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
  • C22C21/04—Modified aluminium-silicon alloys
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C21/00—Alloys based on aluminium
  • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C21/00—Alloys based on aluminium
  • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
  • C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
  • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
  • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
  • C22F1/05—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions
• • C—CHEMISTRY; METALLURGY
  • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
  • C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
  • C25D11/00—Electrolytic coating by surface reaction, i.e. forming conversion layers
  • C25D11/02—Anodisation
  • C25D11/04—Anodisation of aluminium or alloys based thereon
• • 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.]
  • Y10T428/1266—O, S, or organic compound in metal component
  • Y10T428/12667—Oxide of transition metal or Al

Definitions

• the invention relates to a decoratively anodizable, easily deformable and mechanically highly resilient aluminum alloy of the AlMgSi type, a semifinished product made of this alloy, in the form of strips, sheets or extruded profiles, and a component, in particular formed and decoratively anodized, made from the aforementioned semifinished products.
• a method for producing such an aluminum alloy is also within the scope of the invention.
• Unalloyed aluminum (lxxx alloys), AlMg alloys (5xxx alloys or plated systems of the 8xxx alloy type, cladding made of unalloyed aluminum (lxxx alloy) are generally used to manufacture decorative anodized aluminum sheet components. All of these material classes are not hardenable, ie an increase in strength takes place exclusively by strain hardening, a decrease in succession then by softening annealing. All these systems therefore have in common that their formability and their state of strength due to Semi-finished product delivery state, which can be either solidified by rolling or softened by a subsequent annealing, is fixed. In terms of good formability, it is therefore possible to use these systems in a state of maximum softening and then to form them.
• the systems can be used in a state of high strength, but the formability for a shaping step is severely limited due to the high initial strength of the delivery state.
• Heat-hardenable AlMgSi alloys (6xxx) with good formability are known, for example, from EP 0 714 993 and EP 0 81 1 700.
• the disclosed AlMgSi alloys are also used for the production of strips and sheets. Due to the good deep-drawing properties, they are suitable for the production of body panels for the automotive industry.
• the alloy composition disclosed therein achieves an optimum between good strength and good forming behavior.
• these alloys are not decorative, especially not high-gloss, anodizable, since on the one hand the iron content of 0.25 to 0.55% by weight disclosed in EP 0 81 1 700 is too high and leads to a clouding of the anodized layer.
• the invention has for its object to provide an aluminum alloy for components that have good formability, that have sufficient strength and ductility in the application state and that can be decoratively anodized.
• This object is achieved with an aluminum alloy with the composition mentioned in claim 1 and the features listed there.
• the optimal properties with regard to mechanical strength and forming behavior are achieved on the one hand by the proportion of 0.3 to 0.9% by weight of silicon and 0.1 to 0.5% by weight of magnesium, the weight ratio of these two components being adjusted such that a There is an excess of silicon over magnesium, in particular a silicon-magnesium weight ratio of 1.8 to 3.3.
• the strength is further supported by a proportion of 0.1 to 0.4% by weight of copper, which causes mixed crystal hardening.
• the good formability is due to the proportion the recrystallization inhibitor (iron, zirconium, chromium, vanadium) ensures. Iron is often present as an impurity in a starting alloy.
• the alloy according to the invention can be decoratively anodized and shows no yellowish or cloudy anodized layer. This is caused by the proportion of 0.005 to 0.1% by weight of strontium. It is assumed that the strontium changes the phases containing iron zirconium, chromium and / or vanadium, in particular refined to such an extent that, even if they are incorporated in the anodized layer, they do not cause any visible clouding. It has surprisingly been found that a weight ratio of iron to strontium
• Such an alloy is made of aluminum base material with more than 99.85% by weight of aluminum.
• the alloy components are added to the melt as follows, namely 0.3 to 0.9% by weight of silicon, 0.1 to 0.5% by weight of magnesium, the weight ratio of silicon to magnesium being 1.8: 1 to 3.3: 1 is.
• additional iron is added if necessary, so that the alloy to be produced contains up to 0.2% by weight of iron.
• 0.005 to 0.1% by weight of strontium is added, the weight ratio of iron to strontium being set from 3: 1 to 5: 1.
• An addition of 0.008 to 0.07% by weight of strontium is preferred.
• 0.1 to 0.4% by weight of copper, 0.03 to 0.2% by weight of manganese, 0.01% by weight of titanium and zirconium and / or chromium and / or vanadium in total 0.08 to 0.22 are further alloy components % By weight added.
• the alloy should contain a maximum of 0.04% by weight of zinc and a maximum of 0.02% by weight. contain unavoidable contamination individually or a maximum of 0.15% by weight in total. Furthermore, a certain proportion, namely 0.0005 to 0.005% by weight of silver, can be added to identify the alloy.
• the melt produced in this way is cast in a continuous casting process to form a rolled ingot or continuous casting bolt and then homogenized (annealing for at least 2 hours at at least 500 ° C.).
• Pure aluminum with at least 99.85% by weight of aluminum is preferably used as the aluminum base material in order to limit the proportion of impurities; in total, a maximum of 0.15% by weight of unavoidable impurities should not be exceeded.
• the alloy components can be added in the form of pure metals or master alloys.
• the strontium is preferably added in the form of an aluminum strontium master alloy, in particular by means of an AlSr3.5 master alloy, an AlSr5 master alloy or an AlSrlO master alloy.
• extruded or hollow-section sections can be obtained by extrusion, which are usually stretched and assembled by sawing.
• Subsequent forming in particular cold forming, such as rolling, bending, deep drawing or active media-based sheet metal and tube forming, can be used to produce three-dimensionally shaped raw components from the profile pieces brought to the desired length. Regardless of whether the forming is a bending process, active-media-based forming or deep drawing, the resulting component shows good contour accuracy with very little orange peel formation, caused by low springback. Due to the hardenability of the alloy, the strength and ductility can be adjusted after the forming.
• chemical and electrolytic treatment of the component follows in particular.
• Such chemical and electrolytic treatment includes polishing, shining, anodizing, possibly a coloring and a final compression of the components.
• the resulting anodized layer of the decoratively anodized shaped aluminum component is very satisfactory, it is transparent, ie not cloudy and also not yellowish.
• Pre-sheets can be obtained from the rolled ingot by hot rolling, which can be further processed by cold rolling and intermediate annealing.
• further forming steps if necessary recrystallization and / or softening annealing), such as deep drawing, active media-based sheet metal forming, including designing and smoothing or roughening the surfaces and possibly further soft annealing, if necessary mechanical processing, a raw part is formed, which is also subsequently chemically or electrolytically treated with can be provided with a decorative anodized layer.
• the aluminum alloy has good to very good forming behavior at room temperature with little orange peeling, has stable forming behavior and leads to good contour accuracy of the component.
• the anodized layer has no defects, on the contrary, even shiny surfaces can be achieved if pure aluminum with at least 99.9% by weight aluminum is used as the base material.
• Exemplary embodiments of aluminum alloys according to the invention are shown in three tables below.
• Table 1 shows higher-strength AlMgSi alloys, Table 2 medium-strength AlMgSi alloys and Table 3 low-strength AlMgSi alloys.
• Known comparative alloys are listed in Table 4, including the applicant's alloy AA6401-special, a medium-strength AlMgSi alloy which has hitherto been used for decorative applications, but which does not show optimum forming behavior.
• the other comparison alloys represent optimum strength and forming behavior, but cannot be decoratively anodized.
• An aluminum component was produced according to one of these process variants from an alloy according to the invention by continuous casting, homogenizing, extrusion, stretching, cutting to length, deep drawing, polishing, glossing, anodizing.
• components of the same shape were produced from a 6401 alloy and a 6016 alloy using the same method.
• the properties of the components are shown in Table 5.
• the image sharpness was measured in different surface areas of the finished components. High image sharpness is an expression of a high gloss and high accuracy of an image, i.e. whether lines are displayed straight or distorted.
• the formability was listed as a comparative degree of deformation.
• the degrees of deformation were determined from the changed line grid using a deep-drawing-like process. It is clear that the component according to the invention is the only component that has high image sharpness (80%) and good formability (40%).

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• Chemical & Material Sciences (AREA)
• Engineering & Computer Science (AREA)
• Materials Engineering (AREA)
• Metallurgy (AREA)
• Organic Chemistry (AREA)
• Mechanical Engineering (AREA)
• Physics & Mathematics (AREA)
• Thermal Sciences (AREA)
• Crystallography & Structural Chemistry (AREA)
• Electrochemistry (AREA)
• Chemical Kinetics & Catalysis (AREA)
• Continuous Casting (AREA)
• Metal Rolling (AREA)
• Extrusion Of Metal (AREA)
• Laminated Bodies (AREA)
• Shaping Metal By Deep-Drawing, Or The Like (AREA)
• Powder Metallurgy (AREA)
• Sliding-Contact Bearings (AREA)
• Forging (AREA)
• Eyeglasses (AREA)
• Adornments (AREA)
• Conductive Materials (AREA)

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• 2004
  • 2004-05-08 DE DE102004022817A patent/DE102004022817A1/de not_active Withdrawn
• 2005
  • 2005-04-30 RU RU2006143448/02A patent/RU2355801C2/ru not_active IP Right Cessation
  • 2005-04-30 DE DE502005007622T patent/DE502005007622D1/de active Active
  • 2005-04-30 CN CNB2005800146820A patent/CN100500905C/zh not_active Expired - Fee Related
  • 2005-04-30 KR KR1020067025814A patent/KR100903249B1/ko not_active IP Right Cessation
  • 2005-04-30 JP JP2007513725A patent/JP4761275B2/ja not_active Expired - Fee Related
  • 2005-04-30 WO PCT/EP2005/004721 patent/WO2005108633A2/fr active Application Filing
  • 2005-04-30 AT AT05759604T patent/ATE435310T1/de active
  • 2005-04-30 EP EP05759604A patent/EP1749112B1/fr not_active Not-in-force
  • 2005-04-30 US US11/579,520 patent/US20080318081A1/en not_active Abandoned
  • 2005-04-30 CA CA2563515A patent/CA2563515C/fr not_active Expired - Fee Related
• 2006
  • 2006-12-07 NO NO20065655A patent/NO20065655L/no not_active Application Discontinuation

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