EP0470599A1 - High strength magnesium-based alloys - Google Patents

High strength magnesium-based alloys Download PDF

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Publication number
EP0470599A1
EP0470599A1 EP91113280A EP91113280A EP0470599A1 EP 0470599 A1 EP0470599 A1 EP 0470599A1 EP 91113280 A EP91113280 A EP 91113280A EP 91113280 A EP91113280 A EP 91113280A EP 0470599 A1 EP0470599 A1 EP 0470599A1
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Prior art keywords
alloy
matrix
group
elements
element selected
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German (de)
French (fr)
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Kazuo Aikawa
Katsuyuki Taketni
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YKK Corp
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YKK Corp
Yoshida Kogyo KK
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C45/00—Amorphous alloys
    • C22C45/005—Amorphous alloys with Mg as the major constituent
    • 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
    • C22C1/11—Making amorphous alloys
    • 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

Definitions

  • the present invention relates to aluminum-based alloys having superior hardness and strength together with high corrosion resistance.
  • amorphous magnesium-based alloys As conventional amorphous magnesium-based alloys, for example, an amorphous magnesium-based alloys has been proposed in Japanese Patent Application Laid-Open No. 3 - 10041. Known magnesium-based alloys have all been produced in order to form an amorphous single-phase structure and thereby obtain an enhanced strength.
  • the amorphous magnesium based alloy described in the above Japanese Patent Application Laid-Open No. 3 - 10041 exhibits superior properties such as high strength and high hardness, and, thus, it is especially superior as a high strength material.
  • the present inventors considered that the strength and hardness of alloy materials would be still improved by directing their attention to the ratio between the amorphous phase and the crystalline phase in the alloy materials.
  • magnesium-based alloys which are further improved in their hardness and strength by investigating in detail the amorphous phase and the crystalline phase existing therein.
  • La, Ce, Nd and Sm may be replaced with misch metal (Mm) which contains these elements as main components.
  • Mm used herein is intended to mean a composite comprising, in atomic percentage, 40 to 50% Ce and 20 to 25% La and the balance being other rare earth elements and tolerable levels of impurities (e.g., Mg, Al, Si and Fe, etc.).
  • the Mm may be substituted by the other Ln elements in an Mm : Ln ratio of 1 : 1 (by atomic percent).
  • the Mm is a highly cost-effective source for the Ln alloying elements because of its cheap price.
  • the single figure shows a schematic illustration of a single-roller melt spinning apparatus employed to prepare thin ribbons by rapidly quenching and solidifying alloys of the present invention.
  • the magnesium-based alloys of the present invention can be obtained by rapidly solidifying a melt of the alloy having the composition as specified above, employing liquid quenching techniques.
  • the liquid quenching techniques are methods for rapidly cooling a molten alloy and, particularly, single-roller melt-spinning, twin-roller melt-spinning and in-rotating-water melt-spinning are effective. In these techniques, a cooling rate of about 10 4 to 10 6 K/sec can be obtained.
  • the molten alloy 3 is ejected from the bore 5 of a nozzle 1 onto a roll 2 of, for example, copper or steel, with a diameter of about 30 - 3000 mm, which is rotating at a constant rate within the range of about 300 - 10000 rpm.
  • various thin ribbon materials with a width of about 1 - 300 mm and a thickness of about 5 - 500 /1.m can be readily obtained.
  • a jet of the molten alloy is directed, under application of a back pressure of argon gas, through a nozzle into a liquid refrigerant layer having a depth of about 1 to 10 cm which is held by centrifugal force in a drum rotating at a rate of about 50 to 500 rpm.
  • the angle between the molten alloy ejecting from the nozzle and the liquid refrigerant surface is preferably in the range of about 60 to 90 and the relative velocity ratio of the ejected molten alloy to the liquid refrigerant surface is preferably in the range of about 0.7 to 0.9.
  • the alloy of the present invention may also be obtained by firstly forming an amorphous alloy in the same procedure as described above, except employing a slightly increased cooling rate, and, then, heating the resultant amorphous alloy to the vicinity of its crystallization temperature (crystallization temperature ⁇ 100 C), thereby causing crystallization.
  • the intended alloys can be produced at temperatures lower than 100 ° C less than their crystallization temperature.
  • the alloy of the present invention can also be obtained in the form of a thin film by sputtering. Further, rapidly solidified powder of the alloy composition of the present invention can be obtained by various atomizing processes (e.g., high pressure gas atomizing), spraying, mechanical alloying, mechanical grinding, etc.
  • a is limited to the range of 40 to 95 atomic % and b is limited to the range of 5 to 60 atomic %.
  • the reason for such limitations is that when a and b are outside the specified ranges, it is difficult to form a supersaturated solid solution containing therein solute elements in amounts exceeding their solid solubility limits and amorphization becomes difficult. Consequently, alloys having properties contemplated by the present invention can not be obtained by industrial rapid quenching processes employing the above-mentioned liquid quenching or the like.
  • a, c and d are limited to the atomic percentages ranging from 40 to 95%, 1 to 35% and 1 to 25%, respectively.
  • the reason for such limitations is that when a, c and d are outside the specified ranges, it is difficult to form a supersaturated solid solution containing therein solute elements in amounts exceeding their solid solubility limits and amorphization becomes difficult. Consequently, alloys having properties contemplated by the present invention can not be obtained by industrial rapid quenching processes employing the foregoing liquid quenching or the like.
  • a, c and e are limited to the atomic percentages ranging from 40 to 95%, 1 to 35% and 3 to 25%, respectively.
  • the reason for such limitations is that when a, c and e are outside the specified ranges, it is difficult to form a supersaturated solid solution containing therein solute elements in amounts exceeding their solid solubility limits and amorphization partially becomes difficult. Consequently, alloys having properties contemplated by the present invention can not be obtained by industrial rapid quenching processes employing the above liquid quenching or the like.
  • a, c, d and e are limited to the atomic percentages ranging from 40 to 95%, 1 to 35%, 1 to 25% and 3 to 25%, respectively.
  • the reason for such limitations is that when a, c, d and e are outside the specified ranges, it is difficult to form a supersaturated solid solution containing therein solute elements in amounts exceeding their solid solubility limits and amorphization becomes difficult. Consequently, alloys having properties contemplated by the present invention can not be obtained by industrial rapid quenching processes employing the above-mentioned liquid quenching or the like.
  • the X element is at least one element selected from the group consisting of Cu, Ni, Sn and Zn.
  • the X element exhibits superior effects in stabilizing the resulting fine crystalline phase and improving the amorphous-forming ability, under the conditions of the preparation of the alloys of the present invention.
  • the X element has a strengthening effect while retaining the ductility.
  • the M element is at least one element selected from the group consisting of Al, Si and Ca and forms stable or metastable intermetallic compounds in combination with Mg or other additive elements in the fine crystalline phase of the present invention.
  • the intermetallic compounds thus formed are uniformly and finely distributed throughout a magnesium matrix (a -phase), and, thereby, considerably improve the hardness and strength of the resultant alloys.
  • the M element further prevents coarsening of the fine crystalline phase at high temperatures and provides a good heat resistance. Also, the M element also stabilizes the amorphous phase at relatively elevated temperatures.
  • AI and Ca have an effect of improving the corrosion resistance and Si improves the fluidity of the molten alloy.
  • the Ln element is at least one element selected from the group consisting of Y, La, Ce, Nd and Sm or a misch metal (Mm) which is a mixture of rare earth elements. Addition of the Ln element to the Mg-X system or the Mg-X-M system alloys develops a further stabilized fine crystalline phase in these alloys and makes possible great improvement in their hardness. In the amorphous phase, the Ln element exhibits a significant effect of improving the amorphous-phase forming ability.
  • Mm misch metal
  • the magnesium-based alloys of the present invention show superplasticity in the vicinity of their crystallization temperature (Tx ⁇ 100 C), they can be readily processed by extrusion, press working, hot-forging, etc. Therefore, the magnesium-based alloys of the present invention, obtained in the form of thin ribbons, wires, sheets or powder, can be successfully formed into bulk materials by extrusion, press working, hot-forging, etc., within the range of Tx ⁇ 100 C. Further, some of the magnesium-based alloys of the present invention are sufficiently ductile to permit a high degree of bending.
  • Molten alloy 3 having a predetermined composition, was prepared using a high-frequency melting furnace and charged into a quartz tube 1 having a small opening 5 (diameter: 0.5 mm) at the tip thereof, as shown in the drawing. After being heated to melt the alloy 3, the quartz tube 1 was disposed right above a copper roll 2. Then, the molten alloy 3 contained in the quartz tube 1 was ejected from the small opening 5 of the quartz tube 1, under the application of an argon gas pressure of 0.7 kg/cm 2 , and brought into contact with the surface of the copper roll 2 rapidly rotating at a rate of 5,000 rpm. The molten alloy 3 was rapidly quenched and solidified into an alloy thin ribbon 4.
  • the hardness (Hv) is indicated by values (DPN) measured using a microVickers hardness tester under a load of 25 g.
  • test specimens showed a high level of hardness Hv (DPN) of at least 185 which is about 2.0 to 3.0 times the hardness Hv (DPN), i.e., 60 - 90, of the conventional magnesium-based alloys. Further, the test specimens of the present invention all exhibited a high tensile-strength level of not less than 630 MPa and such a high strength level is at least approximately 1.5 times the highest strength level of 400 MPa achieved in known magnesium-based alloys. It can be seen from such results that the alloy materials of the present invention are superior in hardness and strength.
  • the magnesium-based alloy of the present invention have a high hardness and a high strength which are, respectively, at least 2.0 times and at least 1.5 times those of a similar type of magnesium-based alloy which has been heretofore evaluated as the most superior alloy and yet also have a good processability permitting extrusion or similar operations. Therefore, the alloys of the present invention exhibit advantageous effects in a wide variety of industrial applications.

Abstract

Disclosed are high-strength magnesium-based alloys having a composition consisting of the general formula (I) MgaXb , (II) MgaXcMd , (III) MgaXcLne or (IV) MgaXcMdLne , wherein X is at least one element selected from the group consisting of Cu, Ni, Sn and Zn; M is at least one element selected from the group consisting of Al, Si and Ca; Ln is at least one element selected from the group consisting of Y, La, Ce, Nd and Sm or misch metal (Mm) which is a composite of rare earth elements; and a, b, c, d and e are, in atomic percentage, 40 ≦ a 95, 5 ≦ b ≦ 60, 1 ≦ c 35, 1 ≦ d 25 and 3 ≦ e 25, the alloy consisting of an amorphous phase forming a matrix containing Mg and the other elements as set forth above and a crystalline phase composed of various intermetallic compounds, which are formed between the matrix-forming elements and/or the above-mentioned elements and finely dispersed throughout the matrix, wherein the crystalline phase is contained in the alloy in a higher volume percentage than the amorphous phase.

Description

    BACKGROUND OF THE INVENTION 1. Field of the Invention
  • The present invention relates to aluminum-based alloys having superior hardness and strength together with high corrosion resistance.
    • 2. Description of the Prior Art
  • As conventional amorphous magnesium-based alloys, for example, an amorphous magnesium-based alloys has been proposed in Japanese Patent Application Laid-Open No. 3 - 10041. Known magnesium-based alloys have all been produced in order to form an amorphous single-phase structure and thereby obtain an enhanced strength.
  • The amorphous magnesium based alloy described in the above Japanese Patent Application Laid-Open No. 3 - 10041 exhibits superior properties such as high strength and high hardness, and, thus, it is especially superior as a high strength material. The present inventors considered that the strength and hardness of alloy materials would be still improved by directing their attention to the ratio between the amorphous phase and the crystalline phase in the alloy materials.
    • SUMMARY OF THE INVENTION
  • In view of the foregoing, it is an object of the present invention to provide magnesium-based alloys which are further improved in their hardness and strength by investigating in detail the amorphous phase and the crystalline phase existing therein.
  • According to the present invention, the following high strength magnesium-based alloys are provided:
    • (1) A high strength magnesium-based alloy having a composition consisting of the general formula
      Figure imgb0001
      wherein:
      • X is at least one element selected from the group consisting of Cu, Ni, Sn and Zn; and
      • a and b are, in atomic percentage,
      • 40 ≦ a ≦ 95 and 5 ≦ b ≦ 60,
      • the alloy consisting of an amorphous phase forming a matrix containing Mg and the X element and a crystalline phase composed of various intermetallic compounds which are formed between the matrix-forming elements and/or the above-mentioned elements and finely dispersed throughout the matrix, wherein the crystalline phase is contained in the alloy in a higher volume percentage than the amorphous phase.
    • (2) A high strength magnesium-based alloy having a composition consisting of the general formula
      Figure imgb0002
      wherein:
      • X is at least one element selected from the group consisting of Cu, Ni, Sn and Zn;
      • M is at least one element selected from the group consisting of Al, Si and Ca; and
      • a, c and d are, in atomic percentage,
      • 40 ≦ a ≦ 95,1 ≦ c ≦ 35 and 1 ≦ d ≦ 25,
      • the alloy consisting of an amorphous phase forming a matrix containing magnesium, the X element and the M element and a crystalline phase composed of various intermetallic compounds which are formed between the matrix-forming elements and/or the above-mentioned elements and finely dispersed throughout the matrix, wherein the crystalline phase is contained in the alloy in a higher volume percentage than the amorphous phase.
    • (3) A high strength magnesium-based alloy having a composition consisting of the general formula
      Figure imgb0003
      wherein:
      • X is at least one element selected from the group consisting of Cu, Ni, Sn and Zn;
      • Ln is at least one element selected from the group consisting of Y, La, Ce, Nd and Sm or misch metal (Mm) which is a composite of rare earth elements; and
      • a, c and e are, in atomic percentage,
      • 40 ≦ a ≦ 95,1 ≦ c ≦ 35 and 3 ≦ e ≦ 25
      • the alloy consisting of an amorphous phase forming a matrix containing Mg, the X element and the Ln element and a crystalline phase composed of various intermetallic compounds which are formed between the matrix-forming elements and/or the above-mentioned elements and finely dispersed throughout the matrix, wherein the crystalline phase is contained in the alloy in a higher volume percentage than the amorphous phase.
    • (4) A high strength magnesium-based alloy having a composition consisting of the general formula
      Figure imgb0004
      wherein:
      • X is at least one element selected from the group consisting of Cu, Ni, Sn and Zn;
      • M is at least one element selected from the group consisting of Al, Si and Ca;
      • Ln is at least one element selected from the group consisting of Y, La, Ce, Nd and Sm or misch metal (Mm) which is a composite of rare earth elements; and
      • a, c, d and e are, in atomic percentage,
      • 40 ≦ a ≦ 95,1 ≦ c ≦ 35,1 ≦ d ≦ 25 and 3 ≦ e ≦ 25,
      • the alloy consisting of an amorphous phase forming a matrix containing Mg, the X element, the M element and the Ln element and a crystalline phase composed of various intermetallic compounds which are formed between the matrix-forming elements and/or the above-mentioned elements and finely dispersed throughout the matrix, wherein the crystalline phase is contained in the alloy in a higher volume percentage than the amorphous phase.
  • Among the elements of the above compositions, La, Ce, Nd and Sm may be replaced with misch metal (Mm) which contains these elements as main components.
  • The term "Mm" used herein is intended to mean a composite comprising, in atomic percentage, 40 to 50% Ce and 20 to 25% La and the balance being other rare earth elements and tolerable levels of impurities (e.g., Mg, Al, Si and Fe, etc.). The Mm may be substituted by the other Ln elements in an Mm : Ln ratio of 1 : 1 (by atomic percent). The Mm is a highly cost-effective source for the Ln alloying elements because of its cheap price.
    • BRIEF DESCRIPTION OF THE DRAWING
  • The single figure shows a schematic illustration of a single-roller melt spinning apparatus employed to prepare thin ribbons by rapidly quenching and solidifying alloys of the present invention.
    • DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS
  • The magnesium-based alloys of the present invention can be obtained by rapidly solidifying a melt of the alloy having the composition as specified above, employing liquid quenching techniques. The liquid quenching techniques are methods for rapidly cooling a molten alloy and, particularly, single-roller melt-spinning, twin-roller melt-spinning and in-rotating-water melt-spinning are effective. In these techniques, a cooling rate of about 104 to 106 K/sec can be obtained. In order to produce thin ribbon materials 4 by single-roller melt-spinning or twin-roller melt-spinning, the molten alloy 3 is ejected from the bore 5 of a nozzle 1 onto a roll 2 of, for example, copper or steel, with a diameter of about 30 - 3000 mm, which is rotating at a constant rate within the range of about 300 - 10000 rpm. In such a process, various thin ribbon materials with a width of about 1 - 300 mm and a thickness of about 5 - 500 /1.m can be readily obtained. Alternatively, in order to produce wire materials by in-rotating-water melt-spinning, a jet of the molten alloy is directed, under application of a back pressure of argon gas, through a nozzle into a liquid refrigerant layer having a depth of about 1 to 10 cm which is held by centrifugal force in a drum rotating at a rate of about 50 to 500 rpm. In such a manner, fine wire materials can be readily obtained. In this process, the angle between the molten alloy ejecting from the nozzle and the liquid refrigerant surface is preferably in the range of about 60 to 90 and the relative velocity ratio of the ejected molten alloy to the liquid refrigerant surface is preferably in the range of about 0.7 to 0.9.
  • The alloy of the present invention may also be obtained by firstly forming an amorphous alloy in the same procedure as described above, except employing a slightly increased cooling rate, and, then, heating the resultant amorphous alloy to the vicinity of its crystallization temperature (crystallization temperature ±100 C), thereby causing crystallization. In some alloys, the intended alloys can be produced at temperatures lower than 100 ° C less than their crystallization temperature.
  • Besides the above processes, the alloy of the present invention can also be obtained in the form of a thin film by sputtering. Further, rapidly solidified powder of the alloy composition of the present invention can be obtained by various atomizing processes (e.g., high pressure gas atomizing), spraying, mechanical alloying, mechanical grinding, etc.
  • In the magnesium-based alloy represented by the general formula (I), a is limited to the range of 40 to 95 atomic % and b is limited to the range of 5 to 60 atomic %. The reason for such limitations is that when a and b are outside the specified ranges, it is difficult to form a supersaturated solid solution containing therein solute elements in amounts exceeding their solid solubility limits and amorphization becomes difficult. Consequently, alloys having properties contemplated by the present invention can not be obtained by industrial rapid quenching processes employing the above-mentioned liquid quenching or the like.
  • In the magnesium-based alloy represented by the general formula (II), a, c and d are limited to the atomic percentages ranging from 40 to 95%, 1 to 35% and 1 to 25%, respectively. The reason for such limitations is that when a, c and d are outside the specified ranges, it is difficult to form a supersaturated solid solution containing therein solute elements in amounts exceeding their solid solubility limits and amorphization becomes difficult. Consequently, alloys having properties contemplated by the present invention can not be obtained by industrial rapid quenching processes employing the foregoing liquid quenching or the like.
  • In the magnesium-based alloy represented by the general formula (III), a, c and e are limited to the atomic percentages ranging from 40 to 95%, 1 to 35% and 3 to 25%, respectively. As set forth above, the reason for such limitations is that when a, c and e are outside the specified ranges, it is difficult to form a supersaturated solid solution containing therein solute elements in amounts exceeding their solid solubility limits and amorphization partially becomes difficult. Consequently, alloys having properties contemplated by the present invention can not be obtained by industrial rapid quenching processes employing the above liquid quenching or the like.
  • In the magnesium-based alloy represented by the general formula (IV), a, c, d and e are limited to the atomic percentages ranging from 40 to 95%, 1 to 35%, 1 to 25% and 3 to 25%, respectively. As set forth above, the reason for such limitations is that when a, c, d and e are outside the specified ranges, it is difficult to form a supersaturated solid solution containing therein solute elements in amounts exceeding their solid solubility limits and amorphization becomes difficult. Consequently, alloys having properties contemplated by the present invention can not be obtained by industrial rapid quenching processes employing the above-mentioned liquid quenching or the like.
  • The X element is at least one element selected from the group consisting of Cu, Ni, Sn and Zn. The X element exhibits superior effects in stabilizing the resulting fine crystalline phase and improving the amorphous-forming ability, under the conditions of the preparation of the alloys of the present invention. In addition, the X element has a strengthening effect while retaining the ductility.
  • The M element is at least one element selected from the group consisting of Al, Si and Ca and forms stable or metastable intermetallic compounds in combination with Mg or other additive elements in the fine crystalline phase of the present invention. The intermetallic compounds thus formed are uniformly and finely distributed throughout a magnesium matrix (a -phase), and, thereby, considerably improve the hardness and strength of the resultant alloys. The M element further prevents coarsening of the fine crystalline phase at high temperatures and provides a good heat resistance. Also, the M element also stabilizes the amorphous phase at relatively elevated temperatures. Among the above elements, AI and Ca have an effect of improving the corrosion resistance and Si improves the fluidity of the molten alloy.
  • The Ln element is at least one element selected from the group consisting of Y, La, Ce, Nd and Sm or a misch metal (Mm) which is a mixture of rare earth elements. Addition of the Ln element to the Mg-X system or the Mg-X-M system alloys develops a further stabilized fine crystalline phase in these alloys and makes possible great improvement in their hardness. In the amorphous phase, the Ln element exhibits a significant effect of improving the amorphous-phase forming ability.
  • Since the magnesium-based alloys of the present invention show superplasticity in the vicinity of their crystallization temperature (Tx ± 100 C), they can be readily processed by extrusion, press working, hot-forging, etc. Therefore, the magnesium-based alloys of the present invention, obtained in the form of thin ribbons, wires, sheets or powder, can be successfully formed into bulk materials by extrusion, press working, hot-forging, etc., within the range of Tx ± 100 C. Further, some of the magnesium-based alloys of the present invention are sufficiently ductile to permit a high degree of bending.
    • Example
  • Molten alloy 3, having a predetermined composition, was prepared using a high-frequency melting furnace and charged into a quartz tube 1 having a small opening 5 (diameter: 0.5 mm) at the tip thereof, as shown in the drawing. After being heated to melt the alloy 3, the quartz tube 1 was disposed right above a copper roll 2. Then, the molten alloy 3 contained in the quartz tube 1 was ejected from the small opening 5 of the quartz tube 1, under the application of an argon gas pressure of 0.7 kg/cm2, and brought into contact with the surface of the copper roll 2 rapidly rotating at a rate of 5,000 rpm. The molten alloy 3 was rapidly quenched and solidified into an alloy thin ribbon 4.
  • According to the processing conditions as described above, 20 different alloy thin ribbons (width: 1 mm, thickness: 20 /1.m) having the compositions (by at.%) as shown in the Table were obtained and test specimens were prepared from the respective thin ribbons. Hardness and tensile strength were measured for each test specimen and the results are shown in a right column of the Table.
  • It has been confirmed through observation by transmission electron microscopy (TEM) that the above alloy thin ribbons were composed of a fine crystalline phase and an amorphous phase and contained the crystalline phase in a higher volume percentage than the amorphous phase.
  • The hardness (Hv) is indicated by values (DPN) measured using a microVickers hardness tester under a load of 25 g.
  • As shown in the Table, all test specimens showed a high level of hardness Hv (DPN) of at least 185 which is about 2.0 to 3.0 times the hardness Hv (DPN), i.e., 60 - 90, of the conventional magnesium-based alloys. Further, the test specimens of the present invention all exhibited a high tensile-strength level of not less than 630 MPa and such a high strength level is at least approximately 1.5 times the highest strength level of 400 MPa achieved in known magnesium-based alloys. It can be seen from such results that the alloy materials of the present invention are superior in hardness and strength.
    Figure imgb0005
  • As described above, the magnesium-based alloy of the present invention have a high hardness and a high strength which are, respectively, at least 2.0 times and at least 1.5 times those of a similar type of magnesium-based alloy which has been heretofore evaluated as the most superior alloy and yet also have a good processability permitting extrusion or similar operations. Therefore, the alloys of the present invention exhibit advantageous effects in a wide variety of industrial applications.

Claims (4)

1. A high strength magnesium-based alloy having a composition consisting of the general formula (I) MgaXb ,
wherein:
X is at least one element selected from the group consisting of Cu, Ni, Sn and Zn; and
a and b are, in atomic percentage,
40 ≦ a ≦ 95 and 5 ≦ b ≦ 60,
the alloy consisting of an amorphous phase forming a matrix containing Mg and the X element and a crystalline phase composed of various intermetallic compounds which are formed between the matrix-forming elements and/or the above-mentioned elements and finely dispersed throughout the matrix, wherein the crystalline phase is contained in the alloy in a higher volume percentage than the amorphous phase.
2. A high strength magnesium-based alloy having a composition consisting of the general formula (II) MgaXcMd ,
wherein:
X is at least one element selected from the group consisting of Cu, Ni, Sn and Zn;
M is at least one element selected from the group consisting of Al, Si and Ca; and
a, c and d are, in atomic percentage,
40 ≦ a ≦ 95,1 ≦ c ≦ 35 and 1 ≦ d ≦ 25,
the alloy consisting of an amorphous phase forming a matrix containing magnesium, the X element and the M element and a crystalline phase composed of various intermetallic compounds which are formed between the matrix-forming elements and/or the above-mentioned elements and finely dispersed throughout the matrix, wherein the crystalline phase is contained in the alloy in a higher volume percentage than the amorphous phase.
3. A high strength magnesium-based alloy having a composition consisting of the general formula (III) MgaXcLne ,
wherein:
X is at least one element selected from the group consisting of Cu, Ni, Sn and Zn;
Ln is at least one element selected from the group consisting of Y, La, Ce, Nd and Sm or misch metal (Mm) which is a composite of rare earth elements; and
a, c and e are, in atomic percentage,
40 ≦ a ≦ 95,1 ≦ c ≦ 35 and 3 ≦ e ≦ 25
the alloy consisting of an amorphous phase forming a matrix containing Mg, the X element and the Ln element and a crystalline phase composed of various intermetallic compounds which are formed between the matrix-forming elements and/or the above-mentioned elements and finely dispersed throughout the matrix, wherein the crystalline phase is contained in the alloy in a higher volume percentage than the amorphous phase.
4. A high strength magnesium-based alloy having a composition consisting of the general formula (IV) MgaXcMdLne ,
wherein:
X is at least one element selected from the group consisting of Cu, Ni, Sn and Zn;
M is at least one element selected from the group consisting of Al, Si and Ca;
Ln is at least one element selected from the group consisting of Y, La, Ce, Nd and Sm or misch metal (Mm) which is a composite of rare earth elements; and
a, c, d and e are, in atomic percentage,
40 ≦ a ≦ 95,1 ≦ c ≦ 35,1 ≦ d ≦ 25 and 3 ≦ e ≦ 25,
the alloy consisting of an amorphous phase forming a matrix containing Mg, the X element, the M element and the Ln element and a crystalline phase composed of various intermetallic compounds which are formed between the matrix-forming elements and/or the above-mentioned elements and finely dispersed throughout the matrix, wherein the crystalline phase is contained in the alloy in a higher volume percentage than the amorphous phase.
EP91113280A 1990-08-09 1991-08-07 High strength magnesium-based alloys Withdrawn EP0470599A1 (en)

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JP2209159A JPH0499244A (en) 1990-08-09 1990-08-09 High strength magnesium base alloy

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Cited By (17)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0548875A1 (en) * 1991-12-26 1993-06-30 Ykk Corporation High-strength magnesium-based alloy
EP0661384A1 (en) * 1993-12-03 1995-07-05 Toyota Jidosha Kabushiki Kaisha Heat resistant magnesium alloy
US5552110A (en) * 1991-07-26 1996-09-03 Toyota Jidosha Kabushiki Kaisha Heat resistant magnesium alloy
EP0531165B1 (en) * 1991-09-06 1998-04-29 Tsuyoshi Masumoto High-strength amorphous magnesium alloy and method for producing the same
EP1111082A1 (en) * 1999-11-18 2001-06-27 Ykk Corporation Formed article of amorphous alloy having hardened surface and method for production thereof
WO2002072905A1 (en) * 2001-03-13 2002-09-19 Forskningscenter Risø A method of producing articles with fine outlines by way of shaping and crystallizing armophous alloys
EP2295613A1 (en) * 2008-06-03 2011-03-16 National Institute for Materials Science Mg-BASE ALLOY
WO2016016628A3 (en) * 2014-07-28 2016-03-31 Magnesium Elektron Limited Corrodible downhole article
CN109504884A (en) * 2019-01-10 2019-03-22 吉林大学 Polynary a small amount of high-strength plasticity magnesium alloy and its heavy reduction short flow process
US10329653B2 (en) 2014-04-18 2019-06-25 Terves Inc. Galvanically-active in situ formed particles for controlled rate dissolving tools
US10625336B2 (en) 2014-02-21 2020-04-21 Terves, Llc Manufacture of controlled rate dissolving materials
US10689740B2 (en) 2014-04-18 2020-06-23 Terves, LLCq Galvanically-active in situ formed particles for controlled rate dissolving tools
US10758974B2 (en) 2014-02-21 2020-09-01 Terves, Llc Self-actuating device for centralizing an object
US10865465B2 (en) 2017-07-27 2020-12-15 Terves, Llc Degradable metal matrix composite
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US11365164B2 (en) 2014-02-21 2022-06-21 Terves, Llc Fluid activated disintegrating metal system
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Cited By (31)

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US5552110A (en) * 1991-07-26 1996-09-03 Toyota Jidosha Kabushiki Kaisha Heat resistant magnesium alloy
EP0531165B1 (en) * 1991-09-06 1998-04-29 Tsuyoshi Masumoto High-strength amorphous magnesium alloy and method for producing the same
EP0548875A1 (en) * 1991-12-26 1993-06-30 Ykk Corporation High-strength magnesium-based alloy
EP0661384A1 (en) * 1993-12-03 1995-07-05 Toyota Jidosha Kabushiki Kaisha Heat resistant magnesium alloy
CN1041000C (en) * 1993-12-03 1998-12-02 丰田自动车株式会社 Heat resistant magnesium alloy
CN1309858C (en) * 1999-11-18 2007-04-11 Ykk株式会社 Non-crystal alloy formed workpieces with hardened surface and production thereof
US6530998B1 (en) 1999-11-18 2003-03-11 Ykk Corporation Formed article of amorphous alloy having hardened surface and method for production thereof
EP1111082A1 (en) * 1999-11-18 2001-06-27 Ykk Corporation Formed article of amorphous alloy having hardened surface and method for production thereof
WO2002072905A1 (en) * 2001-03-13 2002-09-19 Forskningscenter Risø A method of producing articles with fine outlines by way of shaping and crystallizing armophous alloys
EP2295613A1 (en) * 2008-06-03 2011-03-16 National Institute for Materials Science Mg-BASE ALLOY
EP2295613A4 (en) * 2008-06-03 2013-07-24 Nat Inst For Materials Science Mg-BASE ALLOY
US11674208B2 (en) 2014-02-21 2023-06-13 Terves, Llc High conductivity magnesium alloy
US11685983B2 (en) 2014-02-21 2023-06-27 Terves, Llc High conductivity magnesium alloy
US11613952B2 (en) 2014-02-21 2023-03-28 Terves, Llc Fluid activated disintegrating metal system
US10758974B2 (en) 2014-02-21 2020-09-01 Terves, Llc Self-actuating device for centralizing an object
US11365164B2 (en) 2014-02-21 2022-06-21 Terves, Llc Fluid activated disintegrating metal system
US10625336B2 (en) 2014-02-21 2020-04-21 Terves, Llc Manufacture of controlled rate dissolving materials
US11167343B2 (en) 2014-02-21 2021-11-09 Terves, Llc Galvanically-active in situ formed particles for controlled rate dissolving tools
US11097338B2 (en) 2014-02-21 2021-08-24 Terves, Llc Self-actuating device for centralizing an object
US10329653B2 (en) 2014-04-18 2019-06-25 Terves Inc. Galvanically-active in situ formed particles for controlled rate dissolving tools
US10760151B2 (en) 2014-04-18 2020-09-01 Terves, Llc Galvanically-active in situ formed particles for controlled rate dissolving tools
US10724128B2 (en) 2014-04-18 2020-07-28 Terves, Llc Galvanically-active in situ formed particles for controlled rate dissolving tools
US10689740B2 (en) 2014-04-18 2020-06-23 Terves, LLCq Galvanically-active in situ formed particles for controlled rate dissolving tools
US10337086B2 (en) 2014-07-28 2019-07-02 Magnesium Elektron Limited Corrodible downhole article
US10329643B2 (en) 2014-07-28 2019-06-25 Magnesium Elektron Limited Corrodible downhole article
WO2016016628A3 (en) * 2014-07-28 2016-03-31 Magnesium Elektron Limited Corrodible downhole article
US10865465B2 (en) 2017-07-27 2020-12-15 Terves, Llc Degradable metal matrix composite
US11649526B2 (en) 2017-07-27 2023-05-16 Terves, Llc Degradable metal matrix composite
US11898223B2 (en) 2017-07-27 2024-02-13 Terves, Llc Degradable metal matrix composite
CN109504884B (en) * 2019-01-10 2020-07-28 吉林大学 Multi-element small-quantity high-strength plastic magnesium alloy and large-reduction-quantity short-flow preparation method thereof
CN109504884A (en) * 2019-01-10 2019-03-22 吉林大学 Polynary a small amount of high-strength plasticity magnesium alloy and its heavy reduction short flow process

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