Classifications

• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B22—CASTING; POWDER METALLURGY
  • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
  • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
  • B22D11/12—Accessories for subsequent treating or working cast stock in situ
  • B22D11/124—Accessories for subsequent treating or working cast stock in situ for cooling
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B22—CASTING; POWDER METALLURGY
  • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
  • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
  • B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B22—CASTING; POWDER METALLURGY
  • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
  • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
  • B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
  • B22D11/0605—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by two belts, e.g. Hazelett-process
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B22—CASTING; POWDER METALLURGY
  • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
  • B22D17/00—Pressure die casting or injection die casting, i.e. casting in which the metal is forced into a mould under high pressure
• • 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
  • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
  • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
  • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
  • C22F1/05—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions

Definitions

• the present invention relates to a structural aluminum alloy, and particularly to a structure of a member requiring high rigidity and a low coefficient of linear expansion, such as a ladder type frame, a perimeter type frame, and cases of various vehicles such as automobiles.
• the present invention relates to a structural aluminum alloy which can be suitably used for aluminum.
• an aluminum alloy having high rigidity an aluminum alloy composite material in which A10, SiC, or the like is compounded as a reinforcing material in an aluminum alloy is known.
• the material has a problem that the manufacturing process is complicated and the cost is high. Also, A1 0
• Japanese Patent Application Laid-Open No. 1-180938 discloses an aluminum alloy having improved abrasion resistance.
• the aluminum alloy disclosed herein is used in steel frames and the like used in automobile frames and the like.
• Japanese Patent Application Laid-Open No. 3-199336 similarly discloses an aluminum alloy having improved wear resistance.
• the aluminum alloy disclosed herein is also used for a frame of an automobile. In the case of replacing with an iron product, there is a problem that the rigidity is small and the linear expansion coefficient is too large, and further, the seizure to a mold is easily caused.
• Patent Document 1 JP-A-1180938
• Patent Document 2 JP-A-3-199336
• Ni 0.5 to 6% by mass may be added so that the total amount of Fe, Mn and Ni is 3.0% by mass or more.
• Ni 0. 1-1 0 weight 0/0
• Mg 0. 0. 05 one 1.5 mass 0 / o
• Ti 0. 01 . -1 0 mass 0/0
• B 0.. 0 0001-1 0 mass 0 / o
• Zr 0. 1-1 0 wt%
• V 0. 1-1 0 wt%
• Mo 0 . 01-1. 0% by mass.
• Si is crystallized as eutectic Si, primary crystal Si, and Fe-Si-based compound, and has the effect of improving rigidity. This effect is remarkable at 13% by mass or more, but when it exceeds 25% by mass, the primary crystals are coarsened, and conversely, the effect of improving rigidity is reduced. Also, it is necessary to increase the production temperature. Furthermore, the machinability is significantly deteriorated by the coarse Si. Si also has a function of lowering the coefficient of linear expansion and a function of improving wear resistance. A more preferred range of Si is 13-17% by mass. [0011] 01: 2-8 mass%
• Cu is crystallized as an A-to-Cu-based compound and an A-to-N-to-Cu-based compound, contributing to an improvement in rigidity. This effect becomes remarkable when added at 4% by mass or more, but when it exceeds 8% by mass, the compound becomes coarse, conversely the elongation is reduced, and the corrosion resistance is also reduced.
• a more preferred range for Cu is 3-6% by mass.
• Fe + Mn (+ Ni) 3. 0 mass 0/0 or more
• Fe, Mn, Ni are A-Fe-Mn, A-Fe-Si, A-Ni, A-Ni-Cu, A-Ni-Fe-Mn, A-Si-Fe-Mn It has the effect of crystallizing as a compound, contributing to the improvement of rigidity, and lowering the coefficient of linear expansion. It also has the effect of improving heat resistance. This effect is remarkable when Fe + Mn (+ Ni) is 3% by mass or more, but when it exceeds 12% by mass, the crystallized material becomes coarse and the effect of improving the rigidity becomes small, so that Fe + Mn + It is preferable that the total amount of Ni is 12% by mass or less.
• P has a function of making primary crystal Si fine and dispersing it uniformly. This effect is remarkable at 0.001% by mass or more, but if it exceeds 0.02% by mass, the viscosity of the molten metal increases, and the formability deteriorates.
• Mg forms a solid solution in the parent phase and contributes to improvement in rigidity. This effect is remarkable at 0.05% by mass or more, but when it exceeds 1.5% by mass, the elongation is reduced, and the formability is significantly deteriorated. More preferably, Mg is at most 0.4% by mass.
• Cr is crystallized as an Fe-Mn-Cr-based compound, contributing to an improvement in rigidity. It also has the function of dispersing primary Si finely and uniformly. This effect is remarkable when Cr is 0.1% by mass or more, but when it exceeds 1.0% by mass, a coarse compound is formed, and on the contrary, elongation is reduced.
• Ti has the effect of making the ⁇ phase finer, contributing to the improvement of the formability, and preventing the coarse force of the Ni-based compound. The effect is remarkable when Ti is 0.01% by mass or more, but when it exceeds 1.0% by mass, a coarse compound is formed, and on the contrary, elongation is reduced.
• B 0.0001—1.0% by mass
• V 0.1—1.0% by mass
• Zr 0.1—1.0% by mass
• Mo 0.01—1.0% by mass
• B, V, Zr, and Mo form high rigidity crystallized substances and contribute to improvement in rigidity.
• any of the elements is added in excess of the upper limit, coarse crystals are formed and elongation is reduced.
• the inventor of the present application manufactured the aluminum alloy according to the present invention, and experimentally confirmed the relationship between the composition, the crystal structure, and the rigidity and the linear expansion coefficient. The results are described below. .
• Table 1 shows the composition of the aluminum alloy used in the experiment.
• the aluminum alloy used in the experiment was manufactured by a PF die-casting method into a flat plate shape of 200 ⁇ 200 ⁇ 10 mm at a manufacturing temperature of 720 ° C, kept at 200 ° C for 4 hours, aged, and then stiffened (Young's Rate) and the coefficient of linear expansion (coefficient of thermal expansion) were measured.
• Alloy Nos. 1-17 are aluminum alloys according to the present invention, and Alloy Nos. 18-24 are comparative examples in which at least one of the composition ranges does not satisfy the above conditions. When the conditions were satisfied, the composition was underlined.
• the reference value with respect to Young's modulus it is determined that no more things to satisfaction criteria, the reference value as a 18 X 10 one 6 Z ° C for the linear expansion coefficient, which less than one reference was determined to be satisfied.
• the alloy No. 18 has a Young's modulus is below 80GPa and a reference value (90 GPa), at the same time, the linear expansion coefficient 20. 0 X 10- 6 / ° C and the reference value (18 X 10- 6 ° C) than the large instrument any value nor is it satisfy the criteria. This is probably because the contents of Si, Cu, and Ni + Fe + Mn are all insufficient, that is, they are below the above-mentioned range.
• Alloy No. 19 also, like Alloy No. 18, does not satisfy the standards in both Young's modulus and coefficient of linear expansion. This is because Cu is within the above range, but the content of both Si and Ni + Fe + Mn is insufficient (below the above range! /). Conceivable.
• Alloy No. 20 has a Young's modulus lower than the reference value, but this is because the total content of Ni + Fe + Mn is 2.0% by mass, and the above conditions, Ni + Fe + Mn3 It is thought that the cause was less than 0% by mass.
• Alloy No. 22 exerted insufficient force to measure the Young's modulus due to insufficient elongation and cracking of the test piece in the elastic deformation region. This is considered to be because Mn was not substantially added and did not satisfy the above-mentioned conditions regarding the composition.
• Alloy No. 23 does not satisfy the standards in both Young's modulus and linear expansion coefficient. This is considered to be because 1% by mass is insufficient (below the above range).
• Alloy No. 24 also does not satisfy the standards in both Young's modulus and linear expansion coefficient. This is thought to be due to the fact that 12% by mass of Si is insufficient (below the above range).
• the aluminum alloy No. 1-17 of the present invention satisfying the above-mentioned composition range has a Young's modulus and a coefficient of linear expansion which are all based on the values shown in Table 1. Is pleased.
• the aluminum alloy for production of the present invention is particularly useful for producing members requiring high rigidity and low coefficient of linear expansion, such as ladder-type frames, perimeter-type frames and cases of various vehicles such as automobiles. It can be suitably used.

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• 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)
• Body Structure For Vehicles (AREA)
• Continuous Casting (AREA)

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• 2004
  • 2004-03-23 JP JP2004084256A patent/JP4665413B2/ja not_active Expired - Lifetime
• 2005
  • 2005-03-22 MY MYPI20051266A patent/MY139116A/en unknown
  • 2005-03-23 KR KR1020067021516A patent/KR20060130753A/ko not_active Withdrawn
  • 2005-03-23 WO PCT/JP2005/005225 patent/WO2005090624A2/ja active Application Filing
  • 2005-03-23 EP EP05726972.2A patent/EP1728882B1/en not_active Expired - Lifetime
  • 2005-03-23 US US10/593,338 patent/US20070193663A1/en not_active Abandoned
• 2010
  • 2010-08-02 US US12/848,859 patent/US20100296964A1/en not_active Abandoned

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