EP0846781B1 - Procédé de production d'une tole en alliage d'aluminium presentant une excellente aptitude au formage superplastique à haute vitesse. - Google Patents

Procédé de production d'une tole en alliage d'aluminium presentant une excellente aptitude au formage superplastique à haute vitesse. Download PDF

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Publication number
EP0846781B1
EP0846781B1 EP95940435A EP95940435A EP0846781B1 EP 0846781 B1 EP0846781 B1 EP 0846781B1 EP 95940435 A EP95940435 A EP 95940435A EP 95940435 A EP95940435 A EP 95940435A EP 0846781 B1 EP0846781 B1 EP 0846781B1
Authority
EP
European Patent Office
Prior art keywords
elongation
alloy
forming
temperature
less
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.)
Expired - Lifetime
Application number
EP95940435A
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German (de)
English (en)
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EP0846781A1 (fr
EP0846781A4 (fr
Inventor
Hideo Sumitomo Light Metal Ind. Ltd. YOSHIDA
Hiroki Sumitomo Light Metal Ind. Ltd. TANAKA
Kouichirou Sumitomo Light Met.Ind.Ltd. TAKIGUCHI
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Sumitomo Light Metal Industries Ltd
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Sumitomo Light Metal Industries Ltd
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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
    • 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

  • This invention relates to a method of producing an aluminum alloy sheet which has excellent high-speed superplastic formability, and more specifically, to a method involving an Al-Mg alloy sheet which enables superplastic forming at high strain rate of 10 -2 to 10 0 /s.
  • an aluminum alloy sheet containing 2.0 to 6.0% of Mg, 0.0001 to 0.01% of Be, and 0.001 to 0.15% of Ti, with Fe and Si as impurities being controlled each at 0.2% or less and the largest grain diameter of impurity-based intermetallic compounds limited to 10 ⁇ m or less is proposed in Japanese Patent Application Laid-Open No. 72030/1992. While such a product does show an elongation of 350% or more at a strain rate of 10 -3 /s under a high-temperature deformation condition of 400°C, the elongation decreases as the forming speed increases and becomes insufficient at strain rates of 10 -2 /s or higher.
  • Another aluminum alloy sheet proposed in Japanese Patent Application Laid-Open No. 318145/1992, contains 2 to 5% of Mg, 0.04 to 0.10% of Cu, as well as optional small quantities of certain transition elements, Cr, Zr, or Mn; with Si and Fe as impurities being controlled at 0.1% or less, and at 0.15% or less, respectively; while controlling the crystal grain diameter at 20 ⁇ m or less and maintaining the grain diameter and the cubic ratio of transition metal-based intermetallic compounds within certain specific ranges.
  • Such an alloy sheet also has a limited application range of strain rates in the order of 10 -4 /s, and is not suitable for high strain rate superplastic forming at a higher strain rate.
  • the present invention has been achieved as a result of diverse examination and exhaustive experiments concerning the relationships of superplastic formability with various alloy constituents and their quantitative combinations, in addition to those with impurity content and their distribution, as well as with crystal grain diameters of impurity-based intermetallic compounds, made in an attempt to overcome the aforementioned shortcomings of the Al-Mg superplastic aluminum alloy.
  • the object of the present invention is to provide, by identifying a particular distribution and crystal grain diameter range for Al-Fe-Si compounds to be controlled based on restriction of Fe and Si as impurities, a method of producing an aluminum alloy sheet using a high strain rate superplastic forming in a forming process with a high forming speed such as at a strain rate ranging from 10 -2 to 10 0 /s.
  • Mg acts to recrystallize the alloy during the high-temperature deformation.
  • the content range is between 3.0 and 8.0%, below which the effect on promoting the recrystallization is insufficient while a content in excess of 8.0% acts to reduce hot workability of the material.
  • Cu acts to improve the superplastic elongation of the Al-Mg alloy system.
  • the content range is between 0.05 to 0.50%, where a content below 0.05% fails to give sufficient elongation while a content in excess of 0.50% acts to reduce the hot workability.
  • Ti acts to turn the ingot crystals into finer grains and to provide the alloy with a better superplastic formability.
  • the content range is between 0.001 to 0.1%, where a content below 0.001% will fail to give the expected effect and a content in excess of 0.1% will yield coarse compounds that hinder workability as well as ductility.
  • Mn and Cr act to make recrystallized grains finer in the alloy recrystallization process that occurs during high-temperature deformation.
  • the content range is below 0.10% for each, where a content in excess of 0.10% will act to increase a constituent particle whose grain diameter is 1 ⁇ m or above to decrease the superplastic formability of the alloy.
  • Fe and Si are impurities each at 0.06% or less.
  • These impurities form an Al-Fe-Si compound that is insoluble and prone to precipitate along the grain boundary, increasing cavities and thereby impairing the superplastic elongation.
  • the Fe and Si should each be controlled at 0.05% or less. It is also noted here that up to 50 ppm of Be may be added to prevent oxidation of the molten metal, just as in the case of ordinary Al-Mg alloys.
  • the Al-Fe-Si compound present in the alloy matrix gives rise to the above mentioned problem, it is better to allow as little of such a compound as possible, and, in particular, the limit in terms of number per square millimeter of an Al-Fe-Si compound having a grain diameter of 1 ⁇ m or more should be 2000 or less, since particles in excess of 2000 per square millimeter will increase cavities and thereby impair the superplastic elongation.
  • the original mean crystal grain diameter of the aluminum alloy sheet it is preferrably required to regulate the original mean crystal grain diameter of the aluminum alloy sheet within a range of 25 to 200 ⁇ m. If the original mean crystal grain diameter is below 25 ⁇ m, the original crystal grains will be recreated when recrystallization occurs during high temperature deformation, making it difficult to obtain a recrystallized structure with clean crystal grains as a result of a recrystallization process to obliterate the grain boundary with precipitation of the aforementioned insoluble compounds. If the original mean crystal grain diameter exceeds 200 ⁇ m, the shearing deformation within the crystal grains becomes more prominent with increasing deformation rate, causing the crystal grains to rupture more easily, thus suppressing the superplastic elongation.
  • the range of the strain rate during the forming process is between 10 -2 to 10°/s, where a rate below 10 -2 /s will cause the crystal grains to become coarser, reducing elongation, while a strain rate exceeding 10°/s creates a shearing deformation within the crystal grains causing cracks, or forms precipitation along the grain boundary, reducing elongation.
  • an aluminum alloy material with the above mentioned composition is melted, cast, and homogenized according to a conventional method. It is preferable to carry out the homogenizing process at a temperature between 450 to 550°C. At temperatures below 450°C, Mg or Cu that are formed along the grain boundary or the cell boundary of the ingot by segregation will not be fully dissolved and may contribute to cracks in a subsequent hot rolling step. Conversely, at temperatures exceeding 550°C, the Al-Mg or Al-Mg-Cu crystallization products will cause a eutectic fusion thereby giving rise to cracks during the hot rolling process.
  • the ingot is hot-rolled to obtain a structure suitable as a forming material. While the required starting temperature for hot rolling is between 250 to just under 400°C. If the hot rolling process is started at a temperature below 250°C, the deformation resistance is too high, making proper rolling difficult. If the rolling temperature is too high, this could alter the distribution form of the precipitation, thereby making it difficult to obtain the required crystal grain structure as well as proper distribution of precipitated compounds.
  • a cold rolling is provided.
  • an intermediate annealing may be provided as necessary.
  • the final annealing of the cold rolled stock should be provided at a temperature between 350 to 550°C. If the annealing is performed at a temperature below 350°C, the isotropy created during the cold rolling process may not completely disappear; if higher than 550°C, a local melting may occur at the recrystallization boundary. As such, it is preferred to conduct the final annealing in a rapid annealing process such as continuous annealing.
  • the Al-Fe-Si compounds present in the matrix are controlled within certain specific distribution while maintaining the crystal grain diameter within a certain specific range, resulting in such alloy structure and characteristics to produce cleaner grain boundaries with less compounds formed along these bounderies to suppress cavity formation. Recrystallized grains having an average diameter of 20 ⁇ m or less are formed during a high-temperature deformation, thereby achieving an excellent elongation of 380% or greater in high speed forming at a strain rate of 10 -2 to 10°/s in a temperature range of 350 to 550°C.
  • Al-Mg based aluminum alloys having compositions as listed in Table-1 below were melted and cast into ingots via a DC casting method.
  • the resultant ingots were homogenized at 530°C for 10 hours to a thickness of 30 mm, and then hot rolled at 390°C to a thickness of 4 mm.
  • the sheets were subsequently cold rolled to a thickness of 2 mm and then rapidly annealed by heating rapidly to 480°C and holding at this temperature for 5 minutes.
  • Specimens prepared from the test materials produced in the above process were evaluated by a tensile test at a strain rate of 10 -2 /s at 480°C.
  • Table 1 lists the average crystal grain diameter for each specimen(as measured at the sheet surface), the number per square millimeter of grains of the AL-Fe-Si compound having a diameter of 1 ⁇ m or above, and the elongation measurement results. Note here that the grain count of the compound was made using image processing.
  • Al-Mg based aluminum alloys having compositions as listed in Table 2 were melted and cast into ingots in the same manner as in Examples 1, and made into 2-mm thick test materials using the same process as in Examples 1. Specimens were then evaluated in the same tensile test under the same conditions. Table 2 lists the average crystal grain diameter, the number per square millimeter of grains of the AL-Fe-Si compound having a diameter of 1 ⁇ m or above, and the elongation measurement results.
  • the average crystal grain diameter (as measured at the sheet surface) for all of these specimens was in the range of 50 to 60 ⁇ m, and the number per square millimeter of grains of the AL-Fe-Si compound having a diameter of 1 ⁇ m or above, likewise, was below 2000.
  • the present invention provides a method for the production of an Al-Mg aluminum alloy sheet having excellent superplastic elongation in high speed forming such as at high strain rate of 10 -2 to 10 0 /s at a high temperature, and a superplastic forming process using this aluminum alloy sheet shortens the forming time to improve productivity.

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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)
  • Shaping Metal By Deep-Drawing, Or The Like (AREA)
  • Heat Treatment Of Steel (AREA)

Claims (4)

  1. Procédé de production d'une tôle d'alliage d'aluminium avec une excellente capacité de formage superplastique à grande vitesse par fusion d'un alliage comportant :
    3,0 à 8,0% en poids de Mg, 0,001 à 0,1% en poids de Ti,
    0,06% en poids ou moins de Fe et Si chacun, éventuellement 0,05 à 0,50% en poids de Cu, 0 à 50 ppm de Be, pas plus de 0,10% en poids de Mn, pas plus de 0,1% en poids de Cr et le reste étant de l'Al et des impuretés inévitables,
    coulée et homogénéisation de l'alliage, suivies d'un laminage à chaud à 250 jusqu'à juste en dessous de 400°C et recuit de la tôle d'alliage à 350 à 550°C,
    et formage de l'alliage ainsi obtenu à une vitesse de déformation de 10-2 à 100/s à une température de 350 à 550°C avec un allongement supérieur à 380%.
  2. Procédé selon la revendication 1, selon lequel les quantités commandées de Fe et Si sont de 0,05 ou moins.
  3. Procédé selon la revendication 1 ou 2, selon lequel le nombre par millimètre carré de grains d'un composé Al-Fe-Si dans la structure de matrice dudit alliage ayant un diamètre de 1 µm ou plus est de 2000 ou moins.
  4. Procédé selon la revendication 1, 2 ou 3, selon lequel le diamètre de grain de cristal moyen d'un composé Al-Fe-Si est de 25 à 200 µm.
EP95940435A 1995-08-23 1995-12-12 Procédé de production d'une tole en alliage d'aluminium presentant une excellente aptitude au formage superplastique à haute vitesse. Expired - Lifetime EP0846781B1 (fr)

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
JP23770795A JP3145904B2 (ja) 1995-08-23 1995-08-23 高速超塑性成形に優れたアルミニウム合金板およびその成形方法
JP23770795 1995-08-23
JP237707/95 1995-08-23
PCT/JP1995/002564 WO1997008354A1 (fr) 1995-08-23 1995-12-12 Tole en alliage d'aluminium presentant une excellente aptitude au formage superplastique a haute vitesse et procede de production de cette tole

Publications (3)

Publication Number Publication Date
EP0846781A1 EP0846781A1 (fr) 1998-06-10
EP0846781A4 EP0846781A4 (fr) 1998-11-18
EP0846781B1 true EP0846781B1 (fr) 2000-11-15

Family

ID=17019320

Family Applications (1)

Application Number Title Priority Date Filing Date
EP95940435A Expired - Lifetime EP0846781B1 (fr) 1995-08-23 1995-12-12 Procédé de production d'une tole en alliage d'aluminium presentant une excellente aptitude au formage superplastique à haute vitesse.

Country Status (5)

Country Link
US (1) US20010001969A1 (fr)
EP (1) EP0846781B1 (fr)
JP (1) JP3145904B2 (fr)
DE (1) DE69519444T2 (fr)
WO (1) WO1997008354A1 (fr)

Families Citing this family (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP4534573B2 (ja) * 2004-04-23 2010-09-01 日本軽金属株式会社 高温高速成形性に優れたＡｌ‐Ｍｇ合金板およびその製造方法
US8420011B2 (en) 2005-01-19 2013-04-16 Kobe Steel, Ltd. Aluminum alloy plate and process for producing the same
EP1975263A4 (fr) 2006-01-12 2012-03-07 Furukawa Sky Aluminum Corp Alliages d aluminium pour une formation a haute temperature et a grande vitesse, leurs procedes de production et procede de production des formes d alliage d aluminium
KR100676174B1 (ko) * 2006-05-25 2007-02-01 주식회사 엠코 철골건축구조물용 착탈식 안전망 설치대
US8323428B2 (en) * 2006-09-08 2012-12-04 Honeywell International Inc. High strain rate forming of dispersion strengthened aluminum alloys
JP2016191137A (ja) * 2015-03-31 2016-11-10 株式会社神戸製鋼所 樹脂被覆缶胴用アルミニウム合金板
JP2018199866A (ja) * 2018-08-24 2018-12-20 株式会社神戸製鋼所 樹脂被覆缶胴用アルミニウム合金板
CN113695538B (zh) * 2021-09-03 2023-07-25 中铝河南洛阳铝加工有限公司 一种高成形性镜面铝板带材的制备方法及镜面铝板带材

Family Cites Families (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS59159961A (ja) * 1983-02-28 1984-09-10 Mitsubishi Alum Co Ltd 超塑性Ａｌ合金
JPH02285046A (ja) * 1989-04-26 1990-11-22 Sky Alum Co Ltd 超塑性加工用アルミニウム合金圧延板およびその製造方法
JP2517445B2 (ja) * 1990-06-05 1996-07-24 スカイアルミニウム株式会社 ダイアフラム成形用ａ１合金板およびその製造方法
JP2865499B2 (ja) * 1991-09-26 1999-03-08 健 増本 超塑性アルミニウム基合金材料及び超塑性合金材料の製造方法
JP2510449B2 (ja) * 1992-01-31 1996-06-26 スカイアルミニウム株式会社 ロ―ルボンドパネル用クラッド板の製造方法
JPH05230583A (ja) * 1992-02-25 1993-09-07 Mitsubishi Alum Co Ltd 成形加工性のすぐれた高強度Ａｌ合金板材
JPH05345963A (ja) * 1992-06-12 1993-12-27 Furukawa Alum Co Ltd 高成形性アルミニウム合金板の製造方法
DE69304009T2 (de) * 1992-10-23 1997-02-06 Kawasaki Steel Co Verfahren zur Herstellung von Blech aus Al-Mg - Legierung für Pressformen
US5518558A (en) * 1992-11-17 1996-05-21 The Furukawa Electric Co., Ltd. Aluminum alloy sheets excellent in strength and deep drawing formability and process for manufacturing same
JPH07145441A (ja) * 1993-01-27 1995-06-06 Toyota Motor Corp 超塑性アルミニウム合金およびその製造方法
JPH06240395A (ja) * 1993-02-12 1994-08-30 Sky Alum Co Ltd 超塑性成形用アルミニウム合金板、その製造方法およびそれを用いた超塑性成形体
JPH07197177A (ja) * 1994-01-10 1995-08-01 Sky Alum Co Ltd キャビテーションの少ない超塑性成形用アルミニウム合金圧延板
JPH08199272A (ja) * 1995-01-19 1996-08-06 Nippon Steel Corp アルミニウム合金板とその成形方法

Also Published As

Publication number Publication date
EP0846781A1 (fr) 1998-06-10
US20010001969A1 (en) 2001-05-31
JPH0959736A (ja) 1997-03-04
JP3145904B2 (ja) 2001-03-12
WO1997008354A1 (fr) 1997-03-06
DE69519444D1 (de) 2000-12-21
EP0846781A4 (fr) 1998-11-18
DE69519444T2 (de) 2001-06-13

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