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WO2009147861A1 - Tôle d'alliage de magnésium facilement formable et son procédé de fabrication - Google Patents

Tôle d'alliage de magnésium facilement formable et son procédé de fabrication Download PDF

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Publication number
WO2009147861A1
WO2009147861A1 PCT/JP2009/002536 JP2009002536W WO2009147861A1 WO 2009147861 A1 WO2009147861 A1 WO 2009147861A1 JP 2009002536 W JP2009002536 W JP 2009002536W WO 2009147861 A1 WO2009147861 A1 WO 2009147861A1
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Prior art keywords
magnesium alloy
mass
easily formable
alloy sheet
total amount
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Japanese (ja)
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千野靖正
馬渕守
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National Institute of Advanced Industrial Science and Technology AIST
Kyoto University NUC
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National Institute of Advanced Industrial Science and Technology AIST
Kyoto University NUC
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    • 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
    • C22F1/06—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of magnesium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C23/00—Alloys based on magnesium
    • C22C23/04—Alloys based on magnesium with zinc or cadmium as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C23/00—Alloys based on magnesium
    • C22C23/06—Alloys based on magnesium with a rare earth metal as the next major constituent
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals

Definitions

  • the present invention relates to a method for producing an easily formable magnesium alloy, a magnesium alloy sheet material, a magnesium alloy press-formed body and a magnesium alloy member, and more specifically, a light rare earth element (Y, Sc, La, Ce, Hot and warm rolling and annealing of a magnesium alloy containing Pr, Nd, Sm) and Zn and added with a specific amount of Mn and Zr improves the texture by annealing, and even at normal temperature, 5000
  • the present invention relates to a method of producing an easily formable magnesium alloy sheet which can have the same formability as that of a series or 6000 series aluminum alloy, a magnesium alloy sheet, a press-formed body and a member thereof.
  • a magnesium alloy containing Ca and Zn instead of the above-described light rare earth elements, and added with a specified amount of Al, Mn, and Zr, is hot-warm rolled and annealed to form a texture.
  • the present invention relates to a method of producing an easily formable magnesium alloy sheet material which is reformed and has the same formability as 5000 series or 6000 series aluminum alloy even at ordinary temperature, a magnesium alloy sheet, its press-formed body and members .
  • the present invention provides an easily formable magnesium alloy sheet material that can be used in a wide range of fields such as space and aviation materials, electronic equipment materials, automobile parts, etc., and magnesium alloy parts such as its press-formed body and casing. It is.
  • most magnesium products in Japan are manufactured by a casting method such as die casting. By these methods, thin-walled forming is possible, which is the biggest factor promoting industrialization of magnesium alloys.
  • magnesium alloy castings are used for housings of home appliances such as personal computers, mobile phones, digital cameras and the like.
  • problems such as the need for post-treatment to compensate for casting defects, low yield, and problems in strength and rigidity of members.
  • press forming can be said to be an effective means for expanding demand because it has a high yield and can achieve high strength and high toughness simultaneously with forming.
  • a compact can be produced from a magnesium alloy sheet by press molding, a thin-walled, high-strength compact can be produced by an inexpensive process, and there is much demand for it in the field of home electric appliance housing etc. It can be predicted.
  • HCP structure hexagonal structure
  • the critically resolved shear stress (CRSS) of non-bottom sliding of magnesium alloy is very large at ordinary temperature as compared with other sliding systems, and cold formability is necessarily low. Furthermore, in the magnesium alloy sheet, a texture is formed in which the (0002) plane is oriented in parallel to the sheet plane, so that distortion in the sheet thickness direction at the time of plastic deformation can not be expected. It is a factor that hinders cold formability.
  • Patent Documents 1 and 2 As a method of improving the cold formability of a magnesium alloy having poor formability, a method of using a magnesium alloy sheet material to which a specified amount of lithium is added is known (Patent Documents 1 and 2). Specifically, this method adds 8% by mass or more of Li to magnesium (alloy), crystallizes a body-centered cubic ( ⁇ phase) in magnesium having an HCP structure, and significantly improves formability. To improve. Furthermore, the addition of Li lowers the c / a ratio (Non-Patent Document 1) to synergistically improve the formability. On the other hand, the addition of Li is not practical because it significantly deteriorates the corrosion characteristics of magnesium. Therefore, a technique for improving the formability without adding Li is desired.
  • Non-Patent Document 2 differential circumferential speed rolling
  • Patent Document 3 Cross Rolling Method
  • Patent Document 4 As means for realizing press forming at low temperature (150 ° C. or less), use of a magnesium alloy sheet material to which an appropriate amount of a light rare earth element such as Ce, La, Y or the like has been added through an appropriate heat treatment (Patent Document 4).
  • a light rare earth element is added in an appropriate amount to lower the c / a ratio of magnesium and reduce the plastic anisotropy of magnesium.
  • the formability at normal temperature (30 ° C.) of the magnesium alloy produced by this method is at most about 4 to 5 in Erichsen value.
  • the cold formability (Erichsen value) of aluminum alloys currently used in a wide range of fields is significantly higher than that of the above magnesium alloys, and in the 5000 series alloy, 8.3 (5083-O material), 6000 series alloy, In 9.2 (6061-T4 material) and 1000 series alloy, it is 11.0 (1100-O material) (non-patent document 4).
  • JP 2004-156089 A Japanese Patent Laid-Open No. 4-32535 JP 2004-10959 A Japanese Patent Application No. 2008-148538
  • the inventors of the present invention are cold-formability comparable to or comparable to aluminum alloy sheet material, that is, formability having an Erichsen value of 8.0 or more at ordinary temperature.
  • 1 of light rare earth elements Y, Sc, La, Ce, Pr, Nd, Sm
  • Hot and warm rolling of an alloy to which at least species, Zn and, if necessary, Mn and Zr are added are subjected to appropriate conditions, and then subjected to appropriate heat treatment to modify the texture, so that the normal temperature (30 C.) succeeded in producing a magnesium alloy sheet having excellent formability which conforms to or is comparable to an aluminum alloy.
  • an alloy obtained by adding a specified amount of Ca, Zn and, if necessary, Al, Mn, and Zr to magnesium is hot-rolled under appropriate conditions, warm-rolled, and further subjected to appropriate heat treatment.
  • the present inventors have succeeded in modifying the structure and producing a magnesium alloy sheet having excellent formability that is equivalent to or comparable to an aluminum alloy at normal temperature (30 ° C.), and the present invention has been completed.
  • An object of the present invention is to provide a method for producing an easily formable magnesium alloy sheet having excellent formability.
  • the present invention also provides a method for producing a magnesium alloy press-formed body having a complex shape, and a magnesium alloy press-formed body having a complex shape and a magnesium alloy-made member produced at normal temperature. Purpose. Furthermore, this invention aims at providing the magnesium alloy board
  • a light rare earth element (Y, Sc, La, Ce, Pr, Nd, Sm) containing one or more elements and Zn, and the total amount of the light rare earth elements is 0.01 to 1.0% by mass;
  • the magnesium alloy which is composed of 0.4 to 2.6 mass% of the total amount of H and contains impurities inevitably mixed with it, is subjected to hot / warm rolling and annealing after rolling to obtain an XRD
  • a method for producing an easily formable magnesium alloy sheet material comprising producing a magnesium alloy sheet material having poles in the sheet width direction of a (0002) plane texture by measurement according to the method (Schultz reflection method).
  • a method of producing an easily formable magnesium alloy sheet material comprising: producing a magnesium alloy sheet material having an electrode in the sheet width direction. (6) The method for producing an easily formable magnesium alloy sheet according to (5), wherein the total amount of Ca is 0.01 to 0.3% by mass.
  • One or more kinds of light rare earth elements (Y, Sc, La, Ce, Pr, Nd, Sm), and Zn, and the total amount of light rare earth elements is 0.01 to 1.0% by mass, It consists of a magnesium alloy composed of 0.4 to 2.6 mass% of the total amount of Zn and containing other unavoidable impurities, as measured by the XRD method (Schultz reflection method), (0002) An easily formable magnesium alloy sheet material characterized by having a pole in the sheet width direction of the surface texture. (18) The manufacturing method of the easily formable magnesium alloy board
  • a magnesium alloy press-formed product comprising the formed product of the easily formable magnesium alloy sheet material according to any one of (16) to (26).
  • a magnesium alloy member comprising the magnesium alloy press-formed body according to (27) or (28).
  • the present invention is a method for producing an easily formable magnesium alloy sheet having an excellent formability having an Erichsen value of 8.0 or more at normal temperature (30 ° C.), comprising a light rare earth element (Y, Sc, La, Ce) , Pr, Nd, Sm), and Zn, and the total amount of light rare earth elements is in the range of 0.01 to 1.0% by mass, preferably 0.01 to 0.7% by mass;
  • the total amount of is in the range of 0.4 to 2.6% by mass, optionally containing Mn and / or Zr in the range of 0.01 to 0.8% by mass, preferably 0.01 to 0.5% by mass.
  • the magnesium alloy which is constituted by containing the other impurities which are inevitably mixed, is subjected to hot and warm rolling under appropriate conditions and is subjected to heat treatment under appropriate conditions.
  • the Erichsen value of 8.0 or more means that the Erichsen value is at least a value of 8.0.
  • the present invention is also a method for producing an easily formable magnesium alloy sheet having excellent formability having an Erichsen value of 8.0 or more at normal temperature (30 ° C.), comprising Ca and Zn,
  • the total amount is in the range of 0.01 to 0.6% by mass, preferably 0.01 to 0.3% by mass, and the total amount of Zn is in the range of 0.4 to 2.6% by mass;
  • / or Zr is contained in the range of 0.01 to 0.8% by mass, preferably 0.01 to 0.5% by mass, and Al is contained in the range of 0.01 to 2.0% by mass, and is inevitably mixed with others
  • a magnesium alloy constituted by containing impurities is hot-warm rolled under appropriate conditions and annealed under appropriate conditions.
  • the present invention is also an easily formable magnesium alloy sheet produced by the above production method, comprising one or more kinds of light rare earth elements (Y, Sc, La, Ce, Pr, Nd, Sm), and Zn.
  • the total amount of light rare earth elements is in the range of 0.01 to 1.0% by mass, preferably 0.01 to 0.7% by mass, and the total amount of Zn is in the range of 0.4 to 2.6% by mass,
  • the present invention is also an easily formable magnesium alloy sheet produced by the above production method, which contains Ca and Zn, and the total amount of Ca is 0.01 to 0.6 mass%, preferably 0.01 to 0. In the range of 3% by mass, the total amount of Zn is in the range of 0.4 to 2.6% by mass, and, if necessary, 0.01 to 0.8% by mass of Mn and / or Zr, preferably 0.
  • It is a magnesium alloy sheet which is constituted by containing an impurity contained in the range of 01 to 0.5% by mass, 0.01 to 2.0% by mass of Al, and other unavoidable inclusions. It is characterized in that it has a pole in the width direction of the (0002) surface texture, and shows a formability having an Erichsen value of at least 8.0 at normal temperature (30 ° C.) as measured by the reflection method). .
  • the present invention is a magnesium alloy press-formed body which is a formed body of an easily formable magnesium alloy sheet material produced by the above-mentioned production method, and which has a texture having electrodes of (0002) plane in the sheet width direction;
  • the present invention is characterized in the point of a magnesium alloy member made of a magnesium alloy press-formed body.
  • the present inventors added a slight amount of light rare earth elements (Ce, Y) to magnesium as a means for producing a magnesium alloy pressed body at a lower temperature than the conventional press forming method. It was conceived to improve the formability of magnesium.
  • the addition of light rare earth elements to magnesium reduced the difference in CRSS between bottom slip and non-bottom slip, resulting in reduced plastic anisotropy of the rolled material and excellent rolled formability.
  • the Erichsen value of these alloys is at most about 4 to 5 and is lower than that of the aluminum alloy.
  • FIGS. 1 to 4 show the (0002) plane texture of the rolled Mg-1.5 mass% Zn-0.2 mass% Ce alloy used in the examples described later.
  • the c / a ratio (normal temperature) of the Mg-18 at% Li alloy is 1.6086, which is a significantly lower value than pure Mg (1.6236) (Non-patent Document 1). Therefore, it can be considered that the addition of the light rare earth elements and Zn affects the c / a ratio of the magnesium alloy, and as a result, the texture shown in FIGS. 1 to 4 is developed.
  • the present inventors added magnesium to one or more kinds of light rare earth elements (Y, Sc, La, Ce, Pr, Nd, Sm) in a prescribed amount, Zn, and optionally Mn, Zr.
  • the resulting alloy is subjected to hot and warm rolling under appropriate conditions and further subjected to appropriate heat treatment to make the (0002) plane texture of the plate appear pole in the direction of sheet width, and at normal temperature (30 ° C.)
  • the inventors have succeeded in producing an easily formable magnesium alloy sheet having a formability and ductility conforming to or comparable to an aluminum alloy and a processed material thereof.
  • the present inventors specifically have an excellent formability that conforms to or is comparable to an aluminum alloy at normal temperature (30 ° C.) without using Li, that is, has an Erichsen value of 8.0 or more.
  • the present inventors tried further detailed and systematic experiments, and as a result, it was found that the alloys added with specified amounts of Ca, Zn and, if necessary, Al, Mn and Zr, under appropriate conditions, hot / warm under appropriate conditions. By rolling and further performing heat treatment under appropriate conditions, it was discovered that almost the same texture as that of the alloy to which the rare earth element was added was formed, and excellent cold formability was developed.
  • FIG. 8 shows the (0002) plane texture of the rolled Mg-1.5 mass% Zn-0.08 mass% alloy used in the examples described later.
  • This sample is the result of a sample of 5 mm in thickness rolled to 1 mm at a sample temperature of 450 ° C. and subjected to heat treatment at 350 ° C. (90 minutes).
  • the present inventors hot-warm-warm-roll the alloy which added the specified amount of Ca, Zn and, if necessary, Mn, Zr, Al to magnesium under appropriate conditions, further, it is appropriate.
  • Heat treatment is performed under the conditions to make the (0002) plane texture of the plate appear in the plate width direction, and at normal temperature (30 ° C.), a magnesium alloy plate having a formability and ductility comparable to an aluminum alloy is produced. Succeeded in doing.
  • the present inventors do not utilize Li or a light rare earth element, and at an ordinary temperature (30 ° C.), the formability comparable to an aluminum alloy, ie, an Erichsen value of 8.0 or more We succeeded in producing a magnesium alloy sheet with formability.
  • the alloy composition necessary for realizing the present invention will be described in detail.
  • an alloy composition of a magnesium alloy to which one or more of light rare earth elements (Y, Sc, La, Ce, Pr, Nd, and Sm) is added will be described.
  • one or more kinds of light rare earth elements mean one or two or more kinds of the above-mentioned elements.
  • Ce, La, Nd, Pr, and Sm when one or more of Ce, La, Nd, Pr, and Sm is added in an amount of 1.0% by mass or more, the light rare earth element precipitates and the formability and ductility decrease, so in the present invention, Ce, La, Nd
  • the addition amount of one or more of Pr and Sm should be set to 1.0% by mass or less, preferably 0.7% by mass or less.
  • Y and Sc form a solid solution of 2% by mass or more in magnesium at normal temperature [Reference: L. L. Rokhkin: “Magneium Alloys Containing Rare Earth Metals”, (Taylor & Francis, London, 2003) pp. 18-67].
  • the addition amount of Y and / or Sc should be set to 0.5% by mass or less.
  • misch metal a rare earth element group containing a light rare earth element as a main component
  • the misch metal (Mm) is treated as "a rare earth element group containing any one of La, Ce, Pr, Nd, Sm, Y and Sc as a main component" as equivalent to them. .
  • Ce, La, Nd, Pr, and Sm do not form a solid solution in Mg at normal temperature, and when one or more of them is added by 1.0% by mass or more, the formability of the material is adversely affected as a precipitate. Exert.
  • Y and Sc form a solid solution in Mg at normal temperature, but if one or more of them is added in an amount of 0.5% by mass or more, the influence of solid solution hardening can not be ignored, which adversely affects the formability of the material.
  • the factor which each additional element exerts on the moldability of a raw material is independent, and it can be added combining a light rare earth element group.
  • the addition amount of Mn and Zr is preferably set to 0.01 to 0.8% by mass, more preferably 0.01 to 0.5% by mass.
  • the addition amount of Mn and Zr is preferably set to 0.01 to 0.8% by mass, more preferably 0.01 to 0.5% by mass.
  • Al is dissolved in magnesium at 1 to 2 mass% at normal temperature [Reference: Binary alloy phase diagrams, T. et al. B. Massalski (ed.) (American Society for Metals, Metals Park, Ohio, 1986), pp. 169-171], it is effective for material strengthening by means of solid solution strengthening.
  • the sample temperature is 400 ° C. or higher. ⁇ It is necessary to carry out warm processing.
  • the sample temperature suitable for the Mg—Zn—Ce based alloy and the Mg—Zn—La based alloy slightly differs depending on the presence or absence of the roll heating mechanism. When the roll has a heating mechanism and the roll surface can be heated to about 200 ° C., the sample temperature at the time of rolling can be set low. Specifically, the sample temperature may be set to about 400 to 430.degree.
  • the roll has no heating mechanism and the roll surface temperature is from normal temperature to 100 ° C., it is necessary to set the sample temperature before rolling to about 430 to 480 ° C. When the sample temperature before rolling is set to 500 ° C. or more, abnormal grain growth of crystal grains occurs at the time of heating, and the sample structure after rolling becomes nonuniform, and therefore, it should be avoided.
  • magnesium alloys mainly added with light rare earth elements other than Ce and La, and magnesium alloys added with Ca there is no restriction on the rolling temperature, and the formability can be achieved by performing hot and warm rolling. Can create a collective organization that contributes to the improvement of
  • FIGS. 5 to 8 show (0002) plane textures of a rolled rolled material of Mg-1.5% by weight Zn-0.08% by weight Ca alloy described later.
  • This sample was rolled to a thickness of 4 mm (reduction of 20%) or 1 mm (reduction of 80%) at a sample temperature of 450 ° C. or 350 ° C. and subjected to heat treatment of 350 ° C. (90 minutes). It is a result of a sample.
  • plane texture of the sample subjected to rolling at a rolling reduction of 20% a clear pole does not appear in the sheet width direction regardless of the sample temperature.
  • FIGS. 9 to 14 show (0002) plane textures before and after heat treatment of a rolled material of Mg-1.5 mass% Zn-0.08 mass% Ca alloy described later.
  • the pole of the (0002) plane does not appear in the sheet width direction regardless of the rolling temperature (390 ° C. and 450 ° C.).
  • the pole of the (0002) plane does not appear in the sheet width direction. That is, annealing is performed under appropriate conditions, 260 ° C., 10 minutes or more, preferably 300 ° C. or more, 10 minutes or more, and recrystallization with a new arrangement of grain boundaries does not occur. The pole does not appear, and the excellent cold formability does not appear.
  • the annealing conditions should be set to 450 ° C. or less and less than 3 hours.
  • recrystallization with a new arrangement of grain boundaries refers to recrystallization with the generation of new high angle grain boundaries during annealing, and is distinguished from recrystallization without the generation of high angle grain boundaries (so-called recovery). Be done.
  • recrystallization accompanied by the occurrence of high angle grain boundaries occurs when the processed metal is heated to a temperature of about 1/2 or more of the melting point. Since the melting point of magnesium is 650 ° C., it is most preferable to conduct annealing at 300 ° C. to 400 ° C. in order to cause recrystallization accompanied by a new arrangement of grain boundaries while suppressing grain growth during annealing. .
  • the magnesium alloy sheet produced by making full use of the above-mentioned element of the present invention exhibits a cold formability comparable to that of an aluminum alloy, that is, a formability having an Erichsen value of 8.0 or more at normal temperature (30 ° C.).
  • Erichsen value was adopted as an index showing the formability of the magnesium alloy sheet.
  • the Erichsen test refers to a test according to JIS B7729 and JIS Z2274.
  • An alloy sheet can be produced.
  • the (0002) plane texture of the rolled Mg-1.5% by mass-0.2% by mass Ce alloy used in the examples is shown, and the sample temperature is 390 ° C., and the thickness is rolled from 5 mm to 1 mm.
  • the texture of the sample before annealing is shown.
  • Level No. in the figure. Is the order of Level-7 to Level 1 in order from the central Level-7 (the same applies to FIGS. 2 to 14).
  • the (0002) plane texture of the rolled Mg-1.5% by mass-0.2% by mass Ce alloy used in the examples is shown, and the sample temperature is 390 ° C., and the thickness is rolled from 5 mm to 1 mm.
  • the texture of the sample after annealing is shown.
  • the (0002) plane texture of the rolled Mg-1.5% by mass-0.2% by mass Ce alloy used in the example is shown, and the sample temperature is 450 ° C., and the thickness is rolled from 5 mm to 1 mm.
  • the texture of the sample before annealing is shown.
  • the (0002) plane texture of the rolled Mg-1.5% by mass-0.2% by mass Ce alloy used in the example is shown, and the sample temperature is 450 ° C., and the thickness is rolled from 5 mm to 1 mm.
  • the texture of the sample after annealing is shown.
  • the (0002) plane texture of Mg-1.5 mass% Zn-0.08 mass% Ca alloy rolled material rolled in different reduction ratios prepared in the examples is shown, and the sample temperature It shows rolling texture at 350 ° C. to a thickness of 4 mm, and further, a texture of a sample subjected to annealing at 350 ° C. for 90 minutes.
  • the (0002) plane texture of Mg-1.5 mass% Zn-0.08 mass% Ca alloy rolled material rolled in different reduction ratios prepared in the examples is shown, and the sample temperature It represents rolling texture at 350 ° C. to a thickness of 1 mm, and further, a texture of a sample subjected to annealing at 350 ° C. for 90 minutes.
  • the (0002) plane texture of Mg-1.5 mass% Zn-0.08 mass% Ca alloy rolled material rolled in different reduction ratios prepared in the examples is shown, and the sample temperature It shows rolling texture at 450 ° C. to a thickness of 4 mm, and further, a texture of a sample subjected to annealing at 350 ° C. for 90 minutes.
  • the (0002) plane texture of Mg-1.5 mass% Zn-0.08 mass% Ca alloy rolled material rolled in different reduction ratios prepared in the examples is shown, and the sample temperature It shows rolling texture at 450 ° C. to a thickness of 1 mm, and further, a texture of a sample subjected to annealing at 350 ° C. for 90 minutes.
  • the (0002) plane texture before and after heat treatment of the rolled Mg-1.5 mass% Zn-0.08 mass% Ca alloy prepared in the example is shown, and the sample temperature is 390 ° C., and the thickness is 5 mm.
  • the (0002) plane texture before and after heat treatment of the rolled Mg-1.5 mass% Zn-0.08 mass% Ca alloy prepared in the example is shown, and the sample temperature is 390 ° C., and the thickness is 5 mm. Of the sample rolled to 1 mm to a heat treatment of 250 ° C. (90 minutes).
  • the (0002) plane texture before and after heat treatment of the rolled Mg-1.5 mass% Zn-0.08 mass% Ca alloy prepared in the example is shown, and the sample temperature is 390 ° C., and the thickness is 5 mm. Of the sample rolled to 1 mm to a heat treatment of 350 ° C. (90 minutes).
  • the (0002) plane texture before and after heat treatment of the rolled Mg-1.5 mass% Zn-0.08 mass% Ca alloy prepared in the example is shown, and the sample temperature is 450 ° C., and the thickness is 5 mm.
  • the (0002) plane texture before and after heat treatment of the rolled Mg-1.5 mass% Zn-0.08 mass% Ca alloy prepared in the example is shown, and the sample temperature is 450 ° C., and the thickness is 5 mm. Of the sample rolled to 1 mm to a heat treatment of 250 ° C. (90 minutes).
  • the (0002) plane texture before and after heat treatment of the rolled Mg-1.5 mass% Zn-0.08 mass% Ca alloy prepared in the example is shown, and the sample temperature is 450 ° C., and the thickness is 5 mm. Of the sample rolled to 1 mm to a heat treatment of 350 ° C. (90 minutes).
  • Examples 1 to 39 and Comparative Examples 1 to 14 (1) Production of magnesium alloy sheet material containing light rare earth element After melting a pure magnesium ingot using a high frequency furnace, light rare earth elements (Y, Sc, La, Ce, Pr, Nd, Sm), misch metal (Mm) Mg alloy was produced by adding suitably), Zn, Mn, and Zr. The composition of Mm used is shown in Table 1.
  • Table 2 described later shows the composition of the Mg alloy material.
  • the magnesium alloy 50 ⁇ 30 ⁇ 50 mm 3
  • was subjected to hot extrusion (extrusion temperature 673 K, extrusion speed 3 mm / min, extrusion ratio 6) to produce an extruded plate (cross-sectional area: 50 ⁇ 5 mm 2 ).
  • test pieces of 60 mm ⁇ 50 mm ⁇ 5 mm were cut out and those test pieces were subjected to rolling.
  • the sample temperature during rolling was set to 350 ° C. to 450 ° C., the rolling speed was 5 m / min, the rolling reduction per pass was set to 15 to 20%, and a sample of 5 mm in thickness was rolled to 1 mm.
  • the rolled material was subjected to heat treatment at 350 ° C. for 90 minutes to produce a magnesium alloy sheet.
  • the roll diameter was 152 mm and the roll temperature was 80.degree.
  • a lubricant for ester hot rolling was used as a lubricant for the roll and the sample.
  • a rolled material of a commercial magnesium alloy (AZ31B: Mg-3 mass% Al-1 mass% Zn-0.5 mass% Mn) was produced.
  • Mg alloy was produced by melting pure magnesium and adding predetermined amounts of Ca, Zn, Al, Mn, and Zr using a high frequency furnace.
  • the composition of the Mg alloy material is shown in Table 3 to be described later.
  • the Mg alloy (50 ⁇ 30 ⁇ 50 mm 3 ) was subjected to hot extrusion (extrusion temperature 673 K, extrusion speed 3 mm / min, extrusion ratio 6) to produce an extruded plate (cross-sectional area: 50 ⁇ 5 mm 2 ).
  • test pieces of 60 mm ⁇ 50 mm ⁇ 5 mm were cut out, and those test pieces were subjected to rolling.
  • the sample temperature during rolling was 350 ° C. to 450 ° C.
  • the rolling speed was 5 m / min
  • the sample with a thickness of 5 mm was rolled to 4 mm or 1 mm.
  • the rolling reduction per pass was set to 15 to 20%.
  • the rolled material was subjected to annealing at 250 ° C. or 350 ° C. for 90 minutes.
  • the roll diameter was 152 mm, and the roll temperature was 80 ° C. or higher.
  • the (0002) plane texture of the magnesium alloy sheet was measured by the XRD method (Schultz reflection method), and the presence or absence of a pole in the TD direction of the (0002) plane was investigated.
  • a plate material of 20 mm ⁇ 20 mm ⁇ 1 mm was cut out from the rolled material, cut to a thickness of 0.5 mm, and a sample subjected to surface polishing with # 4000 SiC abrasive paper was used.
  • Table 2 summarizes the Erichsen value and the presence or absence of the pole in the TD direction which are the results of the Erichsen test and texture measurement of the magnesium alloy sheet material to which the light rare earth element is added.
  • Test Nos. 4 to 7, 10 to 25, 27 to 32 are examples, and sample Nos. 1 to 3, 8, 9, 26 are comparative examples.
  • the sample numbers 3 to 8 are the results when the amount of Ce is fixed at 0.2 mass% and the amount of Zn is changed.
  • test numbers 6 and 9 (Example 3, Comparative Example 5) in Table 2 are samples obtained by rolling an alloy having Zn of 1.5% by mass and Ce of 0.2% by mass at 450 ° C. or 390 ° C. Is the result of the Erichsen test.
  • Mg—Zn—Ce alloy when the rolling temperature was set to 450 ° C., a pole in the TD direction appeared in the (0002) face texture, and a formability of Erichsen value of 8.0 or more developed.
  • the test number 10 (Example 5) in Table 2 is an Erichsen test result of a sample obtained by rolling an alloy having Zn of 1.5% by mass and Ce of 0.5% by mass at 450 ° C. Even when the amount of Ce added was changed within the specified amount, a formability of Erichsen value of 8.0 or more appeared.
  • test numbers 11 and 12 (Examples 6 and 7) in Table 2 add 0.1 mass% Mn or 0.3 mass% Zr to Mg-1.5 mass% Zn-0.2 mass% Ce. Erichsen test results of the plate material. It can be seen that, even if Mn and Zr are added, the texture is modified to ensure high formability.
  • test numbers 13 to 16 (Examples 8 to 11) in Table 2, an alloy to which 1.5% by mass of Zn was added and 0.2 to 0.4% by mass of Y was added was used at a sample temperature of 350 ° C. to 450 It is an Erichsen test result of the sample rolled at ° C. It can be seen that, even if Ce is replaced by Y, at any rolling temperature, the texture is modified and the plate exhibits an Erichsen value of 8.0 or more.
  • test number 22-25 (Examples 17-20) in Table 2 makes Zn 1.5 mass%, La, Pr, Nd, and the alloy which added 0.2 mass% Sm sample temperature 450 degreeC of rolling. Results of the Erichsen test of the sample. It can be seen that the Erichsen values of all samples show a value of 8.0 or more.
  • test numbers 26 to 29 are samples of an alloy in which Zn is 1.5 mass% and La, Pr, Nd and Sm are 0.2 mass% added. It is an Erichsen test result of the sample which temperature 390 degreeC rolled. The sample to which Pr, Nd, and Sm are added exhibits an Erichsen value of 8.0 or more. On the other hand, the Erichsen value of the sample to which La is added is less than 8.0.
  • test numbers 30 to 32 are Erichsen test results of alloys in which Zn is 1.0 to 1.5 mass% and Mm is 0.2 to 0.5 mass%. is there. Even when a mixture of light rare earth elements is used, it exhibits an Erichsen value of 8.0 or more.
  • Table 3 summarizes the Erichsen test of the magnesium alloy sheet material to which Ca is added and the pole in the TD direction.
  • the sample numbers 33 and 47 to 53 are comparative examples, and the sample numbers 34 to 46 are examples.
  • sample number 33 to sample number 36 are rolled to 1 mm at a sample temperature of 450 ° C, and subjected to heat treatment at 350 ° C (90 minutes) Is the result of
  • test numbers 35, 37 and 38 in Table 3 were such that the amount of Ca was 0.08 mass%, the amount of Zn was changed, the sample temperature was rolled to 1 mm at 450 ° C., and subjected to heat treatment at 350 ° C. (90 minutes) It is the result of the case.
  • Zn By setting Zn to a predetermined value, a pole in the TD direction appeared in the texture, and the Erichsen value showed a value of 8.0 or more.
  • the Zn content is 1.5 mass%
  • the Ca content is 0.04 mass% to 0.12 mass%
  • rolling is performed to 1 mm at a sample temperature of 350 ° C. or 390 ° C. It is a result at the time of using for heat processing at 350 degreeC (90 minutes).
  • the composition of the magnesium alloy was set to a predetermined value, a pole in the TD direction appeared in the texture regardless of the rolling temperature, and the Erichsen value showed a value of 8.0 or more.
  • the Zn content is 1.5% by mass
  • the Ca content is 0.08% by mass
  • the result is the result of heat treatment. If rolling is performed at a rolling reduction lower than the specified value, the pole in the TD direction does not appear in the texture even if heat treatment is performed.
  • test numbers 49 to 53 in Table 3 are the results of the samples rolled to 1 mm at a sample temperature of 350 ° C. to 450 ° C., with the amount of Zn being 1.5% by mass and the amount of Ca being 0.08% by mass. In the texture of the sample (Test No. 50, 52) not subjected to heat treatment, no pole in the TD direction appeared.
  • FIGS. 1 to 4 show the (0002) plane texture of the rolled Mg-1.5 mass% -0.2 mass% Ce alloy used in the examples. This represents the texture of a sample which has been rolled from a thickness of 5 mm to 1 mm at a predetermined sample temperature and further subjected to annealing at 350 ° C. for 90 minutes.
  • FIG. 1 shows the texture before annealing of the sample rolled at a sample temperature of 390 ° C.
  • FIG. 2 shows the texture after annealing of the sample rolled at a sample temperature of 390 ° C.
  • FIG. 3 shows the texture of the sample subjected to rolling at a sample temperature of 450 ° C. before annealing
  • FIG. 4 shows the texture of a sample subjected to rolling at a sample temperature of 450 ° C. after annealing.
  • 2 shows the texture of the sample of Test No. 9
  • FIG. 4 shows the texture of the sample of Test No. 6.
  • FIGS. 5 to 8 show (0002) surface textures of the rolled Mg-1.5 mass% Zn-0.08 mass% Ca alloy rolled at different reduction ratios used in the examples. This represents the texture of a sample subjected to rolling at a sample temperature of 350 ° C. or 450 ° C. to a thickness of 5 mm to 4 mm, or to a thickness of 5 mm to 1 mm, and further subjected to annealing at 350 ° C. for 90 minutes. It is.
  • FIG. 5 shows the texture of the sample rolled to 4 mm at 350 ° C. (Test No. 47)
  • FIG. 6 shows the texture of the sample rolled to 1 mm at 350 ° C. (Test No. 43)
  • 7 shows the texture of the sample rolled to 4 mm at 450 ° C. (Test No. 48)
  • FIG. 8 shows the texture of the sample rolled to 1 mm at 450 ° C. (Test No. 35).
  • FIGS. 9 to 14 show (0002) surface texture before and after heat treatment of the rolled Mg-1.5 mass% Zn-0.08 mass% Ca alloy used in the examples. This represents the texture of a sample subjected to rolling at a sample temperature of 390 ° C. or 450 ° C. to a thickness of 5 mm to 1 mm, and further subjected to annealing for 90 minutes at 250 ° C. or 350 ° C. for some samples. It is a thing.
  • FIG. 9 shows the texture of the sample before heat treatment rolled at 390 ° C. (Test No. 50), and FIG. 10 shows the sample rolled at 390 ° C. subjected to heat treatment at 250 ° C. (90 minutes)
  • the texture of the sample (Test No. 51)
  • FIG. 11 shows the texture of the sample obtained by subjecting the sample rolled at 390 ° C. to a heat treatment at 350 ° C. (90 minutes) (Test No. 45).
  • FIG. 12 shows the texture of the sample before heat treatment rolled at 450 ° C. (Test No. 52), and FIG. 13 shows the set of samples subjected to heat treatment at 250 ° C. (90 minutes) for the sample rolled at 450 ° C. The tissue is shown (Test No. 53) and FIG. 14 shows the texture of a sample obtained by subjecting a rolled sample at 450 ° C. to a heat treatment at 350 ° C. (90 minutes) (Test No. 35).
  • the present invention relates to an easily formable magnesium alloy sheet material and a method for producing the same, wherein a specific amount of light rare earth elements (Y, Sc, La, Ce, Pr, Nd, Sm
  • a specific amount of light rare earth elements Y, Sc, La, Ce, Pr, Nd, Sm
  • An alloy containing at least one of Zn, Zn, and optionally Mn and Zr added is subjected to hot and warm rolling, and is further subjected to an appropriate heat treatment to form easily formable magnesium without using Li.
  • An alloy sheet can be produced.
  • an alloy prepared by adding a specified amount of Ca, Zn and, if necessary, Al, Mn, and Zr to magnesium is subjected to hot and warm rolling, and is further subjected to an appropriate heat treatment to obtain Li.
  • An easily formable magnesium alloy sheet material can be produced without using it.
  • a pole of (0002) face appears in the sheet width direction in the (0002) face texture of the manufactured magnesium alloy sheet, and by reforming the texture, according to the aluminum alloy or comparable at normal temperature (30 ° C.) Formability.
  • the present invention is an easily formable magnesium alloy sheet material that can be actively applied mainly to a press-formed body of a home appliance such as a digital camera, a notebook computer, a PDA, etc., members such as the press-formed body and the casing It is useful as what provides.

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Abstract

L'invention porte sur une tôle d'alliage de magnésium facilement formable présentant une excellente aptitude au formage et sur un procédé permettant sa fabrication, plus spécifiquement sur un procédé pour la fabrication d'une tôle d'alliage de magnésium facilement formable qui présente un pôle dans la direction transverse de la tôle de texture du plan (0002) et une valeur d'indice Erichsen supérieure ou égale à 8,0 à température ordinaire, consistant à soumettre soit un alliage de magnésium contenant un ou plusieurs éléments terres rares légers, Zn et, si nécessaire, Mn et/ou Zr en quantités prescrites, soit un alliage de magnésium contenant Ca, Zn et, si nécessaire, un ou plusieurs éléments parmi Al, Mn et Zr en quantités prescrites, à un laminage à chaud ou tiède, puis à un recuit; sur une telle tôle d'alliage de magnésium facilement formable; et sur des articles fabriqués à l'aide de celle-ci. Ainsi, l'invention porte sur une tôle d'alliage de magnésium facilement formable applicable à des éléments formés à la presse pour des appareils électriques ménagers tels qu'un appareil photo numérique, un ordinateur portatif et un assistant numérique personnel; et sur des articles fabriqués à l'aide de la tôle.
PCT/JP2009/002536 2008-06-05 2009-06-04 Tôle d'alliage de magnésium facilement formable et son procédé de fabrication Ceased WO2009147861A1 (fr)

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Publication number Priority date Publication date Assignee Title
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WO2021131205A1 (fr) * 2019-12-23 2021-07-01 住友電気工業株式会社 Plaque en alliage de magnésium et matériau de bobine en alliage de magnésium
WO2021215241A1 (fr) 2020-04-21 2021-10-28 国立研究開発法人産業技術総合研究所 Alliage de magnésium, plaque en alliage de magnésium, tige en alliage de magnésium, procédés de production de ceux-ci et élément en alliage de magnésium
CN113073275B (zh) * 2021-03-22 2021-11-30 湖南工程学院 具有四峰非基面织构特征的镁合金板材的制备方法

Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2005298885A (ja) * 2004-04-09 2005-10-27 Nippon Kinzoku Co Ltd 塑性加工性に優れたマグネシウム又はマグネシウム合金の板及びその製造方法

Family Cites Families (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH06293944A (ja) * 1993-04-06 1994-10-21 Nippon Steel Corp プレス成形性に優れたマグネシウム合金薄板の製造方法
JP3657217B2 (ja) * 2001-10-19 2005-06-08 日本金属株式会社 熱間圧延用マグネシウム合金スラブの製造方法及びマグネシウム合金の熱間圧延方法

Patent Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2005298885A (ja) * 2004-04-09 2005-10-27 Nippon Kinzoku Co Ltd 塑性加工性に優れたマグネシウム又はマグネシウム合金の板及びその製造方法

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CN110117743A (zh) * 2019-05-24 2019-08-13 珠海中科先进技术研究院有限公司 一种耐蚀高强韧镁合金管材及制备工艺
CN113278857A (zh) * 2021-04-02 2021-08-20 中国兵器科学研究院宁波分院 一种高强韧镁合金及其制备方法
CN113444945A (zh) * 2021-07-02 2021-09-28 云南大学 一种具有环形发散织构的高塑性、高成形性镁合金板材及其制备方法
CN115044813A (zh) * 2022-04-29 2022-09-13 北京工业大学 一种低成本高强度镁合金材料及其制备方法
CN117051296A (zh) * 2023-08-16 2023-11-14 浙江镁格尼亚新材料有限公司 一种耐腐蚀镁合金材料及其制备方法
CN118028671A (zh) * 2023-12-25 2024-05-14 鞍钢股份有限公司 一种拉深性能良好的稀土镁合金板带及其制备方法

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