EP1715067A1 - Verfahren zur herstellung einer auf al-mg-si basierenden aluminiumlegierungsplatte mit hervorragender bake-hardenability - Google Patents
Verfahren zur herstellung einer auf al-mg-si basierenden aluminiumlegierungsplatte mit hervorragender bake-hardenability Download PDFInfo
- Publication number
- EP1715067A1 EP1715067A1 EP04807567A EP04807567A EP1715067A1 EP 1715067 A1 EP1715067 A1 EP 1715067A1 EP 04807567 A EP04807567 A EP 04807567A EP 04807567 A EP04807567 A EP 04807567A EP 1715067 A1 EP1715067 A1 EP 1715067A1
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- EP
- European Patent Office
- Prior art keywords
- degrees
- rolling
- aluminum alloy
- ingot
- casting
- 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.)
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Links
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 29
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 15
- 229910018464 Al—Mg—Si Inorganic materials 0.000 title claims abstract description 14
- 238000005266 casting Methods 0.000 claims abstract description 49
- 238000001816 cooling Methods 0.000 claims abstract description 39
- 238000005097 cold rolling Methods 0.000 claims abstract description 29
- 238000005098 hot rolling Methods 0.000 claims abstract description 28
- 238000000265 homogenisation Methods 0.000 claims abstract description 22
- 238000000137 annealing Methods 0.000 claims abstract description 19
- 238000005096 rolling process Methods 0.000 claims abstract description 19
- 229910052802 copper Inorganic materials 0.000 claims abstract description 6
- 229910052751 metal Inorganic materials 0.000 claims description 18
- 239000002184 metal Substances 0.000 claims description 18
- 238000007711 solidification Methods 0.000 claims description 11
- 230000008023 solidification Effects 0.000 claims description 11
- 238000005728 strengthening Methods 0.000 abstract description 8
- 238000009749 continuous casting Methods 0.000 description 35
- 238000000034 method Methods 0.000 description 34
- 239000000243 solution Substances 0.000 description 19
- 229910021365 Al-Mg-Si alloy Inorganic materials 0.000 description 14
- 229910019752 Mg2Si Inorganic materials 0.000 description 12
- 230000000694 effects Effects 0.000 description 12
- 239000000463 material Substances 0.000 description 12
- 230000032683 aging Effects 0.000 description 9
- 238000001556 precipitation Methods 0.000 description 9
- 239000000203 mixture Substances 0.000 description 7
- 238000010791 quenching Methods 0.000 description 7
- 230000000171 quenching effect Effects 0.000 description 7
- 229920006395 saturated elastomer Polymers 0.000 description 7
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 7
- 230000000052 comparative effect Effects 0.000 description 5
- 229910052748 manganese Inorganic materials 0.000 description 5
- 239000006104 solid solution Substances 0.000 description 5
- 230000035882 stress Effects 0.000 description 5
- 230000002411 adverse Effects 0.000 description 4
- 239000000956 alloy Substances 0.000 description 4
- 229910052782 aluminium Inorganic materials 0.000 description 4
- 229910000765 intermetallic Inorganic materials 0.000 description 4
- 239000011159 matrix material Substances 0.000 description 4
- 229910045601 alloy Inorganic materials 0.000 description 3
- 238000010438 heat treatment Methods 0.000 description 3
- 239000012535 impurity Substances 0.000 description 3
- 229910052742 iron Inorganic materials 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 239000000047 product Substances 0.000 description 3
- 229910018191 Al—Fe—Si Inorganic materials 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- 230000001276 controlling effect Effects 0.000 description 2
- 230000001105 regulatory effect Effects 0.000 description 2
- 239000004566 building material Substances 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 239000010960 cold rolled steel Substances 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000005496 eutectics Effects 0.000 description 1
- 230000002431 foraging effect Effects 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 239000003973 paint Substances 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- 239000013585 weight reducing agent Substances 0.000 description 1
- 229910052725 zinc Inorganic materials 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/05—Mixtures of metal powder with non-metallic powder
-
- 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
- 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
- B22D11/16—Controlling or regulating processes or operations
- B22D11/22—Controlling or regulating processes or operations for cooling cast stock or mould
-
- 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
- B21B2003/001—Aluminium or its alloys
Definitions
- the present invention relates to a manufacturing method for Al-Mg-Si alloy sheets.
- the present invention concerns a manufacturing method for Al-Mg-Si aluminum alloy sheets, characterized in that a molten aluminum alloy metal containing a predetermined amount of Mg, Si as essential elements besides Al, and additionally in some cases a predetermined amount of Fe, Cu, Mn, and Cr is used, and during continuous casting of this, casting so that the average cooling rate at the time of solidification is 20 degrees C or above, and making the temperature of the ingot at the time it is taken out of the casting machine 250 degrees C or below, or cooling the ingot so that the temperature of the ingot is 250 degrees C or below within two minutes after the molten metal is poured into the casting machine, and further, after then having done rolling to the final sheet thickness by cold rolling only and without homogenization or hot rolling, solution treatment is done in a continuous annealing furnace.
- the Al-Mg-Si alloy sheet obtained by the present invention has excellent bake hardenability, so that by making use
- cold-rolled steel has been used conventionally for automobile panel materials.
- a trend towards using aluminum alloy materials that are lightweight and have high specific strength, and have excellent metal forming processability is rapidly increasing.
- Al-Mg-Si alloy As an aluminum alloy sheet for automobiles that is often used with a paint coating for aesthetic improvement, Al-Mg-Si alloy, with its excellent bake hardenability, is getting attention, and its practical realization is being advanced in some quarters.
- the method that has generally been implemented in the past as a manufacturing for aluminum alloy sheets is the method whereby after scalping and homogenization, the processes such as hot rolling, cold rolling, and annealing are sequentially performed on an ingot produced by a semi-continuous casting method.
- Conventional aluminum alloy sheets produced through such processes since their press formability is excellent, and their bake hardenability is also excellent, were sufficient for the requirements of customers.
- a method has been proposed whereby, during the production of an aluminum alloy sheet using molten aluminum alloy, hot rolling is done after continuous casting, and cold-rolling is further done, the precipitation of super-saturated solute elements during the sequence of the processes of continuous casting, hot rolling, cold rolling, and intermediate annealing in particular is reduced as much as possible, and the strength of the final cold rolling product is increased, and bake hardenability and press formability are improved markedly ( JP-A H7-252616 ).
- This method uses a molten aluminum alloy containing specific amounts of alloy elements such as Mg, Mn, and Si in particular, and manufactures an Al-Mg-Si alloy sheet by hot rolling after continuous casting, and further performing cold rolling, but at that time, by regulating the cooling rate during continuous casting and after hot rolling, and additionally by controlling the heat processing conditions after the cold rolling that is subsequently performed, an Al-Mg-Si alloy sheet with improved press formability and bake hardenability and the like is obtained.
- Patent Citation 3 JP-A H7-252616
- Continuous casting methods utilized in such continuous casting/direct rolling methods are the water cooled continuous casting method (a continuous casting method whereby continuous casting slabs that are formed into sheets and come out of a stationary type water cooled continuous casting mold are directly cooled and solidified), a twin roll casting method developed at Hunter Engineering (a continuous casting method whereby molten metal is supplied between a pair of rotating cooled rollers, and cooling and solidification is done between said rollers), a belt type continuous casting method developed at Hazelett (a method whereby molten metal is supplied between two movable belt-shaped cooling members, and casting in the shape of a sheet continuously while cooling and solidifying between said belts), a block-type continuous casting method developed at Swiss Aluminum (a method whereby molten metal is supplied between two movable block-shaped cooling members, and casting in the shape of a sheet while cooling and solidifying between said blocks), and the like.
- intermediate annealing is done at a relatively low temperature in the range of 350 to 500 degrees C in order to prevent process cracking, but a problem arises in that precipitation of super-saturated solute elements occurs during the intermediate annealing process, and inhibits strengthening of the final cold rolling product.
- the present invention was made with attention to the problems with the conventional art described above, and concerns a manufacturing method for Al-Mg-Si aluminum alloy sheets with excellent bake hardenability, characterized in that during twin belt casting of Al-Mg-Si aluminum, casting is done at an average cooling rate of 20 degrees C per second or above at the time of solidification, and the temperature of the ingot when coming out of the casting machine is 250 degrees C or below, and additionally, the ingot is cooled so that the ingot temperature is 250 degrees C or below within 2 minutes from pouring the molten metal into the casting machine, and further, after subsequently rolling to the final sheet thickness by cold rolling and without homogenization or hot rolling, solution treatment is done in a continuous annealing furnace.
- the first invention for solving the abovementioned problems is a manufacturing method for Al-Mg-Si aluminum alloy sheets with excellent bake hardenability, the main points being that a molten Al-Mg-Si aluminum alloy comprising Mg: 0.3 - 1.0 wt%, Si: 0.3 - 1.5 wt%, Cu: 1.0 wt% or below (including 0%), Fe: 1.2 wt% or below (including 0%), and according to need, containing Mn: 0.1 - 0.7 wt% and/or Cr: 0.1 - 0.3 %, and the remnant being Al is twin belt cast at an average cooling rate of 20 degrees C per second or above at the time of solidification, and at this time, the temperature of the ingot coming out of the casting machine is 250 degrees C or below, and subsequently rolling is done to the final sheet thickness by cold rolling and without homogenization or hot rolling, and solution treatment is done in a continuous annealing furnace.
- the second invention for solving the abovementioned problems is a manufacturing method for Al-Mg-Si aluminum alloy sheets with excellent bake hardenability, the main points being that a molten Al-Mg-Si aluminum alloy comprising Mg: 0.3 - 1.0 wt%, Si: 0.3 - 1.5 wt%, Cu: 1.0 wt% or below (including 0%), Fe: 1.2 wt% or below (including 0%), and according to need, containing Mn: 0.1 - 0.7 wt% and/or Cr: 0.1 - 0.3 %, and the remnant being Al is twin belt cast at an average cooling rate of 20 degrees C per second or above at the time of solidification, and at this time, the ingot is cooled so that the ingot temperature is 250 degrees C or below within 2 minutes of pouring molten metal into the casting machine, and after this rolling is done to the final sheet thickness by cold rolling and without homogenization or hot rolling, and solution treatment is done in a continuous annealing furnace.
- the reason for making the average cooling rate 20 degrees C or above is that if the average cooling rate is less than 20 degrees C per second, coarse Mg 2 Si readily precipitates during solidification, and this coarse Mg 2 Si is difficult to be dissolved into the matrix sufficiently during solution treatment with a continuous annealing furnace, so as a result, the bake hardenability is inferior.
- the reason for making the temperature of the ingot when coming out of the casting machine 250 degrees C or below is that if said temperature is above 250 degrees C, since Mg 2 Si precipitates during the cooling process of the ingot, the temperature and time needed for the solution treatment of the final sheet with a continuous annealing furnace increases, and as a result, bake hardenability is inferior.
- the reason for not doing homogenization or hot rolling is that even if the precipitation of Mg 2 Si is suppressed during the casting and cooling processes, since Mg 2 Si precipitates again during homogenization or hot rolling, it becomes difficult to be dissolved into the matrix sufficiently during solution treatment, and as a result, the bake hardenability is inferior.
- the reason for cooling the ingot to 250 degrees C or below within 2 minutes of pouring the molten metal is that if 2 minutes is passed, the precipitation of Mg 2 Si occurs, and it becomes difficult to dissolve this Mg 2 Si into the matrix during solution treatment of the final sheet with a continuous annealing furnace, and as a result, bake hardenability is inferior.
- the manufacturing conditions prescribed for the present invention including composition of the Al-Mg-Si alloy and cooling conditions during continuous casting and after heat rolling shall be explained in detail.
- the reason for prescribing the composition of the Al-Mg-Si alloy used in the present invention shall be explained.
- Mg (0.3 -1.0 wt%) is an element that forms Mg 2 Si and contributes to strengthening, and it is necessary to include 0.3 wt% or above in order to secure the strength necessary for outer panel materials as described above. However, if the content is too high, this reduces formability, so that it is also necessary to keep the content at 1.0 wt% or below.
- a more preferable lower bound for Mg is 0.4 wt%, and a more preferable upper bound is 0.8 wt%.
- Si (0.3 - 1.5 wt%) is an element that forms Mg 2 Si with the abovementioned Mg, and contributes to strengthening, and in order to effectively realize the effects of its addition, it is necessary to include 0.3% or above. However, if the content is too high, there is an adverse effect on press formability, so that it is also necessary to keep the content at 1.5 wt% or below. A more preferable lower bound for Si is 0.6%, and a more preferable upper bound is 1.2 wt%. As described above, in the present invention, Mg and Si form aggregates (clusters) of Mg 2 Si composition called a G. P. zone, or an intermediate layer within the aluminum alloy, and are important elements that contribute to hardening by baking treatment.
- Cu (1.0 wt% or below) is not absolutely necessary, but it has a precipitation strengthening effect, so that it is desirable to include proactively in cases where the demands for strength are high. However, if the content is too high, adverse effects will appear, so that it should be kept at 1.0 wt% or below. Considering the balance between strength and formability, a more preferable Cu content is in the range of 0.4 - 0.9 wt%.
- Fe (1.2 wt% or below) is also not absolutely necessary, but it has the effect of increasing strength, so that it is desirable to include proactively in cases where the demands for strength are high. However, if the content is too high, adverse effects will appear, so that it should be kept at 1.2 wt% or below. Considering the balance between strength and formability, a more preferable Fe content is in the range of 0.1- 0.5 wt%.
- Mn (0.1 - 0.7 wt%) is an element that is effective as a solid solution strengthening element and a recrystallized grain refinement element, and in order to effectively realize these effects, 0.1 wt% or above must be included. However, if the content is too high, due to the increase in the amount of Mn that cannot be dissolved into a solid solution, a tendency to worsen the formability appears, so that it must be kept at 0.7 wt% or below.
- Cr (0.1- 0.3 wt%) has an effect as a recrystallized grain refinement element, and in order to effectively realize these effects, a greater amount than the lower bound must be included. However, if the content surpasses the abovementioned upper bound, intermetallic compounds are generated and adverse effects appear. Considering these points, a desirable content for Cr is in the range of 0.1 - 0.3 wt%.
- the components making up the remnant of the aluminum alloy in the present invention are Al and unavoidable impurities, and examples of unavoidable impurities are Ni, Zn, Zr, V, Ti, Li and the like, but as long as these are in unavoidable impurity amounts, they will not be a particular obstacle for securing the properties intended for the present invention.
- unavoidable impurities Ni, Zn, Zr, V, Ti, Li and the like, but as long as these are in unavoidable impurity amounts, they will not be a particular obstacle for securing the properties intended for the present invention.
- the average cooling rate at the time of solidification during continuous casting is prescribed in the above manner, the amount of Al-Fe-Si intermetallic compounds in the continuous cast structure decrease due to forced solid dissolution, and additionally, the size of said Al-Fe-Si intermetallic compounds are refined to an average size of approximately 2 ⁇ m or below, and the press formability and bake hardenability are markedly increased.
- the average cooling rate at the time of solidification during continuous casting is below the abovementioned rate, the amount of intermetallic compounds precipitated increases, and additionally their size becomes coarse, and not only does satisfactory press formability become unobtainable, but bake hardenability also becomes inferior.
- solution treatment is performed in a temperature range of 530 - 570 degrees C in a continuous annealing furnace, and after quenching with hot or cold water, preliminary aging treatment is done.
- the reason for prescribing the solution treatment temperature at this time in the above manner is to suppress the precipitation of solute elements during solution treatment and maintain a sufficient super-saturated solute amount, and increasing strength, to increase bake hardenability by increasing the amount of solute elements.
- the temperature of the solution treatment is below 530 degrees C, the improvement effect on bake hardenability also becomes insufficient.
- the temperature surpasses 570 degrees C the recrystallized grains become coarser, and additionally, burning due to eutectic melting occurs, and press formability is worsened.
- an Al-Mg-Si alloy sheet with extremely excellent press formability and bake hardenability is obtainable.
- the conditions for quenching and aging heat treatment are not particularly restricted, but as preferable conditions, the condition for quenching is hot water quenching, and the condition for aging heat treatment are approximately 10 minutes to 8 hours at 60 - 200 degrees C.
- the present invention in addition to specifying the composition of an Al-Mg-Si alloy as described above, has the characteristic that during continuous casting using said molten alloy, casting is done so that the average cooling rate at the time of solidification is 20 degrees C or above, and the temperature of the ingot at the time it is taken out of the casting machine is made to be 250 degrees C or below, or the ingot is cooled so that the temperature of the ingot is 250 degrees C or below within two minutes after the molten metal is poured into the casting machine, and subsequently rolling to the final sheet thickness by cold rolling only and without homogenization or hot rolling, and prescribing the conditions for solution treatment in a continuous annealing furnace, and there are no specific restrictions on other conditions, but if other preferable conditions and the like are to be explained, then they are as follows.
- the present invention is characterized by continuous casting so that the ingot temperature is 250 degrees C or below, or cooling a continuously cast slab to 250 degrees C or below, rolling this up once, then rolling to the final sheet thickness by only cold rolling and without homogenization or hot rolling, and prescribing the conditions for solution treatment with a continuous annealing furnace, and due to this, compared to the method whereby after rolling up once after continuous casting, cooling is done and then homogenization or hot rolling is further done, the heat loss is small, and it is also effective for increasing productivity.
- an aluminum alloy manufactured sheet is manufactured, by continuously manufacturing sheet-shaped slabs of a thickness of approximately 4 - 15 mm normally by continuous casting, by cold rolling this to a thickness of 0.1 - 1 mm after having rolled this up, and further performing solution treatment with a continuous annealing furnace and preliminary aging.
- the continuous casting method utilized here the aforementioned water-cooled type continuous casting method, twin roll type continuous casting method, belt type continuous casting method, block type continuous casting method, and the like may be selected as appropriate and utilized.
- a cooling device was attached at the exit opening of the casting machine so that the ingot may be cooled immediately after casting.
- the cooling device was running, the temperature of the ingots, which were 357 degrees C immediately after casting, by passing through the cooling device, were reduced to 230 degrees C within 2 minutes after pouring molten metal into the casting machine.
- the cooling device was not running, the temperature of the ingots 2 minutes after molten metal was poured into the casting machine was still hot at 330 degrees. After this, after cold-rolling to a 1 mm sheet, and performing a solution treatment of 545 degrees C x 15 seconds ⁇ hot water quenching, preliminary aging of 85 degrees C x 8 hours was done, and T4 material was made.
- T6 material after naturally aging T4 material for 1 week, 170 degrees C x 30 minutes of artificial aging was done. In order to evaluate bake hardenability, the proof stress of the T4 and T6 materials were measured, and the difference in the proof stress between T4 and T6 materials was taken to be the bake hardenability.
- the target for superior bake hardenability was 100 MPa or above.
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- Engineering & Computer Science (AREA)
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- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Continuous Casting (AREA)
- Metal Rolling (AREA)
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2003432073 | 2003-12-26 | ||
PCT/JP2004/019210 WO2005064025A1 (ja) | 2003-12-26 | 2004-12-22 | ベークハード性に優れたAl-Mg-Si系アルミニウム合金板の製造方法 |
Publications (2)
Publication Number | Publication Date |
---|---|
EP1715067A1 true EP1715067A1 (de) | 2006-10-25 |
EP1715067A4 EP1715067A4 (de) | 2007-10-31 |
Family
ID=34736460
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP04807567A Withdrawn EP1715067A4 (de) | 2003-12-26 | 2004-12-22 | Verfahren zur herstellung einer auf al-mg-si basierenden aluminiumlegierungsplatte mit hervorragender bake-hardenability |
Country Status (8)
Country | Link |
---|---|
US (1) | US20070144630A1 (de) |
EP (1) | EP1715067A4 (de) |
JP (1) | JPWO2005064025A1 (de) |
KR (1) | KR20060135711A (de) |
CN (1) | CN1922336A (de) |
CA (1) | CA2551599A1 (de) |
TW (1) | TW200530406A (de) |
WO (1) | WO2005064025A1 (de) |
Cited By (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2008078399A1 (en) * | 2006-12-22 | 2008-07-03 | Nippon Light Metal Company, Ltd. | Method of producing aluminum alloy sheet |
DE102008008326A1 (de) * | 2008-02-07 | 2011-03-03 | Audi Ag | Aluminiumlegierung |
US20110265606A1 (en) * | 2009-01-06 | 2011-11-03 | Nippon Light Metal Company, Ltd. | Method of production of aluminum alloy |
EP2489755A4 (de) * | 2009-10-16 | 2015-11-11 | Showa Denko Kk | Verfahren zur herstellung eines bremskolbens |
EP2822717A4 (de) * | 2012-03-07 | 2016-03-09 | Alcoa Inc | Verbesserte 6xxx-aluminiumlegierungen und verfahren zur herstellung davon |
EP2822716A4 (de) * | 2012-03-07 | 2016-04-06 | Alcoa Inc | Verbesserte aluminiumlegierungen mit magnesium, silizium, mangan, eisen und kupfer sowie verfahren zur herstellung davon |
EP2553131B1 (de) | 2010-03-30 | 2019-05-08 | Norsk Hydro ASA | Hochtemperaturstabile aluminiumlegierung |
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KR100757586B1 (ko) | 2006-04-29 | 2007-09-10 | 현대자동차주식회사 | 알루미늄-마그네슘 합금판재의 연속주조방법 |
KR101233772B1 (ko) * | 2010-10-15 | 2013-02-15 | 지케이 주식회사 | 다이캐스팅용 알루미늄합금 |
KR101340292B1 (ko) | 2011-05-20 | 2013-12-11 | 한국생산기술연구원 | 알루미늄 합금 및 그 제조방법 |
JP6340170B2 (ja) * | 2013-06-28 | 2018-06-06 | 国立大学法人横浜国立大学 | アルミニウム合金板及びアルミニウム合金部材 |
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JP6719219B2 (ja) * | 2016-01-26 | 2020-07-08 | 日本軽金属株式会社 | 成形性に優れる高強度アルミニウム合金板及びその製造方法 |
CN105671376B (zh) * | 2016-01-26 | 2017-04-26 | 北京航空航天大学 | 高强高塑重力铸造与室温冷轧亚共晶铝硅合金材料及其制造方法 |
KR101950595B1 (ko) * | 2017-08-22 | 2019-02-20 | 현대제철 주식회사 | 알루미늄 합금 및 그 제조방법 |
CN108085545A (zh) * | 2017-12-28 | 2018-05-29 | 河南中孚铝合金有限公司 | 电脑硬盘驱动臂用铝合金圆铸锭及其生产方法 |
MX2020007482A (es) | 2018-01-12 | 2020-11-12 | Accuride Corp | Ruedas de aluminio y metodos de fabricacion. |
DE102018100842B3 (de) | 2018-01-16 | 2019-05-09 | Ebner Industrieofenbau Gmbh | Durchlaufofen für Aluminiumbänder |
CN112195424A (zh) * | 2020-10-29 | 2021-01-08 | 天津忠旺铝业有限公司 | 一种提高6016铝合金板r值及其均匀性的制备工艺 |
US20220274160A1 (en) * | 2020-11-06 | 2022-09-01 | Hazelett Castechnology Ulc | Casting process for aluminium alloys |
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US7267158B2 (en) * | 2003-07-02 | 2007-09-11 | Alcoa Inc. | Control of oxide growth on molten aluminum during casting using a high moisture atmosphere |
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2004
- 2004-12-10 TW TW093138422A patent/TW200530406A/zh unknown
- 2004-12-22 US US10/584,200 patent/US20070144630A1/en not_active Abandoned
- 2004-12-22 CA CA002551599A patent/CA2551599A1/en not_active Abandoned
- 2004-12-22 CN CNA200480042140XA patent/CN1922336A/zh active Pending
- 2004-12-22 EP EP04807567A patent/EP1715067A4/de not_active Withdrawn
- 2004-12-22 WO PCT/JP2004/019210 patent/WO2005064025A1/ja not_active Application Discontinuation
- 2004-12-22 KR KR1020067014313A patent/KR20060135711A/ko not_active Application Discontinuation
- 2004-12-22 JP JP2005516601A patent/JPWO2005064025A1/ja active Pending
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JPS62207851A (ja) * | 1986-03-10 | 1987-09-12 | Sky Alum Co Ltd | 成形加工用アルミニウム合金圧延板およびその製造方法 |
EP1614760A1 (de) * | 2003-04-15 | 2006-01-11 | Nippon Light Metal Company Ltd. | Aluminiumlegierungsplatte mit hervorragender pressformbarkeit und punktschweissbarkeit mit kontinuierlichem widerstand und herstellungsverfahren dafür |
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Cited By (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2008078399A1 (en) * | 2006-12-22 | 2008-07-03 | Nippon Light Metal Company, Ltd. | Method of producing aluminum alloy sheet |
DE102008008326A1 (de) * | 2008-02-07 | 2011-03-03 | Audi Ag | Aluminiumlegierung |
US20110265606A1 (en) * | 2009-01-06 | 2011-11-03 | Nippon Light Metal Company, Ltd. | Method of production of aluminum alloy |
US9096915B2 (en) * | 2009-01-06 | 2015-08-04 | Nippon Light Metal Company, Ltd. | Method of production of aluminum alloy |
EP2489755A4 (de) * | 2009-10-16 | 2015-11-11 | Showa Denko Kk | Verfahren zur herstellung eines bremskolbens |
EP2553131B1 (de) | 2010-03-30 | 2019-05-08 | Norsk Hydro ASA | Hochtemperaturstabile aluminiumlegierung |
EP2822717A4 (de) * | 2012-03-07 | 2016-03-09 | Alcoa Inc | Verbesserte 6xxx-aluminiumlegierungen und verfahren zur herstellung davon |
EP2822716A4 (de) * | 2012-03-07 | 2016-04-06 | Alcoa Inc | Verbesserte aluminiumlegierungen mit magnesium, silizium, mangan, eisen und kupfer sowie verfahren zur herstellung davon |
Also Published As
Publication number | Publication date |
---|---|
TW200530406A (en) | 2005-09-16 |
CA2551599A1 (en) | 2005-07-14 |
CN1922336A (zh) | 2007-02-28 |
EP1715067A4 (de) | 2007-10-31 |
KR20060135711A (ko) | 2006-12-29 |
JPWO2005064025A1 (ja) | 2008-04-17 |
WO2005064025A1 (ja) | 2005-07-14 |
US20070144630A1 (en) | 2007-06-28 |
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