EP1390553A1 - Procede de preparation d'une feuille en alliage d'aluminium a aptitude au pliage amelioree et feuille en alliage d'aluminium ainsi produite - Google Patents
Procede de preparation d'une feuille en alliage d'aluminium a aptitude au pliage amelioree et feuille en alliage d'aluminium ainsi produiteInfo
- Publication number
- EP1390553A1 EP1390553A1 EP02727087A EP02727087A EP1390553A1 EP 1390553 A1 EP1390553 A1 EP 1390553A1 EP 02727087 A EP02727087 A EP 02727087A EP 02727087 A EP02727087 A EP 02727087A EP 1390553 A1 EP1390553 A1 EP 1390553A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- aluminum alloy
- weight
- aging
- sheet material
- alloy sheet
- 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.)
- Withdrawn
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
- 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
- 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
- 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
- C22F1/047—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
- 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 is directed to a process for preparing an aluminum alloy sheet having improved bendability and paint bake response.
- the invention is also directed to an aluminum alloy sheet obtained by the process.
- an aluminum alloy sheet product must possess good forming characteristics in the as-supplied temper so that it can be shaped and bent as desired.
- the alloy product after shaping, painting and baking must have sufficient strength to resist dents and other impacts.
- Aluminum alloys of the AA (Aluminum Association) 6000 series are desired to have low yield strength in the as-supplied temper and high yield strength in the finished product.
- the low yield strength in the as-supplied temper is desirable to obtain excellent formability and reduced springback, while high yield strength in the finished product is required for adequate dent resistance at the lowest possible gauge for maximum weight savings.
- United States Patent No. 5,266,130 Uchida et al issued November 30, 1993 describes a process for manufacturing an aluminum alloy sheet material having good shape fixability and bake hardenability by regulating the heat pattern in the step of cooling after the solution heat treatment.
- the sheet is first rapidly cooled to a quench temperature of 60 to 250°C and then further cooled at a rate based on the specific quench temperature.
- 6000 series aluminum alloys is complex. These alloys in the as-supplied condition contain a large number of fine clusters and zones uniformly distributed throughout the matrix. During a paint cure step, some fine unstable clusters and zones re-dissolve in the matrix, while others grow in size to improve strength during hardening. The exact mechanism explaining how the bendability and paint bake response are improved is not entirely understood. It is believed that the process of the present invention slows the formation of clusters and zones and produces mostly those that do not re-dissolve during the paint cure step. Therefore, a large number of fine clusters and zones become available for nucleation of the hardening particles and hence improve aging response.
- the alloys of the present invention are automotive aluminum alloys of AA6000 series containing (in percentages by weight) 0.50 - 0.75% Mg, 0.7 - 0.85% Si, 0.15 - 0.35% Mn, 0.1 - 0.3% Fe and the balance being aluminum and incidental impurities.
- the alloy also contains 0.2 - 0.4% Cu.
- the alloy is cast into ingots by semi-continuous casting, e.g. direct chill (DC) casting.
- the ingots are homogenized and hot rolled to reroll gauge, then cold rolled and solution heat treated.
- the heat treated sheet may be quenched to a desired initial pre-aging temperature.
- the sheet product thus obtained is subjected to the pre-aging procedure of this invention and this pre-aging can be either the final step of the solution heat treatment stage or it can be part of a separate reheating step.
- the sheet material starts with an initial pre-aging temperature which is at least 80°C and may be as high as 175°C or more.
- a preferred initial pre-aging temperature is in the range of 95 to 200°C, more preferably 95 to 185°C.
- the sheet material is rapidly cooled to ambient, e.g. 25°C, at a rate of more than 5°C/hour. This cooling rate is preferably in the range of 10 to 600°C/hour.
- the combination of excellent bendability and paint bake response is achieved by (a) the specific composition of the alloy and (b) the appropriate pre- aging procedure. This slows the natural aging, stabilizes yield strength at lower values and significantly improves the paint bake response in the sheet compared with conventionally produced counterparts.
- FIG. 1 shows the effect of cooling rate on yield strength (YS) for different pre-aging temperatures
- Figure 2 shows the effect of cooling rate on longitudinal bendability for different pre-aging temperatures
- Figure 3 shows the effect of cooling rate on transverse bendability for different pre-aging temperatures.
- the low T4P yield strength promotes improved formability, particularly hemming performance without cracking.
- the high T8 yield strength indicates a good paint bake response, i.e. after painting and baking the sheet has sufficient strength to resist dents and withstand other impacts.
- the target physical properties for the sheet products of this invention are as follows: T4P, YS 90 -120 MPa T4P, UTS >200 MPa
- the alloy used in this invention is cast by direct chill (DC) casting.
- the ingots are homogenized for more than 5 hours at a temperature of more than 550°C.
- the ingot is hot rolled to a reroll exit gauge of about 2.5 - 6mm at an exit temperature of about 300 - 380°C.
- the cold roll is to about 1mm gauge and the solution heat treatment is typically at a temperature of about 530 - 570°C.
- the reroll sheet is cold rolled to an intermediate gauge of about 2.0 - 3.0mm. This intermediate sheet is batch annealed at a temperature of about 345 - 410°C and then further cold rolled to about 1.0mm.
- Example 1 Alloys containing 0.6% Mg, 0.8% Si, 0.25% Fe and 0.20% Mn and with or without 0.25% Cu were cast as 95mm X 228mm ingots to carry out the experiments.
- the ingots were scalped, homogenized at 560°C for 6 hours, hot rolled to 3.5mm gauge, cold rolled to 2.1mm in one pass, batch annealed at 360°C for one hour and cold rolled to 0.93mm gauge. This sheet material was solution heat treated at 560°C for 5 minutes.
- the solution heat treated sheet material was pre-aged by cooling from different pre-aging temperatures, including 105°C, 125°C, 150°C and 175°C. Different cooling rates were used ranging from 1.25°C hour to 600°C/hour.
- YS yield strength
- UTS tensile strength
- El total elongation
- n strain hardening index
- Bendability r/t
- This r/t ratio was determined from triplicate specimens according to the ASTM E 290C standard wrap bend test method. The minimum r/t value was obtained by dividing with the sheet thickness, the minimum radius of the mandrel that produced a crack free bend.
- the radius of the mandrels used for the measurements were 0.025 mm, 0.057 mm, 0.076 mm, 0.102 mm, 0.152 mm, 0.203 mm, 0.254 mm, 0.305 mm, 0.406 mm, 0.508 mm, 0.610 mm, 0.711 mm, 0.813 mm, 1.02 mm, 1.22 mm, 1.42 mm and so on.
- T4P temper with natural aging of two and four weeks.
- P means that the sheet material has been pre-aged.
- T8 represents the YS after a simulated paint bake of 2% strain and 30 minutes at 177°C.
- Tables 1 and 2 show the mechanical properties for a sheet formed from an alloy containing 0.6% Mg, 0.8% Si, 0.25% Fe, 0.20% Mn and the balance Al and incidental impurities. From Table 1 (two weeks of natural aging) it can be seen that good combinations of low T4P yield strengths and high T8 yield strengths were obtained for a number of combinations of pre-aging temperatures between 105°C and 175°C and cooling rates between 20 and 600°C/hour.
- Figures 1, 2 and 3 show the effects of cooling rates from different start of cooling temperatures on the yield strength and bendability.
- Figure 1 shows that the use of slower cooling rates from high temperatures increases the yield strength in the T4P and T8 tempers due to artificial aging and affects bendability adversely. The best combination of properties is obtained with faster cooling rates from high start of cooling temperatures as seen in Table 1.
- Table 1 Mechanical Properties of Al-0.6% Mg-0.8% Si-0.25% Fe-0.20%
- Tables 3 and 4 summarize the average tensile properties of the 0.25% Cu containing alloy after two and four weeks of natural aging. The trends obtained from this alloy are very similar to the Cu free alloy. Generally, the artificial aging response of the alloy is better and this translates into a higher yield strength, especially in situations where cooling is carried out from high temperatures. In general, the paint bake response and bendability following cooling from 125°C at 20°C/hour are excellent after two weeks of natural aging, although there is a slight deterioration after four weeks of natural aging. Table 3. Mechanical Properties of Al-0.6% Mg-0.8% Si-0.3% Cu-0.25% Fe- 0.20%) Mn Alloy Pre-aged in Different Conditions and Naturally Aged for 2 Weeks
- the pre-aged sheet material obtained according to this invention can be coiled for future use. It is also possible to have the alloy sheet move directly from solution heat treatment to a cleaning bath where the rapid cooling pre- aging takes place.
Landscapes
- 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)
- Heat Treatment Of Sheet Steel (AREA)
- Continuous Casting (AREA)
Abstract
L'invention concerne un procédé de production d'une feuille en alliage d'aluminium dotée d'une excellente aptitude au pliage, ledit procédé étant utilisé dans la formation de panneaux pour automobiles. Cet alliage d'aluminium renferme entre 0,5 et 0,75 % en poids de Mg, entre 0,7 et 0,85 % en poids de Si, entre 0,15 et 0,35 % en poids de Mn, entre 0,1 et 0,3 % en poids de Fe, facultativement entre 0,2 et 0,4 % en poids de Cu, le reste d'Al et des impuretés diverses. On coule de manière semi-continue cet alliage en lingots. On soumet lesdits lingots à un laminage à chaud ou à froid, puis on les traite thermiquement dans une solution. On vieillit préalablement cette matière de feuille en la refroidissant rapidement d'une température initiale d'au moins 80 °C à température ambiante, avec un taux de refroidissement de plus de 5 °C par heure.
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US28838101P | 2001-05-03 | 2001-05-03 | |
US288381P | 2001-05-03 | ||
PCT/CA2002/000653 WO2002090608A1 (fr) | 2001-05-03 | 2002-05-02 | Procede de preparation d'une feuille en alliage d'aluminium a aptitude au pliage amelioree et feuille en alliage d'aluminium ainsi produite |
Publications (1)
Publication Number | Publication Date |
---|---|
EP1390553A1 true EP1390553A1 (fr) | 2004-02-25 |
Family
ID=23106859
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP02727087A Withdrawn EP1390553A1 (fr) | 2001-05-03 | 2002-05-02 | Procede de preparation d'une feuille en alliage d'aluminium a aptitude au pliage amelioree et feuille en alliage d'aluminium ainsi produite |
Country Status (8)
Country | Link |
---|---|
US (1) | US20030015261A1 (fr) |
EP (1) | EP1390553A1 (fr) |
JP (1) | JP2004527658A (fr) |
BR (1) | BR0209385A (fr) |
CA (1) | CA2445667A1 (fr) |
IS (1) | IS6998A (fr) |
NO (1) | NO20034888L (fr) |
WO (1) | WO2002090608A1 (fr) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN112626429A (zh) * | 2019-10-08 | 2021-04-09 | 有研工程技术研究院有限公司 | 一种提高6000系铝合金板材抗时效稳定性的方法 |
Families Citing this family (13)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US6780259B2 (en) * | 2001-05-03 | 2004-08-24 | Alcan International Limited | Process for making aluminum alloy sheet having excellent bendability |
DE10324452B4 (de) * | 2002-07-01 | 2010-05-06 | Aleris Aluminum Duffel Bvba | AI-Mg-Si-Legierungsblech |
DE10324453B4 (de) * | 2002-07-01 | 2008-06-26 | Corus Aluminium N.V. | Gewalztes wärmebehandelbares Al-Mg-Si-Legierungsprodukt |
US7491278B2 (en) * | 2004-10-05 | 2009-02-17 | Aleris Aluminum Koblenz Gmbh | Method of heat treating an aluminium alloy member and apparatus therefor |
JP5709298B2 (ja) * | 2010-08-12 | 2015-04-30 | 株式会社Uacj | 塗装焼付硬化性および成形性に優れたAl−Mg−Si系アルミニウム合金板の製造方法 |
FR3005664B1 (fr) * | 2013-05-17 | 2016-05-27 | Constellium France | Tole en alliage d'alliage pour bouteille metallique ou boitier d'aerosol |
WO2016069695A1 (fr) | 2014-10-28 | 2016-05-06 | Novelis Inc. | Produits en alliage d'aluminium et leur procédé de préparation |
RU2699496C2 (ru) | 2015-01-12 | 2019-09-05 | Новелис Инк. | Автомобильный алюминиевый лист высокой формуемости с уменьшенной или отсутствующей бороздчатостью поверхности и способ его получения |
KR102639005B1 (ko) * | 2015-05-29 | 2024-02-20 | 아르코닉 테크놀로지스 엘엘씨 | 새로운 6xxx 알루미늄 합금 및 이의 제조 방법 |
EP3314028B1 (fr) | 2015-06-24 | 2020-01-29 | Novelis Inc. | Dispositifs de chauffage à réponse rapide et systèmes de commande associés, utilisés conjointement avec des fours de traitement de métaux |
US10995397B2 (en) | 2016-12-16 | 2021-05-04 | Novelis Inc. | Aluminum alloys and methods of making the same |
ES2907839T3 (es) | 2016-12-16 | 2022-04-26 | Novelis Inc | Aleaciones de aluminio de alta resistencia y altamente conformables resistentes al endurecimiento natural por envejecimiento y procedimientos para fabricar las mismas |
CN108796404B (zh) * | 2018-06-11 | 2020-12-18 | 江苏大学 | 一种车身用原位纳米颗粒增强铝基复合材料的挤压工艺 |
Family Cites Families (11)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4082578A (en) * | 1976-08-05 | 1978-04-04 | Aluminum Company Of America | Aluminum structural members for vehicles |
US4808247A (en) * | 1986-02-21 | 1989-02-28 | Sky Aluminium Co., Ltd. | Production process for aluminum-alloy rolled sheet |
US4718948A (en) * | 1986-02-26 | 1988-01-12 | Sky Aluminium Co., Ltd. | Rolled aluminum alloy sheets for forming and method for making |
US4897124A (en) * | 1987-07-02 | 1990-01-30 | Sky Aluminium Co., Ltd. | Aluminum-alloy rolled sheet for forming and production method therefor |
JP2614686B2 (ja) * | 1992-06-30 | 1997-05-28 | 住友軽金属工業株式会社 | 形状凍結性及び塗装焼付硬化性に優れた成形加工用アルミニウム合金の製造方法 |
JPH06136478A (ja) * | 1992-10-23 | 1994-05-17 | Kobe Steel Ltd | 成形加工性に優れた焼付硬化型Al合金板及びその製造方法 |
US5616189A (en) * | 1993-07-28 | 1997-04-01 | Alcan International Limited | Aluminum alloys and process for making aluminum alloy sheet |
MX9701680A (es) * | 1994-09-06 | 1997-06-28 | Alcan Int Ltd | Proceso de tratamiento termico para lamina de aleacion de aluminio. |
BR9807431A (pt) * | 1997-02-19 | 2000-03-21 | Alcan Int Ltd | Processo para a produção de folhas de liga de alumìnio |
JPH11350058A (ja) * | 1998-06-12 | 1999-12-21 | Shinko Alcoa Yuso Kizai Kk | 成形性及び焼き付け硬化性に優れるアルミニウム合金板及びその製造方法 |
US6780259B2 (en) * | 2001-05-03 | 2004-08-24 | Alcan International Limited | Process for making aluminum alloy sheet having excellent bendability |
-
2002
- 2002-05-02 BR BR0209385-5A patent/BR0209385A/pt not_active IP Right Cessation
- 2002-05-02 JP JP2002587665A patent/JP2004527658A/ja active Pending
- 2002-05-02 EP EP02727087A patent/EP1390553A1/fr not_active Withdrawn
- 2002-05-02 CA CA002445667A patent/CA2445667A1/fr not_active Abandoned
- 2002-05-02 US US10/138,846 patent/US20030015261A1/en not_active Abandoned
- 2002-05-02 WO PCT/CA2002/000653 patent/WO2002090608A1/fr not_active Application Discontinuation
-
2003
- 2003-10-22 IS IS6998A patent/IS6998A/is unknown
- 2003-11-03 NO NO20034888A patent/NO20034888L/no not_active Application Discontinuation
Non-Patent Citations (1)
Title |
---|
See references of WO02090608A1 * |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN112626429A (zh) * | 2019-10-08 | 2021-04-09 | 有研工程技术研究院有限公司 | 一种提高6000系铝合金板材抗时效稳定性的方法 |
CN112626429B (zh) * | 2019-10-08 | 2022-10-21 | 有研工程技术研究院有限公司 | 一种提高6000系铝合金板材抗时效稳定性的方法 |
Also Published As
Publication number | Publication date |
---|---|
BR0209385A (pt) | 2004-07-06 |
NO20034888D0 (no) | 2003-11-03 |
JP2004527658A (ja) | 2004-09-09 |
US20030015261A1 (en) | 2003-01-23 |
NO20034888L (no) | 2004-01-02 |
WO2002090608A1 (fr) | 2002-11-14 |
IS6998A (is) | 2003-10-22 |
CA2445667A1 (fr) | 2002-11-14 |
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