EP1614760A1 - Aluminum alloy plate excellent in press formability and continuous resistance spot weldability and method for production thereof - Google Patents
Aluminum alloy plate excellent in press formability and continuous resistance spot weldability and method for production thereof Download PDFInfo
- Publication number
- EP1614760A1 EP1614760A1 EP04727133A EP04727133A EP1614760A1 EP 1614760 A1 EP1614760 A1 EP 1614760A1 EP 04727133 A EP04727133 A EP 04727133A EP 04727133 A EP04727133 A EP 04727133A EP 1614760 A1 EP1614760 A1 EP 1614760A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- less
- aluminum alloy
- alloy plate
- resistance spot
- formability
- 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- Withdrawn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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
- B22D11/003—Aluminium alloys
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
- B22D11/0605—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by two belts, e.g. Hazelett-process
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/12—Accessories for subsequent treating or working cast stock in situ
- B22D11/124—Accessories for subsequent treating or working cast stock in situ for cooling
-
- 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
-
- 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
- C22F1/043—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 aluminum alloy plate with excellent press-formability and continuous resistance spot weldability which is useful as a structural material for forming the outer panels of products such as household appliances or automobiles that are assembled by resistance spot welding before or after press molding.
- the structural materials and the outer panels of products of household appliances and automobiles are pressed firstly forming, then resistance spot welded to assemble the products.
- Al-Mg-Si type alloy plates show a relatively attractive surface appearance after press forming, and are therefore used in various types of outer panels and structural materials, but require good press-formability due to the diversity of product shapes.
- Japanese Patent Application, First Publication No. S62-207851 describes a method for manufacturing a rolled plate such as a body plate with good formability, comprising steps of preparing an aluminum alloy melt containing 0.4-2.5% of Si, 0.1-1.2% of Mg, one or more types chosen from among 1.5% or less of Cu, 2.5% or less of Zn, 0.3% or less of Cr, 0.6% or less of Mn and 0.3% or less of Zr, with the remainder consisting of Al and unavoidable impurities; continuously casting the melt into 3-15 mm thick slabs; performing cold rolling; and then performing a solution heat treatment and quenching.
- Japanese Patent Application, First Publication No. 2001-262264 describes Al-Mg-Si type aluminum alloy plates used for automobile panels with good bendability.
- the publication discloses an Al-Mg-Si type aluminum alloy plate with excellent toughness and bendability, basically comprising 0.1-2.0% of Mg, 0.1-2.0% of Si and 0.1-1.5% of Fe in % by mass, with the remainder consisting of Al, wherein the maximum size of Fe and Si containing compounds is 5 ⁇ m or less, and the average grain size is 30 ⁇ m or less.
- an Al-Mg-Si type aluminum alloy plate with excellent toughness and bendability basically comprising 0.1-2.0% of Mg, 0.1-2.0% of Si, 0.1-1.5% of Fe and 2.0% or less of Fe in % by mass, with the remainder consisting of Al, wherein the maximum size of Fe, Si and Cu containing compounds is 5 ⁇ m or less, and the average crystal grain size is 30 ⁇ m or less. Furthermore, it discloses an Al-Mg-Si type aluminum alloy plate with excellent toughness and bendability such as those described above, further comprising at least one element chosen from the group consisting of 1.0% or less of Mn, 0.3% or less of Cr, 0.3% or less of Zr, 0.3% or less of V and 0.03% or less of Ti.
- the technique described in Japanese Patent Application, First Publication No. S62-207851 uses a twin-roller casting process with casting at a cooling rate of at least 100 °C/sec, so that the size of intermetallic compounds that crystallize during casting is small, as a result of which the number of relatively large compounds that affect the grain size at recrsytallization is not sufficient, so that the grain size after solution heat treatment is large, thus degrading the press-formability, and the number of continuous resistance spot welds is reduced.
- the technique disclosed in Japanese Patent Application, First Publication No. 2001-262264 uses a continuous casting process, with casting at a cooling rate of at least 10 °C/sec, but in the examples, a maximum cooling rate of 30 °C/sec is used. Due to the slow cooling rate, the size of intermetallic compounds that crystallize during casting is large, as a result of which the number of relatively large compounds that affect the grain size at recrsytallization is not sufficient, so that the grain size after solution heat treatment is large, thus degrading the press-formability and reducing the number of continuous resistance spot welds.
- the purpose of the present invention is to offer an aluminum alloy plate with excellent press-formability and continuous resistance spot weldability, and a manufacturing process thereof.
- the present inventors achieved the present invention on the basis of the discovery that by selecting the optimum range for the cooling rate when casting a melt within an appropriate composition range, it is possible to optimize the size and number of intermetallic compounds that crystallize, so as to obtain excellent press-formability and continuous resistance spot weldability in an aluminum alloy plate after a solution heat treatment.
- the present invention offers an aluminum alloy plate with excellent press-forinability and continuous resistance spot weldability comprising, in % by mass, 0.3-1.0% of Mg, 0.3-1.2% of Si, 0.10-1.0% of Fe and 0.05-0.5% of Mn; where Fe + Mn > 0.2%; the remainder consisting of Al and unavoidable impurities; wherein an average value of recrystallized grain size is 25 ⁇ m or less; and there are at least 5000 particles/mm 2 of intermetallic compounds with a circle-equivalent diameter of 1-6 ⁇ m.
- the present invention excels in press-formability and continuous resistance spot weldability due to the fineness of the recrsytallization grain size and the large number of compounds of optimum size.
- the strength can be further improved by making the above composition contain Cu in an amount of 0.5-1.0%.
- the recrystallization grain size can be made finer and the strength further improved by making the above composition contain Zr in an amount of 0.1-0.4%.
- Casting cracks can be reliably prevented from occurring during casting by making the above composition contain Ti in an amount of 0.05% or less, or Ti in an amount of 0.05% or less and B in an amount of 0.01% or less.
- a second aspect of the present invention is a method of manufacturing an aluminum alloy plate with excellent press-formability and continuous resistance spot weldability, comprising steps of pouring a melt consisting of the above-claimed composition into an opposing rotating belt cast that is forcibly cooled; casting the melt at a cooling rate of 40-90 °C/sec to form a 5-10 mm thick slab; drawing said slab from the side opposite the side where the melt was poured; rolling directly or after winding into a coil; and subjecting to a solution heat treatment.
- a large number of compounds of optimum size can be crystallized by casting the alloy melt at an optimal cooling rate when casting, thereby refining the recrystallization grain size to result in aluminum alloy plates with excellent press-formability, and continuous spot weldability is good.
- Mg and Si are added to improve the strength and to provide press-formability.
- concentration is less than the indicated lower limit, the effects are inadequate, and when more than the indicated upper limit, the press -formability deteriorates.
- Cu is added to further improve the strength and press-formability.
- concentration is less than the lower limit, its effect is small, and when the quantity exceeds the upper limit, the corrosion resistance is degraded.
- Zr promotes the crystallization of the intermetallic compound Al 3 Zr, further induces crystallization of many compounds of specific size to increase the number of recrystallized nuclei, and thereby make the size of the recrsytallized grains smaller, so as to improve press-formability The effect is lost when the concentration is less than the lower limit, and when the quantity exceeds the upper limit, large compounds are formed so that the rollability is reduced.
- Rapid cooling during casting of the melt can cause casting cracks to occur, and the addition of Ti or Ti and B can prevent such cracks. It is possible to add either Ti alone at a quantity of 0.05% or less, or to also add 0.01% or less of B to obtain a composite with Ti, in which case there is a synergistic effect. The effect is most apparent when the lower limit of the Ti is at least 0.002%, and the lower limit of B is at least 0.0005%.
- the unavoidable impurities can come from the base aluminum, scrap and ingot jigs or the like, some of the typical elements including Cr, Ni, Zn, Ga and V. Since Cr is added to prevent stress corrosion of the Al-Mg alloy, it can easily be introduced from scrap, but is allowable in the present invention if less than 0.3%.
- the quantity of Ni should be held to less than 0.2%, that of Ga and V respectively less than 0.1%, and that of any other unavoidable impurities to less than 0.3% in order to maintain the formability.
- the recrystallization grain size should preferably be 20 ⁇ m or less, and 15 ⁇ m or less.
- Intermetallic compounds having a circle equivalent diameter of 1-6 ⁇ m are of a size promoting the accumulation the integration of dislocations during cold rolling and having an effect of refining the recrystallized grains, so that if the size and number is less than the lower limit, the dislocation accumulation rate is low, and if the number is less than 5000 particles/mm 2 , fine recrystallized grains of a preferable size cannot be obtained. Additionally, if the size exceeds the upper limit, the large compounds can cause streaks or cracks during rolling and thereby lower the rollability.
- the quantity of the compounds is more preferably at least 6000 particles/mm 2
- the melt is prepared by adjusting the composition, degassing, settling, making fine adjustments of the composition as needed, adding Ti or Ti and B as a mother alloy and casting.
- the melt is poured into forcibly cooled rotating belters facing each other, with the cooling rate 40-90 °C/sec, to form a 5-10 mm thick slab, then drawing the slab from the opposite side to where the melt was poured, to roll it directly or after winding into a coil.
- Continuous casting processes include a twin -roller casting process of pouring the melt between forcibly cooled rotating rollers that are facing each other, rapidly cooling the melt on the roller surfaces, and continuously withdrawing thin slabs from the opposite side, and a twin-belt casting process of pouring the melt between forcibly cooled rotating belts that are facing each other, rapidly cooling the melt on the belt surfaces, and continuously withdrawing thin slabs from the opposite side.
- the twin-roller casting process has a cooling rate during casting of at least 300 °C/sec which is considerably high, while the size of compounds in the resulting slab are small and the plates of the present invention are not obtained.
- the twin-belt casting process involves rapidly cooling the melt on the belt surface, but the cooling rate is not as high as with the twin-roller casting process.
- the casting conditions of the twin-belt casting process are adjusted so as to make the melt cooling rate 40-90 °C/sec (at a position of 1/4 thickness of the slab), so as to form more than 5000 particles/mm 2 of intermetallic compounds with a circle-equivalent diameter of 1-6 ⁇ m in the final plates. If the melt cooling rate is less than 40 °C/sec, larger compounds are crystallized, causing a deficiency of compounds in the above-defined size range, so that the recrystallized grains are not refined and plates with excellent press-formability cannot be obtained. Additionally, at more than 90 °C/sec, fine compounds are crystallized, causing a reduction of compounds in the above-defined size range, so that a plate with refined recrsytallized grains cannot be obtained.
- a slab obtained by a twin-belt casting process is cold-rolled to form a plate of a desired thickness, which undergoes a solution heat treatment and is recrsytallized. At this time, it is possible to provide an anneal during the cold rolling step, but the rolled plate provided for the solution heat treatment has at least a cold reduction of 55%.
- the solution heat treatment is performed in a continuous annealing furnace. The heating temperature is at least 500 °C, the cooling rate to 100 °C is set to at least 1 °C/sec.
- the recrystallized grains of the rolled plates that have undergone the solution heat treatment have an average grain size of 25 ⁇ m or less due to the size and number of the intermetallic compound and the reduction. Such plates can be used either as they are, or after passing through a skin pass or leveler of about 1-5% in order to obtain flatness.
- Example 13 7521 9 131 251 23 13.6 A Comp.
- Example 14 3924 26 112 215 26 13.5 C Comp.
- Example 15 36721 6 133 241 21 13.5 A Comp.
- Example 16 7820 11 134 248 20 13.7 A Comp.
- Example 17 7541 9 160 288 22 13.8 A Comp.
- Example 18 8783 7 142 235 21 13.9 A Comp.
- Example 19 2215 29 109 215 20 12.5 C
- Example (Note) A: at least 500 consecutive hits B: at least 200 less than 500 consecutive hits C: less than 200 consecutive hits Underlined values are outside the range of the present invention. Recrystallized grain size was measured by liner intercept method.
- the aluminum alloy plates according to the present invention excel in press-formability and continuous resistance spot weldability, and surface appearance after press is good, enabling continuous assembly by resistance spot welding, therefore productivity is high.
- This 6000 type alloy plate also has higher strength improves in a baking step after coating or the like, so as to have excellent industrial value in a wide range of applications such as in the body panels of automobiles.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Continuous Casting (AREA)
Abstract
Description
- The present invention relates to an aluminum alloy plate with excellent press-formability and continuous resistance spot weldability which is useful as a structural material for forming the outer panels of products such as household appliances or automobiles that are assembled by resistance spot welding before or after press molding.
- The structural materials and the outer panels of products of household appliances and automobiles are pressed firstly forming, then resistance spot welded to assemble the products.
- Al-Mg-Si type alloy plates (JIS 6000) show a relatively attractive surface appearance after press forming, and are therefore used in various types of outer panels and structural materials, but require good press-formability due to the diversity of product shapes.
- Additionally, there is a demand for increases in the number of consecutive welds capable of being performed by resistance spot welding in order to reduce the times the electrodes are replaced during resistance spot welding work.
- Japanese Patent Application, First Publication No. S62-207851 describes a method for manufacturing a rolled plate such as a body plate with good formability, comprising steps of preparing an aluminum alloy melt containing 0.4-2.5% of Si, 0.1-1.2% of Mg, one or more types chosen from among 1.5% or less of Cu, 2.5% or less of Zn, 0.3% or less of Cr, 0.6% or less of Mn and 0.3% or less of Zr, with the remainder consisting of Al and unavoidable impurities; continuously casting the melt into 3-15 mm thick slabs; performing cold rolling; and then performing a solution heat treatment and quenching.
- Additionally, Japanese Patent Application, First Publication No. 2001-262264 describes Al-Mg-Si type aluminum alloy plates used for automobile panels with good bendability. For example, the publication discloses an Al-Mg-Si type aluminum alloy plate with excellent toughness and bendability, basically comprising 0.1-2.0% of Mg, 0.1-2.0% of Si and 0.1-1.5% of Fe in % by mass, with the remainder consisting of Al, wherein the maximum size of Fe and Si containing compounds is 5 µm or less, and the average grain size is 30 µm or less. Additionally, it discloses an Al-Mg-Si type aluminum alloy plate with excellent toughness and bendability, basically comprising 0.1-2.0% of Mg, 0.1-2.0% of Si, 0.1-1.5% of Fe and 2.0% or less of Fe in % by mass, with the remainder consisting of Al, wherein the maximum size of Fe, Si and Cu containing compounds is 5 µm or less, and the average crystal grain size is 30 µm or less. Furthermore, it discloses an Al-Mg-Si type aluminum alloy plate with excellent toughness and bendability such as those described above, further comprising at least one element chosen from the group consisting of 1.0% or less of Mn, 0.3% or less of Cr, 0.3% or less of Zr, 0.3% or less of V and 0.03% or less of Ti.
- The technique described in Japanese Patent Application, First Publication No. S62-207851 uses a twin-roller casting process with casting at a cooling rate of at least 100 °C/sec, so that the size of intermetallic compounds that crystallize during casting is small, as a result of which the number of relatively large compounds that affect the grain size at recrsytallization is not sufficient, so that the grain size after solution heat treatment is large, thus degrading the press-formability, and the number of continuous resistance spot welds is reduced.
- The technique disclosed in Japanese Patent Application, First Publication No. 2001-262264 uses a continuous casting process, with casting at a cooling rate of at least 10 °C/sec, but in the examples, a maximum cooling rate of 30 °C/sec is used. Due to the slow cooling rate, the size of intermetallic compounds that crystallize during casting is large, as a result of which the number of relatively large compounds that affect the grain size at recrsytallization is not sufficient, so that the grain size after solution heat treatment is large, thus degrading the press-formability and reducing the number of continuous resistance spot welds.
- The purpose of the present invention is to offer an aluminum alloy plate with excellent press-formability and continuous resistance spot weldability, and a manufacturing process thereof.
- The present inventors achieved the present invention on the basis of the discovery that by selecting the optimum range for the cooling rate when casting a melt within an appropriate composition range, it is possible to optimize the size and number of intermetallic compounds that crystallize, so as to obtain excellent press-formability and continuous resistance spot weldability in an aluminum alloy plate after a solution heat treatment.
- That is, the present invention offers an aluminum alloy plate with excellent press-forinability and continuous resistance spot weldability comprising, in % by mass, 0.3-1.0% of Mg, 0.3-1.2% of Si, 0.10-1.0% of Fe and 0.05-0.5% of Mn; where Fe + Mn > 0.2%; the remainder consisting of Al and unavoidable impurities; wherein an average value of recrystallized grain size is 25 µm or less; and there are at least 5000 particles/mm2 of intermetallic compounds with a circle-equivalent diameter of 1-6 µm.
- The present invention excels in press-formability and continuous resistance spot weldability due to the fineness of the recrsytallization grain size and the large number of compounds of optimum size.
- The strength can be further improved by making the above composition contain Cu in an amount of 0.5-1.0%.
- The recrystallization grain size can be made finer and the strength further improved by making the above composition contain Zr in an amount of 0.1-0.4%.
- Casting cracks can be reliably prevented from occurring during casting by making the above composition contain Ti in an amount of 0.05% or less, or Ti in an amount of 0.05% or less and B in an amount of 0.01% or less.
- A second aspect of the present invention is a method of manufacturing an aluminum alloy plate with excellent press-formability and continuous resistance spot weldability, comprising steps of pouring a melt consisting of the above-claimed composition into an opposing rotating belt cast that is forcibly cooled; casting the melt at a cooling rate of 40-90 °C/sec to form a 5-10 mm thick slab; drawing said slab from the side opposite the side where the melt was poured; rolling directly or after winding into a coil; and subjecting to a solution heat treatment.
- A large number of compounds of optimum size can be crystallized by casting the alloy melt at an optimal cooling rate when casting, thereby refining the recrystallization grain size to result in aluminum alloy plates with excellent press-formability, and continuous spot weldability is good.
- Herebelow, the preferable amounts of the respective components contained in the aluminum alloy plates of the present invention shall be described, followed by the reasons for the upper and lower limits. In this specification, all quantities expressed in % refer to percentage by mass except where indicated otherwise.
[Mg: 0.3-1.0%]
[Si: 0.3-1.2%] - Mg and Si are added to improve the strength and to provide press-formability. When the concentration is less than the indicated lower limit, the effects are inadequate, and when more than the indicated upper limit, the press -formability deteriorates.
[Fe: 0.10-1.0%]
[Mn: 0.05-0.5%]
[Fe + Mn ≥ 0.2%] - By adding Fe and Mn together and keeping Fe + Mn ≥ 0.2%, it is possible to crystallize a large quantity of compounds of a specific size, increase the amount recrystallized, and the size of the recrystallized grains becames small. Both elements have little effect when their concentration are less than the respective lower limits, and when their concentrations exceed the upper limits, cause bulky crystals to occur, so that surface blemishes such as streaks can appear during cold rolling and the press-formability also deteriorates. Mn does not crystallize into an intermetallic compound of desirable size and number unless it coexists with Fe. The total quantity of Fe and Mn is more preferably such that Fe + Mn ≥0.3%.
[Cu: 0.5-1.0%] - Cu is added to further improve the strength and press-formability. When the concentration is less than the lower limit, its effect is small, and when the quantity exceeds the upper limit, the corrosion resistance is degraded.
[Zr: 0.1-0.4%] - Zr promotes the crystallization of the intermetallic compound Al3Zr, further induces crystallization of many compounds of specific size to increase the number of recrystallized nuclei, and thereby make the size of the recrsytallized grains smaller, so as to improve press-formability The effect is lost when the concentration is less than the lower limit, and when the quantity exceeds the upper limit, large compounds are formed so that the rollability is reduced.
[Ti: 0.05% or less; or Ti: 0.05% or less and B: 0.01% or less] - Rapid cooling during casting of the melt can cause casting cracks to occur, and the addition of Ti or Ti and B can prevent such cracks. It is possible to add either Ti alone at a quantity of 0.05% or less, or to also add 0.01% or less of B to obtain a composite with Ti, in which case there is a synergistic effect. The effect is most apparent when the lower limit of the Ti is at least 0.002%, and the lower limit of B is at least 0.0005%.
- The unavoidable impurities can come from the base aluminum, scrap and ingot jigs or the like, some of the typical elements including Cr, Ni, Zn, Ga and V. Since Cr is added to prevent stress corrosion of the Al-Mg alloy, it can easily be introduced from scrap, but is allowable in the present invention if less than 0.3%. The quantity of Ni should be held to less than 0.2%, that of Ga and V respectively less than 0.1%, and that of any other unavoidable impurities to less than 0.3% in order to maintain the formability.
- If the recrystallized grains of plates after the solution heat treatment are small, then they can be formed without damage even if the press draft is set high and the drawing height is set high. If the grains size exceeds the upper limit, the effect is lost, and the surface appearance after pressing is not good. The recrystallization grain size should preferably be 20 µm or less, and 15 µm or less.
- Intermetallic compounds having a circle equivalent diameter of 1-6 µm are of a size promoting the accumulation the integration of dislocations during cold rolling and having an effect of refining the recrystallized grains, so that if the size and number is less than the lower limit, the dislocation accumulation rate is low, and if the number is less than 5000 particles/mm2, fine recrystallized grains of a preferable size cannot be obtained. Additionally, if the size exceeds the upper limit, the large compounds can cause streaks or cracks during rolling and thereby lower the rollability. Additionally, with the state of the compounds as described above, a erosion effect occurring due to a reaction between the copper electrodes and the Al when performing continuous resistance spot welding can be prevented, thus reducing the number of times the electrode needs to be replaced and improving the productivity. The quantity of the compounds is more preferably at least 6000 particles/mm2
- Next, a preferable process for manufacturing the aluminum alloy plates of the present invention shall be described.
- The melt is prepared by adjusting the composition, degassing, settling, making fine adjustments of the composition as needed, adding Ti or Ti and B as a mother alloy and casting. When casting, the melt is poured into forcibly cooled rotating belters facing each other, with the cooling rate 40-90 °C/sec, to form a 5-10 mm thick slab, then drawing the slab from the opposite side to where the melt was poured, to roll it directly or after winding into a coil.
- Continuous casting processes include a twin -roller casting process of pouring the melt between forcibly cooled rotating rollers that are facing each other, rapidly cooling the melt on the roller surfaces, and continuously withdrawing thin slabs from the opposite side, and a twin-belt casting process of pouring the melt between forcibly cooled rotating belts that are facing each other, rapidly cooling the melt on the belt surfaces, and continuously withdrawing thin slabs from the opposite side.
- The twin-roller casting process has a cooling rate during casting of at least 300 °C/sec which is considerably high, while the size of compounds in the resulting slab are small and the plates of the present invention are not obtained. On the other hand, the twin-belt casting process involves rapidly cooling the melt on the belt surface, but the cooling rate is not as high as with the twin-roller casting process.
- In the present invention, the casting conditions of the twin-belt casting process are adjusted so as to make the melt cooling rate 40-90 °C/sec (at a position of 1/4 thickness of the slab), so as to form more than 5000 particles/mm2 of intermetallic compounds with a circle-equivalent diameter of 1-6 µm in the final plates. If the melt cooling rate is less than 40 °C/sec, larger compounds are crystallized, causing a deficiency of compounds in the above-defined size range, so that the recrystallized grains are not refined and plates with excellent press-formability cannot be obtained. Additionally, at more than 90 °C/sec, fine compounds are crystallized, causing a reduction of compounds in the above-defined size range, so that a plate with refined recrsytallized grains cannot be obtained.
- A slab obtained by a twin-belt casting process is cold-rolled to form a plate of a desired thickness, which undergoes a solution heat treatment and is recrsytallized. At this time, it is possible to provide an anneal during the cold rolling step, but the rolled plate provided for the solution heat treatment has at least a cold reduction of 55%. The solution heat treatment is performed in a continuous annealing furnace. The heating temperature is at least 500 °C, the cooling rate to 100 °C is set to at least 1 °C/sec. The recrystallized grains of the rolled plates that have undergone the solution heat treatment have an average grain size of 25 µm or less due to the size and number of the intermetallic compound and the reduction. Such plates can be used either as they are, or after passing through a skin pass or leveler of about 1-5% in order to obtain flatness.
- An aluminum alloy melt with the composition shown in Table 1 was degassed, settled, then the melt was cast into a 7 mm thick slab at cooling rates of 50 °C/sec and 75 °C/sec in a twin-belt continuous casting process. The slab drawing speed was 8 m/min. This slab was cold-rolled, and subjected to an intermediate annealing treatment as needed to form a 1 mm thick plate. Next, this plate was subjected to a solution heat treatment, and after the treatment, the size and number of intermetallic compounds, recrsytallization grain size, 0.2% yield strength (YS), ultimate tensile strength (UTS), elongation (EL), deep drawing height and resistance spot weldability were measured. The results are shown in Table 3.
- The deep drawing conditions and evaluation conditions for the resistance spot weldability were as shown below.
-
Mold Used Punch diameter 50 mm shoulder R 5 mm Dies inner diameter 52.5 mm shoulder R 8 mm Blank diameter 112.5 mm -
Single Phase Rectifier Type Spot Welding Machine Electrode Cu - 1% Cr Alloy Pressure 400 kgf
Consecutive welding spots: Number of welding consecutively with strength exceeding grade A average standard when continuous spot welding using the welding current values determined above and with the above welding conditions. - A: at least 500 consecutive hits
- B: at least 200 less than 500 consecutive hits
- C: less than 200 consecutive hits
- Underlined values are outside the range of the present invention.
TABLE 2 Manufacturing Process No. Alloy No. Cast Methods/ Slab Thickness (mm) Cooling Rate (°C/sec) Hot Roll (mm) Cold Roll (mm) Interm. Anneal Temp (°C)/ hour (h) Cold Roll (mm) Soln. Heat Tr. Temp. (°C) Comm. 1 A twin belt/7 50 - - - 1 550 °C Pres Inv 2 B twin belt/7 50 - - - 1 550 °C Pres Inv 3 C twin belt/7 50 - - - 1 550 °C Pres Inv 4 D twin belt/7 50 - - - 1 550 °C Pres Inv 5 E twin belt/7 50 - - - 1 550 °C Pres Inv 6 F twin belt/7 50 - - - 1 550 °C Pres Inv 7 G twin belt/7 50 - - - 1 550 °C Pres Inv 8 H twin belt/7 50 - - - 1 550 °C Pres Inv 9 I twin belt/7 50 - - - 1 550 °C Pres Inv 10 C twin belt/7 50 - 2.5 360/2 1 550 °C Pres Inv 11 B twin belt/7 75 - - - 1 550 °C Pres Inv 12 J twin belt/7 50 - - - 1 550 °C Comp Ex 13 K twin belt/7 50 - - - 1 550 °C Comp Ex 14 L twin belt/7 50 - - - 1 550 °C Comp Ex 15 M twin belt/7 50 - - - 1 550 °C Comp Ex 16 N twin belt/7 50 - - - 1 550 °C Comp Ex 17 O twin belt/7 50 - - - 1 550 °C Comp Ex 18 P twin belt/7 50 - - - 1 550 °C Comp Ex 19 B twin belt/20 20 3 - - 1 550 °C Comp Ex 20 B twin belt/3 150 - - - 1 550 °C Comp Ex (Note) Underlined values are outside the range of the present invention. TABLE 3 Microstractures and Properties No. Density of Intermetallic Compound (/mm2) Grain Size (µm) Tensile Properties Deeping Drawing Height(mm) Resistance Spot Weldability Comments 0/2%YS (MPa) UTS (MPa) EL (%) 1 5917 12 130 238 28 14.5 B Present Invention 2 6812 11 118 222 29 14.1 A Present Invention 3 7185 10 124 228 28 14.3 A Present Invention 4 7726 9 132 239 30 14.7 A Present Invention 5 11254 7 145 249 27 14.2 A Present Invention 6 6917 11 128 235 29 14.8 A Present Invention 7 7435 10 135 264 29 14.9 A Present Invention 8 7982 8 126 230 29 14.8 A Present Invention 9 8013 8 137 266 30 14.9 A Present Invention 10 6725 15 114 219 27 14.0 A Present Invention 11 7820 9 122 230 30 15.1 A Present Invention 12 7543 11 140 252 24 13.5 A Comp. Example 13 7521 9 131 251 23 13.6 A Comp. Example 14 3924 26 112 215 26 13.5 C Comp. Example 15 36721 6 133 241 21 13.5 A Comp. Example 16 7820 11 134 248 20 13.7 A Comp. Example 17 7541 9 160 288 22 13.8 A Comp. Example 18 8783 7 142 235 21 13.9 A Comp. Example 19 2215 29 109 215 20 12.5 C Comp. Example 20 3272 26 113 218 22 12.8 C Comp. Example (Note) A: at least 500 consecutive hits B: at least 200 less than 500 consecutive hits C: less than 200 consecutive hits Underlined values are outside the range of the present invention. Recrystallized grain size was measured by liner intercept method. - As described above, the aluminum alloy plates according to the present invention excel in press-formability and continuous resistance spot weldability, and surface appearance after press is good, enabling continuous assembly by resistance spot welding, therefore productivity is high. This 6000 type alloy plate also has higher strength improves in a baking step after coating or the like, so as to have excellent industrial value in a wide range of applications such as in the body panels of automobiles.
Alloy No. | Mg | Si | Fe | Mn | Cu | Zr | Ti | B | Comments |
A | 0.6 | 0.8 | 0.12 | 0.1 | - | - | 0.02 | Present Invention | |
B | 0.4 | 0.8 | 0.2 | 0.2 | - | - | 0.02 | Present Invention | |
C | 0.5 | 0.7 | 0.2 | 0.2 | - | - | 0.02 | Present Invention | |
D | 0.5 | 0.8 | 0.2 | 0.2 | - | - | 0.01 | Present Invention | |
E | 0.6 | 0.8 | 0.7 | 0.1 | - | - | 0.02 | Present Invention | |
F | 0.5 | 0.9 | 0.15 | 0.3 | - | - | 0.02 | Present Invention | |
G | 0.5 | 0.7 | 0.2 | 0.2 | 0.6 | - | 0.02 | Present Invention | |
H | 0.5 | 0.7 | 0.2 | 0.2 | - | 0.15 | 0.02 | Present Invention | |
I | 0.5 | 0.7 | 0.2 | 0.2 | 0.7 | 0.12 | 0.02 | Present Invention | |
J | 1.2 | 0.7 | 0.2 | 0.2 | - | - | 0.02 | Comparative Example | |
K | 0.5 | 1.4 | 0.2 | 0.2 | - | - | 0.02 | Comparative Example | |
L | 0.5 | 0.7 | 0.05 | 0.2 | - | - | 0.02 | Comparative Example | |
M | 0.5 | 0.7 | 1.5 | 0.2 | - | - | 0.02 | Comparative Example | |
N | 0.5 | 0.7 | 0.2 | 0.7 | - | - | 0.02 | Comparative Example | |
O | 0.5 | 0.7 | 0.2 | 0.2 | 1.2 | - | 0.02 | Comparative Example | |
P | 0.5 | 0.7 | 0.2 | 0.2 | - | 0.5 | 0.02 | Comparative Example |
(Note) Remainder: Al and impurities. |
Claims (5)
- An aluminum alloy plate with excellent press-formability and continuous resistance spot weldability comprising, in % by mass, 0.3-1.0% of Mg, 0.3-1.2% of Si, 0.10-1.0% of Fe and 0.05-0.5% of Mn; where Fe + Mn ≥ 0.2%; the remainder consisting of A1 and unavoidable impurities; wherein an average value of recrystallized grain size is 25 µm or less; and there are at least 5000 particles/mm2 of intermetallic compounds with a circle-equivalent diameter of 1-6 µm.
- An aluminum alloy plate with excellent press-formability and continuous resistance spot weldability in accordance with claim 1, further comprising 0.5-1.0% of Cu.
- An aluminum alloy plate with excellent press-formability and continuous resistance spot weldability in accordance with claim 1 or 2, further comprising 0.1-0.4% of Zr.
- An aluminum alloy plate with excellent press-formability and continuous resistance spot weldability in accordance with any one of claims 1-3, further comprising 0.05'% or less of Ti, or 0.05% or less of Ti and 0.01% or less of B.
- A method of manufacturing an aluminum alloy plate with excellent press-formability and continuous resistance spot weldability in accordance with any one of claims 1-4, comprising steps of pouring a melt consisting of the above-claimed composition into an opposing rotating belt caster that is forcibly cooled; casting the melt at a cooling rate of 40-90 °C/sec to form a 5-10 mm thick slab; drawing said slab from the side opposite the side where the melt was poured; rolling directly or after winding into a coil; and subjecting to a solution heat treatment.
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2003110732 | 2003-04-15 | ||
JP2004048360A JP4379149B2 (en) | 2003-04-15 | 2004-02-24 | Aluminum alloy plate excellent in press formability and continuous resistance spot weldability and method for producing the same |
PCT/JP2004/005258 WO2004092432A1 (en) | 2003-04-15 | 2004-04-13 | Aluminum alloy plate excellent in press formability and continuous resistance spot weldability and method for production thereof |
Publications (2)
Publication Number | Publication Date |
---|---|
EP1614760A1 true EP1614760A1 (en) | 2006-01-11 |
EP1614760A4 EP1614760A4 (en) | 2006-10-18 |
Family
ID=33302213
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP04727133A Withdrawn EP1614760A4 (en) | 2003-04-15 | 2004-04-13 | Aluminum alloy plate excellent in press formability and continuous resistance spot weldability and method for production thereof |
Country Status (7)
Country | Link |
---|---|
US (1) | US20070062618A1 (en) |
EP (1) | EP1614760A4 (en) |
JP (1) | JP4379149B2 (en) |
KR (1) | KR100710795B1 (en) |
CA (1) | CA2521006A1 (en) |
TW (1) | TW200504226A (en) |
WO (1) | WO2004092432A1 (en) |
Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP1715067A1 (en) * | 2003-12-26 | 2006-10-25 | Nippon Light Metal, Co., Ltd. | METHOD FOR PRODUCING Al-Mg-Si BASED ALUMINUM ALLOY PLATE EXCELLENT IN BAKE-HARDENABILITY |
EP2072628A1 (en) * | 2007-12-19 | 2009-06-24 | Aleris Aluminum Bonn GmbH | High strength crash resistant aluminium alloy |
EP2553131B1 (en) | 2010-03-30 | 2019-05-08 | Norsk Hydro ASA | High temperature stable aluminium alloy |
EP3981893A1 (en) | 2020-10-07 | 2022-04-13 | AMAG rolling GmbH | Plate made of a rolled aluminium alloy and production of such a plate |
Families Citing this family (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN100532603C (en) * | 2005-05-25 | 2009-08-26 | 日本轻金属株式会社 | Aluminum alloy thin plate and its making method |
JP2012177171A (en) * | 2011-02-28 | 2012-09-13 | Sumitomo Light Metal Ind Ltd | Aluminum alloy foil for lithium ion battery electrode current collector, and method for producing the same |
KR20130058998A (en) | 2011-11-28 | 2013-06-05 | 현대자동차주식회사 | Aluminum alloy for continuous casting and method for producing the same |
WO2013080650A1 (en) | 2011-12-02 | 2013-06-06 | 古河スカイ株式会社 | Aluminum alloy material and aluminum alloy structure and production process therefor |
BR112014017965B1 (en) * | 2012-01-27 | 2022-07-12 | Uacj Corporation | ALUMINUM ALLOY MATERIAL FOR HEAT EXCHANGER FIN, MANUFACTURING METHOD AND HEAT EXCHANGER USING THE MENTIONED ALUMINUM ALLOY MATERIAL |
TWI507532B (en) * | 2013-03-14 | 2015-11-11 | Superalloyindustrial Co Ltd | High strength aluminum magnesium silicon alloy and its manufacturing process |
DE102015013540A1 (en) * | 2015-10-19 | 2017-04-20 | Trimet Aluminium Se | aluminum alloy |
CN107022698A (en) * | 2016-02-02 | 2017-08-08 | 中兴通讯股份有限公司 | A kind of high heat conduction pack alloy and preparation method thereof |
JP6721782B2 (en) * | 2016-08-15 | 2020-07-15 | ハイドロ アルミニウム ロールド プロダクツ ゲゼルシャフト ミット ベシュレンクテル ハフツングHydro Aluminium Rolled Products GmbH | Aluminum alloy and aluminum alloy strip for pedestrian collision protection |
CN117467872B (en) * | 2023-12-27 | 2024-03-19 | 中铝材料应用研究院有限公司 | 6000 series aluminum alloy plate with high electrode number and preparation method thereof |
Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP0638435A1 (en) * | 1993-07-26 | 1995-02-15 | Fuji Photo Film Co., Ltd. | Support for planographic printing plate |
JPH10152762A (en) * | 1996-11-21 | 1998-06-09 | Furukawa Electric Co Ltd:The | Production of hard aluminum alloy sheet excellent in di workability |
JP2000144294A (en) * | 1998-11-12 | 2000-05-26 | Kobe Steel Ltd | Aluminum alloy sheet excellent in press formability and hem workability |
US6344096B1 (en) * | 1995-05-11 | 2002-02-05 | Alcoa Inc. | Method of producing aluminum alloy sheet for automotive applications |
Family Cites Families (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP3307420B2 (en) * | 1992-03-18 | 2002-07-24 | 住友軽金属工業株式会社 | Spot welding method of A1-Mg-Si based aluminum alloy material |
JP2000262264A (en) * | 1999-03-18 | 2000-09-26 | Daiichi Reito:Kk | Method for thawing of cold mist type and thawing apparatus of cold mist type |
JP2001262264A (en) * | 2000-03-21 | 2001-09-26 | Kobe Steel Ltd | Al-Mg-Si SERIES Al ALLOY SHEET EXCELLENT IN TOUGHNESS AND BENDABILITY |
-
2004
- 2004-02-24 JP JP2004048360A patent/JP4379149B2/en not_active Expired - Fee Related
- 2004-04-08 TW TW093109748A patent/TW200504226A/en not_active IP Right Cessation
- 2004-04-13 WO PCT/JP2004/005258 patent/WO2004092432A1/en not_active Application Discontinuation
- 2004-04-13 US US10/553,316 patent/US20070062618A1/en not_active Abandoned
- 2004-04-13 CA CA002521006A patent/CA2521006A1/en not_active Abandoned
- 2004-04-13 KR KR1020057018560A patent/KR100710795B1/en not_active IP Right Cessation
- 2004-04-13 EP EP04727133A patent/EP1614760A4/en not_active Withdrawn
Patent Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP0638435A1 (en) * | 1993-07-26 | 1995-02-15 | Fuji Photo Film Co., Ltd. | Support for planographic printing plate |
US6344096B1 (en) * | 1995-05-11 | 2002-02-05 | Alcoa Inc. | Method of producing aluminum alloy sheet for automotive applications |
JPH10152762A (en) * | 1996-11-21 | 1998-06-09 | Furukawa Electric Co Ltd:The | Production of hard aluminum alloy sheet excellent in di workability |
JP2000144294A (en) * | 1998-11-12 | 2000-05-26 | Kobe Steel Ltd | Aluminum alloy sheet excellent in press formability and hem workability |
Non-Patent Citations (4)
Title |
---|
HATCH J E: "ALUMINUM" ALUMINUM. PROPERTIES AND PHYSICAL METALLURGY, OHIO, AMERICAN SOCIETY FOR METALS, US, 1984, pages 348-350, XP002397632 * |
PATENT ABSTRACTS OF JAPAN vol. 1998, no. 11, 30 September 1998 (1998-09-30) -& JP 10 152762 A (FURUKAWA ELECTRIC CO LTD:THE), 9 June 1998 (1998-06-09) * |
PATENT ABSTRACTS OF JAPAN vol. 2000, no. 08, 6 October 2000 (2000-10-06) -& JP 2000 144294 A (KOBE STEEL LTD), 26 May 2000 (2000-05-26) * |
See also references of WO2004092432A1 * |
Cited By (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP1715067A1 (en) * | 2003-12-26 | 2006-10-25 | Nippon Light Metal, Co., Ltd. | METHOD FOR PRODUCING Al-Mg-Si BASED ALUMINUM ALLOY PLATE EXCELLENT IN BAKE-HARDENABILITY |
EP1715067A4 (en) * | 2003-12-26 | 2007-10-31 | Nippon Light Metal Co | METHOD FOR PRODUCING Al-Mg-Si BASED ALUMINUM ALLOY PLATE EXCELLENT IN BAKE-HARDENABILITY |
EP2072628A1 (en) * | 2007-12-19 | 2009-06-24 | Aleris Aluminum Bonn GmbH | High strength crash resistant aluminium alloy |
EP2553131B1 (en) | 2010-03-30 | 2019-05-08 | Norsk Hydro ASA | High temperature stable aluminium alloy |
EP3981893A1 (en) | 2020-10-07 | 2022-04-13 | AMAG rolling GmbH | Plate made of a rolled aluminium alloy and production of such a plate |
WO2022074153A1 (en) | 2020-10-07 | 2022-04-14 | Amag Rolling Gmbh | Plate made of a rolled aluminium alloy and a method for producing said plate |
Also Published As
Publication number | Publication date |
---|---|
US20070062618A1 (en) | 2007-03-22 |
KR20050118299A (en) | 2005-12-16 |
KR100710795B1 (en) | 2007-04-25 |
CA2521006A1 (en) | 2004-10-28 |
TWI299755B (en) | 2008-08-11 |
JP2004332106A (en) | 2004-11-25 |
JP4379149B2 (en) | 2009-12-09 |
TW200504226A (en) | 2005-02-01 |
WO2004092432A1 (en) | 2004-10-28 |
EP1614760A4 (en) | 2006-10-18 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
US20070217943A1 (en) | Al-Mg Alloy Sheet with Excellent Formability at High Temperatures and High Speeds and Method of Production of Same | |
JP2614686B2 (en) | Manufacturing method of aluminum alloy for forming process excellent in shape freezing property and paint bake hardenability | |
JPH0127146B2 (en) | ||
KR101277297B1 (en) | High-strength high-ductility magnesium alloy extrusions with low anisotropy and manufacturing method thereof | |
EP0936278B2 (en) | Method of producing a product of an ALMGSI-alloy | |
US20070062618A1 (en) | Aluminum alloy plate excellent in press formability and continuous resistance spot weldability and method for production thereof | |
EP1715067A1 (en) | METHOD FOR PRODUCING Al-Mg-Si BASED ALUMINUM ALLOY PLATE EXCELLENT IN BAKE-HARDENABILITY | |
EP1360341B1 (en) | Production of high strength aluminum alloy foils | |
US5318642A (en) | High-strength rolled sheet of aluminum alloy and process for producing the same | |
JP4701998B2 (en) | Aluminum alloy foil excellent in strength and rough skin resistance and method for producing the same | |
JPH10152762A (en) | Production of hard aluminum alloy sheet excellent in di workability | |
JP4001059B2 (en) | Method for producing aluminum alloy sheet with excellent bake resistance | |
US20080295922A1 (en) | Aluminum Alloy Sheet Excellent in Resistance to Softening by Baking | |
JPS62207850A (en) | Rolled aluminum alloy sheet for forming and its production | |
CN114101612B (en) | Preparation method of jet-cast high-performance 7XXX aluminum alloy thin strip | |
CN100413986C (en) | Aluminum alloy plate excellent in press formability and continuous resistance spot weldability and method for production thereof | |
KR101937928B1 (en) | Magnesium alloy sheet and method for manufacturing the same | |
KR100488500B1 (en) | Production of magnesium-aluminium-zinc alloy thin-plates | |
KR101977830B1 (en) | Magnesium alloy sheet | |
JPH108176A (en) | Aluminum alloy sheet low in proof stress and excellent in ultimate deformability and its production | |
JPH028353A (en) | Manufacture of aluminum alloy for forming excellent in baking strength | |
JPH10130767A (en) | Al-mg-si alloy sheet with high formability, and its production | |
KR20240096119A (en) | Aluminum extruded material and method of manufacturing thereof | |
JPH08302440A (en) | Aluminum alloy sheet with high strength | |
CN116516221A (en) | 6000-series aluminum alloy medium plate for spinning rim and preparation method thereof |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
PUAI | Public reference made under article 153(3) epc to a published international application that has entered the european phase |
Free format text: ORIGINAL CODE: 0009012 |
|
17P | Request for examination filed |
Effective date: 20051010 |
|
AK | Designated contracting states |
Kind code of ref document: A1 Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IT LI LU MC NL PL PT RO SE SI SK TR |
|
AX | Request for extension of the european patent |
Extension state: AL HR LT LV MK |
|
RBV | Designated contracting states (corrected) |
Designated state(s): DE FR GB |
|
RBV | Designated contracting states (corrected) |
Designated state(s): DE FR GB |
|
DAX | Request for extension of the european patent (deleted) | ||
RBV | Designated contracting states (corrected) |
Designated state(s): DE FR GB |
|
A4 | Supplementary search report drawn up and despatched |
Effective date: 20060919 |
|
17Q | First examination report despatched |
Effective date: 20070524 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: THE APPLICATION IS DEEMED TO BE WITHDRAWN |
|
18D | Application deemed to be withdrawn |
Effective date: 20071005 |