US20050095167A1 - Hot-and cold-formed aluminum alloy - Google Patents
Hot-and cold-formed aluminum alloy Download PDFInfo
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- 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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- 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.
Abstract
Description
- 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.
- Another disadvantage of such alloys is that during forming and subsequent heat treatment, highly worked zones of forgings and semi-finished products recrystalize, forming coarse grains. A coarse-grained or brittle and less stable grain structure leads to premature failure of the Al component.
- This is especially true when multiple forming operations are required during forging, for example, to achieve high material yield. In the case of multiple forming operations, the highest degree of deformation usually occurs only at the end of the forming process, and thus at temperatures between 390° C. and 450° C. so that the grain structure recrystallizes during subsequent heat treatment. Even more problematic is the recrystallization behavior of cold-formed Al semi-finished products that are subsequently heat-treated. For example, to produce high-strength Al screws, cold-drawn wire or rods are used, which is/are then cold-formed into a screw blank by upsetting and pressing. During subsequent heat treatment, the grain structure is therefore highly susceptible to recrystallization. The same is true for cold-forged Al wheels.
- 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.
- It is an object of the present invention to provide a component and a method for manufacturing a component whose recrystallization-inhibiting activity is improved over the prior art and which lead to higher strength and corrosion resistance of the components.
- This object is achieved by a component or semi-finished product according to claim 1 and by a method according to claim 9.
- 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. - Advantageously, 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. - Moreover, the alloy may contain the elements
zinc less than 0.2 titanium less than 0.1. - Here, titanium is used for grain refinement, zinc may contribute to an increase in strength. In addition, the alloy contains unavoidable impurities that are attributable to the manufacturing process.
- In an advantageous embodiment, the alloy has a silicon content of between 0.9 and 1.7 percent by weight.
- It is a further feature of the present invention that 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.
- During homogenizing annealing, 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.
- Moreover, for solid solution hardening, i.e., the formation of an AlSi solid solution, it is expedient that there be an excess of silicon that is not bound in Mg2Si precipitates. Therefore, 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.
- It is a feature of the method that the cast raw material of the alloy is homogenized at temperatures between 420° C. and 540° C., preferably between 460° C. and 500° C. During this homogenization, 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.
- It has turned out to be advantageous to homogenize the raw material for at least 4 hrs, particular preference being given to a homogenization of 12 hrs.
- In the further process, 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. If necessary, 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.). During 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. Thus, recrystallization is effectively suppressed, resulting in higher strength levels and, above all, in a significantly higher elongation at break in highly worked areas.
- After the forming process, 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.
- If the composition meets the alloy specifications, 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.
- In the following, the present invention is explained in more detail with reference to two examples. The process procedure on which examples 1 and 2 are based is shown in
FIG. 1 . - An alloy melt having the composition in percent by weight:
silicon 1.2, magnesium 1.0, manganese 0.5, copper 0.05, iron 0.2, chromium 0.2, titanium 0.05, zinc 0.1, circonium 0.2,
is cast in ingots. The ingots are homogenized at a temperature of 480° C. for 12 hrs. In the next process step, the ingots are pressed into round rods (=semi-finished product) at a temperature of 500° C. The round rods are quenched and cut apart into workpieces having a length of about 20 cm. - The workpieces are heated to a temperature of 530° C. and formed into tension rods in several forging operations (=forming process). During forging, the workpiece temperature does not fall below 440° C. 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.
- Analogously to Example 1, cast ingots are homogenized and subsequently rolled into sheets (=semi-finished product) at a temperature of 500° C. Round workpieces are punched out from the sheets and formed into wheels in several steps.
Claims (15)
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 (en) | 2001-12-21 | 2001-12-21 | Hot and cold formable component made of an aluminum alloy and process for its production |
DE10163039.5 | 2001-12-21 | ||
PCT/EP2002/014452 WO2003054243A1 (en) | 2001-12-21 | 2002-12-18 | Hot- and cold-formed aluminium alloy |
Related Child Applications (1)
Application Number | Title | Priority Date | Filing Date |
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US11/974,466 Division US20080078480A1 (en) | 2001-12-21 | 2007-10-12 | Hot-and cold-formed aluminum alloy |
Publications (1)
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US20050095167A1 true US20050095167A1 (en) | 2005-05-05 |
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Family Applications (2)
Application Number | Title | Priority Date | Filing Date |
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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)
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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 (en) |
EP (1) | EP1458898B1 (en) |
AT (1) | ATE294252T1 (en) |
AU (1) | AU2002352255A1 (en) |
DE (2) | DE10163039C1 (en) |
ES (1) | ES2239261T3 (en) |
WO (1) | WO2003054243A1 (en) |
Cited By (6)
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 (en) | 2016-06-01 | 2020-03-11 | Aleris Aluminum Duffel BVBA | 6xxx-series aluminium alloy forging stock material and method of manufacting thereof |
US10646914B2 (en) | 2018-01-12 | 2020-05-12 | Accuride Corporation | Aluminum alloys for applications such as wheels and methods of manufacture |
WO2021064320A1 (en) | 2019-10-04 | 2021-04-08 | Constellium Issoire | Aluminum alloy precision plates |
Families Citing this family (8)
Publication number | Priority date | Publication date | Assignee | Title |
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DE102005060297A1 (en) * | 2005-11-14 | 2007-05-16 | Fuchs Kg Otto | Energieabsorbtionsbauteil |
JP4944525B2 (en) * | 2006-07-18 | 2012-06-06 | 株式会社神戸製鋼所 | Bolt manufacturing method, bolt, bolt profile, bolt molding apparatus, and bolt profile molding method |
DE102007032143A1 (en) * | 2007-07-09 | 2009-01-15 | Thyssenkrupp Drauz Nothelfer Gmbh | Motor vehicle door, has inner panel and reinforcement brackets integrally formed, and frame-shaped component comprising reinforcement regions, where frame shaped component is hot-formed from high-strength steel plate |
DE102009059804A1 (en) | 2009-12-21 | 2011-06-22 | Daimler AG, 70327 | Method for producing and increasing strength of a composite component, which is formed from a cast component made of an aluminum alloy, comprises connecting the cast component over a bolted connection |
JP5872443B2 (en) | 2012-03-30 | 2016-03-01 | 株式会社神戸製鋼所 | Aluminum alloy forgings for automobiles and manufacturing method thereof |
WO2014003074A1 (en) | 2012-06-27 | 2014-01-03 | 株式会社Uacj | Aluminum alloy sheet for blow molding and production method therefor |
SI24911A (en) | 2016-03-04 | 2016-07-29 | Impol 2000, d.d. | High-strength aluminum alloy Al-Mg-Si and procedure for its manufacture |
CN112522552B (en) * | 2020-11-04 | 2022-04-26 | 佛山科学技术学院 | Corrosion-resistant aluminum alloy and preparation method and application thereof |
Citations (7)
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)
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 (en) * | 1982-03-10 | 1983-09-17 | Sumitomo Light Metal Ind Ltd | Super high pressure plate fin type heat exchanger |
FR2617188B1 (en) * | 1987-06-23 | 1989-10-20 | Cegedur | AL-BASED ALLOY FOR CASING AND PROCESS FOR OBTAINING |
US5108519A (en) * | 1988-01-28 | 1992-04-28 | Aluminum Company Of America | Aluminum-lithium alloys suitable for forgings |
JPH03287738A (en) * | 1990-04-03 | 1991-12-18 | Kobe Steel Ltd | Fin material for heat exchanger assembled by vacuum brazing method and its manufacture |
DE4421744C2 (en) * | 1993-07-02 | 1996-05-23 | Fuchs Fa Otto | Use of a wrought alloy of the type AlMgSiCu for the production of high-strength and corrosion-resistant parts |
FR2744136B1 (en) * | 1996-01-25 | 1998-03-06 | Pechiney Rhenalu | THICK ALZNMGCU ALLOY PRODUCTS WITH IMPROVED PROPERTIES |
JPH11310841A (en) * | 1998-04-28 | 1999-11-09 | Nippon Steel Corp | Aluminum alloy extruded shape excellent in fatigue strength, and its production |
-
2001
- 2001-12-21 DE DE10163039A patent/DE10163039C1/en not_active Expired - Fee Related
-
2002
- 2002-12-18 DE DE50202955T patent/DE50202955D1/en not_active Expired - Lifetime
- 2002-12-18 WO PCT/EP2002/014452 patent/WO2003054243A1/en not_active Application Discontinuation
- 2002-12-18 ES ES02787956T patent/ES2239261T3/en not_active Expired - Lifetime
- 2002-12-18 EP EP02787956A patent/EP1458898B1/en not_active Expired - Lifetime
- 2002-12-18 US US10/499,755 patent/US20050095167A1/en not_active Abandoned
- 2002-12-18 AT AT02787956T patent/ATE294252T1/en not_active IP Right Cessation
- 2002-12-18 AU AU2002352255A patent/AU2002352255A1/en not_active Abandoned
-
2007
- 2007-10-12 US US11/974,466 patent/US20080078480A1/en not_active Abandoned
Patent Citations (7)
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)
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 (en) | 2016-06-01 | 2020-03-11 | Aleris Aluminum Duffel BVBA | 6xxx-series aluminium alloy forging stock material and method of manufacting thereof |
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 (en) | 2019-10-04 | 2021-04-08 | Constellium Issoire | Aluminum alloy precision plates |
CN114450425A (en) * | 2019-10-04 | 2022-05-06 | 伊苏瓦尔肯联铝业 | Aluminum alloy precision plate |
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DE50202955D1 (en) | 2005-06-02 |
DE10163039C1 (en) | 2003-07-24 |
AU2002352255A1 (en) | 2003-07-09 |
WO2003054243A1 (en) | 2003-07-03 |
ATE294252T1 (en) | 2005-05-15 |
US20080078480A1 (en) | 2008-04-03 |
ES2239261T3 (en) | 2005-09-16 |
EP1458898A1 (en) | 2004-09-22 |
EP1458898B1 (en) | 2005-04-27 |
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