EP2327808A1 - Materiau composite a base de magnesium dans lequel sont dispersees des particules de ti et procede de production associe - Google Patents

Materiau composite a base de magnesium dans lequel sont dispersees des particules de ti et procede de production associe Download PDF

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EP2327808A1
EP2327808A1 EP09811322A EP09811322A EP2327808A1 EP 2327808 A1 EP2327808 A1 EP 2327808A1 EP 09811322 A EP09811322 A EP 09811322A EP 09811322 A EP09811322 A EP 09811322A EP 2327808 A1 EP2327808 A1 EP 2327808A1
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magnesium
powder
composite material
dispersed
based composite
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Kantaro Kaneko
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Kurimoto Ltd
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Kurimoto Ltd
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    • 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
    • C22C1/02—Making non-ferrous alloys by melting
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
    • B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
    • B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
    • 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
    • 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
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/0408—Light metal alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C14/00—Alloys based on titanium
    • 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
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/02—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working in inert or controlled atmosphere or vacuum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/06—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of magnesium or alloys based thereon
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
    • B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
    • B22F2009/0804—Dispersion in or on liquid, other than with sieves
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • B22F2998/10—Processes characterised by the sequence of their steps

Definitions

  • the present invention relates to magnesium alloys, and more particularly to titanium (Ti) particle-dispersed magnesium-based composite materials that can be used in various fields such as household electric appliances, automotive parts, and aircraft members by increasing both strength and ductility, and manufacturing methods thereof.
  • magnesium Due to the lowest specific gravity of magnesium (Mg) among metal materials for industrial use, magnesium is expected to be used for parts and members of two-wheeled vehicles, automobiles, aircrafts, etc. for which reduction in weight is strongly desired.
  • Mg specific gravity
  • the use of magnesium alloys is limited as magnesium is not strong enough as compared to conventional industrial materials such as ferrous materials and aluminum alloys.
  • Composite materials in which particles, fibers, etc. having higher strength and hardness characteristics than those of magnesium are dispersed as a second phase have been developed in order to solve this problem.
  • An effective second phase to be dispersed is titanium (Ti).
  • the rigidity of Mg is 45 GPa, whereas the rigidity of Ti is 105 GPa.
  • the hardness of Mg is 35 to 45 Hv (Vickers hardness), whereas the hardness of Ti is 110 to 120 Hv.
  • dispersing titanium particles in a magnesium matrix can be expected to increase the strength and hardness of magnesium-based composite materials.
  • ceramic particles and ceramic fibers such as oxides, carbides, and nitrides are commonly dispersed. Such particles and fibers have high rigidity and high hardness, but have poor ductility. Thus, dispersing these particles and fibers in magnesium alloys reduces the ductility (e.g., breaking elongation) of the resultant composite materials.
  • titanium is a metal and has high ductility, adding and dispersing titanium particles does not reduce the ductility of the resultant composite materials.
  • magnesium has lower corrosion resistance.
  • titanium particles as a dispersion strengthening material in magnesium matrix.
  • Non-Patent Document 1 Collected Abstracts of the 2008 Spring Meeting of the Japan Institute of Metals (March 26, 2008), p. 355, No. 464 (Kataoka and Kitazono: Effect of Microstructure on Mechanical Characteristics of Ti Particle-Dispersed Mg-Based Composite Material ).
  • Non-Patent Document 2 Collected Abstracts of the 2008 Spring Meeting of the Japan Institute of Light Metals (May 11, 2008), p. 13, No. 7 (Kitazono, Kataoka, and Komazu: Effect of Addition of Titanium Parties on Mechanical Characteristics of Magnesium ).
  • Non-Patent Document 3 Abstracts of Spring Meeting of Japan Society of Powder and Powder Metallurgy, 2007 (June 6, 2007), p. 148, No. 2-51 A (Enami, Fujita, Ohara, and Igarashi: Development of Magnesium Composite Material by Bulk Mechanical Alloying Method ).
  • Non-Patent Document 4 Journal of Japan Society of Powder and Powder Metallurgy, Vol. 55, No. 4 (2008), p. 244 (Enami, Fujita, Hone, Ohara, Igarashi, and Kondo: Development of Magnesium Composite Material by Bulk Mechanical Alloying Method ).
  • Non-Patent Document 5 Journal of Japan Institute of Light Metals, Vol. 54, No. 11 (2004), p. 522-526 (Sato, Watanabe, Miura, and Miura: Development of Titanium Particle-Dispersed Magnesium-Based Functionally Graded Material by Centrifugal Solid-Particle Method ).
  • Non-Patent Documents 1 and 2 disclose production of a Ti particle-dispersed magnesium-based composite material by the following method. Pure titanium particles are applied to the surface of a pure magnesium plate, and another pure magnesium plate is placed thereon. In this state, the pure magnesium plates are heated and pressed to produce a composite material having the titanium particles interposed between the pure magnesium plates. A plurality of such composite materials are superposed on each other, and are heated and pressed to produce a Ti particle-dispersed magnesium-based composite material having the titanium particles arranged in the direction of the plane of the plates.
  • Non-Patent Documents 3 and 4 disclose production of a Ti particle-dispersed magnesium-based composite material by the following method. Magnesium alloy powder is mixed with pure titanium powder, and molds are filled with the mixed powder. In this state, the mixed powder is continuously subjected to a severe plastic working process, and is then subjected to a hot extrusion process to produce a Ti particle-dispersed magnesium-based composite material.
  • Non-Patent Documents 1 to 4 the heating temperature is sufficiently lower than the melting point of magnesium, and composite materials are produced in a completely solid-phase temperature range without melting.
  • the tensile test result of the composite materials shows that the strength is increased by about 5 to 10% but the ductility (breaking elongation) is reduced by about 20 to 30%, as compared to materials containing no Ti particle. Since magnesium and titanium do not form a compound, the bonding interface strength therebetween is not sufficient, and thus the strength is not increased sufficiently. On the other hand, a stress concentrates on the interface, whereby the ductility is reduced.
  • adhesion at the Mg-Ti interface needs to be increased in order to significantly increase both the strength and ductility of titanium particle-dispersed magnesium-based composite materials.
  • Non-Patent Document 5 describes a manufacturing method in which molten magnesium or a molten magnesium alloy (AZ91 D) containing titanium particles that are present as a solid phase is subjected to a centrifugal force, and a composition gradient is controlled by using the difference in traveling speed which is caused by the difference in centrifugal force due to the difference in density between the dispersed particles and the molten magnesium or the molten magnesium alloy. Since the specific gravity of titanium is at least twice that of magnesium, it is difficult to uniformly disperse titanium particles in the molten magnesium or the molten magnesium alloy by the centrifugal solid-particle method disclosed in Non-Patent Document 5.
  • this document describes that "it was found difficult to disperse titanium particles by this method.”
  • This document also describes that, in the case of adding titanium particles to a molten magnesium alloy (AZ91D) containing aluminum, and using the centrifugal solid-particle method, the aluminum concentration is very high in a portion where the titanium particles are aggregated, and regions where aluminum is solid-solved are also present in the outer periphery of the titanium particles.
  • this document describes that "there is a possibility that the initial melt having a high aluminum concentration may have penetrated the gaps between the titanium particles due to a capillary phenomenon, and may have been involved in aggregation and sintering of the titanium particles.
  • the use of the centrifugal solid-particle method in the AZ91D alloy containing aluminum is problematic in view of the composition of the melt.”
  • the present invention was developed to solve the above problems, and it is an object of the present invention to provide a Ti particle-dispersed magnesium-based composite material having high strength by uniformly dispersing titanium particles in a magnesium matrix, and increasing adhesion at the interface between titanium and magnesium.
  • a Ti particle-dispersed magnesium-based composite material according to the present invention is a material having titanium particles uniformly dispersed in a magnesium matrix.
  • the Ti particle-dispersed magnesium-based composite material is characterized in that magnesium that forms the matrix and titanium particles are bonded together with satisfactory wettability without titanium oxide at an interface between the titanium particles and the magnesium matrix, and the magnesium-based composite material has a tensile strength of 230 MPa or more.
  • a magnesium-based composite material having a tensile strength as high as 230 MPa or more can be obtained.
  • One embodiment of the present invention is directed to powder for manufacturing the Ti particle-dispersed magnesium-based composite material.
  • This powder is produced by making a cast material, which has the titanium particles uniformly dispersed in the magnesium matrix, into powder by a machining process.
  • Powder according to another embodiment of the present invention is powder for manufacturing the Ti particle-dispersed magnesium-based composite material.
  • the powder is produced by solidifying molten magnesium, which has the titanium particles uniformly dispersed therein, into powder by using an atomization process.
  • a method for manufacturing a Ti parties-dispersed magnesium-based composite material according to the present invention includes the steps of: placing titanium particles into molten magnesium; stirring the molten magnesium so that the titanium particles are uniformly dispersed therein; producing a composite material having the titanium particles uniformly dispersed in a magnesium matrix by solidifying the molten magnesium; and producing a magnesium-based composite material having a tensile strength of 230 MPa or more by subjecting the composite material to a hot plastic working process.
  • the step of producing the composite material includes solidifying the molten magnesium to produce a cast material having the titanium particles dispersed in the magnesium matrix, machining the cast material so as to make the cast material into powder, and compacting and solidifying the powder to produce a compacted body.
  • the step of producing the composite material includes solidifying the molten magnesium into powder by using an atomization process, and compacting and solidifying the powder to produce a compacted body.
  • a method for manufacturing a Ti particle-dispersed magnesium-based composite material includes the steps of: mixing magnesium powder with titanium particles; holding the mixed powder at a temperature higher than a liquid phase transition temperature of the magnesium powder; sintering and solidifying the mixed powder held at the high temperature; and producing a magnesium-based composite material having a tensile strength of 230 MPa or more by subjecting the sintered solidified body to a hot plastic formation process.
  • the inventors of the present application focused on wettability between titanium and magnesium, and evaluated characteristics of the wettability and examined manufacturing methods of composite materials by using high wettability.
  • the inventors of the present application examined wettability between pure titanium plates and pure magnesium droplets. Specifically, pure magnesium droplets (held at 800°C) melted in a high vacuum state were statically discharged from the tip of a nozzle made of magnesium oxide (MgO) onto the surface of a pure titanium plate, and the wettability between pure Mg and pure Ti at 800°C was evaluated by continuous shooting. The result is shown in Fig. 1 .
  • the wetting angle decreased with time, and decreased to 13° after 6 minutes. In general, it is determined that the wetting phenomenon has occurred if the wetting angle becomes smaller than 90°.
  • the wettability increases as the wetting angle becomes closer to 0°.
  • titanium carbide which is said to have satisfactory wettability with magnesium, has a wetting angle of about 33° at 900°C (reference: A. Contrerasa et al., Scripta Materialia, 48 (2003) 1625-1630 ), it is recognized that the wettability between pure Mg and pure Ti is highly satisfactory.
  • the interface between the solidified pure Mg and the titanium plate of a test piece was observed by using a scanning electron microscope (SEM). The result is shown in Fig. 2 . It is recognized that the molten Mg closely contacts the titanium plate in a satisfactory manner with no gap or void therebetween, in the entire region where the molten Mg contacts the titanium plate.
  • Non-Patent Documents 1 to 4 For comparison, such composite materials as reported in related art (Non-Patent Documents 1 to 4) were produced. That is, composite materials were produced by heating and pressing mixed powder of pure titanium powder and pure magnesium powder at a solid phase temperature of magnesium powder, and the bonding interface between pure magnesium and pure titanium was observed. The result is shown in Fig. 3 , In producing the composite materials, the heating temperature was 520°C, which is lower than the melting point (650°C) of pure magnesium so as to obtain a completely solid phase state. As shown by arrows, many gaps or voids were observed at the interface between the Ti particles and the Mg matrix, which shows that adhesion is not sufficient.
  • the inventors produced Ti particle-dispersed magnesium-based composite materials by the following method in order to increase adhesion between a magnesium matrix and Ti particles.
  • molten magnesium was held at a temperature higher than the melting point of magnesium or a magnesium alloy that forms a matrix, and a proper amount of Ti particles was added to the molten magnesium or magnesium alloy. After sufficiently stirring the molten magnesium or magnesium alloy so that the titanium particles were uniformly dispersed therein, the molten magnesium or magnesium alloy was solidified.
  • magnesium that forms the matrix and titanium particles are bonded together, with high adhesion due to satisfactory wettability, without titanium oxide at the interface between the titanium particles and the magnesium matrix.
  • These magnesium-based composite materials were subjected to a hot plastic working process, whereby Ti particle-dispersed magnesium-based composite materials having a tensile strength of 230 MPa or more were able to be obtained.
  • Composite materials having titanium particles uniformly dispersed in a magnesium matrix can also be manufactured by conventional methods such as a casting method and a die casting method.
  • the cast materials can be made into powder by a machining process such as a cutting process or a crushing process.
  • the titanium particles are uniformly dispersed in the magnesium matrix.
  • Fig. 4 shows an example of an image of the structure of this magnesium-based composite powder. As can be seen from Fig. 4 , there is no void at the interface between the Ti particles and the Mg matrix, and satisfactory adhesion is obtained.
  • Magnesium-based composite powder having titanium particles uniformly dispersed in a magnesium matrix can also be obtained by solidifying molten magnesium having titanium particles uniformly dispersed therein by using an atomization process.
  • the inventors obtained solidified powder by the following method. Pure magnesium is melted in a carbon crucible, and 3 mass% of pure titanium powder (average particle size: 29.8 ⁇ m) is added to the molten pure magnesium. After stirring sufficiently, the melt is discharged from the bottom of the crucible as a molten flow, and high pressure water is ejected to the molten flow (a water atomization process) to obtain solidified powder.
  • Fig. 5 shows an image of the appearance of the obtained powder, and the observation result of the inner structure of the powder. It is recognized that, in this water atomized powder as well, there is no void at the interface between the Ti particles and the Mg matrix, and satisfactory adhesion is obtained.
  • magnesium-based composite material is produced by adding titanium particles to molten magnesium, and after sufficient uniform stirring, performing a castling method or a die casting method, or in the case where molten magnesium having titanium particles uniformly dispersed therein is directly made into powder by using on atomization process, magnesium that forms the matrix and titanium particles are bonded together, without void and with satisfactory adhesion due to high wettability.
  • the Ti particle-dispersed magnesium-based composite material produced by a casting method or a die casting method may be heated to a predetermined temperature, and then the composite material may be subjected to a hot plastic working process such as a hot extrusion process, a hot rolling process, or a forging process.
  • a hot plastic working process such as a hot extrusion process, a hot rolling process, or a forging process.
  • the tensile strength of the composite material is 230 MPa or more.
  • the Ti particle-dispersed magnesium-based composite material produced from the cast material by a machining process such as a cutting process, or the Ti particle-dispersed magnesium-based composite powder obtained by ejecting high pressure water or high pressure gas to the molten magnesium flow, may be compacted and solidified to produce a compacted body or a sintered solidified body. Subsequently, the compacted body or the sintered solidified body may be subjected to a hot plastic working process such as a hot extrusion process, a hot rolling process, or a forging process, as necessary.
  • a Ti particle-dispersed magnesium-based composite material having particles of the composite powder metallurgically bonded or sintered together can be produced in this manner.
  • a Ti particle-dispersed magnesium-based composite material can also be obtained by the following manufacturing method as another embodiment.
  • magnesium powder is mixed with titanium particles, and the mixed powder is sintered and solidified while being held at a predetermined temperature. The important thing is to hold the mixed powder at a temperature higher than a liquid phase transition temperature of the magnesium powder. By holding the mixed powder at such a high temperature, magnesium that forms the matrix and the titanium particles are bonded together in the sintered solidified body with high adhesion due to satisfactory wettability, without titanium oxide at the interface between the titanium particles and the magnesium matrix.
  • This sintered solidified body is subjected to a hot plastic working process, whereby a Ti particle-dispersed magnesium-based composite material having a tensile strength of 230 MPa or more can be obtained.
  • a mass of pure magnesium having a purity of 99.8%, and titanium powder having an average particle size of 29.8 ⁇ m were prepared as starting materials.
  • the pure magnesium mass was melted by heating to 750°C in a carbon crucible, and three different amounts of the titanium particle, namely 0.5 mass%, 1.5 mass%, and 2.8 mass% in a weight percentage relative to the total weight, were added to the molten magnesium.
  • a water atomization process was performed to produce Ti particle-dispersed magnesium-based composite powder.
  • pure magnesium powder having a purity of 99.9% (average particle size: 162 ⁇ m) was prepared, and the pure magnesium powder and the above Ti powder was weighed so that the ratio of the Ti powder was 0.5 mass%, 1.5 mass%, and 2.8 mass%. Then, the pure magnesium powder was mixed with the Ti powder by using a dry ball mill, thereby producing Mg-Ti mixed powder.
  • the two kinds of powder thus produced were placed in carbon molds, and were pressed at 550°C for 30 minutes (pressure: 30 MPa) in a vacuum atmosphere by using a discharge plasma sintering apparatus to sinter and solidify the particles of the powder together, thereby producing extrusion billets having a diameter of 45 mm.
  • These Ti particle-dispersed magnesium powder billets were held at 200°C for 5 minutes in an argon gas atmosphere, and then immediately subjected to a hot extrusion process (extrusion ratio: 37) to produce round-bar shaped extruded materials having a diameter of 7 mm.
  • round-bar shaped extruded materials were also produced from pure magnesium powder containing no Ti particle, based on the above manufacturing procedures.
  • Fig. 6 shows a stress-distortion curve of the extruded materials using the pure Mg powder containing no Ti particle, and the extruded materials using the Mg powder containing 2.8 mass% of Ti particles. which were produced by the two manufacturing methods.
  • the tensile strength and the yield strength of the Ti particle-dispersed magnesium-based composite powder extruded materials using the water atomization process of the present invention increased by about 35 to 40%, and the breaking elongation thereof was as high as 15% or more, which is about the same as the pure magnesium powder extruded materials containing no Ti particle.
  • Fig. 7 shows a change in tensile strength (TS) and yield strength (YS) of each extruded material with respect to the amount of Ti added.
  • TS tensile strength
  • Yield strength yield strength
  • Example 1 a mass of pure magnesium having a purity of 99.8%, and titanium powder having an average particle size of 29.8 ⁇ m were prepared as starting materials.
  • the magnesium mass was melted by heating to 750°C in a carbon crucible, and three different amounts of the titanium particles, namely 1 mass%, 3 mass%, and 5 mass% in a weight percentage relative to the total weight, were added to the molten magnesium.
  • the molten magnesium was cast into cylindrical molds to produce billets having a diameter of 60 mm.
  • the cast billets were machined to produce extrusion billets having a diameter of 45 mm. These billets were held at 200°C for 5 minutes in an argon gas atmosphere, and then immediately subjected to a hot extrusion process (extrusion ratio: 37) to produce round-bar shaped extruded materials having a diameter of 7 mm,
  • Fig. 8 shows the observation result of the extruded materials by using an optical microscope.
  • the proportion of Ti particles in the extruded material increases as the amount of Ti particles added increases. Even when 5 mass% of Ti particles was added, no aggregation/segregation phenomenon of the Ti particles is observed, and the Ti particles are uniformly dispersed in the magnesium matrix.
  • Example 1 in the extruded materials obtained by extruding the Ti particle-dispersed magnesium-based composite material produced by a casting method according to the present invention, the tensile strength and the yield strength increase and the breaking elongation does not significantly decrease as the content of Ti particles increases.
  • the above result shows that in the Ti parties-dispersed magnesium-based composite material of the present invention, the strength of the magnesium matrix can be increased by adding the Ti particles without causing aggregation and segregation of the Ti particles.
  • Example 1 a mass of pure magnesium having a purity of 99.8%, and titanium powder having an average particle size of 29.8 ⁇ m were prepared as starting materials.
  • the magnesium mass was melted by heating to 750°C in a carbon crucible, and different amounts of the titanium particles, namely 2 mass% and 4 mass% in a weight percentage relative to the total weight, were added to the molten magnesium.
  • the molten magnesium was cast into cylindrical molds to produce billets having a diameter of 60 mm. Chips having a total length of about 1 to 4 mm were produced from the cast billets by a cutting process.
  • the observation result of the chips shows that the Ti particles are uniformly dispersed in the Mg matrix without aggregation and segregation.
  • SKD11 molds were filled with the chips, and were pressed with a pressure of 600 MPa by a hydraulic press to produce billets of a powder molded body having a diameter of 45 mm.
  • the billets were held at 300°C for 5 minutes in an argon gas atmosphere, and then immediately subjected to a hot extrusion process (extrusion ratio: 37) to produce round-bar shaped extruded materials having a diameter of 7 mm.
  • the above result shows that in the Ti particle-dispersed magnesium-based composite material obtained by the manufacturing method of the present invention, the strength of the magnesium matrix can be increased by adding the Ti particles without causing aggregation and segregation of the Ti particles.
  • Example 1 a mass of pure magnesium having a purity of 99.8%, and titanium alloy powder having an average particle size of 22.8 ⁇ m (Ti-6.1Al%-3.8V/mass%) were prepared as starting materials.
  • the magnesium mass was melted by heating to 750°C in a carbon crucible, and three different amounts of the Ti alloy particles, namely 1 mass%, 3 mass%, and 5 mass% in a weight percentage relative to the total weight, were added to the molten magnesium. After sufficiently uniformly stirring the resultant molten magnesium to prevent segregation of the Ti alloy particles and sedimentation thereof at the bottom, the molten magnesium was cast into cylindrical molds to produce billets having a diameter of 60 mm.
  • the cast billets were machined to produce extrusion billets having a diameter of 45 mm. These billets were held at 200°C for 5 minutes in an argon gas atmosphere, and then immediately subjected to a hot extrusion process (extrusion ratio: 37) to produce round-bar shaped extruded materials having a diameter of 7 mm. Tensile test pieces were obtained from these magnesium powder extruded materials, and a tensile strength test was performed at normal temperature.
  • the Ti alloy particles are uniformly dispersed in the matrix in the Ti particle-dispersed magnesium-based composite material of the present invention, without causing aggregation and segregation of the Ti particles.
  • the tensile strength increases as the amount of Ti alloy particles added increases.
  • the amount of increase in tensile strength is increased as compared to the case where the pure Ti particles are added. That is, the strength of the magnesium composite material is further increased as the hardness and strength of the particles that are dispersed are further increased.
  • the present invention can be advantageously used as a Ti particle-dispersed magnesium-based composite material having high strength, and a manufacturing method thereof.
EP09811322A 2008-09-03 2009-03-16 Materiau composite a base de magnesium dans lequel sont dispersees des particules de ti et procede de production associe Pending EP2327808A1 (fr)

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JP2008226260A JP4397425B1 (ja) 2008-09-03 2008-09-03 Ｔｉ粒子分散マグネシウム基複合材料の製造方法
PCT/JP2009/055026 WO2010026793A1 (fr) 2008-09-03 2009-03-16 Materiau composite a base de magnesium dans lequel sont dispersees des particules de ti et procede de production associe

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US (1) US20110150694A1 (fr)
EP (1) EP2327808A1 (fr)
JP (1) JP4397425B1 (fr)
KR (1) KR20100092055A (fr)
CN (1) CN102016094A (fr)
WO (1) WO2010026793A1 (fr)

Families Citing this family (5)

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CN111266592B (zh) * 2020-03-25 2022-04-22 燕山大学 一种双连通结构钛镁复合材料及其制备方法和应用
CN113174519B (zh) * 2021-03-23 2022-04-29 山东科技大学 一种超细钒颗粒强化细晶镁基复合材料及其制备方法
CN114959391B (zh) * 2022-05-30 2023-01-06 广东省科学院新材料研究所 一种钛颗粒增强镁基复合材料及其制备方法
CN115074560B (zh) * 2022-06-30 2023-03-14 广东省科学院新材料研究所 一种钛颗粒增强镁基复合材料及其制备方法
CN116103521B (zh) * 2023-02-15 2024-02-02 重庆大学 一种金属钛颗粒增强镁基复合材料的制备方法

Family Cites Families (7)

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Publication number Priority date Publication date Assignee Title
US4751048A (en) * 1984-10-19 1988-06-14 Martin Marietta Corporation Process for forming metal-second phase composites and product thereof
JPH0617524B2 (ja) * 1988-11-08 1994-03-09 勝廣 西山 マグネシウム―チタン系焼結合金およびその製造方法
JPH05214477A (ja) * 1992-01-31 1993-08-24 Suzuki Motor Corp 複合材料とその製造方法
JP3084512B2 (ja) * 1996-09-24 2000-09-04 広島県 金属間化合物強化マグネシウム基複合材料及びその製造方法
JP2002105575A (ja) * 2000-09-28 2002-04-10 Hokkaido Technology Licence Office Co Ltd 塑性加工用マグネシウム基合金複合材料および塑性加工用薄板材料の製造方法
JP2008163361A (ja) * 2006-12-27 2008-07-17 Mitsubishi Alum Co Ltd 均一微細な結晶粒を有するマグネシウム合金薄板の製造方法
JP2008195978A (ja) * 2007-02-09 2008-08-28 Topy Ind Ltd マグネシウム基複合材料

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See references of WO2010026793A1 *

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US20110150694A1 (en) 2011-06-23
KR20100092055A (ko) 2010-08-19

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