2018-01-12 2020-05-12 Accuride Corporation Aluminum alloys for applications such as wheels and methods of manufacture
WO2021064320A1 (fr) 2019-10-04 2021-04-08 Constellium Issoire Toles de precision en alliage d'aluminium

Families Citing this family (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102005060297A1 (de) * 2005-11-14 2007-05-16 Fuchs Kg Otto Energieabsorbtionsbauteil
JP4944525B2 (ja) * 2006-07-18 2012-06-06 株式会社神戸製鋼所 ボルトの製造方法、ボルト、ボルト用の形材、ボルト用の形材の成形装置及びボルト用の形材の成形方法
DE102007032143A1 (de) * 2007-07-09 2009-01-15 Thyssenkrupp Drauz Nothelfer Gmbh Tür eines Kraftfahrzeuges
DE102009059804A1 (de) 2009-12-21 2011-06-22 Daimler AG, 70327 Verfahren zur Wärmebehandlung von miteinander verschraubbaren Gussbauteilen
JP5872443B2 (ja) 2012-03-30 2016-03-01 株式会社神戸製鋼所 自動車用アルミニウム合金鍛造材およびその製造方法
JP6316747B2 (ja) * 2012-06-27 2018-04-25 株式会社Uacj ブロー成形用アルミニウム合金板およびその製造方法
SI24911A (sl) 2016-03-04 2016-07-29 Impol 2000, d.d. Visokotrdna aluminijeva zlitina Al-Mg-Si in njen postopek izdelave
CN112522552B (zh) * 2020-11-04 2022-04-26 佛山科学技术学院 一种耐蚀的铝合金及其制备方法和应用

Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3717512A (en) * 1971-10-28 1973-02-20 Olin Corp Aluminum base alloys
US3945860A (en) * 1971-05-05 1976-03-23 Swiss Aluminium Limited Process for obtaining high ductility high strength aluminum base alloys
US4174232A (en) * 1976-12-24 1979-11-13 Swiss Aluminium Ltd. Method of manufacturing sheets, strips and foils from age hardenable aluminum alloys of the Al-Si-Mg-type
US4511409A (en) * 1982-07-02 1985-04-16 Cegedur Societe De Transformation De L'aluminium Pechiney Process for improving both fatigue strength and toughness of high-strength Al alloys
US5690758A (en) * 1993-12-28 1997-11-25 Kaiser Aluminum & Chemical Corporation Process for the fabrication of aluminum alloy sheet having high formability
US5738735A (en) * 1995-07-28 1998-04-14 Pechiney Rhenalu Al-Cu-Mg alloy with high creep resistance
US6630037B1 (en) * 1998-08-25 2003-10-07 Kobe Steel, Ltd. High strength aluminum alloy forgings

Family Cites Families (8)

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Publication number Priority date Publication date Assignee Title
CA962172A (en) * 1971-05-05 1975-02-04 Olin Corporation High ductility high strength aluminum base alloys and process for obtaining same
JPS58156197A (ja) * 1982-03-10 1983-09-17 Sumitomo Light Metal Ind Ltd 超高圧用プレ−トフイン型熱交換器
FR2617188B1 (fr) * 1987-06-23 1989-10-20 Cegedur Alliage a base d'al pour boitage et procede d'obtention
US5108519A (en) * 1988-01-28 1992-04-28 Aluminum Company Of America Aluminum-lithium alloys suitable for forgings
JPH03287738A (ja) * 1990-04-03 1991-12-18 Kobe Steel Ltd 真空ろう付け法により組立てられる熱交換器用フィン材及びその製造方法
DE4421744C2 (de) * 1993-07-02 1996-05-23 Fuchs Fa Otto Verwendung einer Knetlegierung des Types AlMgSiCu zur Herstellung von hochfesten und korrosionsbeständigen Teilen
FR2744136B1 (fr) * 1996-01-25 1998-03-06 Pechiney Rhenalu Produits epais en alliage alznmgcu a proprietes ameliorees
JPH11310841A (ja) * 1998-04-28 1999-11-09 Nippon Steel Corp 疲労強度に優れたアルミニウム合金押出形材およびその製造方法

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3945860A (en) * 1971-05-05 1976-03-23 Swiss Aluminium Limited Process for obtaining high ductility high strength aluminum base alloys
US3717512A (en) * 1971-10-28 1973-02-20 Olin Corp Aluminum base alloys
US4174232A (en) * 1976-12-24 1979-11-13 Swiss Aluminium Ltd. Method of manufacturing sheets, strips and foils from age hardenable aluminum alloys of the Al-Si-Mg-type
US4511409A (en) * 1982-07-02 1985-04-16 Cegedur Societe De Transformation De L'aluminium Pechiney Process for improving both fatigue strength and toughness of high-strength Al alloys
US5690758A (en) * 1993-12-28 1997-11-25 Kaiser Aluminum & Chemical Corporation Process for the fabrication of aluminum alloy sheet having high formability
US5738735A (en) * 1995-07-28 1998-04-14 Pechiney Rhenalu Al-Cu-Mg alloy with high creep resistance
US6630037B1 (en) * 1998-08-25 2003-10-07 Kobe Steel, Ltd. High strength aluminum alloy forgings

Cited By (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20100028101A1 (en) * 2008-07-30 2010-02-04 Olab S.R.L. Hot pressing process, particularly for providing metal unions for pneumatic, hydraulic and fluid-operated circuits, and metal union obtained thereby
US20150050520A1 (en) * 2011-12-02 2015-02-19 Uacj Corporation Aluminum alloy material, aluminum alloy structure, and manufacturing method for same
US9574253B2 (en) * 2011-12-02 2017-02-21 Uacj Corporation Aluminum alloy material, aluminum alloy structure, and manufacturing method for same
US9903008B2 (en) 2011-12-02 2018-02-27 Uacj Corporation Aluminum alloy material, aluminum alloy structure, and manufacturing method for same
US10378088B2 (en) * 2015-02-10 2019-08-13 Mitsubishi Aluminum Co., Ltd. Aluminum alloy fin material and heat exchanger
EP3464659B1 (de) 2016-06-01 2020-03-11 Aleris Aluminum Duffel BVBA 6xxx-serien-aluminiumlegierungsschmiederohmaterial und verfahren zur herstellung davon
US10646914B2 (en) 2018-01-12 2020-05-12 Accuride Corporation Aluminum alloys for applications such as wheels and methods of manufacture
US11420249B2 (en) 2018-01-12 2022-08-23 Accuride Corporation Aluminum wheels and methods of manufacture
WO2021064320A1 (fr) 2019-10-04 2021-04-08 Constellium Issoire Toles de precision en alliage d'aluminium
CN114450425A (zh) * 2019-10-04 2022-05-06 伊苏瓦尔肯联铝业 铝合金精密板

Also Published As

Publication number Publication date
AU2002352255A1 (en) 2003-07-09
EP1458898B1 (de) 2005-04-27
ATE294252T1 (de) 2005-05-15
ES2239261T3 (es) 2005-09-16
EP1458898A1 (de) 2004-09-22
US20080078480A1 (en) 2008-04-03
DE50202955D1 (de) 2005-06-02
DE10163039C1 (de) 2003-07-24
WO2003054243A1 (de) 2003-07-03

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