US20030133825A1 - Composition and method of forming aluminum alloy foil - Google Patents
Composition and method of forming aluminum alloy foil Download PDFInfo
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- US20030133825A1 US20030133825A1 US10/051,873 US5187302A US2003133825A1 US 20030133825 A1 US20030133825 A1 US 20030133825A1 US 5187302 A US5187302 A US 5187302A US 2003133825 A1 US2003133825 A1 US 2003133825A1
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- 238000000034 method Methods 0.000 title claims abstract description 24
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 16
- 239000011888 foil Substances 0.000 title claims abstract description 16
- 239000000203 mixture Substances 0.000 title claims abstract description 16
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 57
- 239000000956 alloy Substances 0.000 claims abstract description 57
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 25
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 25
- 238000005097 cold rolling Methods 0.000 claims abstract description 14
- 229910052802 copper Inorganic materials 0.000 claims abstract description 14
- 229910052749 magnesium Inorganic materials 0.000 claims abstract description 10
- 239000012535 impurity Substances 0.000 claims abstract description 4
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 37
- 239000011572 manganese Substances 0.000 claims description 32
- 229910052748 manganese Inorganic materials 0.000 claims description 17
- 238000005266 casting Methods 0.000 claims description 15
- 229910052742 iron Inorganic materials 0.000 claims description 15
- 229910052710 silicon Inorganic materials 0.000 claims description 14
- 239000010703 silicon Substances 0.000 claims description 11
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 10
- 229910052725 zinc Inorganic materials 0.000 abstract description 10
- 239000011701 zinc Substances 0.000 description 14
- 239000010949 copper Substances 0.000 description 13
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 9
- 238000005096 rolling process Methods 0.000 description 9
- 239000011777 magnesium Substances 0.000 description 7
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 6
- 238000009749 continuous casting Methods 0.000 description 5
- 238000005219 brazing Methods 0.000 description 4
- 230000007423 decrease Effects 0.000 description 4
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 3
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 3
- 238000000137 annealing Methods 0.000 description 3
- 229910052804 chromium Inorganic materials 0.000 description 3
- 239000011651 chromium Substances 0.000 description 3
- 238000005098 hot rolling Methods 0.000 description 3
- 239000002245 particle Substances 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 239000011162 core material Substances 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 238000005482 strain hardening Methods 0.000 description 2
- 229910052719 titanium Inorganic materials 0.000 description 2
- 229910018131 Al-Mn Inorganic materials 0.000 description 1
- 229910018125 Al-Si Inorganic materials 0.000 description 1
- 229910000951 Aluminide Inorganic materials 0.000 description 1
- 229910018461 Al—Mn Inorganic materials 0.000 description 1
- 229910018520 Al—Si Inorganic materials 0.000 description 1
- 229910018566 Al—Si—Mg Inorganic materials 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- UJXVAJQDLVNWPS-UHFFFAOYSA-N [Al].[Al].[Al].[Fe] Chemical compound [Al].[Al].[Al].[Fe] UJXVAJQDLVNWPS-UHFFFAOYSA-N 0.000 description 1
- 238000004378 air conditioning Methods 0.000 description 1
- -1 aluminum-silicon-iron aluminum Chemical compound 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000007795 chemical reaction product Substances 0.000 description 1
- 238000005253 cladding Methods 0.000 description 1
- 230000001276 controlling effect Effects 0.000 description 1
- 230000002596 correlated effect Effects 0.000 description 1
- 230000000875 corresponding effect Effects 0.000 description 1
- 230000001419 dependent effect Effects 0.000 description 1
- 238000004512 die casting Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 229910021326 iron aluminide Inorganic materials 0.000 description 1
- XWHPIFXRKKHEKR-UHFFFAOYSA-N iron silicon Chemical compound [Si].[Fe] XWHPIFXRKKHEKR-UHFFFAOYSA-N 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 239000003921 oil Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000004881 precipitation hardening Methods 0.000 description 1
- 238000001953 recrystallisation Methods 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
- 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
Definitions
- the present invention describes a method of forming an aluminum alloy foil suitable for continuous casting in the fabrication of fins used in brazed automotive heat exchangers.
- Aluminum foil is the preferred choice for forming fins used in heat transfer and air conditioning equipment such as radiators, condensers, oil coolers and evaporators.
- Zn is also added to it when the fin is used in the sacrificial mode.
- concentration of Zn can vary between 0.5 to 2%.
- the aluminum foil is usually in the thickness range of 0.002-0.008 in.
- An aluminum sheet is cold rolled to this final gauge starting from a reroll sheet that is in the gauge range of 0.04-0.3 in.
- the reroll sheet is produced by casting DC ingots, homogenizing at elevated temperatures, and then hot rolling to the reroll gauge.
- the reroll sheet is produced by a continuous casting process and is directly hot or warm rolled to the final reroll gauge.
- the continuous casting process is advantageous because it is more productive and less expensive.
- the radiators, evaporators and other heat exchangers are produced by brazing aluminum fins to the clad aluminum sheet of different shapes or forms.
- the brazing operation takes place at around 600° C.
- aluminum fins can sag and collapse or, in some cases, affect the crushing pressure that the finished units can take at ambient and operating temperatures.
- the tendency to sag during brazing cycle is measured by a property that is characterized as sag resistance. It is generally accepted that higher sag resistance improves performance of the unit. Sag resistance in general is dependent upon the post braze grain size of the aluminum foil. Higher grain size produces higher sag resistance. Therefore, higher grain size (>100 micron in transverse and longitudinal directions) after annealing the sheet is preferred in automotive fin applications.
- the aluminum sheet can be used in the fin forming operation in different tempers, such as from fully hard to fully annealed.
- alloy 3003 produced by continuous casting is an excellent choice for auto-fin applications because it yields high post braze strength and sag resistance.
- it contains high amount of Mn and Cu, it gets easily work hardened and is therefore difficult to roll.
- it yields a highly convex profile (>0.6% crown) because it causes high temperature differences between the center and edge of the sheet. This is due to the high Mn and Fe content of the alloy.
- the convex profile causes problems during rolling and the slitting operations that follow after rolling. As a result, the cost of production of continuous cast 3003 is rather high.
- U.S. Pat. No. 4,906,534 discusses a method of preparing thin aluminum plates used as fins of heat exchangers from an aluminum alloy core material, comprising 0.6 to 2.0 wt % of Mn, 0.3 wt % or less of Fe, 0.05 to 0.6 wt % of Si, 0.5 to 2.0 wt % of Zn, 0.05 to 0.2 wt % of Cu, and a balance of Al.
- the patent additionally contemplates use of skin materials of an Al—Si system or an Al—Si—Mg system for cladding the surfaces of the core material.
- U.S. Pat. No. 4,334,935 discloses a fine grained, formable Al—Mn alloy sheet used to make rigid foil containers.
- the alloy consists essentially of 1.3-2.3% Mn, up to 0.5% each of Fe, Mg, and Cu, up to 0.3% Si, up to 2.0% Zn, less than 0.1% each of Zr, Cr, and Ti, other elements up to 0.3% each and up to 1.0% total.
- U.S. Pat. No. 5,888,320 (Dorward) describes a method of producing aircraft and automobile panels.
- the product includes an aluminum base alloy consisting essentially of about 0.6 to 1.4 wt. % silicon, not more than about 0.5 wt. % iron, not more than about 0.6 wt. % copper, about 0.6 to 1.4 wt. % magnesium, about 0.4 to 1.4 wt. % Zn, at least one element selected from the group consisting of about 0.2 to 0.8 wt. % manganese and about 0.05 to 0.3 wt. % chromium.
- U.S. Pat. No. 5,725,695 (Ward) discloses an aluminum foil product made from an aluminum-silicon-iron aluminum alloy consisting essentially of 0.30-1.1% Si, 0.40-1.0% Fe, max 0.10% Cu, max 0.10% Mn, max 0.05% Mg, max 0.05% Cr, max 0.10% Zn, and max 0.08% Ti.
- U.S. Pat. No. 4,169,728 discloses an alloy for die-casting which consists essentially of 0.5-2.5% Zn, 1.1 to 3.0% Mg, 0.3 to 1.2% Si, 0.2 to 1.5% Fe, 0.3 to 1.2% Mn, and 0.1 to 0.3% Cu.
- the disadvantages of prior methods and alloys may be overcome by the present invention, which provides an aluminum alloy foil for fins used in heat exchangers.
- the improved alloy composition of the present invention consists essentially of about 0.25% to about 0.6% by weight of Si, about 0.15% to about 0.50% by weight of Fe, about 0.20% to about 0.70% by weight of Mn, less than about 0.05% Cu, and less than about 0.05% Mg with the balance aluminum including unavoidable impurities.
- the alloy composition may also contain less than 0.10% Zn or an amount of Zn in the range from about 0.50 to 2.00% by weight.
- the invention also provides a method for making an improved aluminum foil.
- the method comprises providing a molten aluminum foil alloy having the composition stated in the previous paragraph.
- the molten alloy is continuously cast into an aluminum alloy strip from the molten aluminum alloy, and cold rolled into a final gauge of between about 0.002-0.008 inches.
- the present invention provides two new alloy compositions, one with Zn and one without Zn.
- the improved alloy has lower density, reduced manganese levels, and larger grain size to improve sag resistance.
- the preferred composition ranges for the aluminum alloy in accordance with the present invention is shown in Table II, below: TABLE II Elements Wt. % Composition A Silicon 0.25-0.60 Iron 0.15-0.50 Manganese 0.20-0.70 Copper ⁇ 0.05 Magnesium ⁇ 0.05 Zinc ⁇ 0.10 Composition B Silicon 0.25-0.60 Iron 0.15-0.50 Manganese 0.20-0.70 Copper ⁇ 0.05 Magnesium ⁇ 0.05 Zinc 0.50 to 2.00
- the alloy of the present invention has a lower density than DC cast 3003. This reduces the cost of using the alloy as fin stock in brazed heat exchangers where surface area is the determining factor.
- Si content ranges between about 0.3 and about 0.5%. Silicon and intermetallic particles of silicon, iron and aluminum precipitate in the sheet, making the surface hard. This reduces smut (reaction product) formation during cold rolling. Si above 0.6% is not desired because it makes the scrap less compatible with can scrap and therefore less desirable. Additionally, the amount of silicon present affects the smut generated during cold rolling. As it exceeds a critical level of 0.25%, smut generation decreases significantly. This is because of precipitation of silicon and intermetallic particles of silicon within the matrix that increase the hardness of the metal and thereby reduce the smut generated during cold rolling.
- Fe content ranges between about 0.15 and about 0.35%.
- Low Fe helps increase grain size of the alloy after annealing because it reduces the amount of iron aluminide and iron silicon aluminide particles which pin grains and reduce grain size.
- Very low Fe is also undesirable as it can affect the total Fe+Mn content in the alloy. The Fe+Mn content needs to be controlled within desired limits, for reasons explained below.
- the reduced manganese levels of the alloy of the present invention accommodate a different strengthening mechanism compared to DC cast 3003.
- DC cast 3003 the Mn precipitates out during the hot rolling/homogenizing steps and the precipitates harden the metal.
- the Mn stays in solution and provides a solution strengthening effect.
- solution strengthening is more effective at producing a strong final product than precipitation hardening.
- Mn content ranges between about 0.30 and about 0.60%. Reducing Mn from the level present in 3003 reduces the required amount of work hardening during cold rolling, and thereby helps improve cold rolling productivity. The lower limit for Mn is necessary because below this level the grain size after annealing decreases to the level at which it can affect the sag resistance.
- the optimal grain size for this application is larger than normal. Generally, small grains are preferred for a good combination of formability and strength. In this application, however, sag resistance is more important and larger grain sizes improve sag resistance.
- Mn+Fe content is 0.40%-0.80%.
- the lower limit is necessary because below this level the shrinkage during casting increases to such an extent that it affects the heat transfer during casting and therefore results in poor surface of the reroll. Poor reroll surface can result in surface cracks in the alloy.
- the center to edge temperature difference during casting is correlated to the amount of Mn+Fe in the alloy. When the amount of Mn+Fe increases, the temperature difference between center and edge also increases. This results in poor profile during hot rolling, which in turn causes problems during cold rolling and slitting.
- Cu content is ⁇ 0.05%. Copper content of the alloy is minimized because copper results in work hardening during cold rolling.
- the alloys of the present invention are continuously cast to form an as-cast strip 30 mm (1.18 inches) or less in thickness.
- the alloys are preferably cast using twin belt casting, block casting or twin roll casting. In all cases the cast strip is not homogenized prior to subsequent rolling.
- the as-cast strip may be optionally hot or warm rolled prior to cold rolling or may be directly cold rolled. Warm rolling is carried out at a temperature low enough to avoid recrystallization.
- Interanneal during cold rolling is carried out at a gauge such that the cold work after interanneal is between 30-70%. This results in large post braze grain size. The lower limit is necessary as below this level rolling speed in the final pass can decrease significantly.
- the composition of the alloy is chosen such that it optimizes performance during casting and rolling to obtain the best combination of post braze properties.
- Mn and Fe are two elements that affect casting performance significantly. Aluminum shrinks during casting. To compensate for this shrinkage, the casting gap is reduced from the starting to the finishing point.
- composition of individual alloys can also affect the amount of shrinkage. Two elements that can reduce the amount of shrinkage are Mn and Fe. Reduced shrinkage results in increased heat transfer during casting and therefore yields excellent surface after rolling. Too low a shrinkage can result in increased transverse temperature difference which in turn leads to poor profile after warm rolling. The two must be optimized to give a satisfactory surface and profile.
- Another aspect of this invention is the control of post braze grain size.
- grain size increases with increasing Mn and decreases with increasing Fe. Accordingly, the two must be optimized while respecting limits for improved casting performance.
- the invention also provides another mechanism for controlling grain size: the alloy is cold worked before brazing to increase the post braze grain size.
- the present invention results in better rolling productivity, improved profile, and density of aluminum reduced by about one percent, which yields more feet of sheet for the same weight and thereby improves productivity for the user.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Continuous Casting (AREA)
- Metal Rolling (AREA)
Abstract
Description
- The present invention describes a method of forming an aluminum alloy foil suitable for continuous casting in the fabrication of fins used in brazed automotive heat exchangers.
- Aluminum foil is the preferred choice for forming fins used in heat transfer and air conditioning equipment such as radiators, condensers, oil coolers and evaporators. A preferred choice of alloy for this application, particularly in automobile heat exchangers, is the alloy AA 3003. It has the composition shown in Table I below:
TABLE I Elements Wt. % Silicon 0.6 max Iron 0.7 max Copper 0.05-0.20% Manganese 1.0-1.5 Zinc 0.10 max - In another version of this alloy, Zn is also added to it when the fin is used in the sacrificial mode. The concentration of Zn can vary between 0.5 to 2%.
- The aluminum foil is usually in the thickness range of 0.002-0.008 in. An aluminum sheet is cold rolled to this final gauge starting from a reroll sheet that is in the gauge range of 0.04-0.3 in. The reroll sheet is produced by casting DC ingots, homogenizing at elevated temperatures, and then hot rolling to the reroll gauge. Alternatively, the reroll sheet is produced by a continuous casting process and is directly hot or warm rolled to the final reroll gauge. The continuous casting process is advantageous because it is more productive and less expensive.
- The radiators, evaporators and other heat exchangers are produced by brazing aluminum fins to the clad aluminum sheet of different shapes or forms. The brazing operation takes place at around 600° C. At this temperature aluminum fins can sag and collapse or, in some cases, affect the crushing pressure that the finished units can take at ambient and operating temperatures. The tendency to sag during brazing cycle is measured by a property that is characterized as sag resistance. It is generally accepted that higher sag resistance improves performance of the unit. Sag resistance in general is dependent upon the post braze grain size of the aluminum foil. Higher grain size produces higher sag resistance. Therefore, higher grain size (>100 micron in transverse and longitudinal directions) after annealing the sheet is preferred in automotive fin applications.
- Alloy 3003, particularly produced by continuous casting method, such as by a belt caster, yields significantly higher grain size than that produced from a corresponding hot rolled and homogenized DC material. The aluminum sheet can be used in the fin forming operation in different tempers, such as from fully hard to fully annealed.
- As stated before, alloy 3003 produced by continuous casting is an excellent choice for auto-fin applications because it yields high post braze strength and sag resistance. However, because it contains high amount of Mn and Cu, it gets easily work hardened and is therefore difficult to roll. Further, during belt casting operation it yields a highly convex profile (>0.6% crown) because it causes high temperature differences between the center and edge of the sheet. This is due to the high Mn and Fe content of the alloy. The convex profile causes problems during rolling and the slitting operations that follow after rolling. As a result, the cost of production of continuous cast 3003 is rather high.
- Previous attempts have been made to develop aluminum alloy based aluminum foils. For example, U.S. Pat. No. 4,906,534 (Bekki) discusses a method of preparing thin aluminum plates used as fins of heat exchangers from an aluminum alloy core material, comprising 0.6 to 2.0 wt % of Mn, 0.3 wt % or less of Fe, 0.05 to 0.6 wt % of Si, 0.5 to 2.0 wt % of Zn, 0.05 to 0.2 wt % of Cu, and a balance of Al. The patent additionally contemplates use of skin materials of an Al—Si system or an Al—Si—Mg system for cladding the surfaces of the core material.
- U.S. Pat. No. 4,334,935 (Morris) discloses a fine grained, formable Al—Mn alloy sheet used to make rigid foil containers. The alloy consists essentially of 1.3-2.3% Mn, up to 0.5% each of Fe, Mg, and Cu, up to 0.3% Si, up to 2.0% Zn, less than 0.1% each of Zr, Cr, and Ti, other elements up to 0.3% each and up to 1.0% total.
- U.S. Pat. No. 5,888,320 (Dorward) describes a method of producing aircraft and automobile panels. The product includes an aluminum base alloy consisting essentially of about 0.6 to 1.4 wt. % silicon, not more than about 0.5 wt. % iron, not more than about 0.6 wt. % copper, about 0.6 to 1.4 wt. % magnesium, about 0.4 to 1.4 wt. % Zn, at least one element selected from the group consisting of about 0.2 to 0.8 wt. % manganese and about 0.05 to 0.3 wt. % chromium.
- U.S. Pat. No. 5,725,695 (Ward) discloses an aluminum foil product made from an aluminum-silicon-iron aluminum alloy consisting essentially of 0.30-1.1% Si, 0.40-1.0% Fe, max 0.10% Cu, max 0.10% Mn, max 0.05% Mg, max 0.05% Cr, max 0.10% Zn, and max 0.08% Ti.
- U.S. Pat. No. 4,169,728 (Takeuchi) discloses an alloy for die-casting which consists essentially of 0.5-2.5% Zn, 1.1 to 3.0% Mg, 0.3 to 1.2% Si, 0.2 to 1.5% Fe, 0.3 to 1.2% Mn, and 0.1 to 0.3% Cu.
- The disclosures of the foregoing references are incorporated by reference into this application in their entirety.
- The disadvantages of prior methods and alloys may be overcome by the present invention, which provides an aluminum alloy foil for fins used in heat exchangers. The improved alloy composition of the present invention consists essentially of about 0.25% to about 0.6% by weight of Si, about 0.15% to about 0.50% by weight of Fe, about 0.20% to about 0.70% by weight of Mn, less than about 0.05% Cu, and less than about 0.05% Mg with the balance aluminum including unavoidable impurities. The alloy composition may also contain less than 0.10% Zn or an amount of Zn in the range from about 0.50 to 2.00% by weight.
- The invention also provides a method for making an improved aluminum foil. The method comprises providing a molten aluminum foil alloy having the composition stated in the previous paragraph. The molten alloy is continuously cast into an aluminum alloy strip from the molten aluminum alloy, and cold rolled into a final gauge of between about 0.002-0.008 inches.
- The present invention provides two new alloy compositions, one with Zn and one without Zn. The improved alloy has lower density, reduced manganese levels, and larger grain size to improve sag resistance. The preferred composition ranges for the aluminum alloy in accordance with the present invention is shown in Table II, below:
TABLE II Elements Wt. % Composition A Silicon 0.25-0.60 Iron 0.15-0.50 Manganese 0.20-0.70 Copper <0.05 Magnesium <0.05 Zinc <0.10 Composition B Silicon 0.25-0.60 Iron 0.15-0.50 Manganese 0.20-0.70 Copper <0.05 Magnesium <0.05 Zinc 0.50 to 2.00 - The alloy of the present invention has a lower density than DC cast 3003. This reduces the cost of using the alloy as fin stock in brazed heat exchangers where surface area is the determining factor.
- In a preferred embodiment of the invention, Si content ranges between about 0.3 and about 0.5%. Silicon and intermetallic particles of silicon, iron and aluminum precipitate in the sheet, making the surface hard. This reduces smut (reaction product) formation during cold rolling. Si above 0.6% is not desired because it makes the scrap less compatible with can scrap and therefore less desirable. Additionally, the amount of silicon present affects the smut generated during cold rolling. As it exceeds a critical level of 0.25%, smut generation decreases significantly. This is because of precipitation of silicon and intermetallic particles of silicon within the matrix that increase the hardness of the metal and thereby reduce the smut generated during cold rolling.
- In a preferred embodiment of the present invention, Fe content ranges between about 0.15 and about 0.35%. Low Fe helps increase grain size of the alloy after annealing because it reduces the amount of iron aluminide and iron silicon aluminide particles which pin grains and reduce grain size. Very low Fe is also undesirable as it can affect the total Fe+Mn content in the alloy. The Fe+Mn content needs to be controlled within desired limits, for reasons explained below.
- The reduced manganese levels of the alloy of the present invention accommodate a different strengthening mechanism compared to DC cast 3003. In DC cast 3003, the Mn precipitates out during the hot rolling/homogenizing steps and the precipitates harden the metal. In the present alloy, the Mn stays in solution and provides a solution strengthening effect. For the composition ranges of the present invention, solution strengthening is more effective at producing a strong final product than precipitation hardening.
- In a preferred embodiment of the invention, Mn content ranges between about 0.30 and about 0.60%. Reducing Mn from the level present in 3003 reduces the required amount of work hardening during cold rolling, and thereby helps improve cold rolling productivity. The lower limit for Mn is necessary because below this level the grain size after annealing decreases to the level at which it can affect the sag resistance.
- The optimal grain size for this application is larger than normal. Generally, small grains are preferred for a good combination of formability and strength. In this application, however, sag resistance is more important and larger grain sizes improve sag resistance.
- In a preferred embodiment of the present invention, Mn+Fe content is 0.40%-0.80%. The lower limit is necessary because below this level the shrinkage during casting increases to such an extent that it affects the heat transfer during casting and therefore results in poor surface of the reroll. Poor reroll surface can result in surface cracks in the alloy. The center to edge temperature difference during casting is correlated to the amount of Mn+Fe in the alloy. When the amount of Mn+Fe increases, the temperature difference between center and edge also increases. This results in poor profile during hot rolling, which in turn causes problems during cold rolling and slitting.
- In a preferred embodiment of the present invention, Cu content is <0.05%. Copper content of the alloy is minimized because copper results in work hardening during cold rolling.
- The alloys of the present invention are continuously cast to form an as-cast strip 30 mm (1.18 inches) or less in thickness. The alloys are preferably cast using twin belt casting, block casting or twin roll casting. In all cases the cast strip is not homogenized prior to subsequent rolling. The as-cast strip may be optionally hot or warm rolled prior to cold rolling or may be directly cold rolled. Warm rolling is carried out at a temperature low enough to avoid recrystallization.
- Interanneal during cold rolling is carried out at a gauge such that the cold work after interanneal is between 30-70%. This results in large post braze grain size. The lower limit is necessary as below this level rolling speed in the final pass can decrease significantly.
- The composition of the alloy is chosen such that it optimizes performance during casting and rolling to obtain the best combination of post braze properties. Mn and Fe are two elements that affect casting performance significantly. Aluminum shrinks during casting. To compensate for this shrinkage, the casting gap is reduced from the starting to the finishing point. However, composition of individual alloys can also affect the amount of shrinkage. Two elements that can reduce the amount of shrinkage are Mn and Fe. Reduced shrinkage results in increased heat transfer during casting and therefore yields excellent surface after rolling. Too low a shrinkage can result in increased transverse temperature difference which in turn leads to poor profile after warm rolling. The two must be optimized to give a satisfactory surface and profile.
- Another aspect of this invention is the control of post braze grain size. We have discovered that grain size increases with increasing Mn and decreases with increasing Fe. Accordingly, the two must be optimized while respecting limits for improved casting performance. The invention also provides another mechanism for controlling grain size: the alloy is cold worked before brazing to increase the post braze grain size.
- The present invention results in better rolling productivity, improved profile, and density of aluminum reduced by about one percent, which yields more feet of sheet for the same weight and thereby improves productivity for the user. There could also be uses for the present invention in other sheet or foil applications.
- It is to be understood that the invention is not limited to the features and embodiments set forth above but may be carried out in other ways without departure from its scope and spirit. Accordingly, it is intended that the present invention be limited only by the following claims.
Claims (23)
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US10/051,873 US20030133825A1 (en) | 2002-01-17 | 2002-01-17 | Composition and method of forming aluminum alloy foil |
US10/921,660 US20050019205A1 (en) | 2001-01-25 | 2004-08-19 | Composition and method of forming aluminum alloy foil |
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US10/051,873 US20030133825A1 (en) | 2002-01-17 | 2002-01-17 | Composition and method of forming aluminum alloy foil |
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US10/921,660 Abandoned US20050019205A1 (en) | 2001-01-25 | 2004-08-19 | Composition and method of forming aluminum alloy foil |
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US10/921,660 Abandoned US20050019205A1 (en) | 2001-01-25 | 2004-08-19 | Composition and method of forming aluminum alloy foil |
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US (2) | US20030133825A1 (en) |
Cited By (4)
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US20070209739A1 (en) * | 2003-12-11 | 2007-09-13 | Nippon Light Metal Company, Ltd. | Method for producing Al-Mg-Si alloy sheet excellent in bake-hardenability and hemmability |
CN102409200A (en) * | 2011-11-15 | 2012-04-11 | 镇江鼎胜铝业股份有限公司 | Container foil material and method for manufacturing container foil |
CN107002235A (en) * | 2014-12-02 | 2017-08-01 | 株式会社电装 | The manufacture method of coating structure, heat exchanger and heat exchanger |
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US6959476B2 (en) * | 2003-10-27 | 2005-11-01 | Commonwealth Industries, Inc. | Aluminum automotive drive shaft |
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JP6247225B2 (en) | 2011-12-16 | 2017-12-13 | ノベリス・インコーポレイテッドNovelis Inc. | Aluminum fin alloy and manufacturing method thereof |
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CN105568071A (en) * | 2015-12-30 | 2016-05-11 | 江苏常铝铝业股份有限公司 | High-strength high-elongation aluminum foil for air-conditioner and manufacturing method of such aluminum foil |
CN110475884A (en) | 2017-03-27 | 2019-11-19 | 古河电气工业株式会社 | Aluminum alloy materials and using the material conductive member, conductive component, spring with component, spring component, semiconductor module component, semiconductor module component, structure component and structure component |
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NO120955B (en) * | 1968-09-27 | 1970-12-28 | Ver Leichtmetallwerke Gmbh | |
US4169728A (en) * | 1978-02-09 | 1979-10-02 | Mitsubishi Kinzoku Kabushiki Kaisha | Corrosion resistant bright aluminum alloy for die-casting |
US4334935A (en) * | 1980-04-28 | 1982-06-15 | Alcan Research And Development Limited | Production of aluminum alloy sheet |
US4511632A (en) * | 1982-07-19 | 1985-04-16 | Mitsubishi Aluminum Kabushiki Kaisha | Aluminum alloy clad sheet having excellent high-temperature sagging resistance and thermal conductivity |
KR920006554B1 (en) * | 1986-06-04 | 1992-08-08 | 후루까와 아루미니우무 고오교오 가부시끼가이샤 | Composite aluminum thin plates for brazing and method for preparing same |
JP2564012B2 (en) * | 1989-11-27 | 1996-12-18 | 大同メタル工業 株式会社 | Aluminum-based alloy bearing with reinforced intermediate adhesive layer |
US5466312A (en) * | 1993-01-11 | 1995-11-14 | Reynolds Metals Company | Method for making aluminum foil and cast strip stock for aluminum foilmaking and products therefrom |
AU5664796A (en) * | 1995-05-11 | 1996-11-29 | Kaiser Aluminum & Chemical Corporation | Improved damage tolerant aluminum 6xxx alloy |
US5725695A (en) * | 1996-03-26 | 1998-03-10 | Reynolds Metals Company | Method of making aluminum alloy foil and product therefrom |
US5906689A (en) * | 1996-06-06 | 1999-05-25 | Reynolds Metals Company | Corrosion resistant aluminum alloy |
US5976278A (en) * | 1997-10-03 | 1999-11-02 | Reynolds Metals Company | Corrosion resistant, drawable and bendable aluminum alloy, process of making aluminum alloy article and article |
-
2002
- 2002-01-17 US US10/051,873 patent/US20030133825A1/en not_active Abandoned
-
2004
- 2004-08-19 US US10/921,660 patent/US20050019205A1/en not_active Abandoned
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US20070209739A1 (en) * | 2003-12-11 | 2007-09-13 | Nippon Light Metal Company, Ltd. | Method for producing Al-Mg-Si alloy sheet excellent in bake-hardenability and hemmability |
CN102409200A (en) * | 2011-11-15 | 2012-04-11 | 镇江鼎胜铝业股份有限公司 | Container foil material and method for manufacturing container foil |
CN107002235A (en) * | 2014-12-02 | 2017-08-01 | 株式会社电装 | The manufacture method of coating structure, heat exchanger and heat exchanger |
US20170327943A1 (en) * | 2014-12-02 | 2017-11-16 | Denso Corporation | Coating structure, heat exchanger, and method for manufacturing heat exchanger |
CN109837428A (en) * | 2017-11-28 | 2019-06-04 | 丹阳市延陵镇优越合金厂 | A kind of automotive hub aluminum alloy materials |
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