WO2006095999A1 - Alliages mg contenant un mischmetal, procede de production d'alliages mg corroyes contenant un mischmetal et alliages mg corroyes obtenus - Google Patents

Alliages mg contenant un mischmetal, procede de production d'alliages mg corroyes contenant un mischmetal et alliages mg corroyes obtenus Download PDF

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WO2006095999A1
WO2006095999A1 PCT/KR2006/000800 KR2006000800W WO2006095999A1 WO 2006095999 A1 WO2006095999 A1 WO 2006095999A1 KR 2006000800 W KR2006000800 W KR 2006000800W WO 2006095999 A1 WO2006095999 A1 WO 2006095999A1
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Prior art keywords
misch metal
magnesium alloy
magnesium
hot
wrought
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PCT/KR2006/000800
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English (en)
Inventor
Dong-Hyun Bae
Jin-Wook Kwon
Yule Kim
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Dong-Hyun Bae
Jin-Wook Kwon
Yule Kim
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Priority claimed from KR1020050019242A external-priority patent/KR100671195B1/ko
Priority claimed from KR1020050027811A external-priority patent/KR100671196B1/ko
Application filed by Dong-Hyun Bae, Jin-Wook Kwon, Yule Kim filed Critical Dong-Hyun Bae
Priority to JP2008500622A priority Critical patent/JP2008536005A/ja
Priority to US11/908,148 priority patent/US20080138236A1/en
Publication of WO2006095999A1 publication Critical patent/WO2006095999A1/fr

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/06—Making non-ferrous alloys with the use of special agents for refining or deoxidising
    • 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
    • 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
    • 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

Definitions

  • the present invention relates to a magnesium alloy with a misch metal, in which a great deal of misch metal is added to magnesium, thereby having a network structure or a dispersed phase which is stable at a high temperature and thus exhibiting excellent mechanical properties. Further, the present invention relates to a method of producing a wrought magnesium alloy which granulates solidification structures, i.e. secondary phases or multi-phases, by means of hot extrusion and hot rolling, and ultra-refines grains of a matrix, and a wrought magnesium alloy produced by the method.
  • ⁇ 2> Today, as environmental and saveenergy problems attract a lot of attention all over the world, it is absolutely required to make parts lighter in weight. There are stronger and stronger requests that an environmental pollution problem resulting from carbon dioxide generated during transportation by road, aviation, and rail should be solved, and that parts or end-products should be made lighter in order to save a transportation fuel.
  • a magnesium alloy suggests a most efficient possibility of making the products lighter, because it has the lowest density among commercial alloys, namely 2/3, and 1/5 times as low density as an aluminum alloy, and a ferrous alloy, respectively.
  • the magnesium alloy has excellent specific strength, rigidity, vibration absorptivity, machinability, dimension stability, and electromagnetic wave shielding effects, so that it is widely used as sheathings of electronic/telecommunication products such as mobile communication equipment and laptop computers.
  • the magnesium alloy for a high-temperature structure is classified into two types: a casting magnesium alloy used without heat treatment, and a sand casting magnesium alloy in which high-temperature properties are improved by precipitating a secondary phase in a matrix.
  • a casting magnesium alloy used without heat treatment a molten metal frequently generates an eddy when passing through the gate of a metal mold to enter a cavity, its product contains a number of blowholes. These remaining blowholes results in generating a blister on a surface of the product during heat treatment including solution heat treatment in the future, the product is not typically subjected to the heat treatment.
  • an AZ91 alloy, a Mg-Al alloy, which is widely used as the casting magnesium alloy at the present time is low in high-temperature properties, especially creep resistance.
  • the AZ91 alloy has a difficulty in being applied to parts exposed to a high temperature (150°C or more) such as a transmission case of an automobile. This is because, when aluminum is added to magnesium, room- temperature strength and fluidity of the molten metal are improved, but a phase of Mg 17 Ah 2 is formed to deteriorate the creep resistance property at a high temperture.
  • a phase of Mg 17 Ah 2 is formed to deteriorate the creep resistance property at a high temperture.
  • either addition of earth-rare elements or addition of calcium (Ca), silicon (Si), strontium (Sr), etc. as disclosed in U.S. Patent No. 6,264,763 is carried out.
  • addition elements should has a great solubility change in a magnesium matrix according to temperature, and maintain soubility at a temperature of 200°C or more, which is mainly used.
  • main addition elements of the sand casting magnesium alloy silver (Ag), thorium (Th), yttrium (Y), neodymium (Nd), scandium (Sc), etc. are used, each of which is too expensive or contains a radioactive substance. Thus, these elements have been restrictively used for the case of giving a greater weight on performance than a cost.
  • the magnesium alloy has a hexagonal close packed structure and restrictions of a slip system required for plastic working. For this reason, it is very difficult to form a product at a room temperature. Hence, the product should be formed through hot working.
  • a magnesium alloy with a misch metal has the formula expressed by Mgi O o- ⁇ - y - z A x B y C z , where A is zinc (Zn) or aluminum (Al); B is the misch metal; C is at least one element selected from the group consisting of manganese (Mn), nickel (Ni), copper (Cu), tin (Sn), yttrium (Y), phosphor (P), silver (Ag), and strontium (Sr); and x, y and z are the compositions of 0 at% ⁇ x ⁇ 6 at%, 0.8 at% ⁇ y ⁇ 7 at%, and 0 at% ⁇ z ⁇ 2 at%, respectively.
  • the misch metal may be a didymium-based misch metal or a cerium-based misch metal.
  • the didymium-based misch metal may be a rare earth alloy composition including neodymium (Nd) and praseodymium (Pr).
  • the cerium-based misch metal may contain 45 wt% ⁇ Ce ⁇ 65 wt%, 20 wt% ⁇ La ⁇ 30 wt%, 5 wt% ⁇ Nd ⁇ 15 wt%, and 0 wt% ⁇ Pr ⁇ 10 wt%.
  • the magnesium alloy may further comprise calcium of 2 at% or less.
  • a method of producing a wrought magnesium alloy with a misch metal comprises the steps of: fusion-casting a magnesium alloy composition having the formula of Mgioo- x -y- z A x ByC z , where A is zinc (Zn) or aluminum (Al); B is the misch metal; C is at least one element selected from the group consisting of manganese (Mn), nickel (Ni), copper (Cu), tin (Sn), yttrium (Y), phosphor (P), silver (Ag), and strontium (Sr); and x, y and z are the compositions of 0 at% ⁇ x ⁇ 6 at%, 0.8 at% ⁇ y ⁇ 7 at%, and 0 at% ⁇ z ⁇ 2 at%, respectively; and hot-extruding the cast, and refining grains through granulation and dispersion of other phases than magnesium in the cast, and recrystallization of a matrix.
  • the method may further comprise a step of hot-rolling the hot- extruded product to form a plate.
  • the hot-extruding step may be performed under the extrusion conditions of a temperature range from 350°C to 450°C, and a ratio of reduction in section of 5 ⁇ 80: 1.
  • the hot-rolling step may be performed under the rolling conditions of a temperature range from 350°C to 500 ° C, and a percentage of single reduction in thickness from 25% to 50%.
  • a wrought magnesium alloy with a misch metal is produced by the steps of: fusion-casting a composition having the formula of Mg 10 o- ⁇ - y - z A x ByC z , where A is zinc (Zn) or aluminum (Al); B is the misch metal; C is at least one element selected from the group consisting of manganese (Mn), nickel (Ni), copper (Cu), tin (Sn), yttrium (Y), phosphor (P), silver (Ag), and strontium (Sr); and x, y and z are the compositions of 0 at% ⁇ x ⁇ 6 at%, 0.8 at% ⁇ y ⁇ 7 at%, and 0 at% ⁇ z ⁇ 2 at%, respectively; hot- extruding the cast, and refining grains through granulation and dispersion of other phases than magnesium in the cast, and recrystallization of a matrix; and hot-rolling the hot-
  • the other phases than magnesium may have a size of 20 ⁇ m or less.
  • the other phases than magnesium may be contained from a solid- solution limit to a eutectic point or a hyper-eutectic area.
  • the misch metal is added, and thus refractory eutectic phases or multi-phases are formed into a stable network structure or a stable dispersed phase, thereby inhibiting deformation of a magnesium matrix at a high temperature.
  • other elements are additionally added, and thus precipitation/solid-solution is strengthened in a matrix structure or the network structure is strengthened, thereby having excellent mechanical properties in which a high strength is maintained at a high temperature.
  • a secondary-phase or multiphase magnesium alloy to which the misch metal is added is recrystallized by the hot extrusion and hot rolling, and the grains are refined.
  • the wrought magnesium alloy with the misch metal according to the present invention has a fine grain structure, and thus exhibits mechanical properties such as a high strength and a high toughness in a room- temperature area in which the alloy is substantially used. Further, the wrought magnesium alloy has a good elongation at a temperature at which formation is substantially carried out, and thus is improved in formability.
  • the magnesium alloy with the misch metal having excellent mechanical properties according to the present invention satisfies the requirements of high strength and heat resistance which are required for power transmission parts of a vehicle.
  • the magnesium alloy with the misch metal according to the present invention exhibits a high-temperature strength better than a heat-resistant magnesium alloy produced by existing heat treatment, so that it can be applied to parts for the vehicle and aircraft.
  • the magnesium alloy with the misch metal according to the present invention exhibits relatively better corrosion resistance than a previously commercialized heat-resistant magnesium alloy, so that it is used for lightweight parts capable of enduring severe conditions such as high temperature and corrosion.
  • the wrought magnesium alloy according to the present invention in the method of producing the wrought magnesium alloy according to the present invention, a magnesium alloy plate containing a great deal of ultra fine particles can be produced, and the produced plate has fine grains and very excellent formability. Accordingly, the wrought magnesium alloy of the present invention can make it lighter road, aviation, and rail transportations, and be widely used as sheathings of electronic/telecommunication products such as mobile communication equipment and laptop computers. [Description of Drawings]
  • FIG. 1 is a scanning electron microscope photograph showing a network structure of an alpha magnesium structure and a Mg ⁇ Ce phase in Alloy 3 of
  • FIG. 2 is a photograph of a molten metal, in which 2 wt% calcium (Ca) is added to Alloy 9 of Table 1 and fused in air;
  • FIG. 3 is a photograph showing a cast structure of an magnesium alloy around a eutectic point, according to a fifth embodiment;
  • FIG. 4 is a microstructure photograph showing a wrought product obtained by performing hot extrusion on a magnesium alloy at a temperature of
  • FIG. 5 is a microstructure photograph showing a wrought product formed by rolling a magnesium alloy under a roll temperature of 100°C with a single reduction in thickness of 40% at a temperature of a test piece of 400°C , according to a fifth embodiment;
  • FIG. 6 is a photograph showing wrought products that is prepared on the conditions of hot extrusion and rolling performed in a fifth embodiment, and -3 -1 -2 -1 subjected to a high-temperature tension test with strains 1x10 s , 1x10 s ,
  • FIG. 7 is a microstructure photograph showing a wrought product obtained by performing hot extrusion on a magnesium alloy at a temperature of
  • FIG. 10 is a microstructure photograph showing a wrought product formed by rolling a magnesium alloy under a roll temperature of 100°C with a single reduction in thickness of 40% at a temperature of a test piece of 400 ° C, according to a seventh embodiment.
  • a magnesium alloy with a misch metal according to the present invention has the formula expressed by Mgioo-x-y-zAxByCz, where A is zinc (Zn) or aluminum
  • B is the misch metal
  • C is at least one element selected from the group consisting of manganese (Mn), nickel (Ni), copper (Cu), tin (Sn), yttrium (Y), phosphor (P), silver (Ag), and strontium (Sr); and
  • x, y and z are the compositions of 0 at% ⁇ x ⁇ 6 at%, 0.8 at% ⁇ y ⁇ 7 at%, and 0 at% ⁇ z ⁇ 2 at%, respectively.
  • Secondary phases are crystallized by the misch metal (element B), and form a network structure or a dispersed phase that is compositely constructed with a magnesium matrix.
  • This network structure is stable at a high temperature, and thus provides excellent machanical properties.
  • tertiary phases can be created by element A and C groups, and mainly strengthen solid-solution/precipitation of the magnesium matrix or the network structure, thereby improving the mechanical properties.
  • the added aluminum is preferably restricted to 5 at% or less.
  • zinc (Zn) has a peak solid-solution limit of 2.4% at 340°Cwith respect to magnesium (Mg).
  • an addition range of the element A group is preferably restricted to 5 at% or less.
  • the magnesium alloy with the misch metal according to the present invention aluminum (Al) and zinc (Zn) of the element A group having solubility with respect to magnesium are contained in Mg-misch metals, so that multiphases can be obtained.
  • the added misch metal is composed of elements having atomic numbers 57 through 71, and includes a didymium-based misch metal or a cerium-based misch metal.
  • the didymium-based misch metal is a rare earth alloy composition including neodymium (Nd) and praseodymium (Pr).
  • the cerium-based misch metal refers to a commercialized misch metal alloy which has a main composition of 45 wt% ⁇ Ce ⁇ 65 wt%, 20 wt% ⁇ La ⁇ 30 wt%, 5 wt% ⁇ Nd ⁇ 15 wt%, and 0 wt% ⁇ Pr ⁇ 10 wt%, and in which other 15 or more trace elements are present in view of a characteristic in which the misch metal is crystallized.
  • This misch metal (element B) is caused to form a network structure or a dispersed phase which is stable at a high temperature, and improve corrosion and fluidity of the molten metal.
  • an addition range of the misch metal (element B) exceeds 7 at%, this is not favorable because a fraction of the secondary phase causing brittleness is increased, so that the elongation of the material is removed at a room temperature.
  • the addition range of the misch metal (element B) is restricted to 7 at% or less.
  • an element C group Si, P, B, Mn, Sr, Y, Ni, Cu, Sn, and Ag.
  • the added element C group has a strong affinity with magnesium (Mg) or the misch metal.
  • Exemplary examples of the element C group are phosphor (P), boron (B), manganese (Mn), strontium (Sr), yttrium (Y), nickel (Ni), copper (Cu), tin (Sn), and silver (Ag). Accordingly, an addition range of the element C group is restricted to 2 at% or less so as to be able to expect effects caused by the precipitation/solid-solution strengthening of the matrix structure while maintaining or strengthening the stable network structure at a high temperature.
  • a small amount of calcium (Ca) is added, so that the magnesium alloy composition can be fused and cast in air without using a shielding gas or flux.
  • An addition range of calcium is restricted to 2 at% or less, so as to be able to provide favorable effects of calcium (Ca).
  • a molten metal of a magnesium alloy composition as given in the following Table 1 was prepared, and a cast was obtained by casting. More specifically, a carbon crucible was heated in an electric induction furnace at a temperature of 700°C. Magnesium was fused in the carbon crucible, and then other addictives were added. Thereby, a molten alloy was formed and poured into a mold, which was pre-heated up to 1200°C . Thereby, the cast was formed.
  • FIG. 1 is a scanning electron microscope photograph of Alloy 3, and shows that an alpha magnesium structure and the Mg 12 Ce phase form a network structure. Because the structures forming the network structure were stable at a high temperature and thus inhibited deformation of the alpha magnesium structure, they exhibited a high strength at a high temperature. Thus, as an amount of element B increased, the Mg 12 Ce phase increased as well, and both a yield strength and a tensile strength increased at room and high temperatures. Further, in the case of Alloy 10, the MgI 2 Ce phase, as the secondary phase, as well as a tertiary phase were crystallized in the form of an aluminum compound, and thereby mechanical properties were improved. ⁇ 54> [Table 1]
  • Alloy l Mg 97 .5ZnJB 1 .5, Alloy 2: Mg 97 Zn 1 B 2 , Alloy 3: Mg 96 .5Zn 1 B 2 .5, ⁇ 60> Alloy 4: Mgg5.5Zn1.5B3, Alloy 5: Mg 96 Zn 2 B 2 , Alloy 6: Mg 95 .5Zn 2 B 2 .5, ⁇ 6i> Alloy 7: Mg 95 Zn 2 B 3 , Alloy 8: Mg 94 .
  • Alloy 9 Mg 94 Zn 2 B 4 , ⁇ 62> Alloy 10: Mg 94 Zn 2 B 4 , Alloy 11: Mg 92 .5Zn 2 . 5 B 5 , Alloy 12: Mg 89 .5Zn 3 .5B 7 .
  • the magnesium alloys with the misch metal according to the present invention were capable of replacing heat-treatment type sand casting heat-resistant magnesium alloys that maintained a high strength at a temperature of 300°C or more, and were mainly used at a temperature of 200°C or more, and magnesium alloys formed by die casting, because the secondary or tertiary phase network structure in which the change in strength depending on the change in temperature was very small was formed.
  • FIG. 2 is a photograph of a molten metal, in which 2 wt% calcium (Ca) is added to Alloy 9 of Table 1 and fused in air, and shows that a magnesium alloy composition can be fused and cast in air by adding calcium (Ca) to the magnesium alloy composition (e.g. Alloy 9). As can be seen from FIG. 2, it could be found that a thick oxide was not formed on a surface of the molten metal when the magnesium alloy composition was fused in air.
  • ⁇ 67> [Embodiment 3]
  • the Mg 12 Ce phase generated by adding the cerium (Ce)- based misch metal to magnesium (Mg) was an intermetallic compound and had brittleness.
  • the magnesium alloy has a property that an elongation was lowered. Therefore, in the current embodiment, an attempt was made to improve the property by adding a specific element.
  • Alloy 12 having the highest fraction of the Mg 12 Ce phase was selected from the compositions given in Table 1, and then it was examined how much the brittleness of the secondary phase was dependent on the addition element.
  • the molten metals of the magnesium alloy compositions were prepared as in Table 2, and casts were obtained by casting, and subjected to Vickers hardness testing. At this time, the examination was performed while the applied load of indentation was varied from lOOg to 100Og. In Table 2, it was shown that a hardness value increased by adding nickel (Ni), copper (Cu), tin (Sn), aluminum (Al), manganese (Mn), or silicon (Si) to Alloy 12.
  • Table 3 represents elongations obtained by performing a tensile test on the alloy compositions (e.g. Alloy 2 and Alloy 6) presented in Embodiment 1, to which Al is added. As shown in Table 3, it can be seen that, as a trace of Al is changed, the elongation increases. However, when Al is added in excess of 4 at%, this is not favorable, because the network structure capable of maintaining the high strength at a high temperature is not maintained, and a Mg 17 Al ⁇ phase is created in the magnesium matrix.
  • the magnesium alloys with the misch metal according to the present invention are high-temperature structural magnesium alloys in which the mechanical properties and the corrosion resistance are greatly improved, compared to the existing heat- resistant magnesium alloys.
  • a magnesium alloy cast to which the misch metal of the foregoing composition is added is extruded and rolled, and thereby a wrought product is formed.
  • the magnesium alloy cannot ensure formability at a room temperature.
  • the magnesium alloy cast is subjected to hot working, and a worked temperature of the magnesium alloy cast is set to a range capable of ensuring soundness of the magnesium alloy cast through a test.
  • the magnesium alloy cast was pre-heated and extruded within a range from 350 to 500 ° C .
  • the following extrusion conditions are used: an extrusion ratio: 6.5:1, an extrusion die angle:180° , a ram speed: 2 cm/min.
  • a grain refinement mechanism of the magnesium alloy with the misch metal according to the present invention makes use of a phenomenon of dynamic recrystallization in which a nucleus of a new grain is created in a structure during hot working of the magnesium alloy.
  • a recrystallization source is increased, and thus grain refinement is conducted in a considerably efficient way.
  • a magnesium alloy in which a volume fraction of other phases than magnesium of a matrix amounts to a range from 5% to 50% in order to maximize such a characteristic is first formed by casting, and the internal phases that are present in the magnesium alloy are effectively dispersed in the magnesium matrix through either hot extrusion or hot extrusion and hot rolling.
  • the wrought magnesium alloy with the misch metal according to the present invention is expressed by an ordinary chemical formula Mg 100 - X - V - Z A x ByCz, where A is zinc (Zn) or aluminum (Al), B is the misch metal, C is at least one element selected from the group consisting of manganese (Mn), nickel (Ni), copper (Cu), tin (Sn), yttrium (Y), phosphor (P), silver (Ag), and strontium (Sr), and x, y and z are the compositions of 0 at% ⁇ x ⁇ 6 at%, 0.8 at% ⁇ y ⁇ 7 at%, and 0 at% ⁇ z ⁇ 2 at%, respectively.
  • the added misch metal is composed of elements having atomic numbers 57 through 71, and includes a didymium-based misch metal or a cerium-based misch metal.
  • the didymium-based misch metal is a rare earth alloy composition including neodymium (Nd) and praseodymium (Pr), and particularly the cerium-based misch metal refers to a commercialized misch metal alloy which has a main composition of 45 wt% ⁇ Ce ⁇ 65 wt%, 20 wt% ⁇ La ⁇ 30 wt%, 5 wt% ⁇ Nd ⁇ 15 wt%, and 0 wt% ⁇ Pr ⁇ 10 wt%, and in which other 15 or more trace elements are present in view of a characteristic in which the misch metal is crystallized.
  • the magnesium alloy containing the great deal of phases as described above can be formed by casting.
  • the magnesium alloy is subjected to hot extrusion, its cast structure is subjected to fracture, and other phases than magnesium are granulated and dispersed. For this reason, the dynamic recrystallization phenomenon is effectively generated to refine the grain.
  • This hot extrusion makes it possible to perform additional, effective fracture and dispersion with respect to particles generated due to impure elements that are inevitably added during the casting of the magnesium alloy. Hence, an extruded product of the magnesium alloy can be made more stable.
  • an extruded product and a plate are formed using a Mg-Ce based misch metal-Zn alloy around a eutectic point.
  • FIG. 3 is a photograph of a cast structure of the Mg-Ce based misch metal-Zn alloy.
  • hot extrusion was performed at a temperature of 450°C, an extrusion speed of 2 mm/sec, a ratio of reduction in section of 6:1.
  • FIG. 4 is a microstructure photograph of a hot-extruded product of the present embodiment. As observed, no crack exists in an internal structure, and the grains are very fine, an average size of which is less than 14 ⁇ m. In general, in a particle-free magnesium alloy, this grain size cannot be obtained through single hot extrusion.
  • the plate of the magnesium alloy was formed by rolling the extruded product under a roll temperature of 100 0 C with a single reduction in thickness of 40% at a temperature of 400°C.
  • FIG. 5 is a microstructure photograph of a rolled plate. As observed, there is no crack, and the grains are very fine, an average size of which is less than 8 ⁇ m.
  • the magnesium alloy having the great deal of phases around the eutectic point was stably subjected to the hot extrusion and the hot rolling, and had excellent formability due to the grain refinement.
  • the present embodiment relates to production of an extruded product and a plate of a Mg-Ce misch metal of a hypo-eutectic area.
  • FIG. 7 is a microstructure photograph of this test piece hot-extruded on the condition, wherein there is no crack, and the grains are very fine, an average size of which is less than 15 ⁇ m.
  • FIG. 8 is a microstructure photograph of a wrought magnesium alloy that is subjected to hot extrusion, wherein there are created very fine grains, an average size of which is less than 8 ⁇ m, without a crack.
  • the present embodiment relates to production of an extruded product and a plate of a Mg-Ce misch metal-Zn alloy of a hypo-eutectic area.
  • FIG. 9 is a microstructure photograph of this test piece hot-extruded on the condition, wherein there is no crack inside, and an average grain size is less than 20 ⁇ m. Further, FIG.
  • FIG. 10 is a microstructure photograph of a wrought magnesium alloy that is subjected to hot extrusion, wherein the grains are very fine, an average size of which is less than 9 ⁇ m-
  • the magnesium alloy having the great deal of phases up to the hypo-eutectic area was stably subjected to the hot extrusion, and thus the grain refinement.

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Abstract

L'invention concerne un alliage de magnésium avec un mischmétal, un procédé de production d'un alliage de magnésium corroyé avec un mischmétal ainsi qu'un alliage de magnésium corroyé ainsi produit, dans lequel une grande quantité de mischmétal est ajoutée au magnésium et ainsi des phases ou multiphases réfractaires eutectiques sont transformées en une structure à réseau stable ou une phase dispersée stable, empêchant ainsi la déformation d'une matrice de magnésium à haute température afin de maintenir une haute résistance. l'alliage de magnésium avec le mischmétal présente la formule de Mg100-x-y-z AxByCz, dans laquelle A représente du zinc (Zn) ou de l'aluminium (Al); B représente le mischmétal; C représente au moins un élément choisi dans le groupe contenant du manganèse (Mn), du nickel (Ni), du cuivre (Cu), de l'étain (Sn), de l'yttrium (Y), du phosphore (P), de l'argent (Ag) ainsi que du strontium (Sr); et x, y et z sont les compositions de 0 % = x =6 %, 0,8 % = y = 7 %, et 0 % = z = 2 % respectivement.
PCT/KR2006/000800 2005-03-08 2006-03-07 Alliages mg contenant un mischmetal, procede de production d'alliages mg corroyes contenant un mischmetal et alliages mg corroyes obtenus WO2006095999A1 (fr)

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JP2008500622A JP2008536005A (ja) 2005-03-08 2006-03-07 ミッシュメタルが添加されたマグネシウム合金、ミッシュメタルが添加されたマグネシウム合金加工材の製造方法及びこれによって製造されるマグネシウム合金加工材
US11/908,148 US20080138236A1 (en) 2005-03-08 2006-03-07 Mg Alloys Containing Misch Metal Manufacturing Method of Wrought Mg Alloys Containing Misch Metal, and Wrought Mg Alloys Thereby

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KR1020050019242A KR100671195B1 (ko) 2005-03-08 2005-03-08 미시메탈이 첨가된 고온 구조용 마그네슘 합금
KR10-2005-0019242 2005-03-08
KR1020050027811A KR100671196B1 (ko) 2005-04-02 2005-04-02 입자 분산된 마그네슘 합금 가공재의 제조방법 및 이에 의해 제조되는 입자분산된 마그네슘 합금 가공재
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Cited By (5)

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US8361251B2 (en) * 2007-11-06 2013-01-29 GM Global Technology Operations LLC High ductility/strength magnesium alloys
EP2764130A4 (fr) * 2011-10-06 2016-03-09 Univ Pittsburgh Alliages métalliques biodégradables
CN104480362A (zh) * 2014-12-15 2015-04-01 苏州昊卓新材料有限公司 用于制备高韧性镁合金的方法
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