WO2010054619A2 - Corps composite en cuivre ou en un alliage de cuivre avec des nanotubes de carbone incrustés et procédé de fabrication d'un tel corps composite ainsi qu'utilisation du corps composite - Google Patents

Corps composite en cuivre ou en un alliage de cuivre avec des nanotubes de carbone incrustés et procédé de fabrication d'un tel corps composite ainsi qu'utilisation du corps composite Download PDF

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Publication number
WO2010054619A2
WO2010054619A2 PCT/DE2009/001508 DE2009001508W WO2010054619A2 WO 2010054619 A2 WO2010054619 A2 WO 2010054619A2 DE 2009001508 W DE2009001508 W DE 2009001508W WO 2010054619 A2 WO2010054619 A2 WO 2010054619A2
Authority
WO
WIPO (PCT)
Prior art keywords
copper
cnts
composite body
production
carbon nanotubes
Prior art date
Application number
PCT/DE2009/001508
Other languages
German (de)
English (en)
Other versions
WO2010054619A3 (fr
Inventor
Carsten Glanz
Tanvir Mahmud
Sheikh Minhaz Uddin
Christoph Volkmer
Helmut HÖLLER
Ulrich Wienecke
Original Assignee
BÖGRA Technologie GmbH
Fraunhofer Gesellschaft zur Förderung der angewandten Forschung e.V.
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 BÖGRA Technologie GmbH, Fraunhofer Gesellschaft zur Förderung der angewandten Forschung e.V. filed Critical BÖGRA Technologie GmbH
Priority to EP09801134A priority Critical patent/EP2347020A2/fr
Publication of WO2010054619A2 publication Critical patent/WO2010054619A2/fr
Publication of WO2010054619A3 publication Critical patent/WO2010054619A3/fr

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C26/00—Alloys containing diamond or cubic or wurtzitic boron nitride, fullerenes or carbon nanotubes
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
    • C22C32/0084—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ carbon or graphite as the main non-metallic constituent
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C33/00—Parts of bearings; Special methods for making bearings or parts thereof
    • F16C33/02—Parts of sliding-contact bearings
    • F16C33/04—Brasses; Bushes; Linings
    • F16C33/06—Sliding surface mainly made of metal
    • F16C33/12—Structural composition; Use of special materials or surface treatments, e.g. for rust-proofing
    • F16C33/121—Use of special materials
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C26/00—Alloys containing diamond or cubic or wurtzitic boron nitride, fullerenes or carbon nanotubes
    • C22C2026/002—Carbon nanotubes
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C2202/00—Solid materials defined by their properties
    • F16C2202/30—Electric properties; Magnetic properties
    • F16C2202/32—Conductivity
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C2204/00—Metallic materials; Alloys
    • F16C2204/10—Alloys based on copper
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C2220/00—Shaping
    • F16C2220/20—Shaping by sintering pulverised material, e.g. powder metallurgy
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C2240/00—Specified values or numerical ranges of parameters; Relations between them
    • F16C2240/40—Linear dimensions, e.g. length, radius, thickness, gap
    • F16C2240/60—Thickness, e.g. thickness of coatings
    • F16C2240/64—Thickness, e.g. thickness of coatings in the nanometer range
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01H—ELECTRIC SWITCHES; RELAYS; SELECTORS; EMERGENCY PROTECTIVE DEVICES
    • H01H2300/00—Orthogonal indexing scheme relating to electric switches, relays, selectors or emergency protective devices covered by H01H
    • H01H2300/036—Application nanoparticles, e.g. nanotubes, integrated in switch components, e.g. contacts, the switch itself being clearly of a different scale, e.g. greater than nanoscale

Definitions

  • Composite body of copper or a copper alloy with intercalated carbon nanotubes and method of making such a body and use of the composite body
  • Carbon nanotubes are a modification of carbon that has a tubular structure, with the ends being open or closed. Closed CNTs occur as a single-walled single-walled nanotube (SWNT), double-walled nanotube (DWNT) or multi-walled nanotube (MWNT). In the case of a two- or multi-walled construction, the carbon tubes are arranged concentrically.
  • CNTs are characterized by high electrical and thermal conductivity, high ductility and high yield strengths at low density.
  • CNTs have a high thermal stability and an extremely high thermal conductivity, which can be up to 6,000 W / mK with defect-free SWNTs.
  • the high binding forces of the sp 2 bonds of individual carbon atoms in SWNTs lead to a high modulus of elasticity of 542 GPa and a tensile strength of 65 GPa at a density of only 1.4 g / cm 3 .
  • Deviations result from the dependence of the properties on the diameter and the structure of the CNTs.
  • MWNTs with a density of 1.8 g / cm 3 have a modulus of elasticity of 1260 GPa.
  • CNTs Due to the relatively long length compared to the small diameter, CNTs have a shape design which promotes electrical conductivity since electrons can not be scattered at edges of the crystal lattice. CNTs are either conductive or semiconducting.
  • US 2008/0093577 A1 also proposes a method for producing a metal-carbon nanotube composite body in which a quantity of carbon nanotubes is mixed with molten metal and this mixture is then to be solidified.
  • the metal matrix consists of zinc, silver, gold, iron, aluminum, copper, tungsten, cobalt, chromium, nickel, platinum and alloys thereof.
  • the carbon nanotubes should be used in an amount of up to 20% by weight of the composite body present.
  • the production of such composites via a melt fails in practice because the specifically much lighter carbon nanotubes float in the melt, resulting in a porous composite body with low tensile strength. Even stirrers used during mixing of the carbon nanotubes with the melt did not give satisfactory results.
  • a method in which a powdered metal mixture is mixed with carbon nanotubes and then sintered and cooled.
  • the powder metallurgical path with final sintering and cooling permits a largely homogeneous distribution of the carbon nanotubes without their segregation, however, the CNTs used with copper or copper alloys, in particular bronzes or brass, in some cases a poor wetting behavior due to different surface tensions, partly CNTs are thermally unstable at high sintering temperatures, in some cases undesirable oxidation processes also occurred.
  • This composite body has a CNT content of between 0.1% by weight and 1.5% by weight, preferably between 0.1% by weight and 1% by weight.
  • the CNTs are at least largely homogeneously distributed in the composite body by sintering or cooling a melt. A deviation of the percentage content of the carbon nanotube to higher values leads to significantly worse mechanical and poorer electrical properties, in particular, the hardness of the composite body decreases significantly.
  • the known in principle according to the prior art ways namely the powder metallurgical path with subsequent sintering or hot isostatic pressing or the melt metallurgical path, in which a molten metal of copper or a copper alloy, in particular bronze or brass, with CNT Contents of 0.1 wt.% To 1, 5 wt.% Is produced in an induction crucible furnace and this is finally solidified by cooling.
  • a copper or copper alloy powder having a particle size of 0.1 ⁇ m to 100 ⁇ m, preferably 0.5 ⁇ m to 50 ⁇ m with 0.1% by weight to 1.5% by weight of carbon nanotubes, preferably 0.1 Wt.% To 1 wt.% Mixed CNTs, pre-pressed and then at a pressure between 5 MPa and 200 MPa, preferably at 30 MPa to 50 MPa, at temperatures between 450 ° C to 900 0 C, preferably 750 0 C and 800 0 0 C sintered or hot-isostatically pressed.
  • the sintering treatment or the hot pressing at least from a temperature above 600 0 C is carried out in an inert gas atmosphere.
  • a copper or a copper alloy which is melted to a temperature above the melting point of the copper or copper alloy and together with the CNTs in an amount of 0.1 wt.% To 1, 5 wt.%, Preferably 0, 1 wt.% To 1 wt.% Are mixed.
  • the uniform distribution of the CNTs in the melt is achieved by heating in an induction crucible furnace, in which the liquid is guided in an ascending and descending motion, in which it leads to an intensive mixing of the CNTs in the melt. Separation of CNTs and liquid metals is prevented by rapid cooling.
  • the preferably selected cooling rate is between 10 K / s and 1,000 K / s.
  • the cooling can be carried out according to a further embodiment of the invention by moving fluids, liquid gases, in particular nitrogen, or liquid baths, each ensuring that the CNTs do not float during solidification.
  • a composite body by powder metallurgy with final sintering, which has a high proportion of CNTs, and to melt this sintered body together with further Cu or Cu alloy bodies or powders in an induction crucible furnace.
  • the melt with the CNTs is finally either solidified at the aforementioned rapid cooling rate or cooled at room temperature without additional cooling acceleration.
  • a solid forms which has primarily solidified areas which are CNT-free and areas in which CNTs are contained.
  • the primary solidified areas are embedded in the secondary solidified areas. The solidification follows the principle of dendrite formation and the congealed residual melt.
  • the components according to the invention can be used in particular for electrical connections in the low-voltage range up to high-current applications up to 5,000 amps as a bearing component or as a sliding material or taking advantage of their higher temperature or pressure resistance as a component in high-temperature systems or high-pressure systems.
  • the milled mixture of Cu or the alloys and the CNTs was hot pressed in different batches at sintering temperatures between 540 ° C and 950 ° C, especially at 750 ° C and 800 ° C at pressures between 30 MPa to 40 MPa and then cooled. Part of the heating, sintering and cooling were carried out under an argon inert gas atmosphere.
  • the results subsequently found on the composite bodies show that the substrate bodies with a CNT content of 10% had a completely insufficient theoretical density, which in one case even led to the fracture of the sintered body. Also, the porosity at a CNT content of 2 wt.% was significantly greater than at lower CNT contents.
  • the hardness of copper is usually reported in the literature as 35 HB.
  • the hardness of the finished sintered body can be increased to above 59 HB.
  • composites with a proportion of 1% by weight of CNT still have a comparatively high hardness of about 55 HB.
  • Significantly worse values were obtained by sintering composites containing a content of 2 wt.% Or 4 wt.% CNT.
  • the Brinell hardness of a Cu matrix was increased from 56.5 HB to 81.3 HB upon incorporation of 0.5 wt% CNTs.
  • a Brinell hardness of 71.9 HB could be achieved using 0.5 wt.% CNT.
  • the results found show that a hardness increase was uniformly observed over a sintered Cu body using a starting mixture containing 0.5 wt% CNT.
  • the hardness continuously decreased at higher CNT contents of 1 wt% to 1.5 wt%, but was still satisfactory, whereas composites containing 2 wt% CNTs or more had inferior hardness values.
  • the measurement results according to FIG. 2 have been obtained with CNTs of the type MWNTs.
  • the electrical conductivity is essentially carried by the outermost nanotube, while it may degrade by interactions with the inner coaxial nanotubes. It can be expected that the use of SWNTs improves the electrical conductivity and preserves it compared to pure metals, while the current density can be significantly increased without damaging the composite body.
  • SWNTs can maintain current densities of 109 A / cm 2 at most , which is an increase in current density of 3 orders of magnitude over pure copper.
  • the CNTs in the composite body by forming processes such as rolling, extrusion or drawing targeted, which can increase the electrical conductivity and strength again.
  • a uniform increase in electrical conductivity is observed, provided that the CNT contents in the alloy are increased to 0.1% by weight.
  • increases in conductivity are observed, at 10 ⁇ m from 5.2 to 6.2 MS / m.
  • Fig. 5 and 6 show the dependence of the electrical conductivity at different CNT contents. Uniformly, both with starting powder particle sizes of 3 ⁇ m and also at 45 ⁇ m, the greatest conductivity is to be measured when using CNT contents of 0.1% by weight. An improved conductivity compared to the reference value of 5.2 MS / m results in powder sizes of 45 microns even at CNT contents of 0.5%, whereas at smaller particle sizes a slight conductivity deterioration is observed (see Fig. 6).
  • composite bodies made of copper and copper alloys with incorporated carbon nanotubes were produced by means of a melting process.
  • CNT contents of 20 wt.% can be set, since these composites are melted together with pure metals in an induction crucible furnace, the amount of metal or metal alloy to be added being chosen to be as large as desired CNT content of not more than 1.5% by weight, preferably not more than 1% by weight, based on the total amount.
  • a first row are copper powders having an average grain size of less than 45 microns with 1 wt.% MWNTs (9.54 ⁇ 2.69 nm inside diameter, 19.21 ⁇ 4.03 nm outside diameter and 0.5 .mu.m to 200 .mu.m in length ) Dispersed in a ball mill for 2 hours. Subsequently, the milled and mixed powder was heated in a graphite crucible, depending on the charge for 1 to 2 hours at a temperature of 1200 ° C in inert gas, namely an argon atmosphere in the oven.
  • a melt-metallurgical production with subsequent rapid cooling in which, for example, the crucible containing the melt is immersed in liquid nitrogen, results in the relative uniform distribution of the CNTs set in the crucible furnace being "frozen.”
  • Such bodies have a low residual porosity for bearing components can be exploited such that the pores serve as "lubrication chambers" (lubricant reservoir).
  • the bodies produced by melt metallurgy have an increased hardness compared to pure copper or copper alloy bodies.
  • the residual porosity can be reduced by rolling or pressing the relevant component.
  • CNTs of type MWNTs were ground in a planetary mill with ethanol for two hours and then dried after milling (until complete removal of the ethanol). Then, a quantity of CNTs was added to a copper melt corresponding to 0.5% by weight. The melt was in an induction crucible furnace, so that the CNTs were distributed substantially homogeneously by the bath movement.
  • the melt After sufficient mixing of the CNTs in the melt, the melt has been cooled in air. Unlike the rapid cooling, different areas were formed, referred to below as two distinct phases be designated. One phase solidifies earlier and consists of pure copper, whereas the other phase contains a copper matrix interspersed with CNTs. The different phases are shown in FIGS. 7 and 8, wherein the Cu phase regions appear bright and the phase containing CNTs in the Cu matrix becomes dark or with black dots.
  • the hardness of the body thus produced was measured to be 54.05 HB, which is a significant increase over the reference value of a pure Cu body with 35 HB.
  • MWNTS 0.5% by weight MWNTS are ground with copper powder having a particle size of less than 45 ⁇ m. This powder / CNT mixture was added with stirring for 15 minutes in a copper melt, which was then cooled in air. Even with this solidified composite, a Brillell hardness of 47 HB, ie a significant increase compared to a pure Cu body, could be determined.
  • the mechanical properties of the composites depend to a considerable extent on the homogeneous distribution of the CNTs and the good bonding of the CNTs to the matrix material.
  • composite bodies with SWNT deposits are preferably used.
  • the proportion of CNTs in the composite body should be limited to 1% by weight.
  • the porosity which increases with higher CNT contents, can be used to make the pores serve as lubricant reservoirs in bearing components.

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

Abstract

L'invention concerne un corps composite en cuivre ou en un alliage de cuivre avec des nanotubes de carbone incrustés, sur un procédé de fabrication d'un tel corps ainsi que sur l'utilisation de ce corps. Selon l'invention, la fraction en nanotubes de carbone se situe entre 0,1 % en poids et 1,5 % en poids. Le corps composite est apte à être obtenu par frittage ou par refroidissement d'une masse métallique fondue contenant des nanotubes de carbone dans une répartition au moins largement homogène. De préférence, le corps composite est utilisé comme constituant pour des raccordements électriques ou dans des installations haute température ou des installation haute pression.
PCT/DE2009/001508 2008-11-11 2009-10-28 Corps composite en cuivre ou en un alliage de cuivre avec des nanotubes de carbone incrustés et procédé de fabrication d'un tel corps composite ainsi qu'utilisation du corps composite WO2010054619A2 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
EP09801134A EP2347020A2 (fr) 2008-11-11 2009-10-28 Corps composite en cuivre ou en un alliage de cuivre avec des nanotubes de carbone incrustés et procédé de fabrication d'un tel corps composite ainsi qu'utilisation du corps composite

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102008056750A DE102008056750A1 (de) 2008-11-11 2008-11-11 Verbundkörper aus Kupfer oder einer Kupferlegierung mit eingelagertem Carbon Nanotubes und Verfahren zur Herstellung eines solchen Körpers sowie Verwendung des Verbundkörpers
DE102008056750.7 2008-11-11

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WO2010054619A2 true WO2010054619A2 (fr) 2010-05-20
WO2010054619A3 WO2010054619A3 (fr) 2010-07-22

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EP (1) EP2347020A2 (fr)
DE (1) DE102008056750A1 (fr)
WO (1) WO2010054619A2 (fr)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB2497725A (en) * 2011-12-08 2013-06-26 Mahle Int Gmbh A sliding bearing having a composite layer
GB2509173A (en) * 2012-12-24 2014-06-25 Mahle Int Gmbh A sliding bearing

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DE102013202123C5 (de) * 2013-02-08 2018-01-04 Ks Gleitlager Gmbh Gleitlagerverbundwerkstoff und hieraus hergestelltes Gleitlagerelement
CN103480837A (zh) * 2013-10-11 2014-01-01 武汉理工大学 高导热CNT-Cu热用复合材料的制备方法
EP3878986A1 (fr) 2020-03-12 2021-09-15 Heraeus Deutschland GmbH & Co KG Fil et ruban avec nanotubes de bornitrure pour contacts électriques

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US20080093577A1 (en) 2006-06-21 2008-04-24 Khraishi Tariq A Metal-carbon nanotube composites for enhanced thermal conductivity for demanding or critical applications

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Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB2497725A (en) * 2011-12-08 2013-06-26 Mahle Int Gmbh A sliding bearing having a composite layer
US9453532B2 (en) 2011-12-08 2016-09-27 Mahle International Gmbh Sliding bearing
GB2509173A (en) * 2012-12-24 2014-06-25 Mahle Int Gmbh A sliding bearing
US10473160B2 (en) 2012-12-24 2019-11-12 Mahle International Gmbh Sliding bearing with lining layer comprising carbon nanostructures

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Publication number Publication date
WO2010054619A3 (fr) 2010-07-22
DE102008056750A1 (de) 2010-05-12
EP2347020A2 (fr) 2011-07-27

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