WO2004085689A1 - Alliage de magnesium de haute resistance et tenacite, et son procede de production - Google Patents

Alliage de magnesium de haute resistance et tenacite, et son procede de production Download PDF

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WO2004085689A1
WO2004085689A1 PCT/JP2004/004201 JP2004004201W WO2004085689A1 WO 2004085689 A1 WO2004085689 A1 WO 2004085689A1 JP 2004004201 W JP2004004201 W JP 2004004201W WO 2004085689 A1 WO2004085689 A1 WO 2004085689A1
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atomic
strength
magnesium alloy
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Yoshihito Kawamura
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Yoshihito Kawamura
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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
    • 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 a high-strength, high-toughness magnesium alloy and a method for producing the same, and more particularly, to a high-strength, high-toughness magnesium alloy which achieves high-strength, high-toughness by containing a specific rare earth element in a specific ratio, and its production. About the method.
  • Magnesium alloys along with their recyclability, have begun to spread rapidly as housings for mobile phones and laptops or as automotive parts.
  • magnesium alloys are required to have high strength and high toughness.
  • Various studies have been made on the production of high-strength, high-toughness magnesium alloys in terms of materials and manufacturing methods.
  • Mg-A1 system Mg-Al-Zn system, Mg_Th-Zn system, Mg_Th-Zn-Zr system, Mg-Zn_Zr system, Mg-Zn-Zr-RE (Rare earth element) alloys such as those based on components are known.
  • Mg-A1 system Mg-Al-Zn system, Mg_Th-Zn system, Mg_Th-Zn-Zr system, Mg-Zn_Zr system, Mg-Zn-Zr-RE (Rare earth element) alloys such as those based on components are known.
  • the strength is higher than when manufactured by the sintering method, but the strength is still insufficient, or the toughness (ductility) is insufficient even if the strength is sufficient.
  • the toughness ductility
  • magnesium alloys are obtained by heat-treating, for example, amo / fus-like alloy materials and fine crystallization. There is a preconception that considerable amounts of zinc and rare earth elements are required to obtain the amorphous alloy material. Magnesium alloys containing relatively large amounts of zinc and rare earth elements have been used.
  • the magnesium alloy described in Japanese Patent No. 3238516 is a Mg—Zn—RE alloy, and uses Y, Ce, La, Nd, Pr, Sm and Mm (misch metal) as rare earth elements.
  • the minimum value of the rare earth element content is 1.0 to 2.0 atomic% as shown in FIG.
  • the rare earth element actually used in Examples and Comparative Examples was only Mm, and the minimum value was 1 atomic% as shown in Tables 2 and 3, and the zinc content at that time was 2 to 10%. Atomic%.
  • Japanese Patent No. 2807374 discloses an Mg-Zn (or Ni, Cu) -RE alloy, and the content of rare earth elements is limited to 1 to 20 atomic%.
  • the rare earth element actually used in the examples is also Mm in Patent No. 2807374, and the minimum value is 1 atomic% in Examples 7 and 13; Is only 1 atomic%.
  • Zinc content of the magnesium alloy of Example 7 is 5 atomic 0/0, the sum of the alloy components other than mug Neshiumu has a 6 atom%.
  • Japanese Patent No. 3238516 and Japanese Patent No. 2807374 disclose that high strength and high toughness have been obtained.
  • applications of magnesium alloys are expanding, and conventional strength and toughness are insufficient, and magnesium alloys having higher strength and toughness are demanded.
  • Japanese Patent Application Laid-Open No. 2002-256370 discloses that a rare earth element contains 0.5 atom. / 0 to 5 atomic%, at least one of zinc and aluminum is 0.2 atomic% More than 4 atoms. / 0 or less contained respectively, are Ma Guneshiumu alloys disclosed have a long period hexagonal structure further into the crystal.
  • the composition range of the rare earth element in Japanese Patent Application Laid-Open No. 2002-256370 is set to be 0.5 atomic% or more and 5 atomic% or less, but in Examples 1 to 6, the rare earth element has 2 atoms. It is fixed at / 0 and its usefulness in other composition ranges has not been proven. Still more 5 atomic 0/0 0.
  • the strength of the alloys is so low that they cannot be put to practical use.
  • the range of rare earth elements contained in JP-A-2002-256370 is specific to magnesium alloys having a long-period hexagonal structure, and is relatively broad. Data is provided for only one rare earth element content range.
  • the present invention has been made in view of the above-described circumstances, and has as its object to provide a high-strength high-toughness magnesium alloy and a high-strength and toughness magnesium alloy which are practically used in both strength and toughness for an expanded use of a magnesium alloy. It is to provide a manufacturing method.
  • a high-strength and toughness magnesium alloy according to the present invention contains Zn and & atomic%, and has at least one rare earth element selected from the group consisting of La, Ce and Mm.
  • the element contains a total of b atomic% and the balance consists of Mg.
  • a and b satisfy the following equations (1) to (3).
  • Mm (Misch metal) is a mixture or alloy of a plurality of rare earth elements mainly composed of Ce and La.
  • a Z n contains% a atom, L a, b atomic 0/0 containing in total of at least one rare earth element selected from the group consisting of C e and Mm And Si, Gd, Dy, Tb, Ho, Er, Ca, Mn, Ag, Li, Zr, Th, Y, Yb, Eu, Pr, 3111 and (group consisting of 1) At least one metal selected from the group consisting of more than 0 atomic% and 1.8 atomic% or less, with the balance being Mg, and a and b satisfy the following formulas (1) to (3).
  • Each of the high-strength and toughness magnesium alloys according to the present invention is useful as an alloy for use in high-tech equipment that requires high performance in both strength and toughness, and La, Ce, and Mm are rare earth elements. It is inexpensive in the inside, and also advantageous in terms of cost.
  • the high-strength high-toughness magnesium alloy according to the present invention contains Zn at & atomic%, and contains b atomic% in total of at least one rare earth element selected from the group consisting of La, Ce and Mm, The balance is made of Mg, and a and b are quenched solids after quenching and solidifying a molten metal satisfying the following equations (1) to (3).
  • an intermetallic compound having a particle size of 100 nm or less is precipitated in a cell or a crystal grain. More specifically, it has a lath-like structure having a fine spherical compound with a particle size of 50 nm or less.
  • High strength and high toughness magnesium alloy according to the present invention, Z n the containing% a atom, L a, C e ⁇ b atom in total of at least one rare earth element selected from the group consisting of Pi Mm 0/0 Contains, Si, Gd, Dy, Tb, Ho, Er, Ca, Mn, Ag, Li, Zr, Th, Y, Yb, Eu, Pr, Sm and Nd
  • the total content of at least one metal selected from the group is more than 0 atomic% and 1.8 atomic% or less, the balance being Mg, and a and b satisfy the following formulas (1) to (3).
  • an intermetallic compound having a particle size of 100 nm or less is precipitated in a cell or a crystal grain. More specifically, it has a lath-like structure having a fine spherical compound with a particle size of 50 nm or less.
  • Each of the high-strength and toughness magnesium alloys according to the present invention is useful as an alloy for high-tech equipment requiring high performance in both strength and toughness, and La, Ce and Mm are rare earth elements. It is inexpensive inside, and is cost-effective.
  • the reason why the content of zinc is set to 0.2 atomic% or more is that if it is less than 0.2 atomic% / 0 , at least one of strength and toughness becomes insufficient.
  • the reason why the content of the rare earth element is 0.3 atomic% or more is that if the content is less than 0.3 atomic%, at least one of strength and toughness becomes insufficient.
  • the increase in strength and toughness, especially the toughness is remarkable when the rare earth element content is 0.5 to 1.5 atomic%.
  • the increase in strength and toughness becomes remarkable at 0.5 to 2.0 atomic%.
  • the strength tends to decrease as the content of the rare earth element decreases, but even in this range, the strength and toughness are higher than before.
  • the high-strength, high-toughness magnesium alloy according to the present invention contains Zn at a atomic%, and contains at least one rare earth element selected from the group consisting of La, Ce and Mm in a total of 13 atomic%, The remainder consists of Mg, and a and b are quenched and solidified melts satisfying the following formulas (1) to (3) to form quenched solids, and are plastically worked products after plastic quenching of the quenched solids. So,
  • an intermetallic compound having a particle size of 100 nm or less is precipitated in a cell or a crystal grain. More specifically, it has a lath-like structure having a fine spherical compound with a particle size of 50 nm or less.
  • a Z n contains% a atom, L a, b atomic 0/0 containing in total of at least one rare earth element selected from the group consisting of C e and Mm From the group consisting of Si, Gd, Dy, Tb, Ho, Er, Ca, Mn, Ag, Li, Zr, Th, Y, Yb, Eu, Pr, Sm and Nd.
  • the total content of at least one selected metal is more than 0 atomic% and 1.8 atomic% or less, and the balance consists of Mg, and a and b satisfy the following formulas (1) to (3).
  • an intermetallic compound having a particle size of 100 nm or less is precipitated in a cell or a crystal grain. More specifically, it has a lath-like structure having a fine spherical compound with a particle size of 50 nm or less.
  • the plastic deformation is any one of extrusion, rolling, ECAE (equal-channel-angular-extrusion), and forging.
  • the rare earth element may be La or Ce.
  • the cooling rate at the time of rapidly solidifying the molten metal is preferably 3.5 ⁇ 10 4 K ns or more. Good. This is because if the cooling rate is less than 3.5 ⁇ 10 4 K / sec, the toughness of the magnesium alloy decreases.
  • the cooling rate when rapidly solidifying the molten metal is 7 ⁇ 10 4 KZ seconds or more.
  • the intermetallic compound for example, the spherical compound is a Mg-— ⁇ -rare earth element-based precipitate.
  • a segregation layer having a thickness of 100 nm or less may be present at a boundary of the cells or a crystal grain boundary.
  • the reason why the thickness of the segregated material segregating at the cell boundary or grain boundary is 100 nm or less is that when a segregated material having a thickness of more than 100 nm segregates at the cell boundary or the grain boundary, it becomes brittle. This is because high toughness cannot be obtained.
  • Mg, Zn, and a rare-earth element system be present in the biased layer.
  • the total volume fraction of the intermetallic compound (for example, spherical compound) and the segregation layer is preferably 3.6% or more and 17% or less.
  • the total content of rare earth elements may be 1.8 atomic% or less.
  • the width of the cell or the crystal grain may be 500 nm or less.
  • the method for producing a high-strength, high-toughness magnesium alloy according to the present invention comprises: a) containing at least one atomic% of Zn, and at least one rare earth element selected from the group consisting of La, Ce, and Mm in a total containing atomic%, and the balance of Mg, a and b the following formula (1) to (3) the melt satisfying, 3. 5 X 1 0 4 rapidly solidified product is rapidly solidified by the KZ seconds or more cooling rate Is provided.
  • the method for producing a high-strength, high-toughness magnesium alloy according to the present invention includes the step of: containing at least one atomic% of Zn; . /. Containing, Si, Gd, Dy, Tb, Ho, Er, Ca, Mn, Ag, Li, Zr, Th, Y, Yb, Eu, Pr, Sm and Nd
  • a total of at least one metal selected from the group consisting of more than 0 atomic% and not more than 1.8 atomic%, with the balance being Mg, and a and b are molten metals satisfying the following formulas (1) to (3).
  • the method for producing a high-strength, high-toughness magnesium alloy according to the present invention includes the step of: containing at least one atomic% of Zn, and adding at least one rare earth element selected from the group consisting of La, Ce and Mm to a total of b atoms % contained, and the balance of Mg, a and b are the molten metal satisfy the following formula (1) to (3), it is rapidly solidified at 7 X 1 0 4 K / sec or more cooling rate making rapidly solidified product Step is provided.
  • the method for producing a high-strength, high-toughness magnesium alloy according to the present invention includes the step of: containing at least one atomic% of Zn and at least one rare earth element selected from the group consisting of La, Ce and Mm in total.
  • b at%, Si, Gd, Dy, Tb, Ho, Er, Ca, Mn, Ag, Li, Zr, Th, Y, Yb, Eu, Pr, Sm and ⁇ Nd
  • the method for producing a high-strength and high-toughness magnesium alloy according to the present invention may further comprise, after the step of forming the rapidly solidified product, a step of plastically adding the rapidly solidified product to form a plastic processed product. It is possible. By applying plastic working, shearing force is applied to bring about metal bonding between rapidly solidified powders, etc., and a dense plastic processed product is created.
  • a step of preforming the rapidly solidified product to form a preformed product after the step of forming the rapidly solidified product, a step of preforming the rapidly solidified product to form a preformed product; and Process of forming a plastic workpiece by plastic working It is also possible to provide further.
  • a step of solidifying and shaping the rapidly solidified product by plastic working after the step of forming the rapidly solidified product, a step of solidifying and shaping the rapidly solidified product by plastic working; It is possible to further provide a step of performing plastic working on the object.
  • the method for producing a high-strength and high-toughness magnesium alloy according to the present invention may further include, after the step of forming the plastic workpiece, a step of performing secondary plastic working on the plastic workpiece.
  • the preforming may be compression molding or canning.
  • the plastic working may be at least one of extrusion, rolling, ECAE, and forging. 4. Brief description of drawings
  • FIG. 1 is a graph showing the results of evaluation of the bite hardness and ductility of each of the magnesium alloys of Examples 1 to 18 and Comparative Examples 1 to 11.
  • Figure 2 shows the relationship between volume fraction (V f) and Vickers hardness (Hv) when annealing was performed at 573K in Examples 2, 3, 5, 6, 8, and 9 and Comparative Examples 2 to 7. It is a graph.
  • Figure 3 shows the relationship between volume fraction (vf) and Vickers hardness (Hv) when annealing was performed at 673 ° in Examples 2, 3, 5, 6, 8, and 9 and Comparative Examples 2 to 7. It is a graph.
  • FIG. 4 is a diagram in which the hardness lines are drawn on the graph of FIG.
  • FIG. 5 is a graph showing the relationship between the cooling rate during rapid cooling, Vickers hardness, and ductility.
  • FIG. 6A is a photograph showing the crystal structure of the test piece denoted by reference numeral 1 shown in FIG. 5, and FIG. 6B is a photograph showing the crystal structure of the test piece denoted by reference numeral 2 shown in FIG.
  • FIG. 7 is a photograph showing the crystal structure of the test piece denoted by reference numeral 3 shown in FIG.
  • FIG. 8 is a view showing a photograph of a crystal structure after preparing a test piece from a molten metal containing 2.0 atomic% of La by a liquid quenching method and annealing this test piece at 573K.
  • FIG. 9 is a view showing a photograph of a crystal structure after preparing a test piece from a molten metal containing 1.5 atomic% of La by a liquid quenching method and annealing the test piece at 573K.
  • FIG. 10 is a graph showing the results of the Pickers hardness and ductility evaluation of each of the magnesium alloys of Examples 19 to 24 and Comparative Examples 12 to 19.
  • FIG. 11 is a graph showing the results of evaluation of the Vickers hardness and ductility of each of the magnesium alloys of Examples 25 to 28 and Comparative Examples 20 to 24.
  • a magnesium alloy having both high strength and toughness is a magnesium alloy having a rare earth element of La, Ce, or Mm, which is a Mg—Zn—RE (rare earth element) alloy described below.
  • a low zinc content of 3.0 atomic% or less and a rare earth element content of 1.8 atomic% or less provide unprecedented high strength and high toughness. This has led to the present invention.
  • the magnesium alloy according to Embodiment 1 of the present invention is basically a ternary or quaternary alloy composed of Mg, Zn, and a rare earth element, and the rare earth element is composed of Ce, La, and Mm.
  • M m mish metal
  • M m is a mixture or alloy of a plurality of rare earth elements mainly composed of Ce and La, and is used to precisely remove useful rare earth elements such as Sm and Nd from ore. After refining, the composition of which depends on the composition of the ore before refining Things.
  • the above-mentioned magnesium alloy by hot melt to prepare a molten alloy, the solvent water 3. 5 X 1 0 4 K / sec or more cooling rate, and more preferably from 7 X 1 0 4 or KZ seconds cooling rate
  • the powder, flakes, ribbons or thin wires obtained are preformed and solidified.
  • the preforming may be through a billet forming step by compressing a powder, a flake, a ribbon or a thin wire, or may be a caning or the like.
  • the preforming is for facilitating plastic working, and has effects such as solidifying powder or the like to prevent oxidation during plastic working and facilitating handling.
  • the plastic working may be performed by extrusion.
  • Rapid solidification includes gun method, piston-anvil method, centrifugal method, single-roll method, twin-roll method, or spray method, high-pressure gas atomization method, spinning in rotating liquid, and injection molding of molten metal.
  • the roll method, twin roll method or high pressure gas atomization method is particularly suitable.
  • the magnesium alloy produced in this way has a normal hcp structure and does not have a long-period hexagonal structure.
  • the cells or crystal grains of the magnesium alloy are rod-shaped, and the width of the cells or crystal grains is 500 nm or less.
  • the crystal structure of the molded product is a structure mainly composed of a lath structure having the spherical compound.
  • the magnesium alloy obtained as described above has high strength and high toughness.Even if there is a magnesium alloy in which the performance of strength and toughness alone is superior to that of the magnesium alloy of the present invention, in both performance of strength and toughness No magnesium alloy has ever surpassed the magnesium alloy of the present invention. Particularly, magnesium alloys of recent years require both high strength and high toughness, but the magnesium alloy of the present invention exactly meets these requirements.
  • both magnesium and zinc are inexpensive metals, and La and Ce are also inexpensive metals of low utility value among rare earth elements.
  • Misch metal can also be obtained as an inexpensive alloy after removing expensive rare earth elements other than La and Ce. Therefore, the Mg—Zn—RE-based magnesium alloy of the present invention can be produced with an inexpensive material despite having high performance, which is extremely advantageous.
  • the Mg—Zn_RE based magnesium alloy of the present invention since the content of zinc and the rare earth element is low, characteristics of Mg having a small specific gravity can be sufficiently obtained.
  • the components other than zinc and the rare earth element having the contents in the above-described range are magnesium, but contain other elements to such an extent that alloy characteristics are not affected. Is also good.
  • the magnesium alloy of the present invention has an M g—Z n— — Z n— RE—Me system (Me is Si, Gd, Dy ⁇ Tb, Ho, Er, Ca, Mn, Ag, Li, Zr, Th, Y, Yb, Eu, Pr, 3111 And 1 ⁇ (at least one element selected from the group consisting of 1.)
  • the content of Me is more than 0 atomic% and 1.8 atomic ° / 0 or less. Other properties can be improved while maintaining strength and toughness.
  • the method of manufacturing a magnesium alloy according to the present embodiment is the same as the method of manufacturing the first embodiment.
  • a magnesium alloy having the composition of Embodiment 1 or 2 is rapidly solidified by the same manufacturing method as in Embodiment 1 and solidified to obtain a molded product.
  • a first plastic working is performed on the molded product to produce a first plastic processed product (primary workpiece).
  • the first type of plastic working refers to processing such as extrusion, rolling, ECAE, and forging.
  • a second plastic working is performed on the first plastic processed product to produce a second plastic processed product (secondary processed product).
  • the second type of plastic working means processing such as extrusion, rolling, ECAE, forging, drawing, and bending. Products and components such as PC housings are manufactured by the second plastic working.
  • the first plastic working is performed, and then the second plastic working is performed to manufacture a product or a part. It is also possible to manufacture products and parts.
  • Mg-Zn-rare earth element-based intermetallic compounds such as spherical compounds are precipitated. These are high strength and high toughness magnesium alloys.
  • the first to third embodiments it is useful as an alloy for high-tech equipment requiring high performance in both strength and toughness, and La, Ce, and Mm are rare earth elements. Inexpensive among the class elements, and also advantageous in terms of cost
  • Examples 1 to 18 and Comparative Examples 1 to 11 relate to a Mg—Zn—La ′ ternary alloy.
  • Mg, Zn, and La were weighed so as to have the alloy compositions shown in Table 1, filled into a ruppo, and subjected to high frequency melting in an Ar gas atmosphere to prepare a total of 29 kinds of molten alloys.
  • extrusion is performed at an extrusion temperature of 250 to 500 ° C and usually at 300 to 400 ° C, so one of the test pieces of each composition is at 300 ° C (573 K) and the other is at 400 ° C.
  • Heat treatment at ° C (673 K) approximated that of a magnesium alloy obtained by normal extrusion forming.
  • an Mg—Zn_La intermetallic compound for example, a spherical compound
  • the volume fraction of the intermetallic compound of the magnesium alloy to which 2. atomic% of lanthanum is added is 18.7%, and the volume fraction of 1.3.7% and 1.0 atomic% when 1.5 atomic% is added. With the addition, the volume fraction was estimated to be 8.7%.
  • V f volume fraction
  • Hv Vickers hardness
  • Zn is contained in an amount of 0.2 to 3.0 atomic%
  • La is contained in an amount of 0.3 to 1.8 atomic%
  • the balance is M
  • FIG. 4 is a diagram in which the hardness lines are drawn on the graph of FIG. Vickers hardness
  • the iso-hardness line of 150 is indicated by reference numeral 150 and the iso-hardness line of Vickers hardness 140 is indicated by reference numeral 140 and the iso-hardness line of Vickers hardness 130 is indicated by reference numeral. It is indicated by the reference numeral 130 and the contour line of the Vickers hardness of 120 is indicated by the reference numeral 120. The reference line is indicated by the contour line of the Vickers hardness of 110.
  • each isohardness line is a composition range showing each Vickers hardness. According to FIG. 4, it can be seen that the results with the best characteristics were obtained in a magnesium alloy having a Zn content of 0.5 at% and a La content of 1.5 at% and the balance being Mg.
  • FIG. 5 is a graph showing the relationship between the cooling rate during rapid cooling, Vickers hardness, and ductility.
  • a Z n contains 0.5 atomic%
  • the L a 1. 5 atoms 0/0 contains, from the molten metal and the balance of M g, by a single roll liquid quenching method, the length Ripon-shaped test pieces of about 100 O mm, width 2 mm, and thickness of 20 to 40 ⁇ m were prepared.
  • the cooling rate during rapid cooling of the liquid was changed, and test specimens were prepared at each cooling rate.
  • FIG. 6A is a photograph showing the crystal structure of the test piece denoted by reference numeral 1 shown in FIG. 5, and FIG. 6B is a photograph showing the crystal structure of the test piece denoted by reference numeral 2 shown in FIG.
  • FIG. 7 is a photograph showing the crystal structure of the test piece denoted by reference numeral 3 shown in FIG.
  • the test specimens with reference numerals 1 to 3 were annealed at 573 K.
  • the structure of the alloy is mainly composed of a lath-like structure having a fine spherical compound with a particle diameter of 50 nm or less, and the width of the cell or crystal grain ( The short diameter of the rod-shaped portion is less than 300 nm.
  • the segregation layer at the cell boundary or grain boundary is as thin as 1 O Onm or less, high toughness (high ductility) can be obtained without embrittlement.
  • the cells or crystal grains are not finer than in Fig. 6A, and the thickness of the segregation layer, which is deviated at the cell boundaries or grain boundaries, is larger than in Fig. 6A. ing.
  • high strength and high strength can be obtained when the fine spherical compound in the cell or crystal grain has a particle size of 50 nm or less and precipitates almost uniformly. It can be seen that toughness characteristics can be obtained. It is considered that high toughness characteristics can be obtained when the thickness of the segregation layer at the cell boundary or crystal grain boundary is as thin as 100 nm or less. Also, it is considered that high strength and high toughness characteristics can be obtained in the case of a fine structure with a cell or crystal grain width of 300 nm or less (500 nm or less is acceptable).
  • sigma 11 contains 0.5 atomic%
  • the L a 2. contains 0 atomic%
  • Figure shows a photograph of the crystal structure after preparing a lipon-shaped test piece with a length of about 100 Omm, a width of 2 mm, and a thickness of 20 to 40 / m by the method, and annealing this test piece at 573 K. It is.
  • Figure 9 contains a 211 0.5 atomic%, 1 ⁇ & 1. containing 5 atomic%, the molten metal and the balance of Mg, 1 X 1 0 5 K / sec single-roll liquid cooling rate of
  • This figure shows a photograph of the crystal structure of a ribbon-shaped test piece with a length of about 1000 mm, a width of 2 mm, and a thickness of 20 to 40 prepared by the quenching method and annealing this test piece at 573 K. .
  • high strength and high toughness characteristics can be obtained when the fine spherical compound in the cell or crystal grain has a particle diameter of 50 nm or less and is almost uniformly precipitated. It is considered that high toughness characteristics can be obtained when the thickness of the segregation layer at the cell boundary or grain boundary is as thin as 100 nm or less. In addition, cells or It is thought that high strength and high toughness characteristics can be obtained in a fine structure with a crystal grain width of 300 nm or less (or 500 nm or less).
  • the cell structure shown in FIG. 8 the cell structure is large, cells or crystal grains are not finely formed, and a thick segregation layer at the cell boundaries or crystal grain boundaries is devoted. It is considered that the alloy properties become brittle due to such a thick segregation layer.
  • the segregation layer contains Mg, Zn, and a rare earth element (La).
  • Examples 19 to 24 and Comparative Examples 12 to 19 relate to a Mg—Zn—Ce ternary alloy.
  • Mg, Zn, and Ce were weighed so as to have the alloy compositions shown in Table 2, filled in a crucible, and subjected to high frequency melting in an Ar gas atmosphere to prepare a total of 14 kinds of molten alloys.
  • Example 2 Under the same conditions as in Example 1, a total of 14 hardness test samples and lipon-shaped test pieces were prepared from these molten alloys, and the Vickers hardness (Hv) of the former and the ductility of the latter were evaluated.
  • Table 2 and FIG. 10 summarize the results of evaluation of Vickers hardness (Hv) and ductility of each of the magnesium alloys of Examples 19 to 24 and Comparative Examples 12 to 19.
  • Table 2 and Fig. 10 show that the hardness of the Mg-Zn-Ce ternary alloy increases as the amount of added cerium increases, but when the amount of added cerium reaches 1.5 atomic%. It was found that the alloy became semi-ductile and became brittle when it reached 2.0 at%.
  • Examples 25 to 28 and Comparative Examples 20 to 24 relate to an Mg—Zn—Mm alloy, and Mm used was Ce rich.
  • Mg, Zn, and Mm were weighed so as to have the alloy compositions shown in Table 3, filled in a ruppo, and subjected to high frequency melting in an Ar gas atmosphere to prepare a total of nine types of molten alloys. Under the same conditions as in Example 1, a total of 9 hardness tests were performed from these molten alloys. We prepared a sample for use and a ripon-shaped test piece, and evaluated the Vickers hardness (Hv) of the former and the ductility of the latter.
  • Hv Vickers hardness
  • Table 3 and FIG. 11 summarize the results of Vickers hardness (Hv) and ductility evaluation of each of the magnesium alloys of Examples 25 to 28 and Comparative Examples 20 to 24.

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Abstract

L'invention porte sur un alliage de magnésium de haute résistance et ténacité comprenant obtenu à partir d'un alliage fondu comportant:(a) un % atomique de Zn et (b) un % atomique d'au moins une terre rare sélectionnée parmi La, Ce, et Mn, et le reliquat de Mg, a et b devant satisfaire aux conditions (1) à (3) suivantes: (1) 0,2 = a = 3,0, (2) 0,3 = b = 1,8, (3) 0,2a + 0,55 = b = -0,2a + 1,95, l'alliage fondu étant ensuite solidifié par refroidissement rapide. Ledit alliage comporte une structure lattée de cellules et de grains à l'intérieur desquels se trouvent de microéléments sphériques de 50 nm ou moins, et présente une résistance et une ténacité suffisantes pour pratiquement toutes les applications des alliages de magnésium couramment répandus.
PCT/JP2004/004201 2003-03-25 2004-03-25 Alliage de magnesium de haute resistance et tenacite, et son procede de production WO2004085689A1 (fr)

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WO2008117890A1 (fr) 2007-03-26 2008-10-02 Toyota Jidosha Kabushiki Kaisha Alliages de magnesium et procede de production associe
CN100434555C (zh) * 2006-05-25 2008-11-19 上海交通大学 自生准晶增强的高塑性变形镁合金
WO2008140062A1 (fr) * 2007-05-09 2008-11-20 National Institute For Materials Science ALLIAGE À BASE DE Mg
WO2009039581A1 (fr) * 2007-09-28 2009-04-02 Cast Crc Limited Alliage de magnésium moulé en coquille
JP2011042847A (ja) * 2009-08-24 2011-03-03 Peter Stolfig マグネシウム合金
JP2014040672A (ja) * 2006-08-03 2014-03-06 National Institute For Materials Science マグネシウム合金とその製造方法
CN104928549A (zh) * 2015-06-16 2015-09-23 上海交通大学 一种高强度高弹性模量的铸造镁稀土合金及其制备方法
EP2764130A4 (fr) * 2011-10-06 2016-03-09 Univ Pittsburgh Alliages métalliques biodégradables
WO2016074424A1 (fr) * 2014-11-13 2016-05-19 比亚迪股份有限公司 Alliage de magnésium, son procédé de préparation et son utilisation
CN108624793A (zh) * 2018-08-23 2018-10-09 中国科学院长春应用化学研究所 一种含Ag的高强耐热镁合金及其制备方法
CN109207825A (zh) * 2018-09-29 2019-01-15 江苏中科亚美新材料有限公司 一种高导热高强韧镁合金材料及其制备方法
CN109898003A (zh) * 2019-04-03 2019-06-18 河海大学 一种基于18r长周期相超细化增强的高强韧镁合金及其制备方法
CN109913725A (zh) * 2019-04-03 2019-06-21 河海大学 一种可控长周期相尺寸的高强韧镁合金及其制备方法
CN110964961A (zh) * 2019-12-31 2020-04-07 龙南龙钇重稀土科技股份有限公司 一种高强高耐腐蚀性镁合金及其制备工艺
CN112941349A (zh) * 2021-02-26 2021-06-11 惠州云海镁业有限公司 高韧耐腐性镁合金制备工艺
CN115747545A (zh) * 2022-12-29 2023-03-07 中北大学 一种加压熔炼和自由流体快速冷却相结合的镁合金制备方法

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Cited By (21)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN100434555C (zh) * 2006-05-25 2008-11-19 上海交通大学 自生准晶增强的高塑性变形镁合金
JP2014040672A (ja) * 2006-08-03 2014-03-06 National Institute For Materials Science マグネシウム合金とその製造方法
US8636853B2 (en) 2007-03-26 2014-01-28 Toyota Jidosha Kabushiki Kaisha Mg alloy and method of production of same
WO2008117890A1 (fr) 2007-03-26 2008-10-02 Toyota Jidosha Kabushiki Kaisha Alliages de magnesium et procede de production associe
WO2008140062A1 (fr) * 2007-05-09 2008-11-20 National Institute For Materials Science ALLIAGE À BASE DE Mg
JP5404391B2 (ja) * 2007-05-09 2014-01-29 独立行政法人物質・材料研究機構 Ｍｇ基合金
WO2009039581A1 (fr) * 2007-09-28 2009-04-02 Cast Crc Limited Alliage de magnésium moulé en coquille
JP2011042847A (ja) * 2009-08-24 2011-03-03 Peter Stolfig マグネシウム合金
EP2764130A4 (fr) * 2011-10-06 2016-03-09 Univ Pittsburgh Alliages métalliques biodégradables
WO2016074424A1 (fr) * 2014-11-13 2016-05-19 比亚迪股份有限公司 Alliage de magnésium, son procédé de préparation et son utilisation
US10358703B2 (en) 2014-11-13 2019-07-23 Byd Company Limited Magnesium alloy and method of preparing the same
CN104928549A (zh) * 2015-06-16 2015-09-23 上海交通大学 一种高强度高弹性模量的铸造镁稀土合金及其制备方法
CN108624793A (zh) * 2018-08-23 2018-10-09 中国科学院长春应用化学研究所 一种含Ag的高强耐热镁合金及其制备方法
CN109207825A (zh) * 2018-09-29 2019-01-15 江苏中科亚美新材料有限公司 一种高导热高强韧镁合金材料及其制备方法
WO2020062874A1 (fr) * 2018-09-29 2020-04-02 江苏中科亚美新材料股份有限公司 Matériau d'alliage de magnésium à haute conductivité thermique et haute résistance et procédé de préparation associé
CN109898003A (zh) * 2019-04-03 2019-06-18 河海大学 一种基于18r长周期相超细化增强的高强韧镁合金及其制备方法
CN109913725A (zh) * 2019-04-03 2019-06-21 河海大学 一种可控长周期相尺寸的高强韧镁合金及其制备方法
CN110964961A (zh) * 2019-12-31 2020-04-07 龙南龙钇重稀土科技股份有限公司 一种高强高耐腐蚀性镁合金及其制备工艺
CN112941349A (zh) * 2021-02-26 2021-06-11 惠州云海镁业有限公司 高韧耐腐性镁合金制备工艺
CN115747545A (zh) * 2022-12-29 2023-03-07 中北大学 一种加压熔炼和自由流体快速冷却相结合的镁合金制备方法
CN115747545B (zh) * 2022-12-29 2023-08-11 中北大学 一种加压熔炼和自由流体快速冷却相结合的镁合金制备方法

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