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WO2013180122A1 - Alliage de magnésium, élément en alliage de magnésium et procédé de fabrication de ce dernier, et procédé d'utilisation de l'alliage de magnésium - Google Patents

Alliage de magnésium, élément en alliage de magnésium et procédé de fabrication de ce dernier, et procédé d'utilisation de l'alliage de magnésium Download PDF

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Publication number
WO2013180122A1
WO2013180122A1 PCT/JP2013/064755 JP2013064755W WO2013180122A1 WO 2013180122 A1 WO2013180122 A1 WO 2013180122A1 JP 2013064755 W JP2013064755 W JP 2013064755W WO 2013180122 A1 WO2013180122 A1 WO 2013180122A1
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Prior art keywords
magnesium alloy
magnesium
mol
temperature range
alloy member
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Ceased
Application number
PCT/JP2013/064755
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English (en)
Japanese (ja)
Inventor
英俊 染川
嘉昭 大澤
敏司 向井
アロック シン
宏太 鷲尾
加藤　晃
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National Institute for Materials Science
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National Institute for Materials Science
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Priority to JP2014518675A priority Critical patent/JP6120380B6/ja
Priority to US14/390,833 priority patent/US20150083285A1/en
Priority to EP13797477.0A priority patent/EP2835437B1/fr
Publication of WO2013180122A1 publication Critical patent/WO2013180122A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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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
    • C22C1/02—Making non-ferrous alloys by melting
    • 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
    • C22C23/06—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
    • 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

Definitions

  • the present invention relates to a magnesium alloy to which a small amount of yttrium, scandium, or a lanthanoid rare earth element is added, and relates to a magnesium alloy member that can be easily plastically processed in a cold or room temperature range.
  • the present invention also relates to a method for producing a magnesium alloy member that is suitable for use in automobiles, railway vehicles, aerospace vehicles, housings for electronic devices, and the like, and that can be easily cold worked.
  • this type of magnesium alloy is desired to be used for reducing the weight of structural members.
  • Applications of structural members include automobiles, railway vehicles, aerospace vehicles, and electronic equipment housings.
  • the magnesium alloy is extremely difficult to be plastically worked in the cold or room temperature range, it has not been used for structural members.
  • wrought magnesium alloys such as rolling and extrusion have the problem of yield stress anisotropy, where the crystal orientation of the bottom surface ⁇ 0001 ⁇ is aligned with the processing direction, resulting in a large difference in yield stress during tension and compression. there were.
  • the cold temperature means room temperature or less than the recrystallization temperature of the material, but the cold working temperature of the magnesium alloy is usually 200 ° C. or less.
  • Patent Documents 1 and 2 disclose wrought magnesium alloys containing 0.1 to 1.5 mol% yttrium. This wrought magnesium alloy has the advantage of eliminating yield stress anisotropy and exhibiting excellent cold workability. However, since it contains yttrium, there is a problem that it is affected by the rise in yttrium prices.
  • Patent Documents 3 and 4 disclose a magnesium alloy rolled material containing 0.01 to 0.5 mol% of yttrium. This magnesium alloy rolled material has the advantage of low yttrium content. However, since the bottom surfaces are aligned in the rolling direction (FIG. 1 of Patent Document 4), there is a problem that it can be easily estimated that a large difference occurs in the yield stress between tension and compression.
  • Patent Documents 5 and 6 disclose a magnesium alloy rolled material having a small amount of yttrium and high workability.
  • This magnesium alloy rolled material has 6 to 16 mass% lithium added, and has a BCC (Body-Centered Cubic lattice, body-centered cubic lattice) in the ⁇ phase of the HCP (hexagonal close-packed structure). )
  • BCC Body-Centered Cubic lattice, body-centered cubic lattice
  • HCP hexagonal close-packed structure
  • Patent Document 7 discloses a magnesium alloy in which quasicrystalline particles are dispersed in a magnesium matrix to reduce yield stress anisotropy.
  • this magnesium alloy is made of an Mg—Zn—Re alloy and has a rare earth element content of 0.2 to 1.5 mol%.
  • rare earth elements are affected by the price increase. Therefore, a reduction in the amount of rare earth element added is required.
  • Patent Document 8 discloses a wrought magnesium alloy containing 0.03 to 0.54 mol% yttrium.
  • the average grain size of magnesium is 1.5 ⁇ m or less, and the strength of the material is increased by segregating yttrium at a high concentration in the vicinity of the grain boundary.
  • the crystal grains are fine, the grain boundary volume ratio is large, so that the solute element is present at a high concentration in the vicinity of the crystal grain boundary.
  • the solute element is not in the vicinity of the crystal grain boundary but exists as a solid solution in the crystal grain, so that the strength of the material cannot be increased. was there.
  • Magnesium alloys like other metal materials, are refined in crystal grain size and improved in strength and ductility by straining such as rolling and extrusion.
  • the bottom surface ⁇ 0001 ⁇ is aligned in the processing direction during hot processing, that is, a bottom surface texture is formed.
  • magnesium that has been rolled or extruded has the crystal orientation of the bottom surface parallel to the rolling or extrusion direction. Therefore, the compressive yield stress is only about 50-60% of the tensile yield stress and has a problem of yield stress anisotropy.
  • quasi-crystal particle dispersion Patent Document 7
  • alloying Patent Documents 1 to 6
  • etc. are used, both of which add 0.1 mol% or more of rare earth elements, There was a problem of being affected by the rising prices.
  • the first of the present invention provides a magnesium alloy in which the addition amount of yttrium, scandium, or a lanthanoid rare earth element is 0.02 mol% or more and less than 0.1 mol%, and the balance is Mg and inevitable impurities.
  • This magnesium alloy has a uniform composition and a uniform crystal structure with an average grain size of several ⁇ m to several tens of ⁇ m.
  • a magnesium alloy having the chemical composition of the first aspect is hot plastic processed in a temperature range of 200 ° C. or higher and 550 ° C. or lower, and then isothermally heat-treated in a temperature range of 300 ° C. or higher and 600 ° C. or lower.
  • a manufactured magnesium alloy member is provided. Isothermal heat treatment means that a sample of the magnesium alloy is placed in a bath maintained at a constant temperature, held for a predetermined time, and then the sample is removed from the bath and slowly cooled in the air. Say that will be.
  • the magnesium alloy member refers to a magnesium wrought material such as a plate material, a bar material, or a pipe material.
  • a third aspect of the present invention provides a magnesium alloy member according to the second aspect of the present invention, wherein the crystal structure of the member is an equiaxed grain structure and has no texture.
  • An equiaxed grain means a three-dimensional isotropic grain structure that does not stretch or flatten in one direction.
  • the texture is a distribution state of crystal lattice orientation (crystal orientation) of each crystal grain present in a polycrystalline material such as metal, and is also referred to as a crystal texture. For example, when a cubic metal is solidified, the preferred orientation [100] is formed.
  • the bottom surface ⁇ 0001 ⁇ is easily oriented in the strain applying direction.
  • a fourth aspect of this invention is a magnesium alloy member of the invention 2 or 3, Comprising: An average crystal grain diameter provides the magnesium alloy member which is 10 micrometers or more.
  • a fifth aspect of the present invention is the magnesium alloy member according to any one of the second to fourth aspects, wherein the room temperature (in this specification, the room temperature is 15 ° C. to 35 ° C .; the same shall apply hereinafter) to 150 ° C.
  • the room temperature in this specification, the room temperature is 15 ° C. to 35 ° C .; the same shall apply hereinafter
  • a magnesium alloy member imparted with a compressive nominal strain of 0.4 or more by cold working.
  • a sixth aspect of the present invention is the magnesium alloy member according to any one of the second to fifth aspects, wherein the average diameter of the cold-worked magnesium alloy crystal grains in the temperature range from room temperature to 150 ° C.
  • the first aspect of the present invention is that the content of one or more elements selected from yttrium, scandium, and lanthanoid rare earth elements is 0.02 mol% or more and less than 0.1 mol%, with the balance being magnesium and inevitable impurities.
  • a magnesium alloy member characterized by subjecting an alloy to hot plastic working in a temperature range of 200 ° C. to 550 ° C., and isothermally heat-treating the hot plastic processed magnesium alloy in a temperature range of 300 ° C. to 600 ° C. It is a manufacturing method.
  • the second aspect of the present invention is that the content of one or more elements selected from yttrium, scandium, and lanthanoid rare earth elements is 0.02 mol% or more and less than 0.1 mol%, with the balance being magnesium and inevitable impurities.
  • a method of using an alloy wherein the magnesium alloy is hot plastic processed in a temperature range of 200 ° C. to 550 ° C., and the hot plastic processed magnesium alloy is isothermally heat treated in a temperature range of 300 ° C. to 600 ° C. And it is the usage method of the magnesium alloy characterized by using as a magnesium extended material.
  • the present invention induces room temperature recrystallization (crystal grain refinement) by controlling the dispersion state of one or more elements selected from yttrium, scandium, and lanthanoid rare earth elements contained in a magnesium alloy. Compression deformation characteristics can be developed. Since the magnesium alloy member of the present invention has a random crystal orientation distribution (after processing), the problem of yield stress anisotropy is solved, and the yield stress during tensile and compressive deformation is maintained while maintaining a high strength level. The same magnesium alloy member is obtained. In addition, the magnesium alloy member of the present invention does not break and exhibits excellent deformability even when a large compressive strain exceeding 50% is applied.
  • the magnesium alloy of the present invention has an extremely small amount of yttrium, scandium, and lanthanoid rare earth elements added, so the effect of the material price of yttrium, scandium, and lanthanoid rare earth elements is less than that of conventional rare earth-added magnesium alloys. Can be reduced.
  • FIG. 1 is a photograph of the appearance of a material when the hot working temperature is in an appropriate range.
  • FIG. 2 is a nominal stress-nominal strain curve obtained by a room temperature tensile / compression test of the Mg-0.05Y extruded material and the Mg-0.05Y extruded + heat treated material.
  • FIG. 3 is a nominal stress-nominal strain curve obtained by room temperature compression test of the Mg—Y alloy extruded material.
  • FIG. 4 is a nominal stress-nominal strain curve obtained by room temperature compression test of Mg—Y alloy extrusion + heat treated material.
  • FIG. 5 is a nominal stress-nominal strain curve obtained by room temperature compression test of Mg-1 mol% Y casting + heat treated material.
  • FIG. 1 is a photograph of the appearance of a material when the hot working temperature is in an appropriate range.
  • FIG. 2 is a nominal stress-nominal strain curve obtained by a room temperature tensile / compression test of the Mg-0.05Y extruded
  • FIG. 6 is a photograph of Mg—0.03Y extruded + heat treated material observed by scanning electron microscope / electron beam backscatter diffraction.
  • FIG. 7 is a positive dot diagram of the region observed in FIG. 5, where ED indicates a parallel direction to the extrusion process and TD indicates a vertical direction with respect to the extrusion process.
  • FIG. 8 is a photograph observed by scanning electron microscope / electron beam backscatter diffraction after 20% compression strain was applied to the extruded Mg-0.03Y + heat treated material.
  • FIG. 9 is a photograph observed by scanning electron microscope / electron beam backscatter diffraction after 50% compression strain was applied to the Mg-0.03Y extruded + heat treated material.
  • FIG. 10 is an appearance photograph of the material when the hot working temperature is low.
  • the magnesium alloy of the present invention contains one or more elements selected from yttrium, scandium, and lanthanoid rare earth elements.
  • a magnesium alloy containing yttrium and an alloy member thereof will be described as an embodiment of the magnesium alloy and the alloy member thereof according to the present invention.
  • the magnesium alloy is subjected to hot plastic working (hereinafter also referred to as “hot working”), yttrium is segregated at the grain boundaries, and then crystallized by isothermal heat treatment. It is necessary to diffuse yttrium in the grains. The procedure is shown below.
  • the magnesium alloy has a yttrium content of 0.02 mol% or more and less than 0.1 mol%, with the remainder being composed of magnesium and inevitable impurities.
  • the yttrium content is preferably 0.025 mol% or more and less than 0.1 mol%, more preferably 0.025 mol% or more and less than 0.05 mol%.
  • yttrium content is 0.02 mol%, yttrium is present at a radius of 19.5 ⁇ 10 ⁇ 10 m. This value corresponds to about three times the size of the Burgers vector of magnesium, and means that it is a limit value at which lattice defects such as dislocations interact in terms of atomic bond theory.
  • the Burgers vector represents the direction of disagreement of atoms around a dislocation line, which is a linear crystal defect contained in the crystal.
  • the dislocation line and the Burgers The vector is vertical, and for screw dislocations, the dislocation line and Burgers vector are parallel.
  • the temperature of hot plastic working is preferably 200 ° C. or higher and 550 ° C. or lower, and more preferably 250 ° C. or higher and 350 ° C. or lower.
  • FIG. 1 is a photograph of the appearance of a material when the hot working temperature is in an appropriate range.
  • FIG. 10 is an appearance photograph of the material when the hot working temperature is low.
  • an appropriate magnesium alloy member can be manufactured by setting the hot working temperature to an appropriate temperature range.
  • the processing temperature is high, so it is difficult to make the average crystal grain size 10 ⁇ m or less.
  • the hot working is typically extrusion, forging, rolling, or drawing, but may be any plastic working method that can impart strain.
  • the equivalent plastic strain at the time of strain application is 1.5 or more, preferably 2.0 or more.
  • the equivalent plastic strain is less than 1.5, the strain is not sufficiently applied, so that a mixed structure of coarse grains and fine grains is exhibited, and it is difficult for yttrium to segregate uniformly near the grain boundaries.
  • yttrium does not diffuse and disperse uniformly in the crystal grains when only the isothermal heat treatment is performed on the cast material without performing hot working. The effect of the present invention cannot be obtained.
  • the temperature of the isothermal heat treatment is preferably equal to or higher than the hot working temperature.
  • the temperature is preferably 300 ° C. or higher and 600 ° C. or lower, and more preferably 350 ° C. or higher and 450 ° C. or lower.
  • the holding time is related to the heat treatment temperature, but is preferably 3 minutes or longer and 24 hours or shorter. When the holding time exceeds 24 hours, there is a concern that abnormal grain growth occurs during the heat treatment.
  • a magnesium alloy member having an equiaxed grain structure and no texture A magnesium alloy member having an average crystal grain size of 10 ⁇ m or more, for example, a magnesium alloy member having an average crystal grain size of 30 ⁇ m or more and 50 ⁇ m or less can also be obtained.
  • the obtained magnesium alloy member can be subjected to cold plastic working (hereinafter also referred to as “cold working”) in a temperature range from room temperature to 150 ° C.
  • cold plastic working for example, a compression nominal strain of 0.4 or more can be applied.
  • the upper limit is 1.5.
  • the crystal grains of the magnesium alloy member are refined by cold working.
  • the average crystal grain size of the magnesium alloy part before cold working can be 80% or less, and the lower limit is not particularly limited, but is 5%.
  • the hardness and strength of the magnesium alloy member can be increased by refining crystal grains by cold working.
  • the hardness of the magnesium alloy member after cold working can be made 15% or more harder than the hardness of the magnesium alloy part before cold working.
  • the strength can also be higher by 15% or more than the strength of the magnesium alloy part before cold working.
  • the magnesium alloy is hot-worked, yttrium is segregated at grain boundaries, and then the yttrium is dispersed in the crystal grains by isothermal heat treatment, thereby controlling the dispersion state of yttrium. ing. And the crystal grain is refined
  • magnesium alloy containing yttrium and the alloy member thereof have been described, but the present invention is not limited to this embodiment.
  • Magnesium alloys in which part or all of yttrium is replaced with scandium, lanthanoid rare earth elements such as lanthanum and cerium, or scandium and lanthanoid rare earth elements, and alloy members thereof are also included in the present invention.
  • Lanthanoid elements such as scandium, lanthanum, cerium and the like are elements of the same family as yttrium. They are elements that are located above or below the yttrium in the periodic table and have many similar chemical and physical properties.
  • the magnesium alloy containing yttrium and its alloy member can exhibit the intended effect of the present invention more effectively.
  • Yttrium (Y) and pure magnesium (Mg) are completely dissolved in an argon atmosphere, cast into an iron mold, and Y target content is 0.01 mol%, 0.02 mol%, 0.03 mol %, 0.04 mol%, and 0.05 mol% of five types of Mg—Y alloy castings were melted.
  • Y target content: 0.03 mol%, 0.04 mol%, 0.05 mol% are examples within the scope of the present invention, Y target content: 0.01 mol%, 0.02 mol% are within the scope of the present invention. It is an outside comparative example.
  • the Y content and other elemental composition concentrations were evaluated by ICP emission spectroscopic analysis after solution treatment of the cast material at 500 ° C. for 2 hours. The results of the composition analysis are shown in Table 1. All five types of alloys were prepared according to the following procedures and conditions.
  • the obtained cast material was subjected to a solution treatment by water cooling after being held in a furnace at a temperature of 500 ° C. for 2 hours. Thereafter, a cylindrical extruded billet having a diameter of 40 mm and a height of 70 mm was produced by machining. The same billet was held in a container held at the extrusion temperature shown in Table 2 for 30 minutes, and then subjected to hot straining by extrusion at an extrusion ratio of 25: 1 to produce an extruded material. Hereinafter, it is referred to as an extruded material.
  • the average equivalent plastic strain obtained from the cross-sectional reduction rate is 3.7.
  • This extruded material was kept isothermal in a furnace at a temperature of 400 ° C. for 15 minutes, and then a sample was prepared by air cooling. Hereinafter, it is referred to as extrusion + heat treatment material.
  • the produced Mg—Y alloy was subjected to a room temperature tensile / compression test at a strain rate of 1 ⁇ 10 ⁇ 3 s ⁇ 1 with respect to a test piece taken from the above extruded material and the extruded + heat treated material. All specimens were taken from a direction parallel to the extrusion direction. 2 to 4 show the nominal stress-nominal strain curves obtained by the room temperature tensile / compression test. Regardless of the amount of yttrium added, it can be confirmed that the extruded material breaks in the range of nominal strain of 0.2 to 0.3.
  • the case where the stress is reduced by 20% or more is defined as “ruptured”, and is indicated as BK in the drawing.
  • the extruded + heat treated material of Mg-0.01Y or Mg-0.02Y is broken at a nominal strain of 0.2 to 0.3, whereas Mg-0.03Y, Mg-0
  • the .04Y and Mg-0.05Y extruded + heat treated materials did not break even when a nominal strain of 0.5 was applied. From these results, it is suggested that the extruded and heat-treated materials of Mg-0.03Y, Mg-0.04Y and Mg-0.05Y are rich in cold working.
  • a Mg-1 mol% Y alloy was melted by a casting method, subjected to a solution treatment, and then subjected to a room temperature compression test without performing hot working.
  • FIG. 5 shows the result. Although the yttrium addition amount is large, it can be confirmed that the fracture occurs at a nominal strain of about 0.3. In order to obtain the effects of the present invention, it can be said that hot straining is indispensable after casting.
  • FIG. 7 shows a positive electrode dot diagram of the region observed in FIG. Each point corresponds to the crystal orientation of the measured crystal grain, but it can be seen that the bottom surface does not accumulate in a specific direction (extrusion direction) and is a random texture.
  • the average diameter of crystal grains having an orientation difference of 15 ° or more is 30 ⁇ m, and it can be confirmed that the grain size is 75% larger than the initial grain diameter by room temperature recrystallization.
  • LG represents a small-angle grain boundary having a misorientation of less than 15 °, and it can be said that room temperature recrystallization is largely due to the formation of a small-angle grain boundary of about 5 ° in the crystal grain.
  • FIG. 10 is an appearance photograph of the material of the comparative example and shows a case where dynamic recrystallization hardly occurs because the processing temperature is low. In the comparative example, since dynamic recrystallization hardly occurs, a sound material cannot be produced.
  • the present invention induces room temperature recrystallization (grain refinement) by controlling the dispersion state of one or more elements selected from yttrium, scandium, and lanthanoid rare earth elements contained in a magnesium alloy. It is characterized by exhibiting compression deformation characteristics.
  • the magnesium alloy member of the present invention is characterized in that the crystal orientation distribution (after processing) is random, so that the yield stress during tensile and compressive deformation is the same while maintaining a high strength level. Therefore, the magnesium alloy member of the present invention can be used as a magnesium expanded material such as a plate material, a bar material, and a pipe material.
  • the magnesium alloy member of the present invention can be used as a structural material or a shock absorbing material for automobiles / railway vehicles, aerospace vehicles, and portable electronic devices.

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PCT/JP2013/064755 2012-05-31 2013-05-28 Alliage de magnésium, élément en alliage de magnésium et procédé de fabrication de ce dernier, et procédé d'utilisation de l'alliage de magnésium Ceased WO2013180122A1 (fr)

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JP2014518675A JP6120380B6 (ja) 2012-05-31 2013-05-28 マグネシウム合金、マグネシウム合金部材並びにその製造方法、マグネシウム合金の使用方法
US14/390,833 US20150083285A1 (en) 2012-05-31 2013-05-28 Magnesium alloy, magnesium alloy member and method for manufacturing same, and method for using magnesium alloy
EP13797477.0A EP2835437B1 (fr) 2012-05-31 2013-05-28 Alliage de magnésium, élément en alliage de magnésium et procédé de fabrication de ce dernier, et procédé d'utilisation de l'alliage de magnésium

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JP2012124127 2012-05-31

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EP3072989A1 (fr) 2015-03-23 2016-09-28 Fuji Jukogyo Kabushiki Kaisha Alliage de magnésium-lithium, procédé de fabrication associé, pièce d'aéronef et procédé de fabrication de pièce d'aéronef
WO2019013226A1 (fr) 2017-07-10 2019-01-17 国立研究開発法人物質・材料研究機構 Matériau d'alliage de corroyage à base de magnésium et procédé de fabrication associé
WO2019017307A1 (fr) 2017-07-18 2019-01-24 国立研究開発法人物質・材料研究機構 Produit corroyé d'alliage à base de magnésium et procédé de production dudit produit
JP2019502821A (ja) * 2015-12-28 2019-01-31 コリア インスティテュート オブ マシーナリー アンド マテリアルズＫｏｒｅａ Ｉｎｓｔｉｔｕｔｅ Ｏｆ Ｍａｃｈｉｎｅｒｙ ＆ Ｍａｔｅｒｉａｌｓ 機械的特性及び耐蝕性に優れたマグネシウム合金及びその製造方法
US10851442B2 (en) 2015-03-25 2020-12-01 Subaru Corporation Magnesium-lithium alloy, rolled stock made of magnesium-lithium alloy, and processed product including magnesium-lithium alloy as material
US11060173B2 (en) 2016-03-10 2021-07-13 National Institute For Materials Science Wrought processed magnesium-based alloy and method for producing same

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EP3975942B1 (fr) 2019-06-03 2024-07-10 Fort Wayne Metals Research Products, LLC Alliages résorbables à base de magnésium
CN114700386B (zh) * 2022-03-25 2024-11-15 重庆大学 一种同时提高纯镁板材强度和塑性的方法

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JP2019502821A (ja) * 2015-12-28 2019-01-31 コリア インスティテュート オブ マシーナリー アンド マテリアルズＫｏｒｅａ Ｉｎｓｔｉｔｕｔｅ Ｏｆ Ｍａｃｈｉｎｅｒｙ ＆ Ｍａｔｅｒｉａｌｓ 機械的特性及び耐蝕性に優れたマグネシウム合金及びその製造方法
US10947609B2 (en) 2015-12-28 2021-03-16 Korea Institute Of Materials Science Magnesium alloy having excellent mechanical properties and corrosion resistance and method for manufacturing the same
US11060173B2 (en) 2016-03-10 2021-07-13 National Institute For Materials Science Wrought processed magnesium-based alloy and method for producing same
WO2019013226A1 (fr) 2017-07-10 2019-01-17 国立研究開発法人物質・材料研究機構 Matériau d'alliage de corroyage à base de magnésium et procédé de fabrication associé
WO2019017307A1 (fr) 2017-07-18 2019-01-24 国立研究開発法人物質・材料研究機構 Produit corroyé d'alliage à base de magnésium et procédé de production dudit produit

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