EP1759029B1 - Schmiedeprodukt aus magnesiumlegierung mit ausgezeichneter formbarkeit und verfahren zu dessen herstellung - Google Patents

Schmiedeprodukt aus magnesiumlegierung mit ausgezeichneter formbarkeit und verfahren zu dessen herstellung Download PDF

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EP1759029B1
EP1759029B1 EP05856294A EP05856294A EP1759029B1 EP 1759029 B1 EP1759029 B1 EP 1759029B1 EP 05856294 A EP05856294 A EP 05856294A EP 05856294 A EP05856294 A EP 05856294A EP 1759029 B1 EP1759029 B1 EP 1759029B1
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magnesium alloy
elements
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wrought magnesium
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EP1759029A4 (de
EP1759029A1 (de
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Kang-Hyung Kim
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PRIMOMETAL Co Ltd
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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
    • C22C23/02—Alloys based on magnesium with aluminium 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
    • 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

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  • the present invention relates to a wrought magnesium alloy, which contains a second phase consisting of an intermetallic compound, thereby having excellent strength, formability, and corrosion resistance. More particularly, the present invention pertains to a wrought magnesium alloy, which comprises 0.1-1.5 at% of a first essential element selected from the group 3 elements Sc, Y and lanthanides and mixtures thereof, 1.0-4.0 at% of a second essential element selected from the group 13 elements Al, B and mixtures thereof, and 0.65 at% or less of a third element selected from the group 12 elements Zn, Cd and mixtures thereof, 0.35 at% or less of one selected from the group consisting of group 2 elements Ca and Sr, group 4 elements Ti, Zr and Hf, group 7 element Mn, group 14 elements Si and Ge, and mixtures thereof, and a balance of Mg and unavoidable impurities, and thus contains a second phase of finely precipitated intermetallic compounds, and a method of producing the same.
  • a wrought magnesium alloy which comprises 0.1-1.5 at
  • the groups of elements arranged into vertical columns in the periodic table of elements are referred to according to the new IUPAC (International Union of Pure and Applied Chemistry) system which numbers each column with Arabic numbers from 1 through 18.
  • the groups of elements are referred to herein according to the old IUPAC system which numbers the columns with Roman numerals followed by either the letter a or b.
  • the correlation between the groups is as follows: New IUPAC system: Old IUPAC system: group 2 group IIa group 3 group IIIa group 4 group IVa group 7 group VIIa group 12 group IIb group 13 group IIIb group 14 group IVb
  • magnesium alloys have been developed as light structural materials for airplanes and automobiles.
  • HCP hexagonal close packed
  • a Mg-Zn alloy shows an excellent age hardening behavior, and is advantageous in that since a microstructure is refined through heat treatments, strength and ductility significantly increase and it is easy to work and weld.
  • it is disadvantageous in that since micropores are formed as a casting process due to the addition of Zn, it is difficult to apply the Mg-Zn alloy to a casting process, such as die-casting. Additionally, it is difficult to desirably improve strength because it is grown as the coarse grain.
  • studies have been made to improve formability using a grain boundary slip, in which some alloy elements are added to Mg-Zn binary alloys to refine grains. With respect to this, J. P. Doan and G.
  • Ansel suggest a method of improving the strength of an alloy, in which Zr is added to refine grains constituting a Mg-Zn alloy (J. P. Doan and G. Ansel, Trans, AIME, vol. 171 (1947), pp. 286-295 ).
  • Zr has a high melting point and a low solubility to Mg at room temperature, it mostly exists at a grain boundary, thus acting as a fracture initiation site when external stress is applied.
  • microstructures have a single-phase solid solution and thus have excellent ductility, they are disadvantageous in that since a strain hardening ability is poor and it is difficult to prevent the grain growth, formability is poor due to anisotropy.
  • a technology in which different portions are heated at different temperatures to achieve a warm working process, is suggested so as to avoid the above disadvantage.
  • the technology is problematic in that the different heating temperatures of the different portions significantly increase the production cost of a press mold.
  • a thixo-molding method in which preliminarily flake shaped powder is compacted at high temperatures in a region where liquid and solid phases coexist, is suggested.
  • this method is disadvantageous in that the powder is expensive, and in that it is difficult to apply an electroplating process because the powder pressed material has a porous structure.
  • Magnesium has low corrosion resistance, and thus, it is necessary to treat a surface of magnesium, but undesirably, a gas phase plating process or an electroless plating process requires chemical and treatment costs that are much higher than the electroplating process.
  • products having high porosity and low density such as die-casting and thixo-molding products, are difficult to apply to a wet-plating process because corrosion occurs due to chemicals soaked into the pores.
  • Korean Pat. Laid-Open Publication No. 2003-0048412 discloses an alloy, which contains 3.0 - 10.0 wt% Zn, 0.25 - 3.0wt% Mn, Al, Si, and Ca.
  • the alloy containing Zn in an amount of 2 % or more has high strength, it has a disadvantage in that free zinc (Zn) readily forms a low melting point eutectic phase.
  • Zn free zinc
  • Mg 7 Zn 3 having a low melting point that is less than 350°C, exists, corrosion resistance is low.
  • the plate is easily cracked at both sides during a rough rolling process for breaking the coarse dendrite structure, so draw-ability is poor because of high anisotropy.
  • Laid-Open Publication No. 2002-0078936 U.S. Pat. No. 6471797 discloses a method of improving strength and formability using a Mg-Zn-Y eutectic ternary alloy quasi-crystalline phase which contains 1 - 10 at% Zn and 0.1 - 3 at% Y.
  • this method is disadvantageous in that the amount of Zn must be enough so as to desirably assure a quasi-crystalline phase effect.
  • the composition of a cast product is not uniform because a specific gravity between zinc and magnesium is significantly different.
  • the micro-pores at the grain boundary reduce corrosion resistance, and tears form at sides of a plate during the hot rolling process.
  • H07-54026 entitled 'magnesium alloy having high strength and method of producing the same', U.S. Pat. 4675157 , 4765954 , 4853035 , 4857109 , 4938809 , 5071474 , 5078806 , 5078807 , 5087304 , 5129960 , and 5316598 , EP No. 0,361,136A1 , and French Pat. No. 2,688,233 disclose the formation of an amorphous structure through a Rapid Solidification process. Since the cooling rate must be conducted at 10 5 - 10 7 °C/s to form the amorphous structure, the patents are useful to produce powder or a thin strip, but not to produce a common plate shape. Accordingly, an ingot, which is produced by compacting amorphous powder under the recrystallization temperature, is employed in order to conduct a rolling or a press forming.
  • U.S. Pat. Nos. 637040 , 3391034 , 4116731 , 4194908 , and 5059390 , and English Pat. No. 2095288 disclose the fact that some rare-earth elements are used to prevent the grain growth or the grain boundary slip at high temperatures while their eutectic phases exist at grain boundary so as to improve creep resistance.
  • the eutectic phase mostly has a coarse microstructure that is incoherent to a matrix microstructure, and thus, formability is insufficiently improved.
  • Japanese Pat. Laid-Open Publication Nos. H7-109538A U.S. Pat. Nos.
  • 5693158 , 5800640 and 6395224 disclose a method of producing goods having low crack sensitivity, in which Sr, Li or B is employed and heat treatments are conducted to refine a particle size of crystals of a cast product.
  • these patents are useful to cast products, but cannot be directly applied to wrought products.
  • Japanese Pat. Laid-Open Publication No. H10-147830A discloses the use of 6 - 12 wt% Y and 1 - 6 wt% Gd, and hot forging and subsequent aging processes to improve creep resistance to be applied to engine parts.
  • the patent cannot be applied to wrought products because the product cost significantly increases due to the use of a lot expensive elements, and the coarse intermetallic compounds are incoherent to the matrix.
  • WO 89/11552 refers to the superplastic forming of rapidly solidified magnesium base metal alloys, particularly containing uniform dispersions of intermetallic compounds that provide the alloys with good corrosion resistance combined with high strength and good ductility.
  • an alloy having a composition consisting essentially of the formula Mg bal Al a Zn b X c , wherein X is at least one element selected from the group consisting of, amongst others, Mn or Y, "a” ranges from about 0 to 15 at%, "b” ranges from about 0 to 4 at%, “c” ranges from about 0.2 to 3 at%, the balance being magnesium and incidental impurities, with the proviso that the sum of aluminum and zinc present ranges from about 2 to 15 at%.
  • US 5,316,598 refers to a superplastically formed product from rolled magnesium base metal alloy sheet.
  • the process of its production comprises compacting a rapidly solidified magnesium based alloy powder to produce a billet, said alloy being defined by the same formula and composition as disclosed in WO 89/11552 (see above).
  • JP 2002 256370 refers to a high strength and high ductility magnesium based alloy. Particularly disclosed is an alloy having the compositional formula of Mg 100-a-b Ln a M b , wherein Ln is one or more kinds of elements selected from e.g. Y and La, M is one or more kinds of elements selected from Al and Zn, "a” ranges from 0.5 to 5 at%, and "b” ranges from 1.5 to 7 at%.
  • an object of the present invention is to provide a wrought magnesium alloy which contains the intermetallic compound coherent to a matrix microstructure and which has a second phase composite microstructure, thereby improving elongation and anisotropy to assure excellent formability and corrosion resistance.
  • an alloy consisting of three or more elements is used to activate a slip plane.
  • 3 and 13 groups are added together to reduce stacking fault energy and to improve corrosion resistance of the matrix microstructure.
  • fine intermetallic compound particles dispersed during extrusion and rolling processes are employed to improve strain hardening ability and formability.
  • the present invention provides a wrought magnesium alloy according to claim 1 and a method according to claim 2.
  • FIG. 1 illustrates a box sample formed using a wrought magnesium alloy sheet, according to the present invention
  • FIG. 2 illustrates a cup-shaped sample formed using the wrought magnesium alloy sheet, according to the present invention
  • FIG. 3 illustrates the box sample formed using AZ31 sheet
  • FIG. 4 illustrates a microstructure of a material of No. 1 in Table 1, which is cast and then diffusion annealed at 400 °C for 5 hours;
  • FIG. 5 illustrates a microstructure of an extruded material according to the present invention, which is annealed
  • FIG. 6 illustrates a microstructure of a rolled sheet according to the present invention.
  • the present invention is characterized in that the fine 2nd phase precipitates, which is coherent to matrix microstructure, is formed in the solid solution microstructure having excellent ductility, thereby making grains fine and improving formability.
  • the strength of most materials increases. The reason is that a dislocation moves along the specific slip plane in the course of plastic deformation of the metal in such a way that the dislocation does not directly move from one grain to another grain. But direction of dislocation changes its route because of the grain boundary barrier effect. Accordingly, since the grain boundaries act as barriers in the movement of the dislocation, dislocations are pile up at a grain boundary, thereby preventing deformation.
  • the high temperature stable phase must be capable of being formed in order to make the grain fine, and desired solid solubility must be assured at high temperatures in order to be coherent to a matrix microstructure. Furthermore, a size difference between elements of a matrix metal and atoms must be about 15 % so as to assure a desirable matrix reinforcement effect.
  • Many studies have been made of the effect of an intermetallic compound on a solid solution. Particularly, a matrix reinforcement effect caused by the dispersion of fine intermetallic compound particles is well known in the metallurgy engineering ( Mechanical Metallurgy, 2nd ed., George E. Dieter, McGraw-Hill, 1981, pp. 221-227 ).
  • the intermetallic compound has a high melting point and strong bonding strength, thus having high hardness and thermally stable. Because of the finely dispersed second phase particles, these alloys are much more resistant to recrystallization and grain growth than single-phase alloys. However, if the intermetallic compound has a microstructure that is incoherent to the matrix microstructure, it acts as a fracture initiation site and thus has increased strength, but elongation or total ductility is reduced even though the matrix microstructure has ductility.
  • the second phase of conventional magnesium alloy is not a high melting point phase in the matrix microstructure.
  • the 2 nd phase is low melting point eutectic phase during the solidification instead of the precipitates. Therefore, the eutectic phase is mostly incoherent to the matrix microstructure. It is scarcely an atomic match for the matrix microstructure, thus effectively preventing grain growth or over-aging.
  • it reduces the formability of a material or acts as a fracture initiation site. And thus, these type alloys are unsuitable for wrought magnesium alloy. Even though a duplex microstructure is formed, the movement of the dislocation is ineffectively prevented if the second phase is not strong, resulting in undesirably improved anisotropy or strength.
  • group 3 elements employed in the present invention readily form intermetallic compounds having a cubic lattice and thus have high a matrix reinforcement effect and ductility.
  • Alan Russel and Karl Gschneidner Jr. of the Ames Laboratory of Iowa State University which is affiliated with the U.S. Department of Energy, reported that an intermetallic compound formed by the group 3 has a B2 cubic lattice, such as CsCl, unlike a B27, B33, or DO 11 orthorhombic lattice of a conventional intermetallic compound. And thus, it has excellent ductility ( Nature Materials, 2, Sep. 2003, PP 587-590 ).
  • group IIIa elements are coherent to the magnesium matrix, and it is presumed that the ductility of the intermetallic compound is caused by stacking faults.
  • the stacking faults are formed because a stacking order of a closely packed side is changed unlike a normal stacking order, and it is known that they are mostly formed due to plastic deformation. It is difficult to form stacking faults if stacking fault energy is high, and thus, strain hardening required as a press material is not high. Accordingly, since pure aluminum or copper has high stacking fault energy, energy supplied during a room temperature process is mostly converted into heat. Thus, it is difficult to accumulate internal deformations, and a driving force for nucleation is reduced during recrystallization.
  • the group 13 and 3 elements are alloyed with magnesium acting as a matrix element, thereby reducing the stacking fault energy of the intermetallic compound to provide ductility. Additionally, fine second phases promote nucleation during a reheating process to make fine grains. Intermetallic compound particles prevent grain growth at a recrystallization temperature or higher.
  • the present inventor came to a conclusion that when a group 3 is alloyed with magnesium to form a solid solution having low stacking fault energy, when a group 13 is added to the solid solution to increase a solid-solution strengthening effect, and when a group 12 and other miniaturized elements are added to form a structure which contains an intermetallic compound coherent thereto, it is possible to create a material having excellent strain hardening ability, fineness through recrystallization by heat treatment, and improved anisotropy.
  • the group 3, that is, an essential element in the present invention includes Sc, Y, lanthanides, and actinides.
  • Sc, Y, or lanthanides be employed alone or in combination instead of actinides radiating radioactive rays. They are solid-solved in Mg, thus reducing a c/a ratio to increase ductility and reducing the stacking fault energy to increase the driving force for nucleation by recrystallization.
  • particles which exist in a form of Mg 5 RE at high temperatures during a solidification process, form prism-shaped plate particles having a HCP structure, that is, a DO 19 lattice structure, such as Mg 3 RE or Mg 17 RE 5 , at about 550 °C through a peritectic transformation.
  • RE is an abbreviated form of rare-earth elements belonging to the group 3
  • the particles have a high reinforcement effect and are coherent to the matrix, and consequently, they do not act as the fracture initiation site.
  • the particles may be compacted into a rod, a sphere, or a cube.
  • a eutectic phase which is not solid-solved after a diffusion heat-treatment, is finely dispersed during extrusion and rolling processes, thereby preventing grain growth during heat-treatment and acting as a site for nucleation by recrystallization.
  • the amount of the group 3 is less than 0.1 %, the second phase is formed in an insufficient amount.
  • the amount is more than 1.5 %, a fineness effect is saturated, and consequently, elongation is reduced and a production cost increases. This is the reason why that amount is limited.
  • the group 13 includes B, Al, Ga, In, and T1. Since Ga, In, and T1 having a low melting point form a low melting point eutectic phase, it is preferable to employ only A1 or a mixture of B and Al. The group 13 forms a fine deposit and thus contributes to reinforcement of the matrix. A1 is used as a main alloy element. Since B has a low solid solubility to magnesium and forms a high melting point compound, such as B 2 Y, B 3 Y 2 , or B 5 Y 3 , it is employed in conjunction with A1 in an amount of 0.010 % or less so as to make the fine grains.
  • A1 of the group 13 is solid-solved in Mg to increase corrosion resistance and to prevent the growth of a dendrite microstructure, thereby making a cast microstructure fine. Furthermore, since A1 forms fine cubes, such as Al 2 RE or Al 3 RE during the solidification process and increases ductility of the matrix microstructure, it is possible to produce goods having high strength and excellent ductility.
  • the amount of Al is less than 1.0 %, it is difficult to assure the desirable reinforcement effect.
  • the amount is more than 4.0 %, since an unstable rod- or plate-shaped Al 2 Mg 3 or Al 12 Mg 17 phase is enlarged in a grain boundary, even though room temperature strength is high, high temperature strength and corrosion resistance are reduced. This is the reason why that amount is limited.
  • group 2 group 4, group 7, or group 14 is selectively employed alone or in combination, and 1.0 % or less of group 12 is employed alone or in combination.
  • the group 2, group 4, and group 7 are used as a supplemental agent of the group IIIa and group IIIb.
  • the group IIa it is preferable to use Ca and Sr. Since Be, Ba, and Ra make toxic gases, they can be used only if a special ventilation device is adopted. Ca and Sr are particularly useful to make a fine cast structure in the casting a billet having a diameter of 200 mm or more in the present invention, and form disk-shaped particles, such as (Mg, Al) 2 Ca, thereby improving a reinforcement effect.
  • the group IVa Ti, Zr, and Hf are most frequently employed, and Rf is added, using a protection device in unavoidable cases, because of the emission of radioactive rays.
  • the group IVb makes a cast microstructure fine, and Si and Ge are most frequently employed because a melting point is high and it is easy to handle.
  • a grain fining effect depends on the amount of each element added. That is, Zr, Si, and Ca make the grains have fine sizes of microns corresponding to the reciprocal of 52, 19, and 15 microns.
  • Mn of the group 7 is a cheap alloy element, prevents the formation of Al 12 Mg 17 and Al 2 Mg 3 phases, and promotes the formation of high temperature cubic Al 2 Y to contribute to the fining of the grains and the improvement of corrosion resistance.
  • Tc and Re of the group 7 are costly and thus are used in unavoidable cases.
  • the group 2, group 4, group 7, and group 14 elements have low solid solubility to magnesium, and thus, if they are excessively added, segregation occurs or coarse particles having high brittleness are formed when a cooling rate is low after a casting process. Accordingly, the amount is limited to 0.35 % or less.
  • the group 12 includes Zn, Cd, and Hg. Since Hg is toxic to humans when breathing, use of Hg is limited, and it is used in conjunction with an additional protection device.
  • Zn and Cd are added alone or in combination, a stacking fault structure is formed in a magnesium matrix microstructure to bring about strain hardening, and Zn and Cd are smoothly solid-solved with the group 3 and group 13 elements to promote the formation of cubic particles, such as (Mg, Zn) 5 RE, Zn 6 Mg 2 RE, or (Mg, Zn) 17 RE 3 .
  • the excessive amount of Zn and Cd increases gas solid solubility, thereby reducing corrosion resistance or plating workability and brining about the occurrence of hot tear and gravity separation phenomena.
  • the amount is limited to 1.0 % or less, and preferably, 0.65 % or less.
  • a magnesium raw material is melted, and an alloy or a master alloy is added to the molten magnesium in a mixed gas atmosphere of SF 6 and Ar or CO 2 , or an Ar gas atmosphere while being blocked from contact with atmospheric air.
  • a slab for a magnesium alloy plate is produced through mold casting, Direct Chilled casting, continuous casting, or strip casting processes.
  • a mold in which a cavity having a thickness of 30 mm, a width of 250 mm, and a height of 400 mm is formed, is preheated in a heating furnace heated to about 200°C.
  • a molten magnesium alloy is poured into the mold at 710 - 760°C, and then machined so as to remove surface defects from a cast product.
  • (b) Diffusion annealing is conducted at 250 - 450°C so that the duration time is 1 min/mm or more with respect to the thickness of the slab.
  • the heating temperature is less than 250°C or the duration time is less than 1 min/mm, the inside of the slab is insufficiently heated, thus forming cracks on a surface or on an edge during a rolling process. It is preferable to heat the slab at 350 - 400°C so as to reduce the diffusion time.
  • the heating temperature is more than 450°C, a free low melting point eutectic phase may be formed during the diffusion annealing. At this stage, the eutectic phase may be remelted and thus separated from the slab. Accordingly, the molten eutectic phase may cling to a rolling roll.
  • the duration time and the heating temperature increase to improve workability.
  • a surface temperature of a rolling roll must be maintained at 50 - 150°C so as to prevent the formation of fine surface cracks caused by the qu enched slab while the slab is in contact with the roll.
  • the temperature of the rolling roll is more than 150°C, delamination, in which a portion of a rolling material clings to the rolling roll and then delaminates, occurs during the rolling process, thus roughening the surface of the slab. If the plate is not excessively cooled after the initial coarse rolling, it is possible to conduct the rolling process again without reheating.
  • a second rolling process is repeatedly conducted in a reduction ratio of 50 % or less each time until the desired thickness is gained.
  • the reduction ratio depends on the capacity of a motor of a rolling mill, a heat emitting state of a plate during a reduction process, elastic deformation of the rolling roll, and flatteness of the plate.
  • a second process annealing be repeatedly conducted at 200 - 450°C each time while a duration time is maintained at 1 min/mm or more during the second rolling process.
  • a rolled microstructure becomes fine, causing crack resistance.
  • annealing is not necessarily conducted every rolling process.
  • the final annealing is conducted at 180 - 350°C while a duration time is maintained at 1 min/mm or more, which depends on the thickness, strength, and elongation of the plate.
  • a duration time is maintained at 1 min/mm or more, which depends on the thickness, strength, and elongation of the plate.
  • a magnesium raw material is melted, and an alloy raw material or a master alloy is added to the molten magnesium raw material in a mixed gas atmosphere of SF 6 and Ar or CO 2 , or an Ar gas atmosphere while being blocked from contact with atmospheric air.
  • a molten magnesium alloy is poured into a mold, having a diameter of 185 mm and a length of 650 mm, at 710 - 760°C to form a billet, and is then processed so as to remove surface defects. Needless to say, it is possible to conduct a continuous casting in addition to a mold casting.
  • Diffusion annealing is conducted at 250 - 450°C while a duration time is maintained at 1 min/mm or more with respect to the diameter of the billet so as to fracture a coarse cast microstructure of a cast material and to remove fine segregation.
  • a heating temperature is less than 250°C or the duration time is less than 1 min/mm, stress is concentrated on a grain boundary, and consequently, alligatoring may occur, cracking the material in a direction of the extrusion. It is preferable to heat the material at 350 - 400°C so as to reduce a diffusion time.
  • the heating temperature is more than 450°C, a free low melting point eutectic phase may be re-melted during the diffusion annealing and thus be separated from the material.
  • the duration time and the heating temperature increase to improve workability.
  • the diffusion-annealed material is reheated in a heating furnace at 250 - 400°C to be extruded.
  • An extruder has an extrusion speed of a maximum of 20 m/min at an extrusion pressure of 850 MPa or more. If the extrusion is conducted at 500 MPa, the extrusion speed is significantly reduced to 3 - 4 m/min.
  • a temperature of a container is 300 - 450°C. When the temperature is less than 300°C, many surface cracks are formed. When the temperature is more than 450°C, high temperature cracks or deformations are significantly formed during the extrusion process.
  • the container is heated at about 350°C, and an extrusion ratio is typically 10 - 100. Additionally, in the present invention, the material may be wound in a coil form during the extrusion process, and thus, it is possible to conduct reciprocating rolling.
  • a first extrusion is conducted to fracture the cast microstructure and to disperse a second phase, and a second extrusion is then conducted.
  • a process annealing at 200 - 450°C while a duration time is maintained at 1 min/mm or more.
  • the microstructure is made fine, causing crack resistance, and the reheating is implemented in the container. Hence, annealing is not necessarily conducted.
  • the final annealing is conducted at 180 - 350°C while a duration time is maintained at 1 min/mm or more, which depends on a thickness, strength, and elongation of the plate.
  • a duration time is maintained at 1 min/mm or more, which depends on a thickness, strength, and elongation of the plate.
  • the annealing temperature is high and the time is long, elongation increases but strength is reduced.
  • the annealing temperature is more than 350°C, undesirably, yield strength is significantly reduced.
  • the heat treatment may be implemented using a rapidly heating device, such as a heater, employing a gas nozzle, or an induction heater, instead of the furnace.
  • the annealing temperature may deviate from the above range, without departing from the scope and concept of the invention.
  • wrought magnesium alloys of the present invention were rolled to obtain test results. They were tested after being rolled into plates having a width of 150 mm and a thickness of 1 mm.
  • Rectangular molds which had a width of 80 mm, a length of 100 mm, and a depth of 45 mm, were formed, and edge cracks of the molds were observed, thereby achieving a forming test.
  • Samples having an area of 80 mm X 50 mm were hung on a nylon thread as a hanger, and immersed in 200 cc of 2 % HCl aqueous solution in a beaker. Thereby, gases, generated from the samples, were dissolved in the solution. At this stage, weight reduction was measured, thereby achieving evaluation of corrosion resistance.
  • the evaluation of formability is as follows.
  • ⁇ means that forming is achieved without cracks and local reduction of a thickness
  • ⁇ means that cracks are not formed but a thickness deviation locally occurs
  • ⁇ means that formability is very poor because of the formation of cracks.
  • ⁇ means a state that plating thickness and adhesion of a plated surface are excellent.
  • ⁇ means a state that adhesion is fair, pinhole is not observed, and plating thickness is ununiform.
  • ⁇ means a state in which the pinholes are observed or plating layer comes off the surface somewhere in the specimen.
  • Table 2 8 Y 0.15 Al 2.00 Ca 0.10Mn 0.10 Zn 0.30 Dia. 185Billet casting T. 245MPaY. 203MPaEl . 18% 4 F. ⁇ 5 C.R. 3.8 6 P. ⁇ 10 I.S. 9 Y 0.25 - Zr 0.80 Zn 1.55 D360 x t120D.C. casting T. 285MPaY. 253MPaEl . 16% 4 F. ⁇ 5 C.R. 3.8 7 failed Ni 11 C.S. 10 Y 0.15 Al 0.90 - Zn 0.75 30 x 250 x 400Mold casting T. 261MPaY. 205MPaEl . 18% 4 F. ⁇ 5 C.R. 5.21ayer off 11 C.S.
  • weights of the beakers, in which the samples were contained were measured every five minutes for 60 min using a precision scale having an allowable margin of error of 1/1000 g to calculate a slope of weight reduction, thereby completing the evaluation of corrosion resistance.
  • the higher slope brings about increased weight reduction, resulting in poor corrosion resistance.
  • a fine second phase intermetallic compound is dispersed so as to significantly improve the poor formability and corrosion resistance of a conventional magnesium plate.
  • the magnesium plate has excellent properties as a structural material, and consequently, it is possible to apply the magnesium plate to structural materials used in portable electronic products, automobiles, or airplanes.

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  • Metal Rolling (AREA)

Claims (2)

  1. Magnesiumknetlegierung mit ausgezeichneten Formbarkeits- und Plattierungseigenschaften, die 0,1 bis 1,0 at% eines ersten wesentlichen Elements, ausgewählt aus den Elementen Sc, Y und Lanthanoiden der 3. Gruppe im Periodensystem der Elemente und Mischungen davon, 1,0 bis 4,0 at% eines zweiten wesentlichen Elements, ausgewählt aus den Elementen Al, B der 13. Gruppe und Mischungen davon, und 0,65 at% oder weniger eines dritten Elements, ausgewählt aus den Elementen Zn, Cd der 12. Gruppe und Mischungen davon, 0,35 at% oder weniger eines Elements, ausgewählt aus der Gruppe, bestehend aus den Elementen Ca und Sr der 2. Gruppe, den Elementen Ti, Zr und Hf der 4. Gruppe, dem Element Mn der 7. Gruppe, den Elementen Si und Ge der 14. Gruppe und Mischungen davon, und einen Ausgleich von Mg und unvermeidbare Beimengungen umfasst, und folglich eine zweite Phase von feinpräzipitierten intermetallischen Verbindungen enthält.
  2. Verfahren zum Herstellen einer Magnesiumknetlegierung, das Folgendes umfasst:
    Herstellen eines Magnesiumgusslegierungsbarren, der 0,1 bis 1,5 at% eines ersten wesentlichen Elements, ausgewählt aus den Elementen Sc, Y und Lanthanoiden der 3. Gruppe des Periodensystems der Elemente und Mischungen davon, 1,0 bis 4,0 at% eines zweiten wesentlichen Elements, ausgewählt aus den Elementen Al, B der 13. Gruppe und Mischungen davon, und 0,65 at% oder weniger eines dritten Elements, ausgewählt aus den Elementen Zn, Cd der 12. Gruppe und Mischungen davon, 0,35 at% oder weniger eines Elements, ausgewählt aus der Gruppe, bestehend aus den Elementen Ca und Sr der 2. Gruppe, den Elementen Ti, Zr und Hf der 4. Gruppe, dem Element Mn der 7. Gruppe, den Elementen Si und Ge der 14.
    Gruppe, und Mischungen davon, und einen Ausgleich von Mg und unvermeidbare Beimengungen umfasst, und folglich eine zweite Phase von feinpräzipitierten intermetallischen Verbindungen enthält;
    Unterziehen des Aluminiumgusslegierungsbarrens einer Diffusionshärtung bei einer Temperatur von 250-400°C;
    Wiedererwärmen des durch Diffusion gehärteten Magnesiumgusslegierungsbarrens durch Wärmebehandlung in einem Ofen bei 250-400°C, Extrudieren des wiedererwärmten Barrens, und dann Walzen des extrudierten Barrens.
EP05856294A 2004-04-06 2005-03-11 Schmiedeprodukt aus magnesiumlegierung mit ausgezeichneter formbarkeit und verfahren zu dessen herstellung Not-in-force EP1759029B1 (de)

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KR1020040023288A KR100605741B1 (ko) 2004-04-06 2004-04-06 내식성과 도금성이 우수한 마그네슘합금 단련재
PCT/KR2005/000697 WO2006075814A1 (en) 2004-04-06 2005-03-11 Wrought magnesium alloy having excellent formability and method of producing same

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RU2006134447A (ru) 2008-05-20
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ATE486145T1 (de) 2010-11-15
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EP1759029A1 (de) 2007-03-07
KR20040035646A (ko) 2004-04-29
WO2006075814A1 (en) 2006-07-20
CN100441717C (zh) 2008-12-10
US20080304997A1 (en) 2008-12-11

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