WO2013065760A1 - 成形加工用アルミニウム合金クラッド材 - Google Patents
成形加工用アルミニウム合金クラッド材 Download PDFInfo
- Publication number
- WO2013065760A1 WO2013065760A1 PCT/JP2012/078241 JP2012078241W WO2013065760A1 WO 2013065760 A1 WO2013065760 A1 WO 2013065760A1 JP 2012078241 W JP2012078241 W JP 2012078241W WO 2013065760 A1 WO2013065760 A1 WO 2013065760A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- mass
- aluminum alloy
- insert
- temperature
- clad
- Prior art date
Links
Images
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B15/00—Layered products comprising a layer of metal
- B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
- B32B15/016—Layered products comprising a layer of metal all layers being exclusively metallic all layers being formed of aluminium or aluminium alloys
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/24—Selection of soldering or welding materials proper
- B23K35/28—Selection of soldering or welding materials proper with the principal constituent melting at less than 950 degrees C
- B23K35/286—Al as the principal 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
- C22C21/003—Alloys based on aluminium containing at least 2.6% of one or more of the elements: tin, lead, antimony, bismuth, cadmium, and titanium
-
- 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
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/10—Alloys based on aluminium with zinc 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
- C22C21/12—Alloys based on aluminium with copper 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
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/14—Alloys based on aluminium with copper as the next major constituent with silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/16—Alloys based on aluminium with copper as the next major constituent with magnesium
-
- 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
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/18—Alloys based on aluminium with copper as the next major constituent with zinc
-
- 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
-
- 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
- C22F1/057—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 copper as the next major constituent
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
- Y10T428/12736—Al-base component
- Y10T428/12764—Next to Al-base component
Definitions
- This invention can be used as a material for parts and parts of various automobiles such as automobile body seats and body panels, ships and aircraft, building materials, structural materials, various other machinery and equipment, home appliances and parts thereof, and the like.
- the present invention relates to an aluminum alloy clad material for forming used by being subjected to paint baking.
- the body sheet of an automobile is used after being subjected to press processing, so that it has excellent molding processability, and is used after being subjected to hem bending to join and integrate the outer panel and the inner panel.
- the hemmability is required to be excellent among the moldability.
- it is usually used after painting and baking when emphasizing strength in the balance between formability and strength, high strength can be obtained after painting and baking, and conversely, forming properties are important.
- an aluminum alloy plate for an automobile body sheet is required to have sufficient corrosion resistance (intergranular corrosion resistance, yarn rust resistance).
- an aging Al—Mg—Si alloy or an Al—Mg—Si—Cu alloy has been mainly used.
- aging Al-Mg-Si alloys and Al-Mg-Si-Cu alloys have the advantage that they are aged by heating during paint baking and the strength after paint baking is increased. Due to the advantages such as being difficult to generate, it is becoming the mainstream of automobile body sheet materials.
- press formability and heme workability are inferior to those of Al—Mg alloys, various studies have been made to improve both. For example, many technologies have been proposed such as control of the amount of Mg and Si, which are main elements, addition of elements such as Cu, control of second phase particles, control of crystal grain size, control of texture, etc. Yes.
- Patent Document 1 the use of a clad material obtained by clad a plate material having different characteristics has been proposed.
- the present invention has been made in view of the above circumstances, and an object of the present invention is to provide an aluminum alloy clad material for forming that has high mass productivity and is particularly excellent in formability, bake hardenability, and corrosion resistance. .
- the aluminum alloy clad material for forming according to the present invention is: Mg: 0.2-1.5% (mass%, the same shall apply hereinafter), Si: 0.2-2.5%, Cu: 0.2-3.0%, the balance from Al and inevitable impurities
- An aluminum alloy core material It is clad on one or both sides of the core material, and the thickness is 3 to 30% of the total thickness per side, Mg: 0.2 to 1.5%, Si: 0.2 to 2.0
- the aluminum alloy skin material the balance of which is composed of Al and inevitable impurities
- the core material and / or the skin material are either Mn: 0.03 to 1.0%, Cr: 0.01 to 0.40%, Zr: 0.01 to 0.40%, V: One or more of 0.01 to 0.40%, Fe: 0.03 to 1.0%, Zn: 0.01 to 2.5%, Ti: 0.005 to 0.30% contains, It is good as well.
- the amount of Mg contained in the insert material is 0.05 to 2.0 mass%
- the amount of Si contained in the insert material mass%, the same applies hereinafter
- the amount of Cu mass%, the same applies hereinafter
- the following formulas (4) to (6) are simultaneously satisfied: It is good as well.
- the solidus temperature of the insert material is lower than the solidus temperature of the core material and the solidus temperature of the skin material, It is good as well.
- the thickness of the insert material when the core material, the insert material and the skin material are joined by high-temperature heat treatment is 10 ⁇ m or more. It is good as well.
- FIG. 5 is a phase diagram of an Al—Si alloy showing the relationship between the composition of the insert material and the temperature.
- (A)-(d) is a schematic diagram which shows the production
- the core material and the skin material used for the aluminum alloy clad material of the present invention may be basically an Al—Mg—Si alloy or an Al—Mg—Si—Cu alloy, and the specific component composition thereof is Although it may be adjusted as appropriate according to the required performance level, it is preferable to adjust the component composition as in this embodiment when emphasizing moldability, bake hardenability and corrosion resistance.
- the reason for limiting the component composition of the material alloy will be described.
- Mg is an alloy element that is a basic alloy of the system targeted by the present invention, and contributes to strength improvement in cooperation with Si. If the amount of Mg is less than 0.20%, G. contributes to strength improvement by precipitation hardening during baking. P. (Guinier-Preston) The amount of formation in the zone is small, so sufficient strength improvement cannot be obtained. On the other hand, if it exceeds 1.5 mass%, coarse Mg-Si based intermetallic compounds are produced and press molding processing is performed. Inhibits sex. Therefore, the Mg amount is set in the range of 0.2 mass% to 1.5 mass%.
- Si is also an alloy element that is fundamental in the alloy of the present invention, and contributes to strength improvement in cooperation with Mg.
- Si is produced as a crystallized product of metal Si during casting, and the periphery of the metal Si particles is deformed by processing and becomes a recrystallization nucleus generation site during solution treatment. It also contributes to If the amount of Si is less than 0.20 mass%, the above effects cannot be obtained sufficiently. On the other hand, if it exceeds 2.5 mass%, coarse Si particles and coarse Mg-Si based intermetallic compounds are produced, and press molding processing is performed. It causes a decline in sex. Therefore, the Si amount is set in the range of 0.20 mass% to 2.5 mass%.
- Cu is an element that may be added to improve strength and formability, but if the amount is less than 0.20 mass%, the above effect cannot be obtained sufficiently, while if it exceeds 3.0 mass%. The strength becomes too high and the press workability deteriorates. Therefore, the Cu content is regulated within the range of 0.20 mass% to 3.0 mass%.
- Mn, Cr, Zr, V, Fe, Zn, Ti may be added depending on the purpose. These elements are effective for improving strength, crystal grain refinement, aging (bake hardenability), and surface treatment.
- Mn, Cr, Zr, V Mn, Cr, Zr, and V are elements that are effective in improving the strength, refining crystal grains, and stabilizing the structure.
- Mn content is 0.03 mass% or more, or the Cr, Zr, and V contents are each 0.01 mass% or more, the above effects can be sufficiently obtained.
- Mn content is 1.0 mass% or less, or the Cr, Zr, and V contents are each 0.40 mass% or less, the above-described effects are sufficiently maintained, and a large number of intermetallic compounds. It is possible to suppress an adverse effect on formability due to the generation. Therefore, Mn is preferably in the range of 0.03 mass% to 1.0 mass%, and Cr, Zr, and V are each preferably in the range of 0.01 mass% to 0.40 mass%.
- Fe is also an element effective for strength improvement and crystal grain refinement, and a sufficient effect can be obtained when its content is 0.03 mass% or more, and by 1.0 mass% or less, A decrease in press formability due to the generation of a large number of intermetallic compounds can be suppressed. Therefore, the amount of Fe is preferably in the range of 0.03 mass% to 1.0 mass%.
- Zn is an element that contributes to strength improvement through aging improvement and is effective in improving surface treatment properties, and the above effect can be sufficiently obtained when the amount of Zn added is 0.01 mass% or more. , The lowering of moldability can be suppressed by being 2.5 mass% or less. Therefore, the Zn content is preferably in the range of 0.01 mass% to 2.5 mass%.
- Ti is effective for improving the strength of the final plate, preventing rough skin, and improving ridging resistance through the refinement of the ingot structure. Therefore, Ti is added for refinement of the ingot structure, and its content is 0.005 mass%. By being above, a sufficient effect can be obtained, and by being 0.30 mass% or less, the formation of coarse crystallized substances can be suppressed while maintaining the effect of adding Ti. Therefore, the Ti amount is preferably in the range of 0.005 mass% to 0.30 mass%.
- B may be added simultaneously with Ti, and by adding B together with Ti, the effect of refining and stabilizing the ingot structure becomes more prominent. The addition of B is preferably acceptable.
- Al and inevitable impurities may be used.
- the skin material is strongly required to have corrosion resistance (intergranular corrosion resistance, yarn rust resistance) and hemmability, and is required to have a minimum surface hardness as a body sheet material for automobiles.
- the alloy composition range of the skin material is the same as that of the core material described above, except that Si is regulated to 2.0 mass% or less and Cu is regulated to 0.1 mass% or less.
- Si is regulated to 2.0 mass% or less
- Cu is regulated to 0.1 mass% or less.
- Si is also an alloy element that is fundamental in the alloy of the present invention, and contributes to strength improvement in cooperation with Mg.
- Si is produced as a crystallized product of metal Si at the time of casting, and the periphery of the metal Si particles is deformed by processing and becomes a recrystallization nucleus generation site during solution treatment. It also contributes to If the amount of Si is less than 0.20 mass%, the above effects cannot be obtained sufficiently. On the other hand, if it exceeds 2.0 mass%, coarse Si particles and coarse Mg-Si intermetallic compounds are produced, resulting in hemmability. Incurs a decline. Therefore, the Si amount is set in the range of 0.20 mass% to 2.0 mass%.
- Cu is an element that may be added to improve strength and formability, but if the amount exceeds 0.1 mass%, corrosion resistance (intergranular corrosion resistance, yarn rust resistance) deteriorates.
- the Cu content is restricted to 0.1 mass% or less.
- the ratio of the thickness of the skin material to the total thickness is 3 to 30% on one side, and clad on one side or both sides as necessary. If the cladding ratio is less than the lower limit of this range, the performance that the skin should exhibit, such as corrosion resistance and hem workability, will not be sufficiently exhibited, and if it exceeds the upper limit, it will be representative of press moldability, bake hardenability, etc. The performance that should be exhibited by the core material is greatly deteriorated.
- the core material and the insert material, and the skin material and the insert material are joined metallically by a joining method that uses a slight liquid phase generated inside the insert material by applying high-temperature heating to prevent interfacial delamination during rolling. is doing.
- rolling is completed without causing interfacial delamination, so that a tightly bonded clad material can be reliably and stably obtained on a mass production scale without causing poor adhesion at the bonding interface.
- the insertion of the insert material is useful for preventing the adhesion failure even in the alloy types for which the cladding technology is established. It is also effective to improve the clad rate or to achieve a cladding ratio that has been difficult with the conventional method.
- the role required of the aluminum alloy insert material is to improve the adhesion failure.
- an Al—Mg—Si alloy or an Al—Mg—Si—Cu alloy is used as a material for the core material and the skin material.
- the thickness of the insert material when joining the insert material, the core material, and the skin material by high-temperature heat treatment is 10 ⁇ m or more.
- the thickness of the insert material is preferably 50 ⁇ m or more, and even more preferably 100 ⁇ m or more, it becomes possible to prevent the bonding interface peeling more reliably.
- the preferable thickness of the insert material does not change depending on the thickness of the core material and the skin material, and the maximum thickness of the insert material is particularly limited. It is not a thing.
- it is desirable that the presence of the insert material does not affect other characteristics such as press molding processability, hem processability, bake hardenability, corrosion resistance, and surface quality.
- the ratio of the insert material to the total plate thickness is 1% or less on one side.
- the material properties of the insert material do not hinder the effect of the core material or skin material.
- the lower limit of the ratio of the insert material is not particularly limited. From the above, the upper and lower limits of the thickness of the insert material are determined for the different purposes described above, the lower limit is a preferred thickness during high-temperature heat treatment, and the upper limit is a preferred ratio with respect to the total thickness. It is more preferable to set in such a manner.
- FIG. 1 schematically shows a phase diagram of an Al—Si alloy which is a typical binary eutectic alloy.
- the composition of the insert material is the Si concentration c1
- the generation of the liquid phase starts at a temperature T1 near the eutectic temperature (solidus temperature) Te.
- T1 near the eutectic temperature (solidus temperature) Te.
- Te eutectic temperature
- FIG. 2A crystal precipitates are distributed in the matrix divided by the grain boundaries.
- FIG. 2B there are many precipitates, or crystal grain boundaries having a high solid solution element concentration are melted due to segregation at the grain boundaries to form a liquid phase.
- the periphery of the Si crystal precipitate particles and intermetallic compounds which are the main additive element components dispersed in the matrix of the aluminum alloy, melts into a spherical shape to form a liquid phase. Further, as shown in FIG. 2 (d), this spherical liquid phase generated in the matrix is re-dissolved in the matrix with the passage of time and temperature due to the interfacial energy, and the grain boundary and the surface are diffused by the solid phase diffusion. Move to.
- the liquid phase amount increases from the state diagram.
- the Si concentration of the insert material is c2
- generation of a liquid phase starts in the vicinity of the solidus temperature Ts2 in the same manner as c1
- the temperature rises to T3 The liquid phase amount increases.
- the liquid phase generated on the surface of the insert material during bonding fills the gap with the core material or skin material, and then the liquid phase near the bonding interface moves to the core material or skin material.
- the solid phase ⁇ phase crystal grains of the insert material in contact with the bonding interface grows toward the inside of the core material or the skin material, whereby metal bonding is performed.
- the joining method according to the present invention utilizes a liquid phase generated by partial melting inside the insert material.
- the thickness of the insert material in the joining of the present invention is within the above-described range, it is good if the temperature is equal to or higher than the solidus temperature determined from the endothermic peak by differential thermal analysis (DTA). Can be obtained.
- the mass ratio of the liquid phase is preferably 5% or more, more preferably 10% or more. Further, even if the insert material is completely dissolved, there is no problem in the present invention, but it is not necessary.
- Al-Mg-Si-based alloys and Al-Mg-Si-Cu-based alloys used as core materials or skin materials may cause eutectic melting with performance deterioration at temperatures exceeding 590 ° C.
- the high-temperature heat treatment performed prior to is usually performed at 590 ° C. or lower. Therefore, the solidus temperature of the aluminum alloy insert material needs to be 590 ° C. or lower. Since a slight liquid phase may be generated, the high-temperature heating holding time may be 5 min or more and 48 hours or less. Furthermore, from the viewpoint of energy saving, the lower the temperature of the high-temperature heat treatment, the better. Therefore, the solidus temperature of the insert material is preferably 570 ° C. or lower.
- the solidus temperature may be 590 ° C. or lower. Therefore, in order to avoid the performance deterioration of the clad material, the high temperature heat treatment is performed on the core material or the skin material. It is preferable to carry out below the solidus temperature. On the other hand, in order to prevent poor adhesion, it is necessary to heat at a temperature higher than the solidus temperature of the insert material as described above. Therefore, the solidus temperature of the insert material is different from that of the core material and the skin material. It is more preferable that the temperature is lower than the temperature.
- the aluminum alloy insert material used for the aluminum alloy clad material of the present invention may have a solidus temperature of 590 ° C. or lower, and its specific composition is not particularly limited, but considers productivity and the like. Accordingly, it is preferable to use an Al—Cu based alloy, an Al—Si based alloy, or an Al—Cu—Si based alloy.
- both Cu and Si are elements that have the effect of greatly lowering the solidus temperature when added to aluminum.
- the present inventors investigated a composition range in which a clad material with good performance without an adhesion failure can be obtained when an Al—Cu, Al—Si, or Al—Cu—Si alloy is used as an insert material. It has been found that it is more preferable that the following expressions (1) to (3) are simultaneously satisfied when the Si amount is x and the Cu amount is y.
- the upper limit of Cu and Si is not particularly limited in order to exhibit the function of the insert material required in the present invention, but when considering productivity such as castability and rollability, Cu is 10 mass. % Or less, and Si is more preferably 15 mass% or less.
- Mg is another element that has an effect of greatly reducing the solidus temperature.
- Mg may be added to the Al—Cu based, Al—Si based, or Al—Cu—Si based alloy as necessary.
- the Mg content is 0.05 mass% or more, the effect of lowering the solidus temperature can be sufficiently obtained, and when it is 2.0 mass% or less, the extreme surface of the insert material during high-temperature heating
- the amount of Mg is preferably in the range of 0.05 mass% to 2.0 mass% because inhibition of bonding due to the formation of a thick oxide film on the surface is suppressed. It should be noted that even if the aforementioned Al—Cu, Al—Si, or Al—Cu—Si alloy contains an Mg amount less than the lower limit specified here, the function of the insert material is not impaired.
- the inventors of the present invention have a composition range in which a clad material having no poor adhesion can be obtained when an Al—Cu—Mg, Al—Si—Mg, or Al—Cu—Si—Mg alloy is used as an insert material. As a result of the same investigation, it was found that it is even more preferable that the following expressions (4) to (6) are simultaneously satisfied when the Si amount is x and the Cu amount is y.
- one or more elements other than the above-described Cu, Si, Mg for example, Fe, Mn, Sn, Zn, Cr, Zr, Ti, V, B, Ni, Sc, or the like, as long as the function of the insert material is not impaired. It is permissible to contain two or more kinds. More specifically, Fe and Mn are 3.0 mass% or less, Sn and Zn are 10.0 mass% or less, and Cr, Zr, Ti, V, B, Ni, and Sc are 1.0 mass% or less. You may add according to the objectives, such as a castability and a rollability improvement. Similarly, inevitable impurities are allowed to be contained.
- the core material, the skin material, and the insert material constituting the aluminum alloy clad material in the present invention may be manufactured according to a conventional method.
- an aluminum alloy having the component composition as described above is first melted in accordance with a conventional method, and a normal casting method such as a continuous casting method or a semi-continuous casting method (DC casting method) is appropriately selected and cast.
- a normal casting method such as a continuous casting method or a semi-continuous casting method (DC casting method) is appropriately selected and cast.
- a normal casting method such as a continuous casting method or a semi-continuous casting method (DC casting method) is appropriately selected and cast.
- a normal casting method such as a continuous casting method or a semi-continuous casting method (DC casting method)
- a predetermined plate thickness may be obtained by mechanical cutting or a combination of rolling and mechanical cutting.
- the core material, skin material, and insert material having a predetermined plate thickness are laminated so that the insert material enters between the core material and the skin material.
- the skin material and the insert material may be laminated on one side or both sides as necessary.
- a flux may be applied to the bonded portion as necessary.
- the bonding interface is sufficiently peeled during rolling without applying the flux. Can be prevented.
- the laminated core material, skin material, and insert material may be fixed by welding. Welding may be carried out according to a conventional method.
- the core material, the skin material, and the insert material are fixed by a fixing device such as an iron band.
- a fixing device such as an iron band.
- high-temperature heating is performed for bonding using the liquid phase of the insert material, but the Al—Mg—Si system or Al—Mg—Si—Cu constituting the core material and the skin material is applied. It is efficient to carry out in combination with a homogenization treatment that is usually performed in a system alloy.
- the temperature in the case of performing the high-temperature heat treatment that also serves as the homogenization treatment is at least the solidus temperature of the insert material, and as described above, 590 ° C. or less, preferably 570 ° C., depending on the solidus temperature of the insert material.
- the holding time is preferably 5 min or more and 48 hours or less. When the holding time is 5 min or more, good bonding can be obtained, and when the holding time is 48 hours or less, the heat treatment can be performed economically while maintaining the above effect.
- the high-temperature heat treatment can be sufficiently performed in an oxidizing atmosphere such as an atmospheric furnace, but in order to prevent interfacial peeling more reliably, in a non-oxidizing atmosphere that does not contain an oxidizing gas such as oxygen. More preferably.
- Non-oxidizing atmosphere includes vacuum, inert atmosphere and reducing atmosphere.
- Inert atmosphere refers to an atmosphere filled with an inert gas such as nitrogen, argon, helium, neon, etc., and reducing atmosphere.
- the term “atmosphere” refers to an atmosphere in which a reducing gas such as hydrogen, carbon monoxide, or ammonia exists.
- the lower temperature limit may be 480 ° C. or higher, more preferably 490 ° C. or higher.
- hot rolling and / or cold rolling in accordance with normal conditions or both are performed to obtain a clad material having a predetermined plate thickness.
- the material reaching temperature is 500 ° C. or more and 590 ° C. or less, and the holding at the material reaching temperature is within 5 minutes to no holding.
- the intermediate temperature between the solidus temperature and the liquidus temperature of the insert material is Tc
- severe melting of the insert layer does not occur by heating to a temperature range lower than Tc, and deterioration of the material characteristics is caused. Since it can be suppressed, the material arrival temperature is more preferably less than Tc even within the above range.
- the upper limit of the material reaching temperature when performing the intermediate annealing as required is also 590 ° C. or less and less than Tc.
- the solution treatment time is not particularly limited, but is usually 5 minutes or less, so that the solution treatment can be performed economically while maintaining the solution effect, and the coarsening of crystal grains is suppressed. Therefore, the solution treatment time is preferably within 5 minutes.
- the cooling rate is 100 ° C./min or higher and the temperature range is 150 ° C. or lower. It is preferable to cool (quenify).
- the cooling rate after the solution treatment is 100 ° C./min or more, press formability, particularly bending workability can be maintained high, and at the same time, a decrease in bake hardenability is suppressed, which is sufficient during paint baking. Can improve the strength.
- a stabilization treatment may be performed as necessary. That is, in the case where bake hardenability (BH property) is more important than moldability, after solution treatment, after cooling (quenching) to a temperature range of 50 ° C. or more and less than 150 ° C. at a cooling rate of 100 ° C./min or more. More preferably, the stabilization treatment is performed within this temperature range (less than 50 to 150 ° C.) before the temperature drops to a temperature range below 50 ° C. (room temperature).
- the holding time in the temperature range of 50 to 150 ° C. in this stabilization treatment is not particularly limited, but it is usually desirable to hold it for 1 hour or longer, and cooling (slow cooling) over 1 hour or more within that temperature range. You may do it.
- cooling is performed to a temperature range of less than 50 ° C. in the cooling process after solution treatment without performing stabilization treatment. It is more preferable to leave in the temperature range of ° C.
- the alloy codes A to F and M to Q used as the core material or the skin material and the alloy codes G to L and R to V used as comparative examples with the composition shown in Table 1, and Tables 2, 3 Alloy codes 3-5, 7-29, 31-57 used as insert material materials and alloy codes 1, 2, 6, 30 which are comparative examples of insert materials are shown in accordance with conventional methods. It was melted and cast into a slab by a DC casting method.
- Table 1 “comparative examples” are indicated in the table for alloys having a component composition outside the scope of the present invention.
- the insert material having a solidus temperature outside the scope of the present invention is indicated as “Comparative Example” in the table.
- the core material is machine-cut and the skin material is hot so that the clad rate, the thickness of the insert material during high-temperature heat treatment, and the thickness of the insert material are as shown in Tables 4-7.
- the core material, skin material, and insert material are placed between the core material and the skin material according to the combinations shown in Tables 4 to 7. Laminated.
- the skin material and the insert material are used as the core material.
- the clad rate and the ratio of the thickness of the insert material are the values for one side of both the double-sided clad material and single-sided clad material.
- high temperature heat treatment was performed for 2 hours at the temperatures shown in Tables 4 to 7 in order to perform bonding using the liquid phase of the insert material.
- high-temperature heat treatment is performed in a nitrogen atmosphere that is a non-oxidizing atmosphere
- 017 and 079 are in a vacuum that is also a non-oxidizing atmosphere, and otherwise the atmosphere is an oxidizing atmosphere. Carried out.
- production hot rolling was performed to obtain a plate having a thickness of 3.0 mm.
- Production codes 016, 017, 078, and 079 subjected to high-temperature heat treatment in a non-oxidizing atmosphere are the maximum rolling ratios in one pass.
- the hot-rolled sheet was subjected to intermediate annealing using a glass furnace at 530 ° C. for 5 minutes, forced air cooling to room temperature with a fan, and then cold-rolled to a thickness of 1.0 mm.
- the obtained cold-rolled sheet was subjected to a solution treatment at 530 ° C. for 1 minute in a glass stone furnace, forced air-cooled with a fan to near room temperature, immediately subjected to a preliminary aging treatment at 80 ° C. for 5 hours, and an aluminum alloy A clad material (test material) was produced.
- production codes 120 to 124 are single alloy specimens, and production codes 120 to 126 did not use insert materials.
- a JIS No. 5 test piece was cut out in a direction parallel to the rolling direction, and 0.2% proof stress before baking and elongation before baking were evaluated by a tensile test. Further, after 2% stretching, 0.2% proof stress was also measured after baking after baking at 170 ° C. for 20 minutes using an oil bath.
- a Vickers hardness test was performed on the post-baked plate material that was subjected to the paint baking process as described above.
- the Vickers hardness test was performed based on JIS Z2244, the test force was 0.015 Kgf, and the hardness measurement position was the rolled surface of the skin material side surface.
- the thickness of the skin material which is a test object layer was less than 1.5 times the diagonal length of a hollow (indentation), it describes as a reference value.
- a JIS No. 5 test piece was cut out in a direction parallel to the rolling direction, stretched 5%, then bent 180 ° with a bending radius R of 0.5 mm and cracked with a loupe.
- the presence or absence of rough skin (hem workability) was evaluated.
- the single-sided clad material was bent so that the surface on the skin side would be the outside of the bend.
- ⁇ indicates that neither cracks nor rough skin has occurred
- ⁇ indicates that no cracks have occurred
- ⁇ indicates that cracks that do not penetrate the plate thickness have occurred
- X indicates the plate thickness. It shows the occurrence of cracks penetrating.
- the maximum yarn rust length was measured by measuring the corrosion length in the direction perpendicular to the crosscut wrinkles.
- L ⁇ 1.5 is ⁇
- 1.5 ⁇ L ⁇ 3.0 is ⁇
- 3.0 ⁇ L was evaluated as x.
- the peak height of the endothermic peaks generated when the test piece cut out from each of the test materials described above was heated from 450 ° C. to 700 ° C. at 5 ° C./min was determined (reference substance).
- the starting point of a large endothermic peak that is 5 ⁇ V or higher (the electromotive force of a thermocouple showing a temperature difference with respect to ⁇ V) was taken as the solidus temperature.
- the starting point of the endothermic peak at the lowest temperature may be the solidus temperature.
- the starting point was defined as a point deviating from the straight line when the straight line portion extending from the target endothermic peak to the high temperature side was drawn to the high temperature side.
- Tables 4 to 6 show the results of various evaluations under conditions within the scope of the present invention. As is clear from the results shown in the table, the production codes 001 to 119 of the present invention material had better elongation before baking and hemmability, and other characteristics were also good.
- Table 7 shows the test results of comparative examples that are outside the scope of the present invention.
- materials that are not used and items that are not evaluated are indicated as “-” in the table.
- the production codes 125 to 132 the clad interface was peeled off during rolling, or many blisters were generated after intermediate annealing, and the material evaluation was not achieved.
- the production code 144 will be described later as a reference example.
- the single alloy material (manufacturing codes 120 to 124) was inferior in terms of performance balance compared to the test materials according to the present invention (manufacturing codes 001 to 119).
- the material of the present invention has both a high level of elongation before baking and corrosion resistance compared to a single alloy material, while having practical strength and hemmability as a material for forming.
- the production code 133 in which the ratio of the skin material to the total plate thickness is less than the specified range the hem workability and the corrosion resistance of the present invention material (for example, the production code 028) composed of the same core material and skin material combination is improved. A decrease was observed.
- the production code 134 in which the ratio of the skin material to the total plate thickness exceeds the specified range is 0.2% before baking as compared with the present invention material (for example, the production code 067) composed of the same core material and skin material combination. The yield strength and the 0.2% yield strength after baking were greatly reduced.
- Production codes 016, 017, 078, and 079 in the present invention are for verifying the effect of the high-temperature heat treatment in the non-oxidizing atmosphere, and the high-temperature heat treatment was performed in the oxidizing atmosphere (in the air). It was found that the rolling rate per pass can be further increased compared to the present invention material.
- the clad plate material of production code 140 to 142 whose composition of the skin material deviated from the upper limit defined in the present invention, the hemming property or the corrosion resistance was deteriorated as compared with the example of the present invention.
- the post-baking surface hardness was deteriorated as compared with the present invention example.
- the manufacturing code 144 has a melting point much higher than that of the insert material in order to verify the technology for joining the insert material and the core material or the insert material and the skin material using the liquid phase of the insert material used in the present invention. Although it was combined with high pure aluminum and subjected to high temperature heat treatment, good bonding was confirmed after high temperature heating as in the case of the material of the present invention. For the production code 144, no evaluation was performed other than the verification of the bonding property.
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)
- Pressure Welding/Diffusion-Bonding (AREA)
- Laminated Bodies (AREA)
- Metal Rolling (AREA)
Abstract
Description
Mg:0.2~1.5%(mass%、以下同じ)、Si:0.2~2.5%、Cu:0.2~3.0%を含有し、残部がAlおよび不可避不純物からなるアルミニウム合金の芯材と、
前記芯材の片面又は両面にクラッドされており、厚さが1面につき全板厚の3~30%であり、Mg:0.2~1.5%、Si:0.2~2.0%を含むとともにCuを0.1%以下に規制した組成を有し、残部がAlおよび不可避不純物からなるアルミニウム合金の皮材と、
前記芯材と前記皮材との間に介在しており、590℃以下の固相線温度を有するアルミニウム合金のインサート材と、を備える、
ことを特徴とする。
こととしてもよい。
こととしてもよい。
x≧0 ・・・(1)
y≧0 ・・・(2)
y≧-15.3x+2.3 ・・・(3)
該インサート材に含有されるSi量(mass%、以下同じ)をx、Cu量(mass%、以下同じ)をyとした際に以下の(4)~(6)式を同時に満足する、
こととしてもよい。
x≧0 ・・・(4)
y≧0 ・・・(5)
y≧-x+0.01 ・・・(6)
こととしてもよい。
こととしてもよい。
Mg:
Mgはこの発明で対象としている系の合金で基本となる合金元素であって、Siと共同して強度向上に寄与する。Mg量が0.20%未満では塗装焼付時に析出硬化によって強度向上に寄与するG.P.(Guinier-Preston)ゾーンの生成量が少なくなるため、充分な強度向上が得られず、一方、1.5mass%を越えれば、粗大なMg-Si系の金属間化合物が生成され、プレス成形加工性を阻害する。したがって、Mg量は0.2mass%~1.5mass%の範囲内とする。
Siもこの発明の系の合金で基本となる合金元素であって、Mgと共同して強度向上に寄与する。またSiは、鋳造時に金属Siの晶出物として生成され、その金属Si粒子の周囲が加工によって変形されて、溶体化処理の際に再結晶核の生成サイトとなるため、再結晶組織の微細化にも寄与する。Si量が0.20mass%未満では上記の効果が充分に得られず、一方、2.5mass%を越えれば粗大なSi粒子や粗大なMg-Si系の金属間化合物が生じて、プレス成形加工性の低下を招く。したがって、Si量は0.20mass%~2.5mass%の範囲内とする。
Cuは強度向上及び成形性向上のために添加されることがある元素であるが、その量が0.20mass%未満では上記の効果が十分に得られず、一方、3.0mass%を越えれば強度が高くなり過ぎてプレス成形加工性が劣化する。したがって、Cuの含有量は0.20mass%~3.0mass%の範囲内に規制する。
Mn、Cr、Zr、Vは、強度向上と結晶粒の微細化及び組織の安定化に効果がある元素である。Mnの含有量が0.03mass%以上、もしくはCr、Zr、Vの含有量がそれぞれ0.01mass%以上であることによって、上記の効果を充分に得ることができる。また、Mnの含有量が1.0mass%以下、あるいはCr、Zr、Vの含有量がそれぞれ0.40mass%以下であることによって、上記の効果が十分に維持されつつ、多数の金属間化合物の生成による成形性への悪影響を抑制することができる。したがって、Mnは、好ましくは、0.03mass%~1.0mass%の範囲内、Cr、Zr、Vはそれぞれ、好ましくは、0.01mass%~0.40mass%の範囲内である。
Feも強度向上と結晶粒微細化に有効な元素であり、その含有量が0.03mass%以上であることによって充分な効果を得ることができ、また、1.0mass%以下であることによって、多数の金属間化合物の生成によるプレス成形性の低下を抑制することができる。したがって、Fe量は、好ましくは、0.03mass%~1.0mass%の範囲内である。
Znは時効性向上を通じて強度向上に寄与するとともに表面処理性の向上に有効な元素であり、Znの添加量が0.01mass%以上であることによって上記の効果を充分に得ることができ、また、2.5mass%以下であることによって成形性の低下を抑制することができる。したがって、Zn量は、好ましくは、0.01mass%~2.5mass%の範囲内である。
Tiは、鋳塊組織の微細化を通じて最終板の強度向上、肌荒れ防止、耐リジング性向上に効果があることから、鋳塊組織の微細化のために添加され、その含有量が0.005mass%以上であることによって充分な効果を得ることができ、また、0.30mass%以下であることによって、Ti添加の効果を維持しつつ、粗大な晶出物の生成を抑制することができる。したがって、Ti量は、好ましくは、0.005mass%~0.30mass%の範囲内である。なおTiと同時にBを添加することもあり、BをTiとともに添加することによって、鋳塊組織の微細化と安定化の効果が一層顕著となるが、この発明の場合も、Tiとともに500ppm以下のBを添加することが好ましくは許容される。
次に、皮材の成分組成の限定理由について以下に述べる。皮材は耐食性(耐粒界腐食性、耐糸錆性)、ヘム加工性に強く影響し、また自動車のボディシート材として最低限の表面硬さを有していることが要求される。皮材の合金組成範囲は、Siを2.0mass%以下、Cuを0.1mass%以下に規制する以外は、前述した芯材と同様である。以下、SiおよびCuの限定理由について説明する。
Siもこの発明の系の合金で基本となる合金元素であって、Mgと共同して強度向上に寄与する。またSiは、鋳造時に金属Siの晶出物として生成され、その金属Si粒子の周囲が加工によって変形されて、溶体化処理の際に再結晶核の生成サイトとなるため、再結晶組織の微細化にも寄与する。Si量が0.20mass%未満では上記の効果が充分に得られず、一方2.0mass%を越えれば粗大なSi粒子や粗大なMg-Si系の金属間化合物が生じて、ヘム加工性の低下を招く。したがって、Si量は0.20mass%~2.0mass%の範囲内とする。
Cuは強度向上及び成形性向上のために添加されることがある元素であるが、その量が0.1mass%を超えれば耐食性(耐粒界腐食性、耐糸錆性)が劣化するため、Cuの含有量は0.1mass%以下に規制する。
Mg量: 0.20mass%~1.0mass%
Si量: 0.20mass%~1.5mass%
Mn量: 0.03mass%~0.60mass%
Fe量: 0.03mass%~0.60mass%
この発明のアルミニウム合金クラッド材に用いられるアルミニウム合金インサート材は、固相線温度が590℃以下であれば良く、その具体的な成分組成は特に制約されるものではないが、生産性などを考慮するとAl-Cu系、Al-Si系、あるいはAl-Cu-Si系合金の使用が好適である。
y≧0 ・・・(2)
y≧-15.3x+2.3 ・・・(3)
y≧0 ・・・(5)
y≧-x+0.01 ・・・(6)
本出願は、2011年11月2日に出願された日本国特許出願第2011-241444号に基づく。本明細書中にその明細書、特許請求の範囲、図面全体を参照として取り込むものとする。
Claims (6)
- Mg:0.2~1.5%(mass%、以下同じ)、Si:0.2~2.5%、Cu:0.2~3.0%を含有し、残部がAlおよび不可避不純物からなるアルミニウム合金の芯材と、
前記芯材の片面又は両面にクラッドされており、厚さが1面につき全板厚の3~30%であり、Mg:0.2~1.5%、Si:0.2~2.0%を含むとともにCuを0.1%以下に規制した組成を有し、残部がAlおよび不可避不純物からなるアルミニウム合金の皮材と、
前記芯材と前記皮材との間に介在しており、590℃以下の固相線温度を有するアルミニウム合金のインサート材と、を備える、
ことを特徴とする成形加工用アルミニウム合金クラッド材。 - 前記芯材および前記皮材、あるいはそのどちらか一方が、Mn:0.03~1.0%、Cr:0.01~0.40%、Zr:0.01~0.40%、V:0.01~0.40%、Fe:0.03~1.0%、Zn:0.01~2.5%、Ti:0.005~0.30%のうち1種又は2種以上を含有する、
ことを特徴とする請求項1に記載の成形加工用アルミニウム合金クラッド材。 - 前記インサート材に含有されるSi量(mass%、以下同じ)をx、Cu量(mass%、以下同じ)をyとしたとき、以下の(1)~(3)式を同時に満足する、
ことを特徴とする請求項1又は2に記載の成形加工用アルミニウム合金クラッド材。
x≧0 ・・・(1)
y≧0 ・・・(2)
y≧-15.3x+2.3 ・・・(3) - 前記インサート材に含有されるMg量が0.05~2.0mass%であり、
該インサート材に含有されるSi量(mass%、以下同じ)をx、Cu量(mass%、以下同じ)をyとした際に以下の(4)~(6)式を同時に満足する、
ことを特徴とする請求項1又は2に記載の成形加工用アルミニウム合金クラッド材。
x≧0 ・・・(4)
y≧0 ・・・(5)
y≧-x+0.01 ・・・(6) - 前記インサート材の固相線温度は、前記芯材の固相線温度及び前記皮材の固相線温度よりも低い、
ことを特徴とする請求項1~4のいずれか1項に記載の成形加工用アルミニウム合金クラッド材。 - 前記芯材、前記インサート材及び前記皮材を高温加熱処理にて接合する際のインサート材の厚さが10μm以上である、
ことを特徴とする請求項1~5のいずれか1項に記載の成形加工用アルミニウム合金クラッド材。
Priority Applications (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
CN201280053950.XA CN104080935A (zh) | 2011-11-02 | 2012-10-31 | 成型加工用的铝合金包层材料 |
JP2013523418A JP5388156B2 (ja) | 2011-11-02 | 2012-10-31 | 成形加工用アルミニウム合金クラッド材 |
US14/356,112 US20140356647A1 (en) | 2011-11-02 | 2012-10-31 | Aluminum alloy clad material for forming |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2011241444 | 2011-11-02 | ||
JP2011-241444 | 2011-11-02 |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2013065760A1 true WO2013065760A1 (ja) | 2013-05-10 |
Family
ID=48192100
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2012/078241 WO2013065760A1 (ja) | 2011-11-02 | 2012-10-31 | 成形加工用アルミニウム合金クラッド材 |
Country Status (4)
Country | Link |
---|---|
US (1) | US20140356647A1 (ja) |
JP (1) | JP5388156B2 (ja) |
CN (1) | CN104080935A (ja) |
WO (1) | WO2013065760A1 (ja) |
Cited By (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN103643092A (zh) * | 2013-12-24 | 2014-03-19 | 北京科技大学 | 高应变强化指数AlMgSi合金板材及其制备方法 |
EP3023189A3 (en) * | 2014-08-08 | 2016-08-17 | UACJ Corporation | Brazing sheet for surface joining |
JP2019189909A (ja) * | 2018-04-24 | 2019-10-31 | 株式会社神戸製鋼所 | アルミニウム合金およびアルミニウム合金製クラッド材 |
CN114752829A (zh) * | 2022-05-05 | 2022-07-15 | 银邦金属复合材料股份有限公司 | 新能源动力电池液冷板用复合铝合金板及其制备方法 |
JP2022545272A (ja) * | 2019-08-22 | 2022-10-26 | ノベリス・コブレンツ・ゲゼルシャフト・ミット・ベシュレンクテル・ハフツング | クラッド2xxxシリーズ航空宇宙用製品 |
Families Citing this family (19)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP6513449B2 (ja) * | 2015-03-25 | 2019-05-15 | 株式会社神戸製鋼所 | アルミニウム合金クラッド板およびアルミニウム合金クラッド構造部材 |
CN104962791B (zh) * | 2015-05-13 | 2017-01-25 | 慈溪智江机械科技有限公司 | 一种投影仪用合金材料及其制备方法 |
FR3036986B1 (fr) * | 2015-06-05 | 2017-05-26 | Constellium Neuf-Brisach | Tole pour carrosserie automobile a resistance mecanique elevee |
BR112018007354B1 (pt) | 2015-10-15 | 2022-05-03 | Novelis Inc | Liga de alumínio, chapa metálica de múltiplas camadas, e uso de produto de chapa metálica |
RU2647070C2 (ru) * | 2016-07-06 | 2018-03-13 | Российская Федерация, от имени которой выступает Государственная корпорация по космической деятельности "РОСКОСМОС" (Госкорпорация "РОСКОСМОС") | Алюминиевый сплав |
CN106222497B (zh) * | 2016-08-24 | 2018-09-14 | 天长市正牧铝业科技有限公司 | 一种耐腐蚀铝合金球棒及其制备方法 |
CN106244873B (zh) * | 2016-08-24 | 2018-09-14 | 天长市正牧铝业科技有限公司 | 一种耐弯曲铝合金球棒 |
CN106735660A (zh) * | 2016-12-14 | 2017-05-31 | 无锡银邦防务科技有限公司 | 一种钎焊蜂窝板面板用高强铝合金复合板、芯材、包覆层及皮材 |
CN108677065A (zh) * | 2018-05-23 | 2018-10-19 | 大力神铝业股份有限公司 | 一种用于生产高强冷凝器复合翅片材料及其制作方法 |
EP3827107A1 (en) | 2018-07-23 | 2021-06-02 | Novelis, Inc. | Methods of making highly-formable aluminum alloys and aluminum alloy products thereof |
US11345980B2 (en) | 2018-08-09 | 2022-05-31 | Apple Inc. | Recycled aluminum alloys from manufacturing scrap with cosmetic appeal |
CN109136670B (zh) * | 2018-08-21 | 2019-11-26 | 中南大学 | 一种6xxx系铝合金及其制备方法 |
CN113574192A (zh) | 2019-03-13 | 2021-10-29 | 诺维尔里斯公司 | 可时效硬化且可高度成形的铝合金及其制备方法 |
CN112553514A (zh) * | 2019-09-25 | 2021-03-26 | 苹果公司 | 由用过的饮料罐废料制成的可热处理的铝合金 |
CN110952051B (zh) * | 2019-12-16 | 2021-01-26 | 邹平宏发铝业科技有限公司 | 一种铝合金部件的处理工艺 |
PL4132743T3 (pl) * | 2020-04-08 | 2024-05-27 | Speira Gmbh | Wysokowytrzymały materiał aluminiowy al-mg-si platerowany przez nalutowywanie |
EP3904073B1 (en) * | 2020-04-29 | 2023-05-31 | Novelis Koblenz GmbH | Clad 2xxx-series aerospace product |
CN112718856A (zh) * | 2020-12-14 | 2021-04-30 | 东北轻合金有限责任公司 | 一种改善5系铝合金带材表面冲制吕德斯带的制造方法 |
CN112813316B (zh) * | 2020-12-30 | 2022-06-28 | 安徽鑫铂铝业股份有限公司 | 一种高强耐蚀铝合金的制备方法 |
Citations (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH0436433A (ja) * | 1990-06-01 | 1992-02-06 | Sumitomo Light Metal Ind Ltd | A1熱交換器用高強度高耐食性a1合金クラッド材 |
JP2003126986A (ja) * | 2001-10-23 | 2003-05-08 | Sky Alum Co Ltd | アルミニウム合金ブレ−ジングシ−ト、それを用いたろう付け方法、およびろう付け製品 |
JP2005523164A (ja) * | 2002-04-18 | 2005-08-04 | アルコア インコーポレイテッド | 高寿命、高成形性ブレージングシート |
JP2006131923A (ja) * | 2004-11-02 | 2006-05-25 | Denso Corp | ろう付け性、耐食性および熱間圧延性に優れた熱交換器用アルミニウム合金クラッド材および該アルミニウム合金クラッド材を用いるろう付けによる熱交換器の製造方法 |
JP2008111143A (ja) * | 2006-10-27 | 2008-05-15 | Furukawa Sky Kk | アルミニウム合金ブレージングシートおよびその製造方法 |
JP2009534531A (ja) * | 2006-04-21 | 2009-09-24 | アルコア インコーポレイテッド | ろう付け可能な多層シート |
JP2011042853A (ja) * | 2009-08-24 | 2011-03-03 | Mitsubishi Alum Co Ltd | 耐食性および耐久性に優れるアルミニウム合金製熱交換器 |
Family Cites Families (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP3869846B2 (ja) * | 2005-03-25 | 2007-01-17 | 神鋼アルコア輸送機材株式会社 | アルミニウム合金板および熱交換器 |
CN101545062A (zh) * | 2009-05-08 | 2009-09-30 | 南通恒秀铝热传输材料有限公司 | 一种蒸发器管板用铝合金复合带材及其制造方法 |
CN101927588B (zh) * | 2010-08-26 | 2011-12-28 | 南通恒秀铝热传输材料有限公司 | 汽车热交换器用复合钎焊铝合金材料 |
-
2012
- 2012-10-31 WO PCT/JP2012/078241 patent/WO2013065760A1/ja active Application Filing
- 2012-10-31 JP JP2013523418A patent/JP5388156B2/ja not_active Expired - Fee Related
- 2012-10-31 CN CN201280053950.XA patent/CN104080935A/zh active Pending
- 2012-10-31 US US14/356,112 patent/US20140356647A1/en not_active Abandoned
Patent Citations (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH0436433A (ja) * | 1990-06-01 | 1992-02-06 | Sumitomo Light Metal Ind Ltd | A1熱交換器用高強度高耐食性a1合金クラッド材 |
JP2003126986A (ja) * | 2001-10-23 | 2003-05-08 | Sky Alum Co Ltd | アルミニウム合金ブレ−ジングシ−ト、それを用いたろう付け方法、およびろう付け製品 |
JP2005523164A (ja) * | 2002-04-18 | 2005-08-04 | アルコア インコーポレイテッド | 高寿命、高成形性ブレージングシート |
JP2006131923A (ja) * | 2004-11-02 | 2006-05-25 | Denso Corp | ろう付け性、耐食性および熱間圧延性に優れた熱交換器用アルミニウム合金クラッド材および該アルミニウム合金クラッド材を用いるろう付けによる熱交換器の製造方法 |
JP2009534531A (ja) * | 2006-04-21 | 2009-09-24 | アルコア インコーポレイテッド | ろう付け可能な多層シート |
JP2008111143A (ja) * | 2006-10-27 | 2008-05-15 | Furukawa Sky Kk | アルミニウム合金ブレージングシートおよびその製造方法 |
JP2011042853A (ja) * | 2009-08-24 | 2011-03-03 | Mitsubishi Alum Co Ltd | 耐食性および耐久性に優れるアルミニウム合金製熱交換器 |
Cited By (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN103643092A (zh) * | 2013-12-24 | 2014-03-19 | 北京科技大学 | 高应变强化指数AlMgSi合金板材及其制备方法 |
EP3023189A3 (en) * | 2014-08-08 | 2016-08-17 | UACJ Corporation | Brazing sheet for surface joining |
JP2019189909A (ja) * | 2018-04-24 | 2019-10-31 | 株式会社神戸製鋼所 | アルミニウム合金およびアルミニウム合金製クラッド材 |
JP2022545272A (ja) * | 2019-08-22 | 2022-10-26 | ノベリス・コブレンツ・ゲゼルシャフト・ミット・ベシュレンクテル・ハフツング | クラッド2xxxシリーズ航空宇宙用製品 |
US11879167B2 (en) | 2019-08-22 | 2024-01-23 | Novelis Koblenz Gmbh | Clad 2XXX-series aerospace product |
CN114752829A (zh) * | 2022-05-05 | 2022-07-15 | 银邦金属复合材料股份有限公司 | 新能源动力电池液冷板用复合铝合金板及其制备方法 |
CN114752829B (zh) * | 2022-05-05 | 2022-10-04 | 银邦金属复合材料股份有限公司 | 新能源动力电池液冷板用复合铝合金板及其制备方法 |
Also Published As
Publication number | Publication date |
---|---|
US20140356647A1 (en) | 2014-12-04 |
JP5388156B2 (ja) | 2014-01-15 |
CN104080935A (zh) | 2014-10-01 |
JPWO2013065760A1 (ja) | 2015-04-02 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP5388156B2 (ja) | 成形加工用アルミニウム合金クラッド材 | |
JP5388157B2 (ja) | 成形加工用アルミニウム合金クラッド材 | |
JP6452627B2 (ja) | アルミニウム合金クラッド材及びその製造方法、ならびに、当該アルミニウム合金クラッド材を用いた熱交換器及びその製造方法 | |
JP5365194B2 (ja) | 高い{222}面集積度を有する鋼板およびその製造方法 | |
JP6418714B2 (ja) | アルミニウム合金クラッド材及びその製造方法、ならびに、当該アルミニウム合金クラッド材を用いた熱交換器及びその製造方法 | |
JP2011162823A (ja) | 熱交換器に用いられるアルミニウム合金クラッド材およびそれに用いるアルミニウム合金クラッド材用芯材 | |
WO2017141921A1 (ja) | アルミニウム合金ブレージングシート及びその製造方法、ならびに、当該ブレージングシートを用いた自動車用熱交換器の製造方法 | |
WO2015002315A1 (ja) | 熱交換器用ブレージングシート及びその製造方法 | |
JP5802762B2 (ja) | 耐酸化性及び耐熱性に優れたアルミニウムメッキ鋼板 | |
JP2004514059A (ja) | ろう付けされる熱交換器の製造のための、アルミニウム合金でクラッドされるストリップの製造方法 | |
US20230078028A1 (en) | High-strength solder-plated al-mg-si aluminum material | |
JP6542649B2 (ja) | アルミニウム合金クラッド板およびアルミニウム合金クラッド構造部材 | |
WO2019044545A1 (ja) | 熱交換器フィン用ブレージングシート及びその製造方法 | |
CN113692454B (zh) | 铝合金硬钎焊板及其制造方法 | |
JP4720618B2 (ja) | 合金化溶融亜鉛めっき鋼板及びその製造方法 | |
CN112955574B (zh) | 铝合金硬钎焊板及其制造方法 | |
CN111409322A (zh) | 铝钢复合材料及其制备方法和5g通讯设备 | |
JP3754624B2 (ja) | 室温時効抑制と低温時効硬化能に優れた自動車用アルミニウム合金パネル材の製造方法および自動車用アルミニウム合金パネル材 | |
KR20120041619A (ko) | 도금성 및 밀착성이 우수한 용융아연 도금강판 및 그 제조방법 | |
JP6813142B1 (ja) | Al系めっきステンレス鋼板、および、フェライト系ステンレス鋼板の製造方法 | |
JP2007146201A (ja) | アルミニウム材料とのスポット溶接性に優れた溶融アルミニウムめっき鋼板 | |
JP2007146200A (ja) | アルミニウム材料に対するスポット溶接性に優れた溶融アルミニウムめっき鋼板 | |
JPS6189498A (ja) | 水冷式Al合金製熱交換器の冷却水管 | |
JPH08132284A (ja) | ろう材が均一な厚さにクラッドされた熱交換器用ブレージングシートの製造方法 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
ENP | Entry into the national phase |
Ref document number: 2013523418 Country of ref document: JP Kind code of ref document: A |
|
121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 12845657 Country of ref document: EP Kind code of ref document: A1 |
|
NENP | Non-entry into the national phase |
Ref country code: DE |
|
WWE | Wipo information: entry into national phase |
Ref document number: 14356112 Country of ref document: US |
|
122 | Ep: pct application non-entry in european phase |
Ref document number: 12845657 Country of ref document: EP Kind code of ref document: A1 |