EP2644728A2 - Feuille d'alliage de magnésium ayant une aptitude supérieure au façonnage à la température ambiante et son procédé de fabrication - Google Patents

Feuille d'alliage de magnésium ayant une aptitude supérieure au façonnage à la température ambiante et son procédé de fabrication Download PDF

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Publication number
EP2644728A2
EP2644728A2 EP11843068.5A EP11843068A EP2644728A2 EP 2644728 A2 EP2644728 A2 EP 2644728A2 EP 11843068 A EP11843068 A EP 11843068A EP 2644728 A2 EP2644728 A2 EP 2644728A2
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EP
European Patent Office
Prior art keywords
magnesium alloy
alloy plate
magnesium
plate
molten
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Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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EP11843068.5A
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German (de)
English (en)
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EP2644728A4 (fr
Inventor
Nack Joon Kim
Jun Ho Bae
Dong Wook Kim
Do Hyang Kim
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POSTECH Academy Industry Foundation
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POSTECH Academy Industry Foundation
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Publication of EP2644728A2 publication Critical patent/EP2644728A2/fr
Publication of EP2644728A4 publication Critical patent/EP2644728A4/fr
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    • 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
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
    • B22D11/0622—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by two casting wheels

Definitions

  • the present invention relates to a magnesium alloy plate having excellent formability at room temperature and a method of manufacturing the same. More particularly, the present invention relates to a method of manufacturing a magnesium alloy plate, wherein a magnesium alloy plate having excellent press formability can be realized by secondary phase control using alloy ingredients added to magnesium, strip casting and subsequent heat treatment, and wherein a magnesium alloy plate having high strength can be obtained by additional heat treatment after forming, and to a magnesium alloy plate manufactured using the method.
  • a magnesium alloy is an alloy for structural materials having the lowest specific gravity, high specific strength and excellent toughness. Recently, demand for magnesium alloys has increased as cases for portable appliances and materials for automobiles, which are required to become lightweight.
  • magnesium alloy plate In order to use a magnesium alloy plate in various fields, it is required to develop a magnesium alloy plate having excellent formability such that it can be formed into parts having various shapes. For the purpose of reflecting this requirement, research into magnesium alloy plates having excellent formability at high temperature has recently been conducted.
  • a method of manufacturing a magnesium alloy plate having targeted thickness by hot-extruding and hot-rolling a cast material obtained by general casting or semi-continuous casting such as die casting is characterized in that a cast material having a large crystal grain size is formed into a cast material having a small crystal grain size by hot extruding.
  • magnesium is a metal having high activity, it is easily surface-blackened or burned by the heat generated during hot extruding. Therefore, in the hot extruding process of magnesium, magnesium must be extruded such that it can be cooled to such a degree that it is not surface-blackened or burned, so there is a limitation to increase an extruding speed.
  • the present inventors proposed a magnesium alloy plate, the press formability of which is improved by adding yttrium (Y) to a Mg-Zn alloy in consideration of the content of zinc (Zn), microfabricating the tissue of the Mg-Zn alloy by strip casting and subsequent heat treatment and then controlling the behavior of the dispersed phase thereof.
  • Y yttrium
  • Zn zinc
  • this magnesium alloy plate is also problematic in that it uses expensive yttrium and has lower press formability than that of a commonly-used aluminum plate, and thus its application is limited.
  • an object of the present invention is to provide a magnesium alloy plate which can be manufactured at low cost using cheap alloy elements and which can be suitably used to manufacture complicated and various parts because it has press formability equivalent to that of a commonly-used aluminum plate, and a method of manufacturing the same.
  • an aspect of the present invention provides a magnesium alloy plate including Zn and Ca as alloy elements.
  • the magnesium alloy has a limiting dome height (LDH) of 7 mm or more, and preferably 8 mm or more.
  • the limiting dome height (LDH) is referred to as an index for evaluating the formability, particularly, press formability of a plate.
  • the limiting dome height (LDH) means the movement distance of a punch (that is, the deformation height of a sample) taken until a disk-shaped sample is fractured when the periphery of the disk-shaped sample having a diameter of 50 mm and a thickness of 0.7 mm is fixed by force of 5 kN and is then deformed at a rate of 0.1 mm/sec by a spherical punch having a diameter of 27 mm.
  • the magnesium alloy plate according to the present invention may include Zn: 1 ⁇ 10 wt%, and preferably 1 ⁇ 7 wt%; and Ca: 0.1 ⁇ 5 wt%, and preferably 0.5 ⁇ 3 wt%.
  • the magnesium alloy plate according to the present invention may have a microtexture having an average crystal grain size of 10 ⁇ m or less.
  • the magnesium alloy plate according to the present invention may have a yield strength (YS) of 200 MPa or more, an ultimate tensile strength (UTS) of 270 MPa or more and an elongation rate (EL) of 12% or more.
  • the magnesium alloy plate according to the present invention may have a (0002) plane having a texture intensity of 2.5 or less.
  • another aspect of the present invention provides a method of manufacturing a magnesium alloy plate having high formability, including the steps of: (a) preparing a molten alloy including Zn: 1 ⁇ 10 wt%, Ca: 0.1 ⁇ 5 wt% and balances of magnesium (Mg) and inevitable impurities; (b) maintaining a temperature of the molten alloy in a range of a temperature at which a liquid fraction is 70% to a ignition temperature; (c) injecting the temperature-maintained molten alloy between two cooling rollers and strip-casting this molten alloy to form a magnesium alloy plate; (d) solution-treating the formed magnesium alloy plate at 300 ⁇ 490°C for 1 ⁇ 24 hours; (e) preheating the solution-treated magnesium alloy plate at 300 ⁇ 400°C and then rolling this magnesium alloy plate to a thickness required at a rate of 1 ⁇ 45% per pass using a heated rolling roller; and (f) solution-treating the rolled magnesium alloy plate at 300 ⁇ 490
  • the interval between the two cooling rollers may be maintained at 1 ⁇ 5 mm, and the rotation speed of each of the cooling rollers may be maintained at 0.2 ⁇ 20 m/min, thus maintaining a cooling rate of the molten alloy at 10 2 ⁇ 10 3 K/s.
  • the amount of Zn may be 1 ⁇ 10 wt%, and preferably 1 ⁇ 7 wt%, and the amount of Ca may be 0.1 ⁇ 5 wt%, and preferably 0.5 ⁇ 3 wt%.
  • the method of manufacturing a magnesium alloy plate according to the present invention may further include the step of aging the solution-treated magnesium alloy plate at 150 ⁇ 200°C for 1 ⁇ 72 hours after the step of rolling the magnesium alloy plate.
  • Ca may be added by the addition of a Mg-Ca matrix alloy.
  • the reason for this is that pure Ca is not easily added in a desired amount because its melting point is high. It is preferred that the Mg-Ca matrix alloy be a Mg-Ca(2 ⁇ 3.5wt%) matrix alloy.
  • the maximum solid solubility of Zn in a Mg matrix is 6.2 wt% at 340°C.
  • Zn is added in an amount of 1.0 wt% or more, a needle-shaped precipitate is formed by heat treatment, and thus an age-enhancing behavior occurs. Therefore, when Zn is added in an amount of less than 1.0 wt%, a precipitation enhancement phenomenon is hardly expected, and when Zn is added in an amount of more than 10 wt%, the precipitation of an equilibrium phase at a crystal grain boundary is promoted to deteriorate the mechanical properties of the aluminum alloy plate. Therefore, it is preferred that the amount of Zn be 1 ⁇ 10 wt%.
  • Ca is an element effective at improving the high-temperature strength of a magnesium alloy.
  • the amount of Ca is less than 0.1 wt%, a high-temperature strength improving effect is insufficient, and when the amount of Ca is more than 5 wt%, the malleability of a magnesium alloy is deteriorated, and the flowability of a molten magnesium alloy is decreased, so the castability of the magnesium alloy is deteriorated, hot tear easily occurs, and the adhesivity between the magnesium alloy and a mold is increased during a solidification process, thereby decreasing productivity. Therefore, it is preferred that the amount of Ca be 0.1 ⁇ 5 wt%. In this case, when Ca is added in an amount of 0.5 ⁇ 3 wt%, the effects thereof can be maximized. Therefore, it is more preferred that the amount of Ca be 0.5 ⁇ 3 wt%.
  • inevitable impurities are referred to as ingredients unintentionally mixed in raw materials or unintentionally introduced in a manufacturing process.
  • the amount of the inevitable impurities may be 0.5 wt% or less, and preferably 0.01 wt% or less, such that the inevitable impurities do not influence the physical properties of the magnesium alloy of the present invention.
  • Fe, Ni, Cr, Cu, Co and the like have a detrimental influence on the corrosion resistance of the magnesium alloy, and thus it is required to control the amount thereof to 0.005 wt% or less.
  • the average crystal grain size of a microtexture of the magnesium alloy plate is more than 10 ⁇ m, the strength and formability of the magnesium alloy plate are deteriorated. Therefore, it is preferred that the average crystal grain size thereof be 10 ⁇ m or less.
  • the increase in texture intensity of a magnesium alloy deteriorates the formability of magnesium having a small amount of slip system.
  • the texture intensity of a (0002) plane (basal plane) of the magnesium alloy plate is more than 2.5, it is difficult to realize press formability equal to that of a magnesium alloy. Therefore, it is preferred that the texture intensity thereof be 2.5 or less, and more preferably, 2.2 or less.
  • the temperature of the molten alloy when the temperature of the molten alloy is lower than the temperature at which a liquid fraction is 70%, the viscosity of the molten alloy is increased, and thus the molten alloy is solidified before it is in contact with the cooling roller in the step (c) to prevent the molten alloy from escaping from the cooling rollers. Further, when the temperature of the molten alloy is higher than the ignition temperature thereof, this process cannot be conducted. Therefore, the temperature of the molten alloy must be maintained in the above range.
  • the cooling rate of the molten alloy when the cooling rate of the molten alloy is less than 10 2 K/s, there is a problem in that, since the molten alloy is slowly cooled, this molten alloy is not greatly different from a molten alloy prepared by general mold casting in microtexture, and the flow of the molten alloy may become unstable before casting. Further, when the cooling rate thereof is more than 10 3 K/s, this rate cannot be easily attained by commercial technigues, except for a rapid cooling process which is applied to formation of a thin ribbon. Therefore, it is preferred that the cooling rate thereof be maintained at 10 2 ⁇ 10 3 K/s. Further, when the interval between the two cooling rollers is maintained at 10 mm or less, it is advantageous to obtain the above cooling rate.
  • the cooling rate of the molten alloy in the step (c) when the cooling rate of the molten alloy in the step (c) is rapid, there is an advantage in that the texture of the molten alloy is microfabricated, and the segregation of the molten alloy is reduced. Further, when the cooling rate thereof is slow, there is an advantage in that intermetallic compounds having a detrimental influence on the tensile characteristics of the molten alloy are finely dispersed in a matrix.
  • the thickness reduction ratio and roll pass in a rolling process can be reduced, so the texture generated from the rolling process can be minimized, thereby reducing the anisotropy of a plate having a bad influence on press formability.
  • this magnesium alloy plate be solution-treated.
  • the solution-treatment temperature and time of the magnesium alloy plate are set in accordance with the diffusivity and SDAS (secondary dendrite arm spacing) of Zn as a main alloy element, whether or not incipient melting exists (measured by DTA/DSC) and the oxidation degree of the magnesium alloy plate.
  • the sufficient solution-treatment result can be obtained only when the solution treatment of the magnesium alloy plate is performed at 300 ⁇ 490°C for 1 ⁇ 24 hours.
  • the thickness reduction ratio of the magnesium alloy plate increases, the texture of the magnesium alloy plate is enhanced, and thus the formability of the magnesium alloy plate deteriorates. Therefore, it is preferred that the thickness reduction ratio of the magnesium alloy plate per pass be maintained in a range of 1 ⁇ 45%.
  • the magnesium alloy plate is not heat-treated at 300 ⁇ 490°C for 0.5 ⁇ 4 hours after rolling the magnesium alloy plate, so it is preferred that the above condition be maintained.
  • the method may further include the step of aging the solution-treated magnesium alloy plate at 150 ⁇ 200°C for 1 ⁇ 96 hours after rolling the magnesium alloy plate.
  • the reason for this is that the tensile characteristics of the magnesium alloy plate can be most efficiently improved under the above heat treatment condition.
  • a magnesium alloy plate having formability at room temperature which can be widely applied in the field of automobile and electronic industries because its strength, extensibility and formability are improved compared to those of a conventional commonly-used magnesium alloy plate by the design of alloy ingredients suitable for twin-roll strip casting, the miniaturization of crystal grains using strip casting and subsequent heat treatment, the formation of intermetallic compounds and the control of volume fraction.
  • a magnesium alloy plate of the present invention can be manufactured at low cost compared to a conventional commonly-used magnesium alloy plate because the number of processes in this method is decreased compared to the number of processes in a conventional method. Further, according to this method, the formation of texture can be minimized, and thus improved press formability can be obtained because the final amount of supplied magnesium alloy can be greatly reduced.
  • FIG. 1 is a schematic view showing a twin-roll strip casting apparatus for manufacturing a magnesium alloy plate according to an embodiment of the present invention.
  • the twin-roll strip casting apparatus includes a melting furnace 10, a nozzle 20 and two cooling rollers 30.
  • a casting method using the twin-roll strip casting apparatus is described in detail as follows. First, the temperature of the molten magnesium alloy having the above composition ratios is maintained in the range of a temperature (about 650°C) at which a liquid fraction is 70% to a temperature (about 950°C) at which the molten magnesium alloy is ignited in the melting furnace 10 under a gas mixture atmosphere of CO 2 and SF 6 , and simultaneously the molten magnesium alloy is transferred to the nozzle 20.
  • the temperature of the molten magnesium alloy is excessively high, liquid phase matter may exist in a plate having passed through the cooling rollers 30. Therefore, in the embodiment of the present invention, considering this point, the molten magnesium alloy is transferred to the nozzle 20 while maintaining its temperature at 750°C or lower, and preferably 710°C.
  • the molten magnesium alloy is injected between the two cooling rollers 30 cooled by a cooler (not shown) provided in the twin-roll strip casting apparatus through the nozzle 20.
  • the interval between the two cooling rollers 30 is maintained at about 2 mm, and the rotation speed of each of the cooling rollers 30 is maintained at about 4 m/min at the time of injecting the molten magnesium alloy.
  • the molten magnesium alloy is cast such that the cooling rate thereof is 200 ⁇ 300 K/s, thus obtaining a magnesium alloy plate having a length of about 5 m, a width of about 70 mm and a thickness of about 2 mm.
  • the obtained magnesium alloy plate is heat-treated as follows. First, the obtained magnesium alloy plate is solution-treated at 440°C for 1 hour. This solution-treatment is conducted in order to remove the cast texture and segregates formed at the time of casting before rolling and to prevent defects from being caused by nonuniform crystal grains and segregates.
  • the solution-treated magnesium alloy plate is preheated to 300°C, and then the preheated magnesium alloy plate is hot-rolled by a rolling roller heated to 200°C.
  • the magnesium alloy plate is rolled at a thickness reduction ratio of 10% per pass until the final thickness reduction ratio is 50% for 5 passes, thus obtaining a magnesium alloy plate having a final thickness of 1 ⁇ 0.7 mm. Then, this magnesium alloy plate is subsequently solution-treated and then aging-treated (T6 heat treatment) as given in Table 2 below.
  • FIG. 3 is a photograph showing a microtexture of the manufactured magnesium alloy plate, wherein the microtexture thereof was observed by an optical microscope after the magnesium alloy plate was heat-treated at 440°C for 1 hour.
  • FIG. 4 is a photograph showing a microtexture of the manufactured magnesium alloy plate, wherein the microtexture thereof was observed by an optical microscope after the magnesium alloy plate was rolled and then solution-heat-treated at 440°C for 30 minutes. As shown in FIG. 4 , it can be seen that the average crystal grain size of the microtexture of the magnesium alloy plate is about 11 ⁇ m, and microprecipitates are uniformly distributed in the microtexture thereof.
  • FIGS. 5 and 6 are photographs showing the microtextures of the magnesium alloy plates manufactured according to the present invention, wherein each of the microtextures thereof were observed by a transmission electron microscope after each of the magnesium alloy plates was rolled and then solution-heat-treated.
  • a precipitated phase is differently formed according to the amount of Zn.
  • the magnesium alloy plate is manufactured while setting the amount of Ca at 1 wt% and changing the amount of Zn to 1 wt%, 4 wt% or 6 wt%, as shown in FIG. 5 , it can be ascertained that a Mg 2 Ca phase is formed when the amount of Zn is 1 wt%, and that a Mg 6 Zn 3 Ca 2 phase is formed when the amount of Zn is 6 wt% (4 wt% or more).
  • each of the magnesium alloy plates has similar basal pole intensity, as given in Table 3 below, even though the precipitated phases are different from each other, it is determined that the difference in formability of the magnesium alloy plates is not influenced by the difference in the precipitated phase of the magnesium alloy plates.
  • FIGS. 7 and 8 are views showing the deformation behaviors of the microtextures of the 0.95Zn-0.9Ca alloy plate and 5.99Zn-0.98Ca alloy plate of the magnesium alloy plates manufactured according to the present invention, wherein the deformation behaviors thereof were analyzed using EBSD (electron backscatter diffraction) after the 0.95Zn-0.9Ca alloy plate and 5.99Zn-0.98Ca alloy plate were rolled and then solution-heat-treated.
  • EBSD electron backscatter diffraction
  • the method of manufacturing a magnesium alloy plate according to an embodiment of the present invention is characterized in that precipitated phases uniformly dispersed in the microtexture of the magnesium alloy plate can be obtained using a hot extruding process that is simple compared to a conventional hot extruding process.
  • FIG. 2 is a schematic view showing a method of obtaining the limiting dome height (LDH) selected as an index for evaluating the formability (particularly, press formability) of the magnesium alloy plate according to an embodiment of the present invention.
  • LDH limiting dome height
  • the limiting dome height (LDH) test was carried out as follows. First, a disk-shaped sample having a diameter of 50 mm and a thickness of 0.7 mm was fabricated, interposed between an upper die and a lower die, and then fixed by a force of 5 kN. Press oil was used as a lubricant. Subsequently, the disk-shaped sample was deformed at rate of 0.1 mm/sec by a spherical punch having a diameter of 27 mm until the disk-shaped sample is fractured. At this time, the deformation height of the disk-shaped sample was measured. For comparison, LDH tests for commercially available magnesium alloy plates (AZ31 H24, ZW41) and an aluminum plate (Al5052), as well as LDH test of the magnesium alloy plate, were carried out.
  • the LDH of each of the magnesium alloy plates manufactured according to Examples of the present invention is 6.6 ⁇ 8.8 mm.
  • the magnesium alloy plates manufactured by Examples of the present invention exhibit excellent formability by three or times compared to that of a commercially available AZ31 H24 alloy plate, and that the LDH of some of the magnesium alloy plates manufactured by Examples of the present invention is greatly improved compared to that of a ZW41 alloy plate generally known to have excellent formability.
  • all of the magnesium alloy plates manufactured by Examples of the present invention exhibit formability equal to that of an aluminum-based A15052 plate or some of the magnesium alloy plates exhibit excellent formability compared to that of the an aluminum-based A15052 plate.
  • FIGS. 9a and 9b show the results of analysis of (002) basal pole figure of the magnesium alloy plate manufactured according to an example of the present invention.
  • the pole intensity of a basal plate thereof becomes high, and such increase in texture intensity deteriorates the formability of magnesium having a small amount of a slip system.
  • FIG. 9a it is shown that the texture of a basal plane of the magnesium alloy plate according to an example of the present invention exhibits low intensity of 3.8 even when it is rolled. Further, referring to FIG. 9b , it is shown that the heat-treated alloy sample having a maximum of LDH exhibits low intensity of 2.0. As shown in Table 3 above, the magnesium alloy plate of the present invention exhibits low intensity compared to that of a conventional magnesium plate.
  • FIG. 10 shows the ratio of a basal plane (002) texture and a pyramid plane (10-11) texture of each of the magnesium alloy plates of Examples and Comparative Examples.
  • the pyramid plane texture of the magnesium alloy plate according to an example of the present invention is relatively strong compared to that of an AZ31 alloy plate. This result means that a random texture is formed in the magnesium alloy plate according to an example of the present invention.
  • the magnesium alloy plates according to examples of the present invention have very high tensile strength compared to that of the magnesium alloy plate manufactured by striping casting, and that some of these magnesium alloy plates have somewhat low tensile strength compared to that of a commercially available AZ31 H24.
  • the mechanical properties of high formability and high strength of the magnesium alloy plate can be controlled such that this magnesium alloy plate has mechanical properties equal to those of aluminum (lightweight metal) by heat treatment after rolling.
  • a magnesium alloy is very rapidly cooled compared to a conventional method, and thus particles can be microfabricated, thereby improving the strength of the magnesium alloy plate.
  • the strength of a conventional magnesium alloy plate is low compared to that of a heat-treated aluminum plate, whereas the strength of the magnesium alloy plate of the present invention is high compared to that of the heat-treated aluminum plate. Therefore, the magnesium alloy plate of the present invention can be applied to the field of automobile and structural materials, and can be used in the various fields requiring magnesium alloy plates having a complicated shape, to which a conventional alloy plate cannot be applied, because its formability is very excellent compared to that of a conventional magnesium plate.

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EP11843068.5A 2010-11-23 2011-11-23 Feuille d'alliage de magnésium ayant une aptitude supérieure au façonnage à la température ambiante et son procédé de fabrication Withdrawn EP2644728A4 (fr)

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KR1020100116975A KR101303585B1 (ko) 2010-11-23 2010-11-23 상온성형성이 우수한 마그네슘 합금 판재 및 그 제조방법
PCT/KR2011/008991 WO2012070870A2 (fr) 2010-11-23 2011-11-23 Feuille d'alliage de magnésium ayant une aptitude supérieure au façonnage à la température ambiante et son procédé de fabrication

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EP2644728A2 true EP2644728A2 (fr) 2013-10-02
EP2644728A4 EP2644728A4 (fr) 2017-05-17

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CN106854724A (zh) * 2016-12-29 2017-06-16 赵建武 一种医用含稀土元素镁合金材料及其制备方法
EP3205736A1 (fr) * 2016-02-11 2017-08-16 Volkswagen AG Feuille en alliage de magnésium obtenue par coulée entre cylindres
CN107541627A (zh) * 2016-06-24 2018-01-05 北京科技大学 一种具有良好室温成形性的变形镁合金板材及其制备方法
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JP2018080363A (ja) * 2016-11-15 2018-05-24 住友電気工業株式会社 マグネシウム合金板材
EP3741880A1 (fr) 2019-05-20 2020-11-25 Volkswagen AG Produit en tôle à flexibilité élevée et son procédé de fabrication

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KR101626820B1 (ko) 2013-12-05 2016-06-02 주식회사 포스코 마그네슘 합금 판재 및 이의 제조 방법
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KR101889019B1 (ko) 2016-12-23 2018-08-20 주식회사 포스코 마그네슘 합금판, 및 그 제조방법
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Cited By (8)

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Publication number Priority date Publication date Assignee Title
EP3205736A1 (fr) * 2016-02-11 2017-08-16 Volkswagen AG Feuille en alliage de magnésium obtenue par coulée entre cylindres
CN107541627A (zh) * 2016-06-24 2018-01-05 北京科技大学 一种具有良好室温成形性的变形镁合金板材及其制备方法
CN107541627B (zh) * 2016-06-24 2019-09-06 北京科技大学 一种具有良好室温成形性的变形镁合金板材及其制备方法
DE102016116244A1 (de) 2016-08-31 2018-03-01 Max-Planck-Institut Für Eisenforschung GmbH Magnesiumlegierung
JP2018080363A (ja) * 2016-11-15 2018-05-24 住友電気工業株式会社 マグネシウム合金板材
CN106854724A (zh) * 2016-12-29 2017-06-16 赵建武 一种医用含稀土元素镁合金材料及其制备方法
EP3741880A1 (fr) 2019-05-20 2020-11-25 Volkswagen AG Produit en tôle à flexibilité élevée et son procédé de fabrication
WO2020234655A1 (fr) 2019-05-20 2020-11-26 Volkswagen Ag Produit métallique en tôle à pliabilité élevée et fabrication associée

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