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EP2396441B1 - Moyen de connexion, procédé de fabrication associé et connexion de matériau - Google Patents

Moyen de connexion, procédé de fabrication associé et connexion de matériau Download PDF

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Publication number
EP2396441B1
EP2396441B1 EP10702252A EP10702252A EP2396441B1 EP 2396441 B1 EP2396441 B1 EP 2396441B1 EP 10702252 A EP10702252 A EP 10702252A EP 10702252 A EP10702252 A EP 10702252A EP 2396441 B1 EP2396441 B1 EP 2396441B1
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Prior art keywords
metal
connection means
cnt
powder
nanoparticles
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German (de)
English (en)
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EP2396441A1 (fr
Inventor
Henning Zoz
Michael Dvorak
Horst Adams
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Bayer Intellectual Property GmbH
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Bayer International SA
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Priority claimed from PCT/EP2009/006737 external-priority patent/WO2010091704A1/fr
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C47/00—Making alloys containing metallic or non-metallic fibres or filaments
    • C22C47/14—Making alloys containing metallic or non-metallic fibres or filaments by powder metallurgy, i.e. by processing mixtures of metal powder and fibres or filaments
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C49/00—Alloys containing metallic or non-metallic fibres or filaments
    • C22C49/02—Alloys containing metallic or non-metallic fibres or filaments characterised by the matrix material
    • C22C49/04—Light metals
    • C22C49/06—Aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C49/00—Alloys containing metallic or non-metallic fibres or filaments
    • C22C49/14—Alloys containing metallic or non-metallic fibres or filaments characterised by the fibres or filaments

Definitions

  • the present invention relates to a connection means made from metal, and in particular a light metal such as Al, Mg, Cu, Ti or an alloy comprising one or more of the same.
  • the invention also relates to a method for producing the same and a material connection employing the connection means.
  • connection means such as screws, bolts, hinges or rivets.
  • connection means such as screws, bolts, hinges or rivets.
  • the ideal connection means would have a small weight, a high strength such as a high Vickers hardness and a high tensile strength, a high temperature stability and a high corrosion resistance.
  • connection means will always resemble some sort of compromise in this regard.
  • Al-based alloys due to their low weight are used for manufacturing connection means.
  • many high strength Al-alloys have an inferior corrosion resistivity and they can often not be anodized.
  • high strength aluminum alloys need a heat treatment to obtain the desired mechanical properties, which often will only be permanent in relatively small temperature ranges. This is especially crucial since the deterioration in the mechanical properties after use at higher temperatures is non-reversible.
  • connection means which is light-weight, corrosion resistant and has a high mechanical strength, in particular a high Vickers hardness and a high tensile strength.
  • connection means which is suitable for mass production at rather moderate costs.
  • connection means made from metal, and in particular a light metal such as Al, Mg, Cu Ti or an alloy comprising one or more of the same is provided, which is made from a compound material of said metal reinforced by nanoparticles, in particular CNT, wherein the reinforced metal has a microstructure comprising metal crystallites at least partly separated by nanoparticles.
  • the compound preferably comprises metal crystallites having a size in a range of 1 nm to 100 nm, preferably 10 nm to 100 nm, or in a range of more than 100 nm and up to 200 nm.
  • CNT as said nanoparticles for simplicity. It is however believed that similar effects could also be achieved when using other types of nanoparticles having a high aspect ratio, in particular inorganic nanoparticles such as carbides, nitrides and silicides. Thus, wherever applicable every disclosure made herein with respect to CNT is also contemplated with reference to other types of nanoparticles having a high aspect ratio, without further mention.
  • the structure of the material constituting the connection means has a new and surprising effect in that the micro structure of the metal crystallites is stabilized by the nanoparticles (CNT).
  • CNT nanoparticles
  • This stabilization is very effective due to the extremely high surface to volume ratio of the nano scale crystallites.
  • alloys strengthened by solid-solution hardening are used as the metal constituents, the phases of the mixed crystal or solid solution can be stabilized by the engagement or interlocking with the CNT.
  • nano-stabilization this new effect which is observed to arise for small metal crystallites in combination with uniformly and preferably isotropically dispersed CNT is called “nano-stabilization” or “nano-fixation” herein.
  • a further aspect of the nano-stabilization is that the CNT suppress a grain growth of the metal crystallites.
  • the nano-stabilization is of course a microscopical (or rather nanoscopical) effect, it allows to produce a compound material as an intermediate product and to further manufacture a finished connection means therefrom having unprecedented macroscopic mechanical properties.
  • the compound material will have a mechanical strength that is significantly higher than that of the pure metal component.
  • a further surprising technical effect is an increased high-temperature stability of the compound material as well as of the connection means produced therefrom. For example, it has been observed that due to the nano-stabilization of the nano crystallites by CNT, a dislocation density and an increased hardness associated therewith can be conserved at temperatures close to the melting point of some of the phases of the metal.
  • connection means can be produced by hot working or extrusion methods at temperatures close to the melting point of some of the phases of the metal while preserving the mechanical strength and hardness of the compound.
  • the metal is aluminum or an aluminum alloy
  • hot working would be an untypical way of processing it, since this would usually severely compromise the mechanical properties of the aluminum.
  • the nano-stabilization described above an increased Young modulus and hardness will be preserved even under hot working.
  • the final connection means formed from the nano-stabilized compound as a source material can be used for high-temperature applications, such as engines or turbines, where light metals typically fail due to lack of high-temperature stability.
  • the nanoparticles are not only partly separated from each other by the CNT, but some CNT are also contained or embedded in crystallites.
  • CNT are also contained or embedded in crystallites.
  • These embedded CNTs are believed to play an important role in preventing grain growth and internal relaxation, i.e. preventing a decrease of the dislocation density when energy is supplied in form of pressure and/or heat upon compacting the compound material.
  • mechanical alloying techniques of the type as described below it is possible to produce crystallites below 100 nm in size with embedded CNTs.
  • the nano-stabilisation has been found to be very effective also for crystallites between 100 nm and 200 nm in size.
  • the invention allows to circumvent many problems currently encountered with Al alloys. While high strength Al alloys are known, such as Al7xxx incorporating Zinc or Al8xxx incorporating Li according to Standard EN 573-3/4, unfortunately, coating these alloys by anodic oxidation proves to be difficult. Also, if different Al alloys are combined, due to a different electro-chemical potentials of the alloys involved, corrosion may occur in the contact region. On the other hand, while Al alloys of the series 1xxx, 3xxx and 5xxx based on solid-solution hardening can be coated by anodic oxidation, they have comparatively poor mechanical properties, a low temperature stability and can only be hardened to a quite narrow degree by cold working.
  • an aluminum based composite material can be provided which due to the nano-stabilization effect has a strength and hardness comparable with or even beyond the highest strength aluminum alloy available today, which also has an increased high-temperature strength due to the nano-stabilization and is open for anodic oxidation. If a high-strength aluminum alloy is used as the metal of the composite of the invention, the strength of the compound can even be further raised. Also, by adequately adjusting the percentage of CNT in the composite, the mechanical properties can be adjusted to a desired value.
  • the present invention also provides a material connection comprising a first part, a second part and a connection means connecting the first and second parts, wherein at least one of said first and second parts comprises a metal or a metal alloy.
  • the connection means has different, in particular superior mechanical properties as compared with the first and second parts that are to be connected thereby.
  • the connection means would be a metal or a metal alloy different from the metal or metal alloy of the first and/or second part having the desired mechanical properties in order to compensate for instance for different thermal expansion coefficients for the two parts to be connected.
  • the connection means will act as a galvanic element with regard to the parts, thus leading to contact corrosion in presence of an electrolyte.
  • connection means of the invention can be adjusted by the content of nanoparticles, it is in many cases possible to use the same metal component in the connection means as in the parts to be connected thereby and to still obtain suitable different mechanical properties. This way, contact corrosion between the first and second part on the one hand and the connection means on the other hand can be reliably avoided.
  • the metal component of the first and/or second parts and the connection means are identical, but in practice it will be sufficient that the respective chemical potentials deviate by less than 50 mV, preferably less than 25 mV from each other.
  • connection means of the invention since in the connection means of the invention, the content of nanoparticles can be controlled to adjust the desired mechanical properties rather than the metal content used, this additional degree of freedom can be advantageously used to provide material connections employing a connection means which is both compatible with the parts to be connected from an electrochemical point of view and still provides the desired mechanical properties, which due to the nanoparticle content can be very different from that of the parts to be connected.
  • the tensile strength and the hardness can be varied approximately proportionally in a wide range with the content of CNT in the composite material.
  • the Vickers hardness increases nearly linearly with the CNT content.
  • the composite material becomes extremely hard and brittle.
  • a CNT content from 0.5 to 10.0wt% will be preferable.
  • a CNT content in the range of 2.0 to 9.0% is extremely useful as it allows to make composite materials of extraordinary strength in combination with the aforementioned advantages of nano-stabilization, in particular high-temperature stability.
  • the mechanical properties of the connection means connecting a first and a second part can be specifically adapted without the necessity to use a different metal component, but by varying the nanoparticle content instead.
  • the same principle is of course also applicable with regard to the first and second parts themselves, which each may be made from a compound material comprising metal or a metal alloy and nanoparticles, and where the mechanical properties of the two parts may be different due to different contents of nanoparticles.
  • the numerical value of nanoparticles by weight of the first and second parts differ at least by 10%, preferably by at least 20% of the higher one of said numerical values.
  • the numerical values of the percentages would differ by 20% of the higher one of said numerical values.
  • This concept may be pushed even one step further by providing an integral part made from a compound material of a metal or metal alloy reinforced be nanoparticles, wherein the concentration of nanoparticles varies between different regions of the integral part.
  • the part would be a plate
  • the nanoparticle content could monotonously increase along a length or width direction between a first and a second end of the plate, which would mean that the plate would have an increased tensile strength or Vickers hardness in a region close to its second end as compared to a region close to its first end.
  • connection to connection means equally apply with regard to the integral part, without further mention.
  • the same type of composite powder material that will be described below and the same type of compacting methods thereof may equally be applied with regard to the integral part, while the explicit description thereof is omitted for brevity.
  • compound metal/CNT materials per se are for example from US 2007/0134496 A1 , JP 2007/154 246 A , WO 2006/123 859 A1 , WO 2008/052 642 , WO 2009/010 297 and JP 2009/030 090 .
  • a detailed discussion thereof is made in the priority application PCT/EP2009/006 737 , which is included herein by reference.
  • connection means based on CNT reinforced metal are to be manufactured, there is a problem arising in prior art which is related to possible exposure when handling CNTs (see e.g. Baron P. A. (2003) “Evaluation of Aerosol Release During the Handling of Unrefined Single Walled Carbon Nanotube Material", NIOSH DART-02-191 Rev. 1.1 April 2003 ; Maynard A. D. et al. (2004) “Exposure To Carbon Nanotube Material: Aerosol Release During The Handling Of Unrefined Singlewalled Carbon Nanotube Material", Journal of Toxicology and Environmental Health, Part A, 67:87-107 ; Han, J. H. et al. (2008) 'Monitoring Multiwalled Carbon Nanotube Exposure in Carbon Nanotube Research Facility', Inhalation Toxicology, 20:8, 741 - 749 ).
  • this can be minimized by providing the CNT in form of a powder of tangled CNT-agglomerates having a mean size sufficiently large to ensure easy handling because of a low potential dustiness.
  • preferably at least 95% of the CNT-agglomerates have a particle size larger than 100 ⁇ m.
  • the mean diameter of the CNT-agglomerates is between 0.05 and 5 mm, preferably 0.1 and 2 mm and most preferably 0.2 and 1 mm.
  • the nanoparticles to be processed with the metal powder can be easily handled with the potential for exposure being minimized.
  • the agglomerates being larger than 100 ⁇ m, they can be easily filtered by standard filters, and a low respirable dustiness in the sense of EN 15051-B can be expected.
  • the powder comprised of agglomerates of this large size has a pourability and flowability which allows an easy handling of the CNT source material.
  • the length-to-diameter ratio of the CNT also called aspect ratio
  • a high aspect ratio of the CNT again assists in the nano-stabilization of the metal crystallites.
  • At least a fraction of the CNTs have a scrolled structure comprised of one or more rolled up graphite layers, each graphite layer consisting of two or more graphene layers on top of each other.
  • This type of nano tubes has for the first time been described in DE 10 2007 044 031 A1 which has been published after the priority date of the present application.
  • This new type of CNT structure is called a "multi-scroll" structure to distinguish it from “single-scroll” structures comprised of a single rolled-up graphene layer.
  • the relationship between multi-scroll and single-scroll CNTs is therefore analogous to the relationship between single-wall and multi-wall cylindrical CNTs.
  • the multi-scroll CNTs have a spiral shaped cross section and typically comprise 2 or 3 graphite layers with 6 to 12 graphene layers each.
  • the multi-scroll type CNTs have found to be extraordinarily suitable for the above mentioned nano-stabilization.
  • One of the reasons is that the multi-scroll CNT have the tendency to not extend along a straight line but to have a curvy or kinky, multiply bent shape, which is also the reason why they tend to form large agglomerates of highly tangled CNTs.
  • This tendency to form a curvy, bent and tangled structure facilitates the formation of a three-dimensional network interlocking with the crystallites and stabilizing them.
  • a further reason why the multi-scroll structure is so well suited for nano-stabilization is believed to be that the individual layers tend to fan out when the tube is bent like the pages of an open book, thus forming a rough structure for interlocking with the crystallites which in turn is believed to be one of the mechanisms for stabilization of defects.
  • the nanoparticles are functionalized, in particular roughened prior to the mechanical alloying.
  • the roughening may be performed by causing at least the outermost layer of at least some of the CNTs to break by submitting the CNTs to high pressure, such as a pressure of 5.0 MPa or higher, preferably 7.8 MPa or higher, as will be explained below with reference to a specific embodiment. Due to the roughening of the nanoparticles, the interlocking effect with the metal crystallites and thus the nano-stabilization is further increased.
  • the processing of the metal particles and the nanoparticles is conducted such as to increase and stabilize the dislocation density of the crystallites by the nanoparticles sufficiently to increase the average Vickers hardness of the composite material to exceed the Vickers hardness of the original metal by 40% or more, preferably by 80% or more.
  • the processing is conducted such as to stabilize the dislocations, i.e. suppress dislocation movement and to suppress the grain growth sufficiently such that the Vickers hardness of the connection means formed by compacting the composite powder is higher than the Vickers hardness of the original metal, and preferably higher than 80% of the Vickers hardness of the composite powder.
  • the high dislocation density is preferably generated by causing numerous high kinetic energy impacts of balls of a ball mill.
  • the balls are accelerated to a speed of at least 8.0 m/s, preferably at least 11.0 m/s.
  • the balls may interact with the processed material by shear forces, friction and collision forces, but the relative contribution of collisions to the total mechanical energy transferred to the material by plastic deformation increases with increasing kinetic energy of the balls. Accordingly, a high velocity of the balls is preferred for causing a high rate of kinetic energy impacts which in turn causes a high dislocation density in the crystallites.
  • the milling chamber of ball mill is stationary and the balls are accelerated by a rotary motion of a rotating element.
  • This design allows to easily and efficiently accelerate the balls to the above mentioned velocities of 8.0 m/s, 11.0 m/s or even higher, by driving the rotating element at a sufficient rotary frequency such that the tips thereof are moved at the above mentioned velocities.
  • This is different from, for example, ordinary ball mills having a rotating drum or planetary ball mills, where the maximum speed of the balls is typically 5 m/s only.
  • the design employing a stationary milling chamber and a driven rotating element is easily scaleable, meaning that the same design can be used for ball mills of very different sizes, from laboratory type mill up to mills for high throughput mechanical alloying on an industrial scale.
  • the axis of the rotary element is oriented horizontally, such that the influence of gravity on both, the balls and the processed material, is reduced to a minimum.
  • the balls have a small diameter of 3.0 to 8.0 mm, preferably 4.0 to 6.0 mm. At this small ball diameters, the contact zones between the balls are nearly point shaped thus leading to very high deformation pressures, which in turn facilitates the formation of a high dislocation density in the metal.
  • the preferred material of the balls is steel, ZiO 2 or yttria stabilized ZiO 2 .
  • the quality of the mechanical alloying will also depend on the filling degree of the milling chamber with the balls as well as on the ratio of balls and processed material. Good mechanical alloying results can be achieved if the volume occupied by the balls roughly corresponds to the volume of the chamber not reached by the rotating element.
  • the ratio of the processed material, i.e. (metal + nanoparticles) / balls by weight is preferably between 1:7 and 1:13.
  • the second problem encountered when processing at high kinetic energies is that the CNT may be worn down or destroyed to an extent that the interlocking effect with the metal crystallites, i.e. the nano-stabilization no longer occurs.
  • the processing of the metal and the CNTs comprises a first and a second stage, wherein in the first processing stage most or all of the metal is processed and in the second stage CNTs are added and the metal and the CNTs are simultaneously processed.
  • the metal in the first stage, can be milled down at high kinetic energy to a crystallite size of 100 nm or below before the CNTs are added, such as to not wear down the CNT in this milling stage.
  • the first stage is conducted for a time suitable to generate metal crystallites having an average size in a range of 1 to 100 nm, which in one embodiment was found to be a time of 20 to 60 minutes.
  • the second stage is then conducted for a time sufficient to cause a stabilization of the nanostructure of the crystallites, which may typically take 5 to 30 min only. This short time of the second stage is sufficient to perform mechanical alloying of the CNT and the metal and to thereby homogeneously disperse the CNT throughout the metal matrix, while not yet destroying too much of the CNT.
  • the rotation speed of the rotating element is cyclically raised and lowered.
  • This technique is for example described in DE 196 35 500 and referred to as "cycle operation". It has been found that by conducting the processing with alternating cycles of higher and lower rotational speeds of the rotating element, sticking of the material during processing can be very efficiently be prevented.
  • the cycle operation which is per se known for example from the above referenced patent has proven to be very useful for the specific application of mechanical alloying of a metal and CNTs.
  • the method of manufacturing the connection means may also comprise the manufacturing of CNTs in the form of CNT powder as a source material.
  • the method may comprise a step of producing the CNT powder by catalytic carbon vapor deposition using one or more of a group consisting of acetylene, methane, ethane, ethylene, butane, butene, butadylene, and benzene as a carbon donor.
  • the catalyst comprises two or more elements of a group consisting of Fe, Co, Mn, Mo and Ni. It has been found that with these catalysts, CNTs can be formed at high yield, allowing a production on an industrial scale.
  • the step of producing the CNT powder comprises a step of catalytic decomposition of C 1 -C 3 -carbo hydrogens at 500°C to 1000°C using a catalyst comprising Mn and Co in a molaric ratio in a range of 2:3 to 3:2.
  • a catalyst comprising Mn and Co in a molaric ratio in a range of 2:3 to 3:2.
  • connection means according to an embodiment of the invention is summarized. For this, a method of producing constituent materials and of producing a composite material from the constituent materials will be explained. Also, different ways of compacting the composite material such as to form a connection means or a blank for a connection means will be discussed.
  • the processing strategy comprises the following steps:
  • a setup 10 for producing high quality CNTs by catalytic CVD in a fluidized bed reactor 12 is shown.
  • the reactor 12 is heated by heating means 14.
  • the reactor 12 has a lower entrance 16 for introducing inert gases and reactant gases, an upper discharge opening 18 for discharging nitrogen, inert gas and by-products from the reactor 12, a catalyst entrance 20 for introducing a catalyst and a CNT discharge opening 22 for discharging CNTs formed in the reactor 12.
  • CNTs of the multi-scroll type are produced by a method as known from DE 10 2007 044 031 A1 , which has been published after the priority date of the present application and the whole content of which is hereby included in the present application by reference.
  • nitrogen as an inert gas is introduced in the lower entrance 16 while the reactor 12 is heated by heating means 14 to a temperature of 650°C.
  • the catalyst is preferably a transition metal catalyst based on Co and Mn, wherein the molaric ratio of Co and Mn with respect to each other is between 2:3 and 3:2.
  • a reactant gas is introduced at the lower entrance 16, comprising a hydrocarbon gas as a carbon donor and an inert gas.
  • the hydrocarbon gas preferably comprises C 1 -C 3 -carbo-hydrogens.
  • the ratio of reactant and inert gas may be about 9:1.
  • Carbon deposited in form of CNT is discharged at the CNT discharge opening 22.
  • the catalyst material is typically milled to a size of 30 to 100 ⁇ m.
  • a number of primary catalyst particles may agglomerate and carbon is deposited by CVD on the catalyst particle surfaces such that CNTs are grown.
  • the CNT form agglomerates of long entangled fibres upon growth, as is schematically shown in the right half of Fig. 2 .
  • At least part of the catalyst will remain in the CNT-agglomerate.
  • the catalyst content in the agglomerates will become negligible, as the carbon content of the agglomerates may eventually be higher than 95%, in some embodiments even higher than 99%.
  • FIG. 3 an SEM image of a CNT-agglomerate thus formed is shown.
  • the agglomerate is very large by "nano-standards", having a diameter of more than 1 mm.
  • Fig. 4 shows an enlarged image of the CNT-agglomerate, in which a multitude of highly entangled CNTs with a large length to diameter ratio can be seen.
  • the CNTs have a "curly” or “kinky” shape, as each CNT has only comparatively short straight sections with numerous bends and curves inbetween. It is believed that this curliness or kinkiness is related to the peculiar structure of the CNTs, which is called the "multi-scroll structure" herein.
  • the multi-scroll structure is a structure comprised of one or more rolled up graphite layers, where each graphite layer consists of two or more graphene layers on top of each other. This structure has for the first time been reported in DE 10 2007 044 031 A1 published after the priority date of the present application.
  • Table 1 summarizes the characteristic properties of high purity multi-scroll CNT that have been produced with the setup of Fig. 1 .
  • the CNTs have a considerably high C-purity of more than 95wt%.
  • the average outer diameter is only 13 nm at a length of 1 to 10 ⁇ m, i.e. the CNTs have a very high aspect ratio.
  • a further remarkable property is the high bulk density being in a range of 130 to 150 kg/m 3 . This high bulk density greatly facilitates the handling of the CNT-agglomerate powder, and allows easy pouring and efficient storing thereof. This is of great importance when it comes to application of the composite material for manufacturing connection means on an industrial scale.
  • the CNT-agglomerates with the properties of Table 1 can be produced rapidly and efficiently with a high throughput. Even today the applicant already has the capacity to produce 60 tons of this type of CNT-agglomerates per year.
  • Table 2 summarizes the same properties for a very high purity CNT-agglomerate which the applicant is also able to produce, although at a lower capacity.
  • Fig. 5 shows a graph of the particle-size distribution of the CNT-agglomerates.
  • the abscissa represents the particle size in ⁇ m, while the ordinate represents the cumulative volumetric content.
  • almost all of the CNT-agglomerates have a size larger than 100 ⁇ m. This means that practically all of the CNT-agglomerates can be filtered by standard filters.
  • These CNT-agglomerates have a low respirable dustiness under EN 15051-B.
  • the extraordinarily large CNT-agglomerates used in the preferred embodiment of the invention allow for a safe and easy handling of the CNT, which again is of highest importance when it comes to transferring the technology from the laboratory to the industrial scale.
  • the CNT powder has a good pourability, which also greatly facilitates the handling.
  • the CNT-agglomerates allow to combine macroscopic handling properties with nanoscopic material characteristics.
  • the CNTs are functionalized prior to performing the mechanical alloying.
  • the purpose of the functionalizing is to treat the CNTs such that the nano-stabilization of the metal crystallites in the composite material will be enhanced.
  • this functionalization is achieved by roughening the surface of at least some of the CNTs.
  • the CNT-agglomerates as shown in Fig. 6a are submitted to a high pressure of 100 kg/cm 2 (9.8 MPa).
  • the agglomerate structure as such is preserved, i.e. the functionalized CNTs are still present in the form of agglomerates preserving the aforementioned advantages with respect to low respirable dustiness and easier handling.
  • the outermost layer or layers burst or break, thereby developing a rough surface, as is shown in Fig. 6c . With the rough surface, the interlocking effect between CNT and crystallites is increased, which in turn increases the nano-stabilization effect.
  • a setup 24 for generating a metal powder through atomization comprises a vessel with heating means in which a metal or metal alloy to be used as a constituent of the composite material is melted.
  • the liquid metal or alloy is poured into a chamber 30 and forced by argon driving gas, represented by an arrow 32 through a nozzle assembly 34 into a chamber 36 containing an inert gas.
  • the liquid metal spray leaving the nozzle assembly 34 is quenched by an argon quenching gas 38, so that the metal droplets are rapidly solidified and form a metal powder 40 piling up on the floor of chamber 36.
  • This powder forms the metal constituent of the composite material used for manufacturing connection means according to an embodiment of the invention.
  • the CNTs need to be dispersed within the metal.
  • this is achieved by a mechanical alloying carried out in a high energy mill 42, which is shown in a sectional side view in Fig. 8a and a sectional end view in Fig. 8b .
  • the high energy mill 42 comprises a milling chamber 44 in which a rotating element 46 having a number of rotating arms 48 is arranged such that the rotary axis extends horizontally. While this is not shown in the schematic view of Fig.
  • the rotating element 46 is connected to a driving means such as to be driven at a rotational frequency of up to 1,500 RPM or even higher.
  • the rotating element 46 can be driven at a rotational speed so that the radially outward lying tips of each arm 48 acquire a velocity of at least 8.0 m/s, preferably more than 11.0 m/s with respect to the milling chamber 44, which itself remains stationary.
  • a multitude of balls are provided in the milling chamber 44 as milling members. A close-up look of two balls 50 is shown in Fig. 9 to be described in more detail below.
  • the balls are made from steel and have a diameter of 5.1 mm.
  • the balls 50 could be made from ZiO 2 or yttria stabilized said ZiO 2 .
  • the filling degree of the balls within the high energy mill 42 is chosen such that the volume occupied by the balls corresponds to the volume of the milling chamber 44 that lies outside the cylindrical volume that can be reached by the rotating arms 48.
  • Similar high energy ball mills are disclosed in DE 196 35 500 , DE 43 07 083 and DE 195 04 540 A1 .
  • Mechanical alloying is a process where powder particles 52 are treated by repeated deformation, fracture and welding by highly energetic collisions of grinding balls 50. In the course of the mechanical alloying, the CNT-agglomerates are deconstructed and the metal powder particles are fragmentized, and by this process, single CNTs are dispersed in the metal matrix. Since the kinetic energy of the balls depends quadratically on the velocity, it is a primary object to accelerate the balls to very high velocities of 10 m/s or even above. The inventors have analyzed the kinetics of the balls using high speed stroboscopic cinematopography and could confirm that the maximum relative velocity of the balls corresponds approximately to the maximum velocity of the tips of the rotating arms 48.
  • the processed media While in all types of ball mills the processed media are subjected to collision forces, shear forces and frictional forces, at higher kinetic energies the relative amount of energy transferred by collision increases.
  • the relative contribution of collisions is as high as possible.
  • the high energy ball mill 42 shown in Fig. 8 is advantageous over ordinary drum-ball mills, planetary ball mills or attritors since the kinetic energy of the balls that can be reached is higher.
  • the maximum relative velocity of the balls is typically 5 m/s or below.
  • the maximum velocity of the balls will depend both on the rotational velocity and the size of the milling chamber.
  • the balls are moved in the so called “cascade mode", in which the frictional and shear forces dominate.
  • the ball motion enters the so called “cataract mode”, in which the balls are accelerated due to gravity in a free fall mode, and accordingly, the maximum velocity will depend on the diameter of the ball mill.
  • the maximum velocity will hardly surpass 7 m/s. Accordingly, the HEM design with a stationary milling chamber 44 and a driven rotating element 46 as shown in Fig. 8 is preferred.
  • the first effect is a decrease of crystallite size.
  • the second effect on the metal due to high energy collision is a work hardening effect due to an increase of dislocation density in the crystallites.
  • the dislocations accumulate, interact with each other and serve as pinning points or obstacles that significantly impede their motion. This again leads to an increase in the yield strength ⁇ y of the material and a subsequent decrease in ductility.
  • ⁇ y G ⁇ ⁇ ⁇ b ⁇ ⁇ , where G is the shear modulus, b is the Burger's vector and a is a material specific constant.
  • the CNT will tend to be damaged to a degree that the envisaged nano-stabilization is greatly compromised.
  • the high energy milling is therefore conducted in two stages.
  • a first stage the metal powder and only a fraction of the CNT powder are processed.
  • This first stage is conducted for a time suitable to generate metal crystallites having an average size below 200 nm, preferably below 100 nm, typically for 20 to 60 min.
  • a minimum amount of CNT is added that will allow to prevent sticking of the metal.
  • This CNT is sacrificed as a milling agent, i.e. it will not have a significant nano-stabilizing effect in the final composite material.
  • a second stage the remaining CNT is added and the mechanical alloying of the CNTs and the metal is performed.
  • the microscopic agglomerates as shown in Fig. 3 and Fig. 6b need to be decomposed into single CNTs which are dispersed in the metal matrix by mechanical alloying.
  • the integrity of the CNTs added during the second stage in the metal matrix is very good, thus allowing for the nano-stabilization effect.
  • the integrity of the disentangled CNTs in the metal matrix it is believed that using agglomerates of larger size is even advantageous, since the CNTs inside the agglomerates are to a certain extent protected by the outside CNTs.
  • the rotational speed of the rotational element 46 is preferably cyclically raised and lowered as is shown in the timing diagram of Fig. 10 .
  • the rotating speed is controlled in alternating cycles, namely a high speed cycle at 1,500 rpm for the duration of 4 min and a low speed cycle at 800 rpm for a duration of one minute.
  • This cyclic modulation of rotating speed is found to impede sticking.
  • Such cycle operation has already been described in DE 196 35 500 and has been successfully applied in the framework of the present invention.
  • a powder composite material can be obtained in which metal crystallites having a high dislocation density and a mean size below 200 nm, preferably below 100 nm are at least partially separated and micro-stabilized by homogeneously distributed CNTs.
  • Fig. 11 a shows a cut through a composite material particle according to an embodiment of the invention.
  • the metal constituent is aluminum and the CNTs are of the multi-scroll type obtained in a process as described in section 1 above.
  • the composite material is characterized by an isotropic distribution of nanoscopic metal crystallites located in a CNT mesh structure.
  • the composite material of WO 2008/052642 shown in Fig. 11b has a non-isotropic layer structure, leading to non-isotropic mechanical properties.
  • Fig. 12 shows an SEM image of a composite material comprised of aluminum with CNT dispersed therein.
  • CNT extending along a boundary of crystallites
  • the CNTs separate individual crystallites from each other and thereby effectively suppress grain growth of the crystallites and stabilize the dislocation density.
  • CNTs can be seen which are contained or embedded within a nanocrystallite and stick out from the nanocrystallite surface like a "hair". It is believed that these CNTs have been pressed into the metal crystallites like needles in the course of the high energy milling described above. It is believed that these CNTs embedded or contained within individual crystallites play an important role in the nano-stabilization effect, which in turn is responsible for the superior mechanical properties of the composite material and of compacted articles formed thereby.
  • the composite powder is subjected to a passivation treatment in a passivation vessel (not shown).
  • a passivation vessel (not shown).
  • the finished composite powder is discharged from the milling chamber 42, while still under vacuum or in an inert gas atmosphere and is discharged into the passivation vessel.
  • the composite material is slowly stirred, and oxygen is gradually added such as to slowly oxidize the composite powder. The slower this passivation is conducted, the lower is the total oxygen uptake of the composite powder.
  • Passivation of the powder again facilitates the handling of the powder as a source material for fabrication of manufactured or semi-finished articles on an industrial scale.
  • the composite material powder is then used as a source material for forming semi-finished or finished connection means by powder metallurgic methods.
  • the powder material of the invention can very advantageously be further processed by cold isostatic pressing (CIP) and hot isostatic pressing (HIP).
  • CIP cold isostatic pressing
  • HIP hot isostatic pressing
  • the composite material can be further processed by hot working, powder milling or powder extrusion at high temperatures close to the melting temperature of some of the metal phases. It has been observed that due to the nano-stabilizing effect of the CNT, the viscosity of the composite material even at high temperatures is increased such that the composite material may be processed by powder extrusion or flow pressing.
  • the powder can be directly processed by continuous powder rolling.
  • the beneficial mechanical properties of the powder particles can be maintained in the compacted finished or semi-finished article.
  • a composite material having a Vickers hardness of more than 390 HV was obtained.
  • the Vickers hardness remains at more than 80% of this value.
  • the stabilizing nano structure the hardness of the individual composite powder particles can largely be transferred to the compacted connection means. Prior to this invention, such a hardness in the compacted article was not possible.
  • Fig. 13 shows a material connection 52 comprising a first part 54, a second part 56 and a connection means 58 connecting the first and second parts.
  • the first part 54 could be a portion of an engine block and the second part 56 could be a part of a cylinder head, which are attached to each other by the connection means 58 according to an embodiment of the invention.
  • the ideal connection means would have a high mechanical strength, a high thermal stability and a light weight.
  • prior art light metal alloys such as high strength Al-alloys will have a small weight and a high mechanical strength, but fail to provide for thermal stability.
  • the manufacturing of connection means from such high strength aluminum alloys is difficult and costly for the reasons given above.
  • connection means Even if a suitable metal alloy is found which has the desired mechanical properties, there is a further problem that the electrochemical potentials between the connection means and each of the first and second parts would be different, which would lead to a contact corrosion in the presence of a suitable electrolyte.
  • connection means 58 according to an embodiment of the invention is used, which allows to control the mechanical properties of the connection means 58 by the content of nanoparticles, in particular CNT, rather than by the metal part used.
  • the material connection 52 can be made by using the same metal components in each of the first and second parts 54, 56 and the connection means 58, where the desired mechanical properties of the connection means 58 are provided by the nanoparticle content based on the above nano-stabilization effect, such that no galvanic potential difference between the parts 54, 56 and the connection means 58 exists. This way, contact corrosion can be reliably prevented without compromising the mechanical properties of the connection means 58.
  • connection means 58 i.e. a connecting screw could be made by a compound material comprising the same metal content but with a fraction of 2 to 6wt% of CNT, which would provide the desired tensile strength.
  • the connection means 58 would also have a sufficient thermal stability such that the mechanical properties would be conserved even during extended operation in a high temperature environment.
  • the increased thermal stability makes the connection means according to the invention well suitable for applications in engines, turbines or other applications where high temperatures arise. Further useful applications for the connection means of the invention in material connections are ultralight constructions, high-end sporting goods, aviation and aerospace technology and walking aids.
  • connection means can be controlled via the content of nanoparticles, in particular CNT, rather than by the metal component used.
  • This concept is not only applicable to the connection means 58, but also to the parts 54 and 56 connected thereby.
  • Fig. 14 showing four parts 60a to 60d, each of which being comprised of a compound material of a metal reinforced by nanoparticles.
  • Fig. 14 shows four parts 60a to 60d, each of which being comprised of a compound material of a metal reinforced by nanoparticles.
  • connection means 62 which are also made from the compound material of a metal reinforced by nanoparticles.
  • a joint product 64 formed by the individual parts 60a to 60d will have different mechanical properties in different regions thereof.
  • the Vickers hardness and tensile strength of the left most part of joint product 64 constituted by part 60a will be larger than that of the rightmost end constituted by part 60d, due to a higher nanoparticle content. This way, a joint product can be formed from the same metal, having different nanoparticle contents and accordingly different mechanical properties in different regions.
  • An exemplary application of this would for example be the wing of an airplane, where it would be desirable if the tensile strength of the wing material would be higher close to the fuselage than at the wing tips.
  • the same metal can be used in different regions of the joint product 46 and its connection means 62 and still each component 60a to 60d, 62 has mechanical properties that can be specifically adapted to its function.
  • contact corrosion problems can be avoided which would generally occur if metals or alloys with different chemical potentials were combined.
  • the embodiment is not limited to this case.
  • the metal components would be selected such that the electrochemical potentials of each two contacting components 60a to 60d, 62 would deviate by less than 50 mV, preferably less than 25 mV.
  • the same concept can be carried even one step further, in that different mechanical properties can be achieved in different regions of a single integral product 66 by locally varying the nanoparticle content, as is shown in Fig. 15 .
  • the integral part 66 is again formed by a metal or metal alloy reinforced by nanoparticles, where the concentration of nanoparticles differs in different regions of the integral part 66.
  • the concentration of nanoparticles on the left end of integral part 66 of Fig. 15 is higher than on the right end, which leads to a higher tensile strength and Vickers hardness on the left end of integral component 66.
  • connection means may equally be applied for manufacturing the integral component 66 of Fig. 15 .
  • the same small crystallite sizes for causing nano stabilization may apply for the material of integral component 66 and preferably, the same type of CNT may be used.
  • the same manufacturing method based on producing a composite powder material and compacting the same into a finished integral part 66 may be applied.
  • the integral part could very efficiently be produced by powder extrusion or powder rolling, where the nanoparticle compound is varied during rolling or extrusion.
  • This could for example be achieved by preparing two or more different types of composite powder materials having different nanoparticle contents, possibly even a powder containing no nanoparticles at all, and appropriately mixing the composite powder materials on rolling or extrusion.
  • integral part 66 shown in Fig. 15 could also be manufactured by hot isostatic pressing, cold isostatic pressing or sintering of a powder material which has been arranged such that different concentrations of nanoparticles at different parts are present, as desired.

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Claims (49)

  1. Moyen de connexion (58) constitué de métal, et en particulier d'Al, Mg, Cu ou Ti, ou d'un alliage comprenant un ou plusieurs de ces éléments et sous la forme d'une vis, d'une fixation, d'une charnière ou d'un rivet, caractérisé en ce que le moyen de connexion (58) est constitué d'un matériau composite composé dudit métal renforcé par des nano-particules, en particulier des nano-tubes de carbone (CNT), le métal renforcé présentant une micro-structure comprenant des cristallites de métal qui sont au moins partiellement séparées par lesdites nano-particules.
  2. Moyen de connexion (58) selon la revendication 1, dans lequel un composite comprend des cristallites de métal dont la taille est comprise dans une gamme de 1 nm à 100 nm, de préférence de 10 nm à 100 nm, ou dans une gamme de plus de 100 nm et jusqu'à 200 nm.
  3. Moyen de connexion (58) selon l'une des revendications précédentes, dans lequel des nano-particules sont également contenues dans au moins plusieurs des cristallites.
  4. Moyen de connexion (58) selon l'une des revendications précédentes, dans lequel la teneur en CNT du matériau composite en poids se situe dans la gamme de 0,5 % à 10,0 %, de préférence de 2,0 % à 9,0 %, et idéalement de 3,0 % à 6,0 %.
  5. Moyen de connexion (58) selon l'une des revendications précédentes, dans lequel les nano-particules sont formées par des CNT, dont au moins une fraction présente une structure de volute qui est constituée d'une ou de plusieurs couche(s) de graphite enroulée(s), chaque couche de graphite étant constituée de deux ou plus de deux couches de graphène les unes au-dessus des autres.
  6. Moyen de connexion (58) selon l'une des revendications précédentes, dans lequel au moins une fraction des nano-particules sont fonctionnalisées, en particulier rendues rugueuses sur leur surface extérieure.
  7. Moyen de connexion (58) selon l'une des revendications précédentes, dans lequel la dureté Vickers du matériau composite dépasse la dureté Vickers du métal original de 40 % ou plus, de préférence de 80 % ou plus.
  8. Moyen de connexion (58) selon l'une des revendications précédentes, dans lequel le métal est constitué par un alliage d'Al, et la dureté Vickers du matériau composite est supérieure à 250 HV, de préférence supérieure à 300 HV.
  9. Connexion de matériau (52) comprenant une première partie (54), une deuxième partie (56) et un moyen de connexion (58) selon l'une des revendications 1 à 8 qui relie les première et deuxième parties (54, 56), dans laquelle au moins une des première et deuxième parties (54, 56) comprend un métal ou un alliage de métal, le moyen de connexion (58) étant constitué d'un matériau composite composé d'un métal renforcé par des nano-particules, ledit métal ou alliage de métal de ladite au moins une desdites première et deuxième parties (54, 56) étant le même que celui du composant de métal du moyen de connexion (58) ou présentant un potentiel électrochimique qui s'écarte de celui du composant de métal du moyen de connexion (58) de moins de 50 mV, de préférence de moins de 25 mV.
  10. Connexion de matériau (52) selon la revendication 9, dans laquelle au moins deux éléments du groupe comprenant la première partie (54), la deuxième partie (56) et le moyen de connexion (58) sont constitués d'un matériau composite composé d'un métal ou d'un alliage de métal renforcé par des nano-particules mais présentent des concentrations différentes de nano-particules.
  11. Connexion de matériau (52) selon la revendication 10, dans laquelle les valeurs numériques du pourcentage de nano-particules en poids desdits deux éléments diffèrent d'au moins 10 %, de préférence d'au moins 20 % de la plus élevée desdites valeurs numériques.
  12. Moyen de connexion (58) selon l'une quelconque des revendications 1 à 8, dans lequel la concentration de nano-particules varie entre différentes régions de ladite partie intégrale.
  13. Moyen de connexion (58) selon la revendication 12, dans lequel la concentration de nano-particules varie le long d'au moins une direction de ladite partie intégrale.
  14. Procédé de fabrication d'un moyen de connexion (58) sous la forme d'une vis, d'une fixation, d'une charnière ou d'un rivet, comprenant les étapes suivantes:
    un matériau de poudre composite, ledit matériau comprenant un métal et des nano-particules, en particulier des nano-tubes de carbone (CNT),
    lesdites particules de poudre composite comprenant des cristallites de métal au moins partiellement séparées les unes des autres par lesdites nano-particules, et
    une étape de compactage de la poudre composite en un moyen de connexion (58) fini.
  15. Procédé selon la revendication 14, dans lequel l'étape de compactage de la poudre composite comprend un pressage isostatique à chaud, un pressage isostatique à froid, une extrusion de poudre, un laminage de poudre ou un frittage.
  16. Procédé selon la revendication 14 ou 15, dans lequel les particules de poudre composite comprennent des cristallites de métal léger dont la taille est comprise dans une gamme de 1 nm à 100 nm, de préférence de 10 nm à 100 nm, ou dans une gamme de plus de 100 nm et jusqu'à 200 nm.
  17. Procédé selon l'une des revendications 14 à 16, comprenant en outre une étape de traitement d'une poudre de métal et desdites nano-particules par alliage mécanique de manière à former ladite poudre composite.
  18. Procédé selon la revendication 17, dans lequel la poudre de métal et les nano-particules sont traitées de telle sorte que des nano-particules soient également contenues dans au moins plusieurs des cristallites.
  19. Procédé selon l'une des revendications 14 à 17, dans lequel ledit métal est un métal léger, en particulier Al, Mg ou Ti, ou un alliage comprenant un ou plusieurs de ces éléments, Cu ou un alliage de Cu.
  20. Procédé selon l'une quelconque des revendications 14 à 19, dans lequel lesdites nano-particules sont formées par des nano-tubes de carbone (CNT) prévus sous forme d'une poudre d'agglomérés de CNT entremêlés ayant une taille moyenne suffisamment grande pour permettre une manipulation aisée en raison d'une faible formation potentielle de poussière.
  21. Procédé selon la revendication 20, dans lequel au moins 95 % des agglomérés de CNT ont une taille de particule supérieure à 100 µm.
  22. Procédé selon la revendication 20 ou 21, dans lequel le diamètre moyen des agglomérés de CNT est compris entre 0,05 mm et 5 mm, de préférence entre 0,1 mm et 2 mm, et idéalement entre 0,2 mm et 1 mm.
  23. Procédé selon l'une des revendications 14 à 22, dans lequel le rapport longueur - diamètre des nano-particules, en particulier des CNT, est supérieur à 3, de préférence supérieur à 10, et idéalement supérieur à 30.
  24. Procédé selon l'une des revendications 14 à 23, dans lequel la teneur en CNT du matériau composite en poids se situe dans une gamme de 0,5 % à 10,0 %, de préférence de 2,0 % à 9,0 %, et idéalement de 3,0 % à 6,0 %.
  25. Procédé selon l'une des revendications 14 à 24, dans lequel les nano-particules sont formées par des CNT, dont au moins une fraction présente une structure de volute qui est constituée d'une ou de plusieurs couche(s) de graphite enroulée(s), chaque couche de graphite étant constituée de deux ou plus de deux couches de graphène les unes au-dessus des autres.
  26. Procédé selon l'une des revendications 14 à 25, comprenant une étape de fonctionnalisation, en particulier ayant pour but de la rendre rugueuse, d'au moins une fraction des nano-particules avant l'alliage mécanique.
  27. Procédé selon la revendication 26, dans lequel les nano-particules sont formées par des CNT à parois multiples ou à volutes multiples, et l'étape consistant à rendre rugueux est exécutée en amenant au moins la couche extérieure extrême d'au moins une partie des CNT à se casser en soumettant les CNT à une pression élevée, en particulier une pression de 5 MPa ou plus, de préférence de 7,8 MPa ou plus.
  28. Procédé selon l'une des revendications 14 à 27, dans lequel le traitement est conduit de manière à augmenter et à stabiliser la densité de dislocations des cristallites par les nano-particules suffisamment pour augmenter la dureté Vickers moyenne du matériau composite et/ou du moyen de connexion (58) qui est formé en compactant celui-ci de manière à dépasser la dureté Vickers du métal original de 40 % ou plus, de préférence de 80 % ou plus.
  29. Procédé selon l'une des revendications 14 à 27, dans lequel le traitement est conduit de manière à stabiliser les dislocations et à supprimer le grossissement des grains suffisamment pour que la dureté Vickers du moyen de connexion (58) formé en compactant la poudre composite soit supérieure à la dureté Vickers du métal original, de préférence supérieure à 80 % de la dureté Vickers de la poudre composite.
  30. Procédé selon l'une des revendications 17 à 29, dans lequel l'alliage mécanique est exécuté en utilisant un broyeur à billes (42) qui comprend une chambre de broyage (44) et des billes (50) comme éléments de broyage.
  31. Procédé selon la revendication 30, dans lequel les billes (50) sont accélérées jusqu'à une vitesse d'au moins 5 m/s, de préférence d'au moins 8 m/s, et idéalement d'au moins 11 m/s.
  32. Procédé selon la revendication 30 ou 31, dans lequel la chambre de broyage (44) est stationnaire, et les billes (50) sont accélérées par un mouvement de rotation d'un élément rotatif (46).
  33. Procédé selon la revendication 32, dans lequel un axe dudit élément rotatif (46) est orienté horizontalement.
  34. Procédé selon l'une des revendications 30 à 33, dans lequel lesdites billes (50) présentent un diamètre qui est compris entre 3 mm et 8 mm, de préférence entre 3 mm et 6 mm, et/ou sont constitués d'acier, de ZiO2 ou de ZiO2 stabilisé à l'oxyde d'yttrium.
  35. Procédé selon l'une des revendications 30 à 34, dans lequel le volume Vb occupé par les billes (50) correspond à Vb = Vc - π · (r R )2 · l ± 20 %, où Vc est le volume de la chambre de broyage (44), rR est le rayon de l'élément rotatif (46) et l est la longueur de la chambre de broyage (44) dans la direction axiale de l'élément rotatif (46).
  36. Procédé selon l'une des revendications 30 à 35, dans lequel un gaz inerte, en particulier de l'Ar, de l'He ou du N2 ou un environnement sous vide est prévu à l'intérieur de la chambre de broyage (44).
  37. Procédé selon l'une des revendications 30 à 36, dans lequel le rapport du (métal plus les nano-particules) aux billes en poids est compris entre 1:7 et 1:13.
  38. Procédé selon l'une des revendications 14 à 37, dans lequel ledit traitement de la poudre de métal et des nano-particules comprend une première et une deuxième étapes de traitement :
    lors de la première étape de traitement, la majeure partie ou la totalité du métal est traité, et
    lors de la deuxième étape, des nano-particules, en particulier des CNT, sont ajoutées et le métal et les nano-particules sont traités simultanément.
  39. Procédé selon la revendication 38, dans lequel une fraction des nano-particules est déjà ajoutée lors de la première étape de traitement afin d'éviter le collage du métal.
  40. Procédé selon l'une des revendications 38 et 39, dans lequel la première étape est conduite pendant une durée appropriée pour générer des cristallites de métal dont la taille moyenne est inférieure à 200 nm, de préférence inférieure à 100 nm, et en particulier pendant 20 à 60 minutes.
  41. Procédé selon l'une des revendications 38 à 40, dans lequel la deuxième étape est conduite pendant une durée suffisante pour entraîner une stabilisation de la micro-structure des cristallites par les nano-particules, et en particulier pendant 5 à 30 minutes.
  42. Procédé selon l'une des revendications 38 à 41, dans lequel la deuxième étape est plus courte que la première étape.
  43. Procédé selon l'une des revendications 32 à 42, dans lequel, pendant le traitement, la vitesse de rotation de l'élément rotatif (46) est augmentée et réduite de façon cyclique.
  44. Procédé selon l'une des revendications 14 à 43, dans lequel lesdites nano-particules sont formées par des CNT qui sont prévus sous la forme d'une poudre de CNT, ledit procédé comprenant en outre une étape de production de ladite poudre de CNT par dépôt catalytique de vapeur de carbone en utilisant un ou plusieurs éléments parmi un groupe comprenant l'acétylène, le méthane, l'éthane, l'éthylène, le butane, le butène, le butadiène et le benzène comme donneur de carbone.
  45. Procédé selon la revendication 44, dans lequel le catalyseur comprend deux ou plus de deux éléments d'un groupe comprenant Fe, Co, Mn, Mo et Ni.
  46. Procédé selon l'une des revendications 44 et 45, dans lequel ladite étape de production de la poudre de CNT comprend une étape de décomposition catalytique d'hydrocarbures C1-C3 réalisée entre 500°C et 1000°C en utilisant un catalyseur contenant du Mn et du Co en un rapport molaire qui est compris dans une gamme de 2:3 à 3:2.
  47. Procédé selon l'une des revendications 14 à 46, comprenant en outre une étape de formation d'une poudre de métal comme composant métallique du matériau composite par pulvérisation d'un métal ou d'un alliage liquide dans une atmosphère inerte.
  48. Procédé selon l'une des revendications 14 à 47, comprenant en outre une étape de passivation du matériau composite fini.
  49. Procédé selon la revendication 48, dans lequel le matériau composite est chargé dans une chambre de passivation et est agité dans celle-ci pendant que de l'oxygène est progressivement ajouté de manière à oxyder le matériau composite.
EP10702252A 2009-02-16 2010-01-28 Moyen de connexion, procédé de fabrication associé et connexion de matériau Revoked EP2396441B1 (fr)

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PCT/EP2009/006737 WO2010091704A1 (fr) 2009-02-16 2009-09-17 Matière composite comprenant un métal et des nanoparticules et son procédé de production
EP10702252A EP2396441B1 (fr) 2009-02-16 2010-01-28 Moyen de connexion, procédé de fabrication associé et connexion de matériau
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CN107058798A (zh) * 2016-11-08 2017-08-18 中航装甲科技有限公司 一种复合装甲材料及其制备方法

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CN111057893B (zh) * 2019-12-17 2021-06-15 西安理工大学 Gr增强的镁合金基复合材料丝材及制备方法

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN107058798A (zh) * 2016-11-08 2017-08-18 中航装甲科技有限公司 一种复合装甲材料及其制备方法

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