EP3719151B1 - Verfahren zur herstellung von verbundwerkstoff auf aluminiumlegierungsbasis und verbundwerkstoff auf aluminiumlegierungsbasis - Google Patents

Verfahren zur herstellung von verbundwerkstoff auf aluminiumlegierungsbasis und verbundwerkstoff auf aluminiumlegierungsbasis Download PDF

Info

Publication number
EP3719151B1
EP3719151B1 EP18884716.4A EP18884716A EP3719151B1 EP 3719151 B1 EP3719151 B1 EP 3719151B1 EP 18884716 A EP18884716 A EP 18884716A EP 3719151 B1 EP3719151 B1 EP 3719151B1
Authority
EP
European Patent Office
Prior art keywords
aluminum alloy
composite material
powder
based composite
aluminum
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Active
Application number
EP18884716.4A
Other languages
English (en)
French (fr)
Other versions
EP3719151A1 (de
EP3719151C0 (de
EP3719151A4 (de
Inventor
Hiroshi MITO
Kenji Watanabe
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Advanced Composite Corp
Original Assignee
Advanced Composite Corp
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Advanced Composite Corp filed Critical Advanced Composite Corp
Publication of EP3719151A1 publication Critical patent/EP3719151A1/de
Publication of EP3719151A4 publication Critical patent/EP3719151A4/de
Application granted granted Critical
Publication of EP3719151B1 publication Critical patent/EP3719151B1/de
Publication of EP3719151C0 publication Critical patent/EP3719151C0/de
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

Classifications

    • 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
    • C22C1/10—Alloys containing non-metals
    • C22C1/1036—Alloys containing non-metals starting from a melt
    • C22C1/1073—Infiltration or casting under mechanical pressure, e.g. squeeze casting
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D18/00—Pressure casting; Vacuum casting
    • B22D18/02—Pressure casting making use of mechanical pressure devices, e.g. cast-forging
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D19/00—Casting in, on, or around objects which form part of the product
    • B22D19/0081—Casting in, on, or around objects which form part of the product pretreatment of the insert, e.g. for enhancing the bonding between insert and surrounding cast metal
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D19/00—Casting in, on, or around objects which form part of the product
    • B22D19/02—Casting in, on, or around objects which form part of the product for making reinforced articles
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D19/00—Casting in, on, or around objects which form part of the product
    • B22D19/14—Casting in, on, or around objects which form part of the product the objects being filamentary or particulate in form

Definitions

  • the present invention relates to a method for producing an aluminum alloy-based composite material containing a reinforcement material distributed uniformly therein, and an aluminum alloy-based composite material.
  • Patent Literature 1 describes a method for producing an aluminum alloy-based composite material, wherein a powder of aluminum borate is used as a ceramic powder being a reinforcement material, and a filled body of this powder is impregnated with a melt of an aluminum alloy. It is to be noted that such a production method is called a melt casting method or a high-pressure casting method.
  • Patent Literature 1 includes: a step of filling an aluminum borate powder raw material, thereby obtaining a filled body; a step of preheating the filled body; a step of heating an aluminum alloy, thereby obtaining a molten aluminum alloy; and a step of pressurizing and penetrating the molten aluminum alloy into the filled body having been preheated.
  • a filled body is obtained by filling a ceramic powder, such as an aluminum borate powder raw material, into a container made of iron or SUS.
  • Patent Literature 1 Japanese Patent Laid-Open No. 2008-38172 JP H11 170027 A , US 3 877 884 A and JP S60 115361 A disclose methods for preparing a metal-ceramic composite.
  • a ceramic powder 102 is filled in a metal container 103 made of iron or SUS to make a filled body, and a melt Al1 of an aluminum alloy is allowed to flow in the metal container 103 from an upper opening of this metal container 103 to impregnate the filled body of the ceramic powder 102 with the aluminum alloy, as shown in Figure 14(a) and Figure 14(b) , and therefore there has been a problem that the impregnation ratio of the aluminum alloy is different between the vicinity of the opening portion in which the melt Al1 of the aluminum alloy flows in and the bottom portion far from the opening portion, so that the whole filled body of the ceramic powder 102 is not impregnated uniformly. Therefore, it has been difficult to obtain a uniform composite material particularly having a complicated shape or a sheet-like shape.
  • the present invention has been completed in view of the previously described problem, and an object of the present invention is to provide a technique of producing an aluminum alloy-based composite material, the technique enabling uniform impregnation with an aluminum alloy.
  • a method for producing an aluminum alloy-based composite material according to the invention is a method for producing an aluminum alloy-based composite material containing a ceramic powder being a reinforcement material composited in an aluminum alloy, the method characterized by including: a filling step of filling the ceramic powder into a porous container formed of a porous material, and tightly closing the porous container with a lid part; a step of placing the porous container in a mold, and pouring a melt of the aluminum alloy into the mold; and an impregnation step of applying pressure to the melt in the mold, thereby impregnating the ceramic powder inside the porous container with the melt through the porous container.
  • This method for producing an aluminum alloy-based composite material includes the impregnation step of impregnating the ceramic powder inside the porous container with the melt through the porous container, and therefore the melt of the aluminum alloy flows evenly in the porous container from almost all the directions through the porous material of the porous container, thereby enabling uniform impregnation of the whole ceramic powder.
  • the method for producing an aluminum alloy-based composite material according to an embodiment is characterized in that the porous container is formed of carbon graphite.
  • the porous container is formed of carbon graphite, and therefore the coefficient of thermal expansion is smaller than that of a container made of iron or SUS, so that deformation of the container due to thermal expansion hardly occurs, which enables using a container having a complicated shape.
  • the porous container is carbon graphite, and therefore the composite material and the porous container can easily be separated when the hardened composite material is taken out of the porous container after the impregnation step.
  • the method for producing an aluminum alloy-based composite material according to a further embodiment is characterized by further including a preheating step of preheating the porous container after the filling step.
  • this method for producing an aluminum alloy-based composite material further includes the preheating step of preheating the porous container after the filling step, and therefore the interfacial energy of the particles of the filled ceramic powder is enhanced, so that the wettability with the melt of the aluminum alloy is ameliorated.
  • the porous container is formed of carbon graphite, the coefficient of thermal expansion of the porous container is low, so that deformation of the container due to the preheating hardly occurs.
  • the method for producing an aluminum alloy-based composite material according to a further embodiment is characterized in that the ceramic powder is a powder of aluminum borate.
  • the ceramic powder is the powder of aluminum borate, and therefore a composite material excellent in processability can be obtained by using the powder of aluminum borate having a relatively low hardness.
  • the method for producing an aluminum alloy-based composite material according to a further embodiment is characterized in that a powder of SiC is further added as the ceramic powder.
  • the powder of SiC is further added as the ceramic powder, and therefore the coefficient of thermal expansion as a whole can be reduced and the hardness can be enhanced according to the proportion of the powder of SiC to be added, which has a lower coefficient of thermal expansion and a higher hardness than aluminum borate.
  • the wettability with the powder of aluminum borate is satisfactory, and the interface with the aluminum borate powder is modified, so that a stronger joint can be obtained.
  • the method for producing an aluminum alloy-based composite material according to a further embodiment is characterized in that the powder of SiC is mixed with the powder of aluminum borate in a volume ratio of the powder of SiC to the powder of aluminum borate of 0.5 to 2.0:20 in the filling step.
  • the powder of SiC is mixed with the powder of aluminum borate in a volume ratio of the powder of SiC to the powder of aluminum borate of 0.5 to 2.0:20 in the filling step, and therefore a composite material which has achieved both reduction of the coefficient of thermal expansion as a whole and satisfactory processability can be obtained.
  • An aluminum alloy-based composite material is characterized by an aluminum alloy-based composite material containing a ceramic powder being a reinforcement material composited in an aluminum alloy, the aluminum alloy-based composite material containing the ceramic powder being the reinforcement material uniformly dispersed and distributed in an aluminum alloy matrix, wherein the aluminum alloy-based composite material is obtained by the method for producing an aluminum alloy-based composite material.
  • the method for producing an aluminum alloy-based composite material according to the present invention includes the impregnation step of impregnating the ceramic powder inside the porous container with the melt through the porous container, and therefore the melt of the aluminum alloy flows evenly in the porous container from almost all the directions through the porous material of the porous container, thereby enabling uniform impregnation of the whole ceramic powder.
  • an aluminum alloy-based composite material having uniform coefficient of thermal expansion and hardness as a whole can be obtained, and a uniform aluminum alloy-based composite material having a complicated shape or a sheet-like shape can be obtained.
  • the aluminum alloy-based composite material prepared by this production method of the present invention is light in weight and has a high Young's modulus, a high vibration damping factor, a high thermal conductivity, and a high wear resistance, and therefore is suitable as a material for an X-Y table of a bonding machine or the like, and a robot arm, a chip mounter, air-compressing scroll parts, and the like, which are used in a semiconductor production apparatus.
  • the method for producing an aluminum alloy-based composite material of the present embodiment is, as shown in Figure 1 to Figure 3(a) , Figure 3(b), and Figure 3(c) , a method for producing an aluminum alloy-based composite material 1 containing a ceramic powder 2 being a reinforcement material composited in an aluminum alloy, and includes: a filling step of filling the ceramic powder 2 into a porous container 3 formed of a porous material; a step of placing the porous container 3 in a mold 4, and pouring a melt Al1 of the aluminum alloy into the mold 4; and an impregnation step of applying pressure to the melt Al1 in the mold 4, thereby impregnating the ceramic powder 2 inside the porous container 3 with the melt Al1 through the porous container 3.
  • the production method of the present embodiment includes a preheating step of preheating the porous container 3 after the filling step.
  • the porous container 3 is formed of a porous (open porous) material which does not melt even when the melt Al1 of the aluminum alloy is put thereinto and which has an infinite number of through holes. Particularly, it is preferable to form the porous container 3 with carbon graphite.
  • a powder of aluminum borate for example 9Al 2 O 3 ⁇ 2B 2 O 3 .
  • a powder of SiC (silicon carbide) is further added as the ceramic powder 2.
  • the powder of SiC with the powder of aluminum borate in a volume ratio of the powder of SiC to the powder of aluminum borate of 0.5 to 2.0:20 in the filling step.
  • the porous container 3 of carbon graphite is used, and a mixed powder of aluminum borate and SiC is used as the ceramic powder 2 in the production method of the present embodiment will be described in more detail.
  • the predetermined ceramic powder 2 is prepared and is filled into the porous container 3 of carbon graphite, as shown in Figure 1 .
  • the mixed powder of aluminum borate and SiC is used as the ceramic powder 2
  • both the powders are mixed in a predetermined ratio and are stirred and mixed sufficiently and uniformly with a rotating mixer or the like in advance.
  • the alloy numbers such as, for example, A1050, A5052, A6061, A7075, AC4C, AC8A, and ADC12 can be adopted, and other types can also be adopted.
  • AC4C, AC8A, and the like which have a high thermal conductivity and a high strength, are preferable as an aluminum alloy.
  • Examples of the chemical composition of such an alloy include an aluminum alloy containing Si: 6 to 13%, Mg: 0.2 to 1.3%, and Al: the balance each on a volume percentage basis.
  • Si it is preferable to set Si to be contained in such a way as to be in a range of a volume percentage of 6 to 12% because when the above-described content of Si is small, impregnation trouble easily occurs at the time of high-pressure impregnation. That is, the reason is that when Si has a volume percentage of less than 6%, the flow of the melt is poor, which makes it difficult for the melt of the aluminum alloy to penetrate among the ceramic powders 2 being a reinforcement material.
  • the powder of aluminum borate which is utilized as the ceramic powder 2 a powder of aluminum borate having a center particle diameter of about 30 to about 50 ⁇ m, for example, is adopted, and as the powder of SiC, a powder of SiC having a center particle diameter of 2 to 4 ⁇ m, for example, is adopted.
  • the porous container porous containers using open porous carbon graphite blocks and having a various shapes can be adopted.
  • the porous container may be a container 3 having a rectangular parallelepiped shape, the container 3 composed of a main body 3a having a box shape, and a lid part 3b, or, as shown in Figure 2(b) , a container 23 composed of a main body 23a having a bottomed cylindrical shape, and a lid part 23b may be adopted.
  • the pore diameter of the porous container 3 is desirably 10 ⁇ m or less. It is to be noted that the pore flow channels of the porous container 3 are complicated, and therefore the SiC powder having a particle diameter which is smaller than the pore diameter never flows outside along the pore flow channels.
  • the ceramic powder 2 When the ceramic powder 2 is filled into the porous container 3, the ceramic powder 2 can be filled in a state where gaps are unlikely to occur by packing the ceramic powder 2 while applying vibration to the porous container 3 with a vibrator or the like.
  • the ceramic powder 2 is put into a preheating furnace (such as muffle furnace) together with the porous container 3 in a state where the porous container 3 is tightly closed with the lid part 3b to perform preheating at 500 to 700°C, for example.
  • This preheating step is a step for enhancing the interfacial energy of the ceramic powder 2 and ameliorating the wettability with the melt of the aluminum alloy.
  • a conventional container made of iron or SUS has an average thermal expansion coefficient of 14 to 17 ppm/k, and therefore there has been a problem that deformation of the container due to expansion occurs at the time of preheating. Particularly, the more complicated the container shape is, the more difficult the design taking thermal expansion into consideration is.
  • the porous container 3 of the present embodiment using carbon graphite blocks, has an average thermal expansion coefficient of about 5 to about 7 ppm/k, and therefore has an advantageous point that the deformation of the container due to thermal expansion at the time of the preheating hardly occurs.
  • the preheated porous container 3 packed with the ceramic powder 2 is placed in the mold 4 preheated to 200 to 250°C in advance, and the melt Al1 of the aluminum alloy is poured into the mold 4.
  • a plurality of protruded portions may be provided at the bottom portion of the mold 4 to mount the porous container 3 on a plurality of the protruded portions in such a way that the melt Al1 flows to the lower bottom portion of the porous container 3.
  • the porous container 3 can be placed in a state of raising the porous container 3 from the bottom portion of the mold 4, which enables the melt Al1 to flow to the lower bottom portion of the porous container 3. Thereby, penetration of the melt Al1 inside from all the directions in the porous container 3 is enabled.
  • melt Al1 of the aluminum alloy is pressurized at 80 to 140 MPa with a punch 5a of a press machine 5, as shown in Figure 3(b) .
  • the porous container 3 is impregnated with the melt Al1 of the aluminum alloy, and further, the ceramic powder 2 in the porous container 3 is impregnated with the melt Al1 of the aluminum alloy.
  • the impregnation speed with (flow rate of) the melt Al1 of the aluminum alloy is fast, turbulence occurs to move the ceramic powder 2, so that the distribution of the ceramic powder 2 is deviated, and insertion of aluminum, called metal vein, occurs, and therefore the impregnation speed is set to a low speed so that the turbulence will not occur. Accordingly, the pressurization force and the pressurization speed by the press machine 5 are adjusted according to the volume percentage and shape of the ceramic powder 2 in the porous container 3.
  • the taken-out integrally molded product 7 is cut, for example, the integrally molded product 7 is cut along a cutting line C, with a band saw or the like, to remove the excess Al2, as shown in Figure 4(a) , thereby exposing the porous container (3), as shown in Figure 4(b) .
  • the lid part 3b of the porous container 3 is detached, as shown in Figure 4(c) , and further, the wall parts and bottom part of the porous container 3 are detached by cutting, as shown in Figure 4(d) , thereby taking out the composite material 1.
  • the porous container 3 is carbon graphite, and therefore the composite material 1 can easily be taken out.
  • the taken-out composite material 1 is processed into an intended shape by a milling cutter, grinding, NC processing, or the like.
  • the aluminum alloy-based composite material 1 prepared in the exemplified present embodiment contains an aluminum alloy as a parent material and, as reinforcement materials, 30 to 40% of aluminum borate and 1.5 to 2% of SiC each on a volume percentage basis, and is a composite material containing the ceramic powder 2, which is composed of a powder of aluminum borate and a powder of SiC, dispersed uniformly in an aluminum alloy matrix.
  • the method for producing an aluminum alloy-based composite material 1 of the present embodiment includes the impregnation step of impregnating the ceramic powder 2 inside the porous container 3 with the melt Al1 through the porous container 3, and therefore the melt Al1 of the aluminum alloy flows evenly in the porous container 3 from almost all the directions through the porous material of the porous container 3, thereby enabling uniform impregnation of the whole ceramic powder 2.
  • the porous container 3 is formed of carbon graphite, and therefore the coefficient of thermal expansion is smaller than that of a container made of iron or SUS, so that deformation of the container due to thermal expansion hardly occurs, which enables using a container having a complicated shape.
  • the porous container 3 is carbon graphite, and therefore the composite material 1 and the porous container 3 can easily be separated when the hardened composite material 1 is taken out of the porous container 3 after the impregnation step.
  • this method for producing an aluminum alloy-based composite material includes a preheating step of preheating the porous container 3 after the filling step, the interfacial energy of the particles of the filled ceramic powder 2 is enhanced, so that the wettability with the melt Al1 of the aluminum alloy is ameliorated.
  • the porous container 3 is formed of carbon graphite, the coefficient of thermal expansion of the porous container 3 is low, and deformation of the container due to the preheating hardly occurs.
  • the ceramic powder 2 is the powder of aluminum borate
  • a composite material excellent in processability can be obtained by using the powder of aluminum borate having a relatively low hardness.
  • the coefficient of thermal expansion as a whole can be reduced, and the hardness can be enhanced according to the proportion of the powder of SiC to be added, which has a lower coefficient of thermal expansion and a higher hardness than aluminum borate to be used together.
  • the wettability with the powder of aluminum borate is satisfactory, and the interface with the aluminum borate powder is modified, so that a stronger joint can be obtained.
  • Figure 7 to Figure 10 show SEM images of aluminum alloy-based composite materials actually prepared based on the above-described production method of the embodiment.
  • Figure 7 and Figure 8 each show a SEM image of an aluminum alloy-based composite material using only aluminum borate as a ceramic powder.
  • Figure 9 and Figure 10 each show a SEM image of an aluminum alloy-based composite material using a mixed powder of aluminum borate and SiC as a ceramic powder. It is to be noted that an aluminum alloy of alloy number AC4C was used in both cases.
  • Figure 5 and Figure 6 each show a SEM image of an aluminum alloy-based composite material prepared based on a conventional production method shown in Figure 14(a) and Figure 14(b) .
  • This conventional example is an aluminum alloy-based composite material using only aluminum borate as a ceramic powder.
  • the powder of aluminum borate and aluminum around the powder can be distinguished by distinct light and shade, and the boundaries of structures are clear in the material obtained in the conventional example, but in both of the materials of the Examples, prepared according to the production method of the present embodiment, the light and shade between the powder of aluminum borate and aluminum around the powder are not distinct and the boundaries of structures are not clear, as compared to the conventional example. It is found that the tendency is more remarkable particularly in the material of the Example of the present invention, in which the powder of SiC was mixed.
  • the ceramic powder is dispersed and distributed uniformly in the aluminum alloy matrix.
  • the vibration damping property was measured with an FFT analyzer in such a way that vibration was applied with an impulse hammer to a test piece (10 ⁇ 10 ⁇ 100 mm) of the composite material, hung with a string, and resultant vibration was detected with an accelerometer.
  • a damping ratio was calculated from a multiplier coefficient and a frequency based on plotting of peaks of a damped wave of each composite material, thereby performing evaluation.
  • Figure 13 shows the vibration damping property of the aluminum alloy-based composite material prepared in the Example of the present invention.
  • Figure 11 shows the vibration damping property of aluminum
  • Figure 12 shows the vibration damping property of the aluminum alloy-based composite material prepared by the method of the conventional example shown in Figure 14(a) and Figure 14(b) .
  • the processability was evaluated by observing, with a metallurgical microscope, a rake face and a front flank of a tool used when three-dimensional cutting of each composite material was performed with a NC lathe under a predetermined condition, and measuring width of flank face friction.
  • the aluminum alloy-based composite material of the Example of the present invention has significantly higher properties as compared to the cast iron, that is, has a Young's modulus about two times that of the cast iron, has a density about 40% higher than the cast iron, and has a thermal conductivity about 2.5 times that of the cast iron.
  • the aluminum alloy-based composite material of the Example of the present invention has a satisfactory processability about the same level as the processability of 2000 series aluminum, as compared to the alumina ceramic.
  • the aluminum alloy (T6 treatment) of the alloy number A6061 had a tensile strength at 300°C of about 30 MPa, but the aluminum alloy-based composite material of the Example of the present invention had a high tensile strength, as high as 90 MPa.
  • the aluminum alloy-based composite material (aluminum alloy-based aluminum borate-reinforced composite material) obtained using only aluminum borate having a low coefficient of thermal expansion, as low as 8 to 10 w/m ⁇ k, as a ceramic powder according to the conventional production method had a low thermal conductivity and a poor heat dissipation.
  • the processability of the aluminum alloy-based composite material of the Example of the present invention was satisfactory because the processing property was hardly changed even though SiC was added.
  • the vibration damping property of the aluminum alloy-based composite material obtained by the production method of the present embodiment are improved as compared to that of the aluminum alloy-based aluminum borate-reinforced composite material obtained by the conventional production method.
  • the conventional aluminum alloy-based silicon carbide-reinforced composite material has an excellent vibration damping property but has a poor processability, but the aluminum alloy-based composite material of the Example of the present invention not only has an excellent vibration damping property but also has a satisfactory processability.
  • the aluminum alloy-based composite material prepared by the production method of the present invention is suitable as a material which is used for an X-Y table of a bonding machine or the like, a robot arm and the like being used in a semiconductor production apparatus, or the like, in which not only light weight and a high Young's modulus are required, but also high vibration damping property and processability are required.
  • a powder of aluminum borate, or a mixed powder of aluminum borate and silicon carbide are used as a ceramic powder.

Landscapes

  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Chemical & Material Sciences (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacture Of Alloys Or Alloy Compounds (AREA)

Claims (7)

  1. Verfahren zur Herstellung eines Verbundmaterials auf Basis einer Aluminiumlegierung, das ein keramisches Pulver umfasst, das ein Verstärkungsmaterial ist, das in eine Aluminiumlegierung eingearbeitet ist, wobei das Verfahren umfasst:
    einen Füllschritt des Einfüllens des Keramikpulvers in einen porösen Behälter, der aus einem porösen Material gebildet ist, und dichtes Verschließen des porösen Behälters mit einem Deckelteil;
    einen Schritt des Einbringens des porösen Behälters in einer Form und des Gießens einer Schmelze der Aluminiumlegierung in die Form; und
    einen Imprägnierschritt des Ausübens von Druck auf die Schmelze in der Form, wodurch das Keramikpulver im Inneren des porösen Behälters mit der Schmelze durch den porösen Behälter hindurch imprägniert wird,
    wobei das Keramikpulver ein Pulver aus Aluminiumborat oder ein gemischtes Pulver aus Aluminiumborat und Siliziumkarbid ist.
  2. Verfahren zur Herstellung eines Verbundwerkstoffs auf Basis einer Aluminiumlegierung nach Anspruch 1, wobei der poröse Behälter aus Kohlenstoffgraphit gebildet ist.
  3. Verfahren zur Herstellung eines Verbundmaterials auf Basis einer Aluminiumlegierung nach Anspruch 1 oder 2, das ferner einen Vorwärmschritt zum Vorwärmen des porösen Behälters nach dem Füllschritt umfasst.
  4. Verfahren zur Herstellung eines Verbundwerkstoffs auf Basis einer Aluminiumlegierung nach einem der Ansprüche 1 bis 3, wobei das keramische Pulver ein Pulver aus Aluminiumborat ist.
  5. Verfahren zur Herstellung eines Verbundwerkstoffs auf Basis einer Aluminiumlegierung nach Anspruch 4, bei dem als Keramikpulver zusätzlich ein SiC-Pulver zugegeben wird.
  6. Verfahren zur Herstellung eines Verbundwerkstoffs auf Basis einer Aluminiumlegierung nach Anspruch 5, wobei das SiC-Pulver mit dem Aluminiumborat-Pulver in einem Volumenverhältnis des SiC-Pulvers zu dem Aluminiumborat-Pulver von 0,5 bis 2,0:20 im Füllschritt gemischt wird.
  7. Verbundwerkstoff auf Basis einer Aluminiumlegierung, umfassend ein keramisches Pulver, das ein mit einer Aluminiumlegierung verbundenes Verstärkungsmaterial ist, wobei der Verbundwerkstoff auf Basis einer Aluminiumlegierung das keramische Pulver umfasst, das das Verstärkungsmaterial ist, das gleichmäßig in einer Aluminiumlegierungsmatrix dispergiert und verteilt ist, wobei
    Verbundwerkstoff auf Basis einer Aluminiumlegierung durch das Verfahren zur Herstellung eines Verbundmaterials auf Basis einer Aluminiumlegierung nach einem der Ansprüche 1 bis 6 erhalten wird,
    wobei das Keramikpulver ein Pulver aus Aluminiumborat oder ein gemischtes Pulver aus Aluminiumborat und Siliziumkarbid ist, und
    wobei die Schwingungsdämpfungseigenschaft des Verbundwerkstoffs auf Basis einer Aluminiumlegierung, gemessen mit einem FFT-Analysator, höher ist und eine gedämpfte Wellenform weniger Rauschen aufweist, verglichen mit einer Schwingungsdämpfungseigenschaft von Aluminium.
EP18884716.4A 2017-11-30 2018-11-30 Verfahren zur herstellung von verbundwerkstoff auf aluminiumlegierungsbasis und verbundwerkstoff auf aluminiumlegierungsbasis Active EP3719151B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2017229851A JP6681079B2 (ja) 2017-11-30 2017-11-30 アルミニウム合金基複合材料の製造方法及びアルミニウム合金基複合材料
PCT/JP2018/044170 WO2019107541A1 (ja) 2017-11-30 2018-11-30 アルミニウム合金基複合材料の製造方法及びアルミニウム合金基複合材料

Publications (4)

Publication Number Publication Date
EP3719151A1 EP3719151A1 (de) 2020-10-07
EP3719151A4 EP3719151A4 (de) 2021-08-25
EP3719151B1 true EP3719151B1 (de) 2023-06-07
EP3719151C0 EP3719151C0 (de) 2023-06-07

Family

ID=66664908

Family Applications (1)

Application Number Title Priority Date Filing Date
EP18884716.4A Active EP3719151B1 (de) 2017-11-30 2018-11-30 Verfahren zur herstellung von verbundwerkstoff auf aluminiumlegierungsbasis und verbundwerkstoff auf aluminiumlegierungsbasis

Country Status (4)

Country Link
EP (1) EP3719151B1 (de)
JP (1) JP6681079B2 (de)
CN (1) CN111479940B (de)
WO (1) WO2019107541A1 (de)

Families Citing this family (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP6966728B1 (ja) * 2020-10-01 2021-11-17 アドバンスコンポジット株式会社 炭素基金属複合材およびその製造方法
CN112548077B (zh) * 2020-11-03 2022-08-12 南京理工大学 一种铝合金-陶瓷复合结构整体液态成型方法
JP7050978B1 (ja) 2021-02-26 2022-04-08 デンカ株式会社 成形体及びその製造方法
JP7197946B1 (ja) * 2022-01-14 2022-12-28 アドバンスコンポジット株式会社 金属基複合材料の製造方法
KR102735722B1 (ko) * 2022-12-29 2024-11-27 국립한국해양대학교산학협력단 알루미늄 합금 스크랩을 이용한 발포 알루미늄 제조 방법

Family Cites Families (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS509802B2 (de) * 1971-10-29 1975-04-16
JPS60115361A (ja) * 1983-11-25 1985-06-21 Toyota Motor Corp 複合材料の製造方法
JPH09192819A (ja) * 1996-01-09 1997-07-29 Mitsubishi Steel Mfg Co Ltd 耐摩耗性複合材鋳造品の製造方法
JPH11170027A (ja) * 1997-12-10 1999-06-29 Taiheiyo Cement Corp 金属−セラミックス複合材料用インゴット及びその製造方法
JP4113971B2 (ja) * 2002-07-30 2008-07-09 株式会社豊田自動織機 低膨張材料及びその製造方法
JP4781934B2 (ja) 2006-08-03 2011-09-28 太平洋セメント株式会社 アルミニウム合金基複合材料の製造方法
JP5601833B2 (ja) * 2009-12-25 2014-10-08 日本ファインセラミックス株式会社 金属−セラミックス複合材料の製造方法
CN103436825A (zh) * 2013-08-23 2013-12-11 哈尔滨理工大学 纳米氧化锡涂覆陶瓷相增强体/铝基复合材料的制备方法
CN103710561B (zh) * 2013-12-23 2016-02-10 上海应用技术学院 一种可调节基体相和增强相组成的多孔陶瓷/金属双连续相复合材料的制备方法
CN104018022B (zh) * 2014-05-28 2016-07-20 成都西顿硬质合金有限公司 碳化硼基微观结构复合材料的制备方法
CN104818402B (zh) * 2015-05-12 2016-11-02 东南大学 一种挤压浸渗制备金刚石-Al复合材料的方法
CN106670430B (zh) * 2016-12-28 2019-04-26 新冶高科技集团有限公司 热等静压浸渍系统、方法和碳/金属复合材料

Also Published As

Publication number Publication date
WO2019107541A1 (ja) 2019-06-06
EP3719151A1 (de) 2020-10-07
JP6681079B2 (ja) 2020-04-15
CN111479940A (zh) 2020-07-31
EP3719151C0 (de) 2023-06-07
EP3719151A4 (de) 2021-08-25
JP2019099850A (ja) 2019-06-24
CN111479940B (zh) 2021-05-11

Similar Documents

Publication Publication Date Title
EP3719151B1 (de) Verfahren zur herstellung von verbundwerkstoff auf aluminiumlegierungsbasis und verbundwerkstoff auf aluminiumlegierungsbasis
Guo et al. Effect of (0–40) wt.% Si addition to Al on the thermal conductivity and thermal expansion of diamond/Al composites by pressure infiltration
EP0188704B1 (de) Faserverstärkter Metall-Verbundwerkstoff
Ghosh et al. Influence of size and volume fraction of SiC particulates on properties of ex situ reinforced Al–4.5 Cu–3Mg metal matrix composite prepared by direct metal laser sintering process
CA2738936C (en) Aluminum alloy powder metal bulk chemistry formulation
Li et al. Effects of pouring temperature on microstructure, mechanical properties, and fracture behavior of Al/Mg bimetallic composites produced by lost foam casting process
Balasubramanian et al. Mechanical characterization and machining of squeeze cast AZ91D/SiC magnesium based metal matrix composites
EP3104995A1 (de) Verfahren zur herstellung eines metall-matrix-verbundstoffs
Kumar et al. Evaluation of Al7075 reinforced with SiC for its mechanical properties & surface roughness by drilling
JPH04319043A (ja) 鋳造用塩コアの製造方法
WO1986001196A1 (en) Novel composite ceramics with improved toughness
KR910001357B1 (ko) 내마모층을 형성하는 방법
JP2004346368A (ja) 複合材料の製造方法、及び複合材料
US4723999A (en) Method of powder metallurgically manufacturing an object
Ahmad et al. The Microsructure and Properties of Aluminium Composite Reinforced with 65 μm Alumina Particles via Powder Metallurgy
Boudreau Characterization of powder metallurgy lightweight alloys
RU2704343C1 (ru) Способ получения объемного композиционного материала никель - диоксид циркония с повышенной устойчивостью к окислению
Prudhvi Raj et al. Mechanical Characterization and Machining of MgAZ91D/SiC/Al2O3MMC by Squeeze Cast Method
RU2001718C1 (ru) Способ получени дисперсно-упрочненного материала
Huchler Pressure infiltration behaviour and properties of aluminium alloy-Oxide ceramic preform composites
RU2625377C1 (ru) Способ изготовления композиционного материала для изделий электронной техники СВЧ
JP2003160825A (ja) 金属間化合物基複合材料及びその製造方法
EP4656750A1 (de) Hochfester metallmatrixverbundstoff und verfahren zur herstellung des hochfesten metallmatrixverbundstoffs
JP2004353087A (ja) 複合材料の製造方法
Zhang et al. Fabrication and Properties of W-SiCP/Cu Composites by Hot Pressing Sintering

Legal Events

Date Code Title Description
STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE INTERNATIONAL PUBLICATION HAS BEEN MADE

PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: REQUEST FOR EXAMINATION WAS MADE

17P Request for examination filed

Effective date: 20200617

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

AX Request for extension of the european patent

Extension state: BA ME

DAV Request for validation of the european patent (deleted)
DAX Request for extension of the european patent (deleted)
A4 Supplementary search report drawn up and despatched

Effective date: 20210727

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 1/10 20060101AFI20210721BHEP

Ipc: B22D 19/14 20060101ALI20210721BHEP

Ipc: B22D 19/00 20060101ALI20210721BHEP

Ipc: B22D 18/02 20060101ALI20210721BHEP

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: EXAMINATION IS IN PROGRESS

17Q First examination report despatched

Effective date: 20220215

REG Reference to a national code

Ref country code: DE

Free format text: PREVIOUS MAIN CLASS: C22C0001100000

Ref country code: DE

Ref legal event code: R079

Ref document number: 602018051611

Country of ref document: DE

Free format text: PREVIOUS MAIN CLASS: C22C0001100000

Ipc: C22C0001040000

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: GRANT OF PATENT IS INTENDED

RIC1 Information provided on ipc code assigned before grant

Ipc: B22D 19/14 20060101ALI20220815BHEP

Ipc: B22D 19/02 20060101ALI20220815BHEP

Ipc: B22D 19/00 20060101ALI20220815BHEP

Ipc: B22D 18/02 20060101ALI20220815BHEP

Ipc: C22C 1/10 20060101ALI20220815BHEP

Ipc: C22C 1/04 20060101AFI20220815BHEP

INTG Intention to grant announced

Effective date: 20220919

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

RIN1 Information on inventor provided before grant (corrected)

Inventor name: WATANABE, KENJI

Inventor name: MITO, HIROSHI

RAP3 Party data changed (applicant data changed or rights of an application transferred)

Owner name: ADVANCED COMPOSITE CORPORATION

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE PATENT HAS BEEN GRANTED

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

Ref country code: AT

Ref legal event code: REF

Ref document number: 1575196

Country of ref document: AT

Kind code of ref document: T

Effective date: 20230615

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 602018051611

Country of ref document: DE

U01 Request for unitary effect filed

Effective date: 20230704

U07 Unitary effect registered

Designated state(s): AT BE BG DE DK EE FI FR IT LT LU LV MT NL PT SE SI

Effective date: 20230712

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG9D

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: NO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20230907

Ref country code: ES

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20230607

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: RS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20230607

Ref country code: HR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20230607

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20230908

U20 Renewal fee for the european patent with unitary effect paid

Year of fee payment: 6

Effective date: 20231129

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20230607

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20231007

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SM

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20230607

Ref country code: SK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20230607

Ref country code: RO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20230607

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20231007

Ref country code: CZ

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20230607

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: PL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20230607

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602018051611

Country of ref document: DE

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

26N No opposition filed

Effective date: 20240308

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MC

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20230607

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20231130

U1N Appointed representative for the unitary patent procedure changed after the registration of the unitary effect

Representative=s name: WAECHTERSHAEUSER & HARTZPATENTANWALTSPARTNERSCHAFT MBB; DE

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MC

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20230607

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20231130

REG Reference to a national code

Ref country code: IE

Ref legal event code: MM4A

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20231130

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20231130

U20 Renewal fee for the european patent with unitary effect paid

Year of fee payment: 7

Effective date: 20241128

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO

Effective date: 20181130

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: HU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO

Effective date: 20181130

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: TR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20230607

U20 Renewal fee for the european patent with unitary effect paid

Year of fee payment: 8

Effective date: 20251125

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: GB

Payment date: 20251120

Year of fee payment: 8