Investigations on micro-mechanical properties of polycrystalline Ti(C,N) and Zr(C,N) coatings

Azhari, Idriss El; García, J.; Zamanzade, Mohammad; Soldera, F.; Pauly, Christoph; Llanes, L.; Mücklich, Frank

doi:10.1016/j.actamat.2018.02.053

Cited by 47 publications

(25 citation statements)

References 74 publications

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“…In this study, Table 1 shows that there is nearly no solubility of Cl in Ti(C,N) (as the concentration is estimated about 200 ppm inside the grain) and the chlorine is rather segregated at the GBs up to 2.2 at.%. Additionally, Ti(C,N) has a finer grain size than Zr(C,N) [3] which is consistent with the role of chlorine in refinement of the microstructure [6,10,23]. Then, it is suggested that chlorine acts as an impurity, which is adsorbed on the crystal facets during film growth and segregates, yielding finally smaller grain sizes.…”

supporting

confidence: 68%

“…Regarding mechanical properties, segregation at the interfaces might reduce or enhance cohesion and bonding strength at GBs [2]. Within this context, the present study is a sequel to a recently published work [3], in which micromechanical properties of MT-CVD Ti(C,N) and Zr(C,N) coatings were studied by means of micropillar compression. A relevant finding of such work was that the brittle behavior of Ti(C,N) is dominated by low cohesive strength along the grain boundaries and pure columnar crack propagation, while Zr(C,N) coatings attested of a better cohesive strength and inter/transgranular failure.…”

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confidence: 99%

“…Comparison of the micromechanical properties for both coating from microcompression tests is not an easy task [3], taking into account, beside their similarities, their differences in grain size, in the transition metal phase and microstructure. Nevertheless, the property that is contrasted in this study is the specific inter-columnar cracking for Ti(C,N) which can be caused either by the reduced dislocation activation at room temperature or lower cohesive strength at the GBs [3]. The APT investigations have provided support to the previous speculations about segregation of impurities as a potential cause of the GB brittleness for Ti(C,N), as given by its specific intergranular fracture during microcompression tests (Fig.…”

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confidence: 99%

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Atom Probe Tomography investigations on grain boundary segregation in polycrystalline Ti(C,N) and Zr(C,N) CVD coatings

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Atom Probe Tomography (APT) was used to obtain a direct evidence of Chlorine segregation and Cobalt diffusion at the grain boundaries (GBs) of polycrystalline coatings deposited by moderate temperature chemical vapor deposition (MT-CVD) on a WC-Co cemented carbide substrate. Reasons behind segregations are discussed, and its effects are correlated to the micromechanical properties of Ti(C,N) and Zr(C,N). It is concluded that chlorine segregation is a relevant factor for explaining the low cohesive strength at the GBs of Ti(C,N) leading to intergranular failure during micro-compression testing, while its absence in Zr(C,N) along with Co diffusion contribute to grain boundary strengthening.

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confidence: 99%

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Atom Probe Tomography investigations on grain boundary segregation in polycrystalline Ti(C,N) and Zr(C,N) CVD coatings

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“…2. Also, the deformation and micromechanical response of Ti(C,N) and Zr(C,N) micro pillars have been shown to be linear elastic with a high yield strength of 14 GPa [48]. Therefore, Hook's law should be sufficient to study the response of the nitrite systems.…”

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confidence: 99%

Exploration of the Microstructure Space in Tialzrn Ultra-Hard Nanostructured Coatings

2018

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Ti 1−x−y Al x Zr y N cubic alloys within the 25-70% Al composition range have high age-hardening capabilities due to metastable phase transition pathways at high temperatures. They are thus ideal candidates for ultra-hard nano-coating materials. There is growing evidence that this effect is associated with the elasto-chemical field-induced phase separation into compositionally-segregated nanocrystaline nitride phases. Here, we studied the microstructural evolution in this pseudo-ternary system within spinodal regions at 1200 ○ C by using an elasto-chemical phase field model. Our simulations indicate that elastic interactions between nitride nanodomains greatly affect not only the morphology of the microstructure but also the local chemical phase equilibria. In Al-rich regions of the composition space we further observe the onset of the transformation of AlN-rich phases into their equilibrium wurtzite crystal structure. This work points to a wide palette of microstructures potentially accessible to these nitride systems and their tailoring is likely to result in significant improvements in the performance of transition metal nitride-based coating materials.Nowadays, many applications demand coatings capable of withstanding increasingly harsh operating conditions. The need to improve the performance of these coatings has lead to considerable efforts towards understanding the factors that control their microstructural evolution. Better understanding in these systems has produced a wide range of strategies to tailor their (nano)structrual features and thus optimize their performance. It is now known, for example, that multi-component alloying via addition of Cr or Zr in TMNs (Ti 1−x−y Al x Cr y N and Ti 1−x−y Al x Zr y N) changes the relative stability of the cubic and hexagonal phases and ultimately results in significant performance improvements [13,14]. Recently, Lind et al., showed theoretically that the cubic-to-wurtzite phase transformation occurs at higher temperatures compared to TiAlN by addition of Cr [15]. Yang et al. [14] investigated the effect of Zr additions on the structure and properties of TiAlN coatings and found that Zr resulted in an increased in hardness and improved oxidation resistance. On the other hand, Yalamanchi et al. [16] proposed interface energy minimization by growth of semi-coherent multilayer structures of TiN/ZrAlN that can offer both Koehler and coherency hardening mechanisms. Furthermore, recent studies report that the cutting performance of high-Al containing Zr-Al-N coatings is comparable to that of commercial grade Ti-Al-N coatings [17]. As interest in the use of Zr as a modifier of TiAlN coatings has increased, a number of theoretical and experimental investigations have focused on the phase stability and phase-decomposition behavior of Zr-containing TMN. Holec et al. [18] investigated theoretically-and verified experimentally-the phase stability of Zr 1−x Al x N and Hf 1−x Al x N alloys in comparison with the Ti 1−x Al x N system and found that Zr (and Hf) contributed to a ...

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“…Zirconium carbonitride (Zr(C,N)) is an alternative coating material to Ti(C,N), which presents excellent characteristics such as high hardness, elevated melting temperature and comparatively high electrical and thermal conductivities (IVASHENKO et al 2009, EL AZHARI et al, 2018.…”

Section: )mentioning

confidence: 99%

>i<In situ>/i< study of residual stress evolution in Zr(C,N)/α-Al>sub<2>/sub<O>sub<3>/sub< and Zr(C,N)/κ-Al>sub<2>/sub<O>sub<3>/sub< CVD multilayers during thermal cycling

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The present work analyses the residual stresses of thin films in coated cutting tools used in milling applications. Typical wear limitation is the formation of comb cracks, which lead to chipping and failure of the tools. The resistance to comb cracks depends on the ability of the coated tools to reduce the formation of thermo-mechanical cracks, which are originated in the coating and propagate into the carbide. By adjusting the residual stress condition of the coating/carbide substrate (which depends among others on the coefficient of thermal expansion of the layers, the processing method as well as the pre-or post-treatment) the resistance to comb crack failure can be improved. The Ti(C,N)/α-Al2O3 system is the most common used in the industry. Recently, an alternative coating with improved comb crack resistance based on Zr(C,N)/α-Al2O3 has been developed. In some applications the use of κ-Al2O3 is of advantage. In this work the residual stress analyses of Zr(C,N)/κ-Al2O3 and Zr(C,N)/α-Al2O3 coatings produced by (CVD) were carried out using Energy Dispersive X-ray diffraction. Furthermore, the residual stresses were analyzed "in situ" at cycling temperature conditions ranging from RT to 800 o C in order to verify the influence of the different systems on the residual stress evolution and behaviour of the composites. In addition, the influence of microtop-blasting on the residual stress of the thin films was investigated. It was observed that both the Zr(C,N)/κ-Al2O3 and Zr(C,N)/α-Al2O3 systems present similar residual stress cycling behaviour. The effect of the top-blasting process is confined to the α-Al2O3 layer, which develops high compressive residual stresses. The results of this work provides valuable information for the design of novel coating systems with enhanced resistance to comb cracks.

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Investigations on micro-mechanical properties of polycrystalline Ti(C,N) and Zr(C,N) coatings

Cited by 47 publications

References 74 publications

Atom Probe Tomography investigations on grain boundary segregation in polycrystalline Ti(C,N) and Zr(C,N) CVD coatings

Atom Probe Tomography investigations on grain boundary segregation in polycrystalline Ti(C,N) and Zr(C,N) CVD coatings

Exploration of the Microstructure Space in Tialzrn Ultra-Hard Nanostructured Coatings

>i<In situ>/i< study of residual stress evolution in Zr(C,N)/α-Al>sub<2>/sub<O>sub<3>/sub< and Zr(C,N)/κ-Al>sub<2>/sub<O>sub<3>/sub< CVD multilayers during thermal cycling

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Investigations on micro-mechanical properties of polycrystalline Ti(C,N) and Zr(C,N) coatings

Cited by 47 publications

References 74 publications

Atom Probe Tomography investigations on grain boundary segregation in polycrystalline Ti(C,N) and Zr(C,N) CVD coatings

Atom Probe Tomography investigations on grain boundary segregation in polycrystalline Ti(C,N) and Zr(C,N) CVD coatings

Exploration of the Microstructure Space in Tialzrn Ultra-Hard Nanostructured Coatings

>i<In situ>/i< study of residual stress evolution in Zr(C,N)/&#945;-Al>sub<2>/sub<O>sub<3>/sub< and Zr(C,N)/&#954;-Al>sub<2>/sub<O>sub<3>/sub< CVD multilayers during thermal cycling

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>i<In situ>/i< study of residual stress evolution in Zr(C,N)/α-Al>sub<2>/sub<O>sub<3>/sub< and Zr(C,N)/κ-Al>sub<2>/sub<O>sub<3>/sub< CVD multilayers during thermal cycling