WO2023080056A1 - Matériau d'extension d'alliage à base de magnésium - Google Patents

Matériau d'extension d'alliage à base de magnésium Download PDF

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WO2023080056A1
WO2023080056A1 PCT/JP2022/040199 JP2022040199W WO2023080056A1 WO 2023080056 A1 WO2023080056 A1 WO 2023080056A1 JP 2022040199 W JP2022040199 W JP 2022040199W WO 2023080056 A1 WO2023080056 A1 WO 2023080056A1
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based alloy
stretched material
mol
alloy stretched
material according
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Japanese (ja)
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英俊 染川
秀樹 山浦
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国立研究開発法人物質・材料研究機構
株式会社プロテリアル
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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
    • 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

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  • the present invention relates to a stretched magnesium (Mg)-based alloy with excellent room-temperature strength and reduced yield anisotropy.
  • addition of one or more elements other than Mg for alloying is well recognized and is being experimented. In particular, the greater the difference in atomic radius from the base metal, the greater the effect of improvement. In Mg alloys, the addition of rare earth metals is most effective. However, the use of rare earth elements is not preferable from an economic point of view because the cost of materials rises.
  • Mg-Al-Zn:AZ alloys containing aluminum and zinc, and Mg-Zn-Zr:ZK alloys containing zinc and zirconium are in circulation.
  • these Mg alloys are subjected to extension work accompanied by heat treatment to improve strength.
  • the basal planes are oriented parallel to the processing direction, forming a basal plane texture. Therefore, due to the refinement of the grain size, although the "tensile” strength is improved, the “compressive” strength is about half the tensile strength, and the yield anisotropy that the yield stress changes depending on the stress application direction is exhibited.
  • Patent Document 1 discloses a fine-grained Mg alloy that contains a very small amount of one element selected from Yb and Lu, and has fine grains and excellent strength characteristics. The main reason for the increase in strength of this alloy is that the added solute elements segregate at the grain boundaries.
  • Patent Document 2 14.5 mass% or less of Sn is contained, the average grain size of the Mg matrix phase is 10 ⁇ m or less, and among the crystal grain boundaries surrounding the Mg matrix phase, subgrain boundaries with an average grain size of 2 ⁇ m or less It discloses an Mg-based alloy having excellent room-temperature strength characteristics due to the large proportion of (small-angle grain boundaries). It was found that the aforementioned knowledge of introducing subgrain boundaries at a high density can also be applied to Mg-based alloys containing 3.5 to 11 mass% of Al, which is disclosed in Patent Document 3.
  • the Mg-based alloys disclosed in Patent Documents 2 and 3 are characterized by not only excellent strength but also reduced yield anisotropy between compressive yield stress and tensile yield stress due to the presence of subgrain boundaries.
  • Patent Document 4 describes a Mg-based alloy to which two or more solute elements are added, containing Ca and Zn within a solid solution amount, and Ca and Zn segregate parallel to the c-axis direction of Mg. Also disclosed is a high-strength Mg-based alloy characterized by:
  • Patent Document 5 discloses an Mg alloy containing 1 mol % or less of Mn and having deformation twins in the Mg matrix phase and having excellent fracture toughness.
  • Patent Document 6 discloses an Mg-based alloy having an Mg parent phase of 5 ⁇ m or less in size and containing 0.07 to 2 mass % of Mn and having excellent room-temperature ductility. These alloys are characterized by exhibiting an elongation at break of about 100% and exhibiting an m value of 0.1 or more, which is an index of the contribution of grain boundary sliding to deformation.
  • Patent Document 7 As an index of formability, the degree of stress reduction is used, and the value is characterized by showing 0.3 or more.
  • Patent Document 7 it consists of Mg-Amol%Mn-Bmol%X, A is 0.03 to 1 mol%, B is 1 times or less than A, contains Bi, Sn, Zr, and has a nominal strain. It discloses an Mg-based alloy with excellent room-temperature ductility that does not break even if 0.2 or more is applied.
  • Patent Documents 5 to 7 relate to improvements in fracture toughness and room temperature ductility, and do not describe or disclose improvements in strength properties.
  • Mn element added to Mg combines with iron (Fe) and silicon (Si) during melting and is mostly used as an impurity element removal element. It is known that Mg alloys containing Mn as the main element (leading element) are endowed with ductility (Patent Documents 6 and 7, Non-Patent Documents 2 and 3). This is because grain boundary sliding is activated by the addition of the Mn element. On the other hand, as far as the inventors know, there are no disclosures or reports regarding the strength properties of Mg--Mn alloys. In addition, the atomic radius of the Mn element is smaller than that of Mg, and the electronic state of Mn is characterized by exhibiting a semi-closed shell structure. is unknown.
  • JP-A-2006-16658 Japanese Patent No. 6080067 Japanese Patent No. 5561592 Japanese Patent No. 5787380 Japanese Patent No. 6587174 Japanese Patent No. 6648894 Japanese Patent No. 6860235
  • An object of the present invention is to provide an expanded Mg-based alloy material containing Mn as a main element, having excellent room-temperature strength and reduced yield anisotropy.
  • the first aspect of the present invention is a Mg-based alloy stretched material containing Amol% of Mn, Bmol% of X, and the balance being Mg and unavoidable impurities (hereinafter, this Mg-based alloy stretched material is referred to as "Mg-A ( mol%) Mn-B (mol%) X”), where X is one or more elements selected from the group consisting of Al, Ca, Li, and Zn , the value of A is 0.03 (mol%) or more and 2 (mol%) or less, the relationship between A and B is A ⁇ B, and the upper limit of B is relative to the upper limit of A It is 1.0 times or less, and the lower limit of B is 0.03 (mol%).
  • Mg-A ( mol%) Mn-B (mol%) X Mg-based alloy stretched material containing Amol% of Mn, Bmol% of X, and the balance being Mg and unavoidable impurities
  • a second aspect of the present invention provides an Mg-based alloy stretched material according to the first aspect of the present invention, wherein the X further contains Sn and/or Bi.
  • a third aspect of the present invention is the Mg-based alloy expanded material according to the second aspect of the present invention, wherein Mn is selected from the group consisting of Amol%, Sn, and Al, Ca, Li, and Zn.
  • Mn is selected from the group consisting of Amol%, Sn, and Al, Ca, Li, and Zn.
  • Mg-based alloy stretched material containing the above B mol % of at least one type of element.
  • a fourth aspect of the present invention is a Mg-based alloy expanded material according to the first or second aspect of the present invention, wherein Mn is the above Amol%, Li, and the group of Al, Ca, Zn, Sn, and Bi Provide a Mg-based alloy stretched material containing the above B mol % of one or more elements selected from
  • a fifth aspect of the present invention is a Mg-based alloy expanded material according to the first or second aspect of the present invention, wherein Mn is the above Amol%, Zn, and the group of Al, Ca, Li, Sn, and Bi Provide a Mg-based alloy stretched material containing the above B mol % of one or more elements selected from
  • a sixth aspect of the present invention is an Mg-based alloy stretched material according to any one of the first to fifth aspects of the present invention, wherein the average crystal grain size of the Mg parent phase is 25 ⁇ m or less. I will provide a.
  • a seventh aspect of the present invention is a Mg-based alloy stretched material according to any one of the first to sixth aspects of the present invention, wherein the Mg parent phase and grain boundaries in the metal structure of the Mg-based alloy stretched material
  • an expanded Mg-based alloy is provided in which intermetallic compound particles having a particle diameter of 0.5 ⁇ m or less are dispersed and precipitated, and the volume fraction thereof is 10% or less.
  • An eighth aspect of the present invention is the Mg-based alloy stretched material according to any one of the first to seventh aspects of the present invention, wherein an element other than Mg is segregated at the grain boundaries of the Mg-based alloy stretched material Provided is a Mg-based alloy stretched material.
  • a ninth aspect of the present invention is a Mg-based alloy stretched material according to any one of the first to eighth aspects of the present invention, and the stress obtained by a room temperature tensile test at an initial strain rate of 1x10 -3 s -1 - Provide a Mg-based alloy expanded material with a yield stress exceeding 200 MPa in the strain curve diagram.
  • a tenth aspect of the present invention is a Mg-based alloy stretched material according to any one of the first to ninth aspects of the present invention, obtained by room temperature tension and compression tests at an initial strain rate of 1x10 -3 s -1
  • a Mg-based alloy stretched material having a yield stress ratio ( compressive yield stress/tensile yield stress), that is, a yield anisotropy exceeding 0.6 or more.
  • Nominal stress-nominal strain curve obtained by room temperature tensile and compression tests of Mg-3 mass% Al-1 mass% Zn alloy extruded material Nominal stress-nominal strain curves obtained by room temperature tensile tests on the Mg-0.3 mol% Mn-0.1 mol% Sn-0.07 mol% X extrusions of the examples.
  • a and B The relationship between A and B is A ⁇ B, and the value of A is preferably 2 mol % or less, more preferably 1.5 mol % or less, still more preferably 1.0 mol % or less. If the value of A exceeds 2 mol %, a high density of ⁇ -Mn grains precipitates within the matrix, causing premature fracture during deformation.
  • the lower limit of A is 0.03 mol%, preferably 0.1 mol%, more preferably 0.3 mol%.
  • the upper limit of B is preferably 1.0 times or less the upper limit of A, more preferably 0.9 times or less, and even more preferably 0.8 times or less.
  • the lower limit of B is 0.03 mol%.
  • 0.03 mol % is a value that defines the boundary between unavoidable impurities and additive elements.
  • various alloy elements may be included in advance. This is to eliminate the content.
  • Elements contained in the unavoidable impurities include, for example, Fe, Si, Cu (copper), and Ni (nickel).
  • the Mg-based alloy stretched material after stretching has an average crystal grain size of 25 ⁇ m or less in the Mg parent phase. More preferably, it is 20 ⁇ m or less, and still more preferably 10 ⁇ m or less. It is preferable to use the intercept method based on the G0551 JIS standard for the measurement of the grain size. Since it is difficult to use the sectioning method when the grain size is very small or when the grain boundaries are unclear, we use a bright-field image obtained by a transmission electron microscope or an electron beam backscatter diffraction image for measurement.
  • heat treatment such as strain relief annealing may be performed after hot working.
  • ⁇ -Mn particles and Mn-bonded intermetallic compound particles are dispersed in the Mg matrix and at the grain boundaries. These dispersed particles contribute to improving the compression yield stress and cause a reduction in yield anisotropy.
  • the size of the dispersed particles is preferably 0.5 ⁇ m or less, more preferably 0.25 ⁇ m or less, and even more preferably 0.1 ⁇ m or less.
  • the intermetallic compound particles are Mn-bonded metal compound particles, that is, intermetallic compound particles in which Mn and Mg are bonded, and Mn and the X (Al, Ca, Li, Zn, Sn, Bi) are bonded.
  • Mn and the X Al, Ca, Li, Zn, Sn, Bi
  • intermetallic compound particles in which Mg and the X are bonded together there are intermetallic compound particles in which Mg and the X are bonded together, and intermetallic compound particles in which the X are bonded to each other.
  • the presence of ⁇ -Mn particles and intermetallic compound particles can be confirmed using XRD, and the particle diameter and volume fraction can be measured by microstructural observation using an optical microscope or scanning electron microscope.
  • the strength of the stretched Mg-based alloy at room temperature is calculated from the nominal stress and nominal strain curves obtained by the room temperature tensile test. Since mechanical properties such as strength are susceptible to the test rate, the nominal stress and nominal strain curves obtained at an initial strain rate of 1x10 -3 s -1 shall be used. When the strength is affected by the test speed, the strength tends to increase as the test speed increases. Therefore, the initial strain rate was set assuming that it is a general-purpose test rate, is within the quasi-static test rate range, and is the minimum test rate.
  • Fig. 1 shows the nominal stress and nominal strain curves obtained from a room temperature tensile test using a comparative example of Mg-3 mass% Al-1 mass% Zn: commonly known as AZ31 extruded material.
  • Yield stress is based on JIS Z2241, and the slope of the straight line obtained in the elastic region is calculated with the value at a nominal strain of 0.2% offset.
  • the calculated yield stress in tension preferably exceeds 200 MPa, more preferably 250 MPa or more, and even more preferably 300 MPa or more.
  • the yield stress is 200 MPa or less, it is equivalent to the general-purpose Mg-based alloy expanded material.
  • the elongation at break is also calculated using the slope of the straight line obtained in the elastic region, and preferably exceeds 15%, more preferably 20% or more, and even more preferably 25% or more. If the elongation at break is 15% or less, it is equivalent to a general-purpose Mg-based alloy expanded material.
  • the elongation at break may be measured by a butt-to-match method using a sample after a tensile test.
  • Yield anisotropy is calculated using the yield stress obtained by tensile and compression tests at an initial strain rate of 1x10 -3 s -1 . That is, the value obtained by dividing the compressive yield stress by the tensile yield stress is the yield anisotropy, which is preferably greater than 0.6, more preferably 0.7 or more, and further preferably 0.75 or more. When the yield anisotropy is 0.6 or less, it is equivalent to a general-purpose Mg alloy expanded material.
  • Example 1 Commercially available pure Mn (99.9 mass%) and commercially available pure Mg (99.98 mass%) were used to prepare an Mg—Mn master alloy using an iron crucible.
  • the target content is adjusted to 0.3 mol% Mn-0.1 mol% Sn-0.07 mol% Zn, and an iron crucible was used to melt a Mg--Mn--Sn--Zn alloy cast material.
  • the melting conditions were an Ar atmosphere, a melting temperature of 700° C., and a melting holding time of 5 minutes. Casting was performed using an iron mold with a diameter of 50 mm and a height of 200 mm. After that, the cast material was solution treated at 500° C. for 24 hours.
  • the cast material after solution treatment was machined into a cylindrical extruded billet with a diameter of 40 mm and a length of 40 mm. After holding the processed billet in a container set at 200 ° C. for 30 minutes, it was subjected to hot strain imparting processing by extrusion at an extrusion ratio of 25: 1, and the shape of Example 1 having a diameter of 8 mm and a length of 500 mm or more.
  • An Mg-based alloy stretched material of the Mg-0.3Mn-0.1Sn-0.07Zn quaternary system alloy hereinafter, the Mg-based alloy stretched material is referred to as an extruded material was produced.
  • extruded materials described in Examples 2 to 44 were produced as described below.
  • Li was used as an additive element, a Mg--Mn master alloy was prepared, and when Al, Bi, and Ca were used as additive elements, a commercially available pure metal was used without preparing a master alloy.
  • Each additive element was adjusted so as to have a target composition, and various casting materials were melted in iron crucibles. Thereafter, various extruded materials were produced under the same conditions as those described above regarding the solution treatment conditions (temperature and time), the dimensions of the cylindrical extruded billet, the extrusion ratio and the holding time during the extrusion process.
  • Extrusion temperature is as shown in Table 1.
  • Example 2 to 4 Mg-0.3Mn according to Examples 2 to 4 in the same manner as in Example 1, except that Al, Ca, and Li were used instead of Zn and the target contents were adjusted to 0.07 mol%, respectively.
  • An extruded material of -0.1Sn-0.07(Al, Ca, Li) quaternary alloy was produced.
  • Example 5 to 8 Mg-0.3Mn-0.15Sn-0.0.3Mn-0.15Sn-0.1 according to Examples 5 to 8 were prepared in the same manner as in Examples 1 to 4, except that the target Sn content was changed from 0.1 mol% to 0.15 mol%.
  • Example 1 except that the target content of Sn was changed from 0.1 mol% to 0.05 mol%, and the target content of Zn, Al, Ca, and Li was changed from 0.07 mol% to 0.03 mol%.
  • Extruded materials of Mg-0.3Mn-0.05Sn-0.03 (Zn, Al, Ca, Li) quaternary alloys according to Examples 9 to 12 were produced in the same manner as in 4 to 4 above.
  • Example 1 Example 1 except that the target content of Mn was changed from 0.3 mol% to 0.52 mol%, and the target content of Zn, Al, Ca, Li was changed from 0.07 mol% to 0.03 mol%.
  • Extruded materials of Mg-0.52Mn-0.1Sn-0.03 (Zn, Al, Ca, Li) quaternary alloys according to Examples 13 to 16 were produced in the same manner as in 4 to 4 above.
  • Example 1 except that the target content of Mn was changed from 0.3 mol% to 0.45 mol%, and the target content of Zn, Al, Ca, Li was changed from 0.07 mol% to 0.05 mol%.
  • Extruded materials of Mg-0.45Mn-0.1Sn-0.05 (Zn, Al, Ca, Li) quaternary alloys according to Examples 17 to 20 were produced in the same manner as in 4 to 4 above.
  • Example 21 to 25 Change the target content of Mn from 0.3 mol% to 0.45 mol%, use Li instead of Sn, set the target content of Li to 0.1 mol%, and target Zn, Al, Ca, Bi, Sn Mg-0.45Mn-0.1Li-0.05 (Zn, Al, Ca, Bi, An extruded material of Sn) quaternary alloy was produced.
  • Example 26 to 28 The target content of Mn was changed to 0.3 mol%, the target content of Li was changed to 0.15 mol%, and the target contents of Zn, Ca, and Sn were each changed to 0.07 mol%.
  • Extrusions of Mg-0.3Mn-0.15Li-0.07 (Zn, Ca, Sn) quaternary alloys according to Examples 26 to 28 were produced in the same manner as in Examples 21, 23 and 25.
  • Example 29 was prepared in the same manner as in Examples 21 to 24, except that the target content of Mn was changed to 0.6 mol% and the target content of Zn, Al, Ca, and Bi was changed to 0.05 mol%.
  • Example 1 except that the target content of Zn was changed from 0.007% to 0.1 mol%, Ca and Li were used instead of Sn, and the target contents of Ca and Li were each set to 0.03 mol%.
  • Extruded materials of Mg-0.3Mn-0.1Zn-0.03(Ca, Li) quaternary system alloys according to Examples 33 and 34 were produced in the same manner as above.
  • Example 35 to 38 Mg according to Examples 35 to 38 in the same manner as in Examples 33 and 34, except that Al, Ca, Li, and Sn were used instead of Ca and Li, and the target contents of these were each set to 0.05 mol%.
  • An extruded material of -0.3Mn-0.1Zn-0.05 (Al, Ca, Li, Sn) quaternary alloy was produced.
  • Example 47-50 The target content of Mn was changed to 0.15 mol%, the target content of Zn was changed to 0.07 mol%, and the target contents of Al, Ca, Li, and Sn were each changed to 0.03 mol%.
  • Extruded materials of Mg-0.15Mn-0.07Zn-0.03 (Al, Ca, Li, Sn) quaternary alloys according to Examples 47 to 50 were produced in the same manner as in Examples 35 to 38. .
  • Example 51 and 52 Mg-0.3Mn according to Examples 51 and 52 in the same manner as in Example 1, except that Zn was used instead of Sn and Zn, and the target Zn content was set to 0.1 mol% and 0.3 mol%. An extruded material of -(0.1, 0.3) Zn ternary alloy was produced.
  • Example 53 Mg-0.3Mn-0.1Ca ternary alloy according to Example 53 in the same manner as in Example 3, except that Ca was used instead of Sn and Ca, and the target content of Ca was set to 0.1 mol%. An extruded material was produced.
  • Example 54 and 55 Mg-0.3Mn according to Examples 54 and 55 in the same manner as in Example 4, except that Li was used instead of Sn and Li, and the target Li content was set to 0.2 mol% and 0.3 mol%.
  • An extruded material of (0.2, 0.3) Li ternary alloy was produced.
  • Example 56 and 57 Mg-0.6Mn-(0.1,0.3)Zn ternary according to Examples 56 and 57 in the same manner as in Examples 51 and 52, except that the target content of Mn was changed to 0.6 mol% An extruded material of the system alloy was produced.
  • Example 58 An extruded material of a Mg-0.6Mn-0.3Al ternary system alloy according to Example 58 was produced in the same manner as in Example 57, except that Al was used instead of Zn.
  • Example 59 A Mg-0.6Mn-0.2Li ternary alloy extruded material according to Example 59 was produced in the same manner as in Example 54, except that the target content of Mn was changed to 0.6 mol%.
  • Example 60-62 Examples 60 to 62 were changed in the same manner as in Examples 57 to 59, except that the target content of Mn was changed to 0.9 mol%, and the target contents of Zn, Al, and Li were each set to 0.1 mol%. An extruded material of the Mg-0.9Mn-0.1 (Zn, Al, Li) ternary alloy was produced.
  • the microstructures of various extruded materials were observed using an optical microscope and an electron beam backscatter diffraction method, and the average crystal grain size of the base material was determined by the intercept method and summarized in Table 1. In any extruded material, the average grain size is 6 ⁇ m or less.
  • X-ray diffraction X-ray diffraction (XRD) was used to evaluate whether intermetallic compounds having a particle size of 0.5 ⁇ m or less combined with ⁇ -Mn particles and Mn were dispersed in the Mg matrix, and the dispersion was confirmed. The case where it did is indicated by a circle in Table 1. It was also confirmed that elements other than Mg were segregated at the grain boundaries of some of the extruded materials.
  • FIG. 3 shows an example of microstructure observation of Example 51.
  • FIG. From the EDS analytical analysis attached to the transmission electron microscope, it can be confirmed that the grain boundaries are clear in the Zn mapping image, and the Zn element is segregated at the grain boundaries. Also, in the mapping image for Mn, there is a clear region with a size of 0.05 ⁇ m. From the Zn mapping image of the same location, no clear region can be confirmed, so it can be seen that the ⁇ -Mn particles are dispersed in the matrix.
  • the Mg-based alloy of the present invention exhibits excellent room-temperature strength properties and has a small yield anisotropy, so it has three-dimensional isotropic deformability. Therefore, application to moving members such as automobiles is conceivable. In addition, since a small amount of general-purpose elements is added and rare earth elements are not used, it is possible to reduce the cost of the material compared to conventional rare earth added Mg alloys.

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Abstract

Le problème décrit par la présente invention est de fournir un matériau d'extension d'alliage à base de Mg permettant de réduire une anisotropie élastique tout en conservant d'excellentes propriétés de résistance à la traction. La solution selon l'invention porte sur un matériau d'extension d'alliage à base de Mg ayant une excellente résistance à température ambiante et contenant du Mn et au moins un élément parmi les quatre éléments Al, Ca, Li, et Zn, ou contenant en outre, en plus des quatre éléments ci-dessus, les deux éléments Sn et/Bi, le reste étant constitué de Mg et d'impuretés inévitables, la teneur en Mn étant de 0,03 à 2 % en moles (inclus), et la teneur en les six éléments mentionnés ci-dessus étant d'au moins 0,03 % en moles mais n'étant pas supérieure à la teneur en Mn. Le matériau d'extension est caractérisé en ce que la limite d'élasticité obtenue par un essai de traction est de 200 MPa ou plus et présente un rapport, par rapport à la limite d'élasticité obtenue par un test de compression, de 0,6 ou plus.
PCT/JP2022/040199 2021-11-05 2022-10-27 Matériau d'extension d'alliage à base de magnésium WO2023080056A1 (fr)

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Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101792878A (zh) * 2009-02-01 2010-08-04 北京有色金属研究总院 导热耐腐蚀镁合金及其制备方法
CN104046868A (zh) * 2014-06-26 2014-09-17 宝山钢铁股份有限公司 一种无稀土低成本高强度导热镁合金及其制备方法
CN106521272A (zh) * 2016-10-26 2017-03-22 北京工业大学 一种耐蚀生物镁合金及其制备方法
KR20190098307A (ko) * 2018-02-13 2019-08-22 서울대학교산학협력단 강도와 내부식성이 우수한 마그네슘 합금 및 이의 제조방법
CN114182147A (zh) * 2021-12-09 2022-03-15 中南大学 一种高强高导热镁合金及其制备方法

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101792878A (zh) * 2009-02-01 2010-08-04 北京有色金属研究总院 导热耐腐蚀镁合金及其制备方法
CN104046868A (zh) * 2014-06-26 2014-09-17 宝山钢铁股份有限公司 一种无稀土低成本高强度导热镁合金及其制备方法
CN106521272A (zh) * 2016-10-26 2017-03-22 北京工业大学 一种耐蚀生物镁合金及其制备方法
KR20190098307A (ko) * 2018-02-13 2019-08-22 서울대학교산학협력단 강도와 내부식성이 우수한 마그네슘 합금 및 이의 제조방법
CN114182147A (zh) * 2021-12-09 2022-03-15 中南大学 一种高强高导热镁合金及其制备方法

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