Microstructure and tribological properties of magnetron sputtered nc-TiC/a-C nanocomposite

Zhang, Sam; Bui, X.L.; Jiang, Jiaren; Li, Xiaomin

doi:10.1016/j.surfcoat.2004.10.041

Cited by 118 publications

(44 citation statements)

References 23 publications

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“…An increase in I(D)/I(G) ratio and G peak position concomitantly with W or Ti concentration has been observed 15,20 . Abrasonis et al 21 reported detailed about the effect of Ni-doping and substrate temperature during growth of a-C:Ni films, but the Ni concentration was fixed to 30 %.…”

Section: Introductionmentioning

confidence: 92%

Influence of doping (Ti, V, Zr, W) and annealing on the sp2 carbon structure of amorphous carbon films

Adelhelm

Balden

Rinke

et al. 2009

Journal of Applied Physics

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The influence of the transition metal (Ti, V, Zr, W) doping on the carbon matrix nanostructuring during the thin film growth and subsequent annealing is investigated. Pure and metal-doped amorphous carbon films (a-C, a-C:Me) were deposited at room temperature by non-reactive magnetron sputtering. The carbon structure of as-deposited and post-annealed (up to 1300 K) samples was analyzed by X-ray diffraction (XRD) and Raman spectroscopy.The existence of graphene-like regions in a-C is concluded from a (10) diffraction peak. A comparison of the XRD and Raman results suggests that XRD probes only the small amount of 2-3 nm large graphene-like regions, whereas the majority of the sp 2 phase is present in smaller distorted aromatic clusters which are probed only by Raman spectroscopy. Annealing leads to an increase of the graphene size and the aromatic cluster size. During the carbon film growth the addition of metals enhances ordering of sp 2 carbon in sixfold aromatic clusters compared to a-C, Ti and Zr showing the strongest effect, W the lowest. This order qualitatively corresponds with the catalytic activity of the respective carbides found during graphitization of carbide-doped graphites published in the literature. With annealing, carbide crystallite formation and growth occurs in a-C:Me films, which destroys the initial carbon structure, reduces the size of the initially formed aromatic clusters and the differences in carbon structure introduced by different dopants. For high annealing temperatures the carbon structure of a-C:Me films is similar to that of a-C, and is determined only by the annealing temperature.2

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Section: Introductionmentioning

confidence: 92%

Influence of doping (Ti, V, Zr, W) and annealing on the sp2 carbon structure of amorphous carbon films

Adelhelm

Balden

Rinke

et al. 2009

Journal of Applied Physics

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“…Figure 4 shows the C1s peaks for Coatings 1-4. The C1s peaks at 281.8 eV and 284.6 eV corresponds to C-Ti and C-C bonds (free carbon), respectively [33,35,36]. Between these contributions C-Si bonds, at 282.5 eV, are expected.…”

Section: The Influence Of the Target-to-substrate Distance And Pressurementioning

confidence: 99%

High-rate deposition of amorphous and nanocomposite Ti–Si–C multifunctional coatings

Lauridsen

Eklund

Joelsson

et al. 2010

Surface and Coatings Technology

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2 transport of the species. Increased target-to-substrate distance from 2 cm to 8 cm resulted in a higher carbon-to-titanium ratio in the coatings than for the Ti 3 SiC 2 compound target, due to different gas-phase scattering properties between the sputtered species. The coatings microstructure could be modified from nanocrystalline to predominantly amorphous by changing the pressure and target-to-substrate conditions to 4 mTorr and 2 cm, respectively. A decreased pressure from 10 mTorr to 4 or 2 mTorr at a target-tosubstrate distance of 2 cm decreased the deposition rate up to a factor of ~7 as explained by resputtering and an increase in the plasma sheath thickness. The coatings exhibited electrical resistivity in the range 160-800 µΩcm, contact resistance down to 0.8 mΩ at a contact force of 40 N, and nanoindentation hardness in the range 6-38 GPa.

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“…By tuning the TiC grain size and fraction of a-C matrix, the properties can be controlled as the matrix phase increases the toughness of the material and softens the nanocomposite compared to pure carbides but also provides a source of solid lubricant. [2][3][4][5][6][7][8] The nc-TiC has a NaCl crystal structure and its bonding is a mixture of covalent, ionic and metallic bonds where the covalent contribution consists of Ti e g -C 2p ͑pd ͒, Ti t 2g -C 2p ͑pd ͒, and Ti-Ti t 2g ͑dd ͒ bonds, 9 which are all found in the valence band.…”

Section: Introductionmentioning

confidence: 99%

Electronic structure and chemical bonding of nanocrystalline-TiC/amorphous-C nanocomposites

et al. 2009

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The electronic structure of nanocrystalline ͑nc-͒ TiC/amorphous C nanocomposites has been investigated by soft x-ray absorption and emission spectroscopy. The measured spectra at the Ti 2p and C 1s thresholds of the nanocomposites are compared to those of Ti metal and amorphous C. The corresponding intensities of the electronic states for the valence and conduction bands in the nanocomposites are shown to strongly depend on the TiC carbide grain size. An increased charge transfer between the Ti 3d-e g states and the C 2p states has been identified as the grain size decreases, causing an increased ionicity of the TiC nanocrystallites. It is suggested that the charge transfer occurs at the interface between the nanocrystalline-TiC and the amorphous-C matrix and represents an interface bonding which may be essential for the understanding of the properties of nc-TiC/amorphous C and similar nanocomposites.

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Microstructure and tribological properties of magnetron sputtered nc-TiC/a-C nanocomposite

Cited by 118 publications

References 23 publications

Influence of doping (Ti, V, Zr, W) and annealing on the sp2 carbon structure of amorphous carbon films

Influence of doping (Ti, V, Zr, W) and annealing on the sp2 carbon structure of amorphous carbon films

High-rate deposition of amorphous and nanocomposite Ti–Si–C multifunctional coatings

Electronic structure and chemical bonding of nanocrystalline-TiC/amorphous-C nanocomposites

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