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Relevant bibliographies by topics / Carbide and nitride precipitation

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Academic literature on the topic 'Carbide and nitride precipitation'

Author: Grafiati

Published: 4 June 2021

Last updated: 1 February 2022

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Journal articles on the topic "Carbide and nitride precipitation"

1

Mitchell,, A., S. L. Cockcroft,, C. E. Schvezov,, A. J. Schmalz,, J. Ν. Loquet,, and J. Fernihough,. "Primary Carbide and Nitride Precipitation in Superalloys Containing Niobium." High Temperature Materials and Processes 15, no. 1-2 (January 1996): 27–40. http://dx.doi.org/10.1515/htmp.1996.15.1-2.27.

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Salem, Islam, Mohamed Kamal El-Fawkhry, Ahmed A. Abdel-Khalek, M. H. Khedr, and Taha Mattar. "Exo-Inoculant Modification of Secondary Phase Precipitation in H13 Tool Steel." Key Engineering Materials 835 (March 2020): 13–21. http://dx.doi.org/10.4028/www.scientific.net/kem.835.13.

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Secondary phase carbides in term of type and morphology are considered as the most challenge facing the applications of hot work tool steel. AISI H13 tool steel is one of the most applicable hot work tool steel grades. M23C6, M6C and MC are the common secondary carbides that are forming throughout the martensite matrix of H13 tool steel. In this research, nanoinoculant silicon nitride was added to the molten H13 tool steel to act as an inoculant for the secondary carbide categories through ladle treatment process. By using OM and SEM, it was observed that nanoinoculant has the great impact in the nucleation of secondary carbides into fine shape, in particular M23C6 type. In addition, mechanical tests proved that the nucleation of secondary carbides promotes the mechanical properties of hot work H13 tool steel to its ultimate. Impact toughness of the inoculated H13 tool steel was observed with higher value than that was done at the ordinary H13 tool steel. At the meantime, wear resistance of inoculated H13 tool steel was multiplied two times higher than as delivered H13 tool steel.

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Zhang, Yaocheng, Zhuguo Li, Pulin Nie, and Yixiong Wu. "Carbide and nitride precipitation during laser cladding of Inconel 718 alloy coatings." Optics & Laser Technology 52 (November 2013): 30–36. http://dx.doi.org/10.1016/j.optlastec.2013.03.023.

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Peng, Jun, Liang Niu, Yong Guo, Li Xia Liu, and Sheng Li An. "Effect of V, Ti, and Ce on Structure and Performance of NM400." Advanced Materials Research 1094 (March 2015): 311–15. http://dx.doi.org/10.4028/www.scientific.net/amr.1094.311.

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To improve the performance of NM400, V, Ti and Ce were added in NM400. The effect of alloy on grain size, precipitation, hardness and toughness was studied. The result shows that V and Ti can improve the performance by grain refiner and dispersion-strengthening. By further adding Ce, the size of grain and precipitations of V and Ti is significantly reduced, the solid solution quantity of V and Ti and the amount of precipitation are increased, and the precipitation shape transforms from cube to sphere. Therefore the hardness and toughness of steel are greatly improved. In this study, 0.2% V and 0.2% Ti were added into NM400. As a result, the precipitation of V and Ti, in form of carbide and nitride, was the smallest and dispersed, and the grain size was the smallest, which leaded to the best performance. The conclusion is that, to ameliorate the performance of NM400, the optimal additive amount of V and Ti is 0.2% no matter whether adding Ce or not.

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Padilha, Angelo Fernando, D. J. M. Aguiar, and R. L. Plaut. "Duplex Stainless Steels: A Dozen of Significant Phase Transformations." Defect and Diffusion Forum 322 (March 2012): 163–74. http://dx.doi.org/10.4028/www.scientific.net/ddf.322.163.

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During processing or use, duplex stainless steels are subject to a great number of significant phase transformations, such as solidification, partial ferrite transformation to austenite, ferrite eutectoid decomposition to sigma phase plus austenite, chi phase precipitation, chromium carbide precipitation, chromium nitride precipitation, ferrite spinodal decomposition, phase dissolution during solution annealing, forming of two types (epsilon and alpha prime) of strain induced martensite, martensite reversion to austenite, ferrite and austenite recrystallization. This paper summarizes the phase transformations that occur (individually or combined) in duplex stainless steels and presents some new results.

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Ducki, Kazimierz J., Jacek Mendala, and Lilianna Wojtynek. "TEM and X-Ray Examinations of Intermetallic Phases and Carbides Precipitation in an Fe-Ni Superalloy during Prolonged Ageing." Solid State Phenomena 212 (December 2013): 15–20. http://dx.doi.org/10.4028/www.scientific.net/ssp.212.15.

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The influence of prolonged ageing on the precipitation process of the secondary phases in an Fe-Ni superalloy of A-286 type has been studied. The samples were subjected to a solution heat treatment at 980°C for 2 h and water quenched, and then aged at temperatures of 715, 750 and 780°C at holding times from 0.5 to 500 h. Structural investigations were conducted using TEM and X-ray diffraction methods. The X-ray phase analyses performed on the isolates were obtained by anodic dissolution of the solid samples. After solution heat treatment the alloy has the structure of twinned austenite with a small amount of undissolved precipitates, such as carbide TiC, carbonitride TiC0.3N0.7, nitride TiN0.3, carbosulfide Ti4C2S2, Laves phase Ni2Si, and boride MoB. The application of ageing causes precipitation processes of γ-Ni3(Al,Ti), G (Ni16Ti6Si7), η (Ni3Ti), β (NiTi) and σ (Cr0.46Mo0.40Si0.14) intermetallic phases, as well as the carbide M23C6. It was found that the main phase precipitating during alloy ageing was the γ intermetallic phase.

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Kokawa, Hiroyuki, W. Z. Jin, Zhan Jie Wang, M. Michiuchi, Yutaka S. Sato, Wei Dong, and Yasuyuki Katada. "Grain Boundary Engineering of High-Nitrogen Austenitic Stainless Steel." Materials Science Forum 539-543 (March 2007): 4962–67. http://dx.doi.org/10.4028/www.scientific.net/msf.539-543.4962.

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Large amount of nitrogen addition into an austenitic stainless steel can improve the mechanical properties and corrosion resistance remarkably as far as the nitrogen is in solid solution. However, once the nitrogen precipitates as nitride, it results in deteriorations in the properties of the high nitrogen austenitic stain steel. During welding, a high nitrogen austenitic stainless steel is ready to precipitate rapidly immense amounts of chromium nitride in the heat affected zone (HAZ), as intergranular or cellular morphologies at or from grain boundaries into grain interiors. The nitride precipitation reduces seriously the local mechanical properties and corrosion resistance. The present authors have demonstrated that a thermomechanical-processing as grain boundary engineering (GBE) inhibited intergranular chromium carbide precipitation in the HAZ of a type 304 austenitic stainless steel during welding and improved the intergranular corrosion resistance drastically. In the present study, the thermomechanical-processing was applied to a high nitrogen austenitic stainless steel containing 1 mass% nitrogen to suppress the nitride precipitation at or from grain boundaries in the HAZ during welding by GBE. GBE increases the frequency of coincidence site lattice (CSL) boundaries in the material so as to improve the intergranular properties, because of strong resistance of CSL boundaries to intergranular deteriorations. The optimum parameters in the thermomechanical-processing brought a very high frequency of CSL boundaries in the high nitrogen austenitic stainless steel. The GBE suppressed the intergranular and cellular nitride precipitation in the HAZ of the high nitrogen austenitic stainless steel during welding.

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Zhang, Yi, Guang Xu, Ming Xing Zhou, Hai Lin Yang, and Min Wang. "The Effect of Reheating Temperature on Precipitation of a High Strength Microalloyed Steel." Applied Mechanics and Materials 508 (January 2014): 8–11. http://dx.doi.org/10.4028/www.scientific.net/amm.508.8.

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High-strength steels are usually microalloyed with niobium (Nb), titanium (Ti) and vanadium (V), individually or in combination. The reheating temperature during austenization has a significant influence on the precipitation of microalloyed steels. The purpose of the study is to investigate the effect of reheating temperature on precipitates of microalloying elements. The research results show that reheating temperature should be high enough to ensure the dissolution of carbide and nitride precipitates in order to improve the precipitation strengthening of microalloying elements during rolling and cooling. The results provide the theoretical reference for the determination of reheating technology of microalloyed steels.

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Cho, Eun-Chel, Martin A. Green, Gavin Conibeer, Dengyuan Song, Young-Hyun Cho, Giuseppe Scardera, Shujuan Huang, et al. "Silicon Quantum Dots in a Dielectric Matrix for All-Silicon Tandem Solar Cells." Advances in OptoElectronics 2007 (August 28, 2007): 1–11. http://dx.doi.org/10.1155/2007/69578.

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We report work progress on the growth of Si quantum dots in different matrices for future photovoltaic applications. The work reported here seeks to engineer a wide-bandgap silicon-based thin-film material by using quantum confinement in silicon quantum dots and to utilize this in complete thin-film silicon-based tandem cell, without the constraints of lattice matching, but which nonetheless gives an enhanced efficiency through the increased spectral collection efficiency. Coherent-sized quantum dots, dispersed in a matrix of silicon carbide, nitride, or oxide, were fabricated by precipitation of Si-rich material deposited by reactive sputtering or PECVD. Bandgap opening of Si QDs in nitride is more blue-shifted than that of Si QD in oxide, while clear evidence of quantum confinement in Si quantum dots in carbide was hard to obtain, probably due to many surface and defect states. The PL decay shows that the lifetimes vary from 10 to 70 microseconds for diameter of 3.4 nm dot with increasing detection wavelength.

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Berns, Hans, Sascha Riedner, and Birger Hussong. "Influence of Molybdenum and Copper on the Corrosion Resistance of High Strength Austenitic Steels." Materials Science Forum 638-642 (January 2010): 2979–85. http://dx.doi.org/10.4028/www.scientific.net/msf.638-642.2979.

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Joint alloying of 0.85 to 1.1 mass% C + N raises the strength and cold work hardening of steels with 18 to 19 mass% Cr and Mn each and allows to produce them at atmospheric pressure. A yield strength of 600 MPa is combined with a true fracture stress of almost 2500 MPa and ≈ 70 % elongation. However, there is a risk of carbide/nitride precipitation during quenching of thicker cross sections after solution annealing. The addition of Mo and Cu affects the corrosion resistance as well as the precipitation. Submersion test and current density/potential tests in several aqueous solutions characterize the corrosion behaviour. Tests on intercrystalline corrosion are used to detect the precipitation as a function of quenching rate. It is shown that the C/N ratio is of key importance in improving the properties.

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Dissertations / Theses on the topic "Carbide and nitride precipitation"

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Sabounchei, S. J. S. Z. "Carbide and nitride clusters." Thesis, University of Liverpool, 1990. http://ethos.bl.uk/OrderDetails.do?uin=uk.bl.ethos.291737.

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Fujita, Nobuhiro. "Modelling carbide precipitation in alloy steels." Thesis, University of Cambridge, 2000. https://www.repository.cam.ac.uk/handle/1810/219197.

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Razzell, Anthony Gordon. "Silicon carbide fibre silicon nitride matrix composites." Thesis, University of Warwick, 1992. http://wrap.warwick.ac.uk/110559/.

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Silicon carbide fibre/silicon nitride matrix composites have been fabricated using the reaction bonded silicon nitride (RBSN) and sintered reaction bonded silicon nitride (SRBSN) processing routes. A filament winding and tape casting system was developed to produce sheets of parallel aligned fibres within a layer of green matrix ('prepreg') which were cut, stacked and hot pressed to form a plate. This was nitrided and (in the case of SRBSN matrix composites) hot pressed at 1700°C to density the matrix. The magnesia (MgO) and the yttria/alumina (Y2O3/AI2O3) additive SRBSN systems were investigated as matrices for ease of processing and compatibility with the matrix. The MgO additive Si3N4 matrix reacted with the outer carbon rich layer on the surface of the fibres, framing a reaction layer approx. 2pm in thickness. A reaction layer was also observed with the Y2O3/AI2O3 additive matrix, but was thinner (< 0.5um), and was identified as silicon carbide from the electron diffraction pattern. X-ray mapping in the SEM was used to investigate the spatial distribution of elements within the interface region to a resolution < lum, including light elements such as carbon. The 6wt%Y203/ 2wt%Al203 additive SRBSN system was chosen for more detailed investigation, and the majority of characterisation was performed using this composition. Oxidation of composite samples was carried out at temperatures between 1000°C and 1400°C for up to 1000 hours. Little damage was visible after 100 hours for all temperatures, corresponding to a relatively small drop in post oxidation bend strength. After 1000 hours at 1000°C both carbon rich outer layers and the central carbon core of the fibre were removed. Samples were severely oxidised after 1000 hours at 1400°C, having a glass layer on the outer surface and replacement of near surface fibre/matrix interfaces with glass. The post oxidation bend strengths for both conditions were approx.2/3 of the as fabricated strength. Less damage was observed after 1000 hours at 1200°C, and the post oxidation bend strength was higher than the 1000°C and 1400°C samples. Mechanical properties of the SRBSN matrix composite were investigated at room temperature and elevated temperatures (up to 1400°C). The average room temperature values for matrix cracking stress and ultimate strength (in bend) were 651.1 and 713.2 MPa respectively, with corresponding Weibull moduli of 5.7 and 8.7. The stresses are comparable to similar monolithic silicon nitrides. Room temperature tensile matrix cracking and ultimate strength were 232MPa and 413MPa, lower than the bend test results, which were attributed to bending stresses in the sample, lowering the apparent failure stresses. The samples failed in a composite like manner (i.e. controlled rather than catastrophic failure), with a substantially higher woric of fracture than monolithic materials. The average matrix cracking and ultimate bend strength at 1200°C were 516MPa and 554MPa, dropping to 178MPa and 486MPa at 1400°C (the matrix cracking stress was indistinct at 1400°C due to plasticity). The creep and stress rupture properties at 1300°C were investigated in four point bend, using dead-weight loading. The creep rate was KH/s at a stress of 200MPa, lower than a hot pressed silicon nitride with MgO additive, and higher than a hot isostatically pressed Y2O2/SÍO2 additive silicon nitride. A cavitation creep mechanism was deduced from the stress exponent, which was >1. Failure by stress rupture did not have a lower limit, which is also associated with cavitation of the amorphous grain boundary phase.

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Gao, Wei. "Oxidation of nitride-bonded silicon carbide (NBSC) and hot rod silicon carbide with coatings." Thesis, University of Strathclyde, 2001. http://ethos.bl.uk/OrderDetails.do?uin=uk.bl.ethos.366751.

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Tatli, Zafer. "Silicon nitride and silicon carbide fabrication using coated powders." Thesis, University of Newcastle Upon Tyne, 2002. http://ethos.bl.uk/OrderDetails.do?uin=uk.bl.ethos.394640.

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Turan, Servet. "Microstructural characterisation of silicon nitride-silicon carbide particulate composites." Thesis, University of Cambridge, 1995. http://ethos.bl.uk/OrderDetails.do?uin=uk.bl.ethos.627653.

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Martinelli, Antonio Eduardo. "Diffusion bonding of silicon carbide and silicone nitride to molybdenum." Thesis, McGill University, 1995. http://digitool.Library.McGill.CA:80/R/?func=dbin-jump-full&object_id=40191.

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This study focuses on various aspects of solid-state diffusion bonding of two ceramic-metal combinations, namely: silicon carbide-molybdenum (SiC-Mo), and silicon nitride-molybdenum (Si$ rm sb3N sb4$-Mo). Single SiC-Mo and $ rm Si sb3N sb4$-Mo joints were produced using hot-uniaxial pressing. The microstructure of the resulting interfaces were characterized by image analysis, scanning electron microscopy (SEM), electron probe micro-analysis (EPMA), and X-ray diffraction (XRD). The mechanical properties of the joints were investigated using shear strength testing, depth sensing nanoindentation, and neutron diffraction for residual stress measurement.
SiC was solid-state bonded to Mo at temperatures ranging from 1000$ sp circ$C to 1700$ sp circ$C. Diffusion of Si and C into Mo resulted in a reaction layer containing two main phases: $ rm Mo sb5Si sb3$ and Mo$ sb2$C. At temperatures higher than 1400$ sp circ$C diffusion of C into $ rm Mo sb5Si sb3$ stabilized a ternary phase of composition $ rm Mo sb5Si sb3$C. At 1700$ sp circ$C, the formation of MoC$ rm sb{1-x}$ was observed as a consequence of bulk diffusion of C into Mo$ sb2$C. A maximum average shear strength of 50 MPa was obtained for samples hot-pressed at 1400$ sp circ$C for 1 hour. Higher temperatures and longer times contributed to a reduction in the shear strength of the joints, due to the excessive growth of the interfacial reaction layer. $ rm Si sb3N sb4$ was joined to Mo in vacuum and nitrogen, at temperatures between 1000$ sp circ$C and 1800$ sp circ$C, for times varying from 15 minutes to 4 hours. Dissociation of $ rm Si sb3N sb4$ and diffusion of Si into Mo resulted in the formation of a reaction layer consisting, initially, of $ rm Mo sb3$Si. At 1600$ sp circ$C (in vacuum) Mo$ sb3$Si was partially transformed into $ rm Mo sb5Si sb3$ by diffusion of Si into the original silicide, and at higher temperatures, this transformation progressed extensively within the reaction zone. Residual N$ sb2$ gas, which originated from the decomposition of $ rm Si sb3N sb4,$ dissolved in the Mo, however, most of the gas escaped during bonding or remained trapped at the original $ rm Si sb3N sb4$-Mo interface, resulting in the formation of a porous layer. Joining in N$ sb2$ increased the stability of $ rm Si sb3N sb4,$ affecting the kinetics of the diffusion bonding process. The bonding environment did not affect the composition and morphology of the interfaces for the partial pressures of N$ sb2$ used. A maximum average shear strength of 57 MPa was obtained for samples hot-pressed in vacuum at 1400$ sp circ$C for 1 hour.

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Kim, Hyoun-Ee. "Gaseous corrosion of silicon carbide and silicon nitride in hydrogen /." The Ohio State University, 1987. http://rave.ohiolink.edu/etdc/view?acc_num=osu1487327695622538.

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Rohatgi, Aashish. "Detection of vanadium nitride precipitation using a creep technique." Thesis, McGill University, 1993. http://digitool.Library.McGill.CA:80/R/?func=dbin-jump-full&object_id=69578.

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Computer programs were developed to perform creep tests on three microalloyed steels, with the aim of determining the precipitation kinetics of VN in austenite in one of the steels. This was a commercial 0.01% Ti- 0.12% V- 0.25% Mo steel. The other two were niobium steels with low (0.04% Nb) and high (0.07% Nb) niobium levels, respectively.
The Ti-V-Mo steel was tested at various stresses between 30 and 50 MPa in the temperature range 850-900$ sp circ$C. A mathematical equation was fitted to the creep strain vs. time curves and the creep strain was expressed as a function of time. The strain rate was determined by differentiating the equation with respect to time and log(strain rate) vs. log(creep strain) or creep strain curves were then plotted for each testing condition. At 850$ sp circ$C and 900 seconds, the strain rate was observed to decrease at a faster rate. This time decreased to 700 seconds at 875$ sp circ$C at the same stress of 36MPa. This effect is attributed to the occurrence of VN precipitation in austenite, which reduces the creep rate. However, precipitation could not be detected by the creep technique at 900$ sp circ$C in this steel.
The 0.07% Nb steel was tested at 950$ sp circ$C under stresses of 42 and 32 MPa. At 32MPa, the strain rate was found to decrease at a faster rate at 250 seconds. The 0.04% Nb steel was tested under stresses of 50 and 40 MPa at 875$ sp circ$C, and under 50 MPa at 850$ sp circ$C. In this steel too, a behaviour similar to that shown by the Ti-V and high Nb steels was observed at 375 seconds, 40MPa (875$ sp circ$C) and at 460 seconds, 50MPa (850$ sp circ$C). This is believed to be due the precipitation of NbCN.

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Sundaresan, Siddarth G. "Ultra-fast high temperature microwave processing of silicon carbide and gallium nitride." Fairfax, VA : George Mason University, 2007. http://hdl.handle.net/1920/2851.

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Thesis (Ph.D.)--George Mason University, 2007.
Title from PDF t.p. (viewed Oct. 29, 2007). Thesis director: Mulpuri V. Rao. Submitted in partial fulfillment of the requirements for the degree of Doctor of Philosophy in Electrical and Computer Engineering. Vita: p. 170. Includes bibliographical references (p. 160-169). Also available in print.

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Books on the topic "Carbide and nitride precipitation"

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Feenstra, Randall M., and Colin E. C. Wood, eds. Porous Silicon Carbide and Gallium Nitride. Chichester, UK: John Wiley & Sons, Ltd, 2008. http://dx.doi.org/10.1002/9780470751817.

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Razzell, A. G. Silicon carbide fibre silicon nitride matrix composites. [s.l.]: typescript, 1992.

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Weimer, Alan W. Carbide, Nitride and Boride Materials Synthesis and Processing. Dordrecht: Springer Netherlands, 1996.

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Weimer, Alan W., ed. Carbide, Nitride and Boride Materials Synthesis and Processing. Dordrecht: Springer Netherlands, 1997. http://dx.doi.org/10.1007/978-94-009-0071-4.

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Raftery, Theresa Maria. Electroconductive sialon-interstitial carbide composites. Dublin: University College Dublin, 1997.

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C, Wood Colin E., ed. Porous silicon carbide and gallium nitride: Epitaxy, catalysis, and biotechnology applications. Chichester, England: John Wiley & Sons, 2008.

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Sloof, Willem Gerrit. Internal stresses and microstructure of layer/substrate assemblies: Analysis of TiC and TiN coatings chemically vapour deposited on various substrates. Delft, Netherlands: Delft University Press, 1996.

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Zhou, Yijian. Effects of grain boundary and triple line structures on carbide precipitation in type 304L stainless steel. Ottawa: National Library of Canada, 2000.

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Reports, Mitchell Market. Boron Carbide and Boron Nitride. Elsevier Science, 1987.

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Gallium Nitride & Silicon Carbide Power Devices. World Scientific Publishing Co Pte Ltd, 2016.

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Book chapters on the topic "Carbide and nitride precipitation"

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Holling, G. "Nitride Bonded Carbide Engineered Ceramics." In 3rd European Symposium on Engineering Ceramics, 149–65. Dordrecht: Springer Netherlands, 1991. http://dx.doi.org/10.1007/978-94-011-7990-4_11.

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Ochoa, R., X. X. Bi, A. M. Rao, and P. C. Eklund. "Transition metal nitride and carbide nanoparticles." In The Chemistry of Transition Metal Carbides and Nitrides, 489–510. Dordrecht: Springer Netherlands, 1996. http://dx.doi.org/10.1007/978-94-009-1565-7_27.

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Kuznetsov, N. T. "Precursors for Carbide, Nitride and Boride Synthesis." In Materials Science of Carbides, Nitrides and Borides, 223–45. Dordrecht: Springer Netherlands, 1999. http://dx.doi.org/10.1007/978-94-011-4562-6_13.

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Ren, Z., and J. Wang. "Carbide, Nitride, Boride, and Sulfide (Chevrel) Superconductors." In Inorganic Reactions and Methods, 265–67. Hoboken, NJ, USA: John Wiley & Sons, Inc., 2007. http://dx.doi.org/10.1002/9780470145333.ch189.

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Gu, Z., J. H. Edgar, Balaji Raghothamachar, Michael Dudley, Dejin Zhuang, and Zlatko Sitar. "The Effect of Aluminum Nitride-Silicon Carbide Alloy Buffer Layers on the Sublimation Growth of Aluminum Nitride on SiC (0001) Substrates." In Silicon Carbide and Related Materials 2005, 1497–500. Stafa: Trans Tech Publications Ltd., 2006. http://dx.doi.org/10.4028/0-87849-425-1.1497.

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Saucedo-Muñoz, M. L., R. Gómez-Martínez, A. Ortiz-Mariscal, V. M. Lopez-Hirata, J. D. Villegas-Cardenas, and J. L. Gonzalez-Velazquez. "Carbide Precipitation in a Low Alloy Ferritic Steel." In TMS 2017 146th Annual Meeting & Exhibition Supplemental Proceedings, 791–99. Cham: Springer International Publishing, 2017. http://dx.doi.org/10.1007/978-3-319-51493-2_76.

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Matocha, Kevin, Ed Kaminsky, Alexei Vertiatchikh, and Jeff B. Casady. "High-Frequency SiC MESFETs with Silicon Dioxide/Silicon Nitride Passivation." In Silicon Carbide and Related Materials 2005, 1239–42. Stafa: Trans Tech Publications Ltd., 2006. http://dx.doi.org/10.4028/0-87849-425-1.1239.

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Atwell, William H. "Polymeric Routes to Silicon Carbide and Silicon Nitride Fibers." In Advances in Chemistry, 593–606. Washington, DC: American Chemical Society, 1989. http://dx.doi.org/10.1021/ba-1990-0224.ch032.

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Yao, Zhiwei, and Pengliang Liang. "Chapter 2. Preparation Methods for Nitride and Carbide Catalysts." In Alternative Catalytic Materials, 27–45. Cambridge: Royal Society of Chemistry, 2018. http://dx.doi.org/10.1039/9781788013222-00027.

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Skybakmoen, Egil, Lisbet I. Stoen, Jarnnicke H. Kvello, and Ove Darell. "Quality Evaluation of Nitride Bonded Silicon Carbide Sidelining Materials." In Essential Readings in Light Metals, 866–71. Hoboken, NJ, USA: John Wiley & Sons, Inc., 2013. http://dx.doi.org/10.1002/9781118647745.ch114.

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Conference papers on the topic "Carbide and nitride precipitation"

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Liu, Kui, Xianchao Hao, Ming Gao, Shuo Li, Yiyi Li, and Bofang Wang. "Effect of N Content on Mechanical Properties and Microstructure of Alloy 690." In 17th International Conference on Nuclear Engineering. ASMEDC, 2009. http://dx.doi.org/10.1115/icone17-75195.

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The microstructures and mechanical properties of nitrogen bearing Alloy 690 have been systematically investigated. Alloy ingots with different N addition, range from 38 to 330wt.ppm, were melted using vacuum induction melting (VIM) plus electro-slag re-melting (ESR) double processing techniques. The forged and hot rolled different N content bars were solid solution treated between 1010°C and 1080°C, thermally treated at 715°C for different state mechanical property testing and microstructure study. Microstructure analysis indicated that nitrogen addition to Alloy 690 can effectively refine the solution treated austenite grains. This may be associated with titanium nitrides pinning the grain boundaries and hindering the grain growth during solid solution treatment. More nitrides, which are identified as TiN, were found on the grain boundaries and in the inside of austenite grains with increasing N contents of the alloy. The carbide precipitation at 715°C showed significant difference identified by SEM. At the level of 38, 100 and 220wt.ppm N, the chromium carbide Cr23C6 distribution on the grain boundaries appeared to be semi-continuous; when the N content reached 330wt.ppm, only few discrete type of carbides were observed. The tension testing results at room temperature of different N content alloys proved that both the ultimate tensile strength (UTS) and the yield strength (YS) enhanced about 50MPa when N content was raised from 38 to 330wt.ppm in this alloy; while the corresponding elongation (EL) and reduction in area (RA) adversely dropped about 5%. Room temperature hardness rose with increasing N content, well matched tensile strength. High temperature tension testing results at the range of 900∼1250°C showed that a severely hot ductility dip, representing by the values of the reduction in area (RA), existed in 300wt.ppm and 100wt.ppm nitrogen containing alloys at the lower end temperature range of 950∼1100°C. However, such ductility dip could be improved when the N content was at 220wt.ppm, and completely eliminated at 38wt.ppm N content. At the higher end temperature rang of 1150∼1250°C, the ductility of all 4 nitrogen bearing alloys did not show significant difference, even though the hot ductility of minimum 38wt.ppm N samples was preferable. Nitrogen content did not affect high temperature strength; the UTS values nearly had no change at the same testing temperature with different nitrogen bearing alloys. The carbide precipitation difference of the thermally treated alloy, induced by N addition, may affect Alloy 690 corrosion properties, which needs to be studied in future. The mechanical properties variation both at room temperature and high temperatures of different nitrogen bearing alloys in this study will be certainly beneficial to determine the practical processing routes of Alloy 690.

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2

Luchinin, Victor V., Andrey V. Korlyakov, and Alexander A. Vasil'ev. "Silicon carbide-aluminum nitride: new high-stability composition for MEMS." In Design, Test, and Microfabrication of MEMS/MOEMS, edited by Bernard Courtois, Selden B. Crary, Wolfgang Ehrfeld, Hiroyuki Fujita, Jean Michel Karam, and Karen W. Markus. SPIE, 1999. http://dx.doi.org/10.1117/12.341273.

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3

Gunaydin, Yasin, Saeed Jahdi, Olayiwola Alatise, Jose Ortiz Gonzalez, Ruizhu Wu, Bernard Stark, Mohammad Hedayati, Xibo Yuan, and Phil Mellor. "Performance of Wide-Bandgap Gallium Nitride vs Silicon Carbide Cascode Transistors." In 2020 IEEE Energy Conversion Congress and Exposition (ECCE). IEEE, 2020. http://dx.doi.org/10.1109/ecce44975.2020.9236187.

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4

Rodak, L. E., A. V. Sampath, C. S. Gallinat, H. Shen, M. Wraback, Y. Chen, Q. Zhou, and J. C. Campbell. "Aluminum gallium nitride/silicon carbide separate absorption and multiplication avalanche photodiodes." In 2012 Lester Eastman Conference on High Performance Devices (LEC). IEEE, 2012. http://dx.doi.org/10.1109/lec.2012.6410964.

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5

Rodak, L. E., A. V. Sampath, C. S. Gallinat, R. W. Enck, J. Smith, H. Shen, M. Wraback, Y. Chen, Q. Zhou, and J. C. Campbell. "Aluminum gallium nitride/silicon carbide separate absorption and multiplication avalanche photodiodes." In 2012 Lester Eastman Conference on High Performance Devices (LEC). IEEE, 2012. http://dx.doi.org/10.1109/lec.2012.6410993.

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6

Rice, Graeme, D. Jones, K. S. Kim, John M. Girkin, D. Jarozynski, and Martin D. Dawson. "Micromachining of gallium nitride, sapphire, and silicon carbide with ultrashort pulses." In SPIE Proceedings, edited by Heinz P. Weber, Vitali I. Konov, and Thomas Graf. SPIE, 2003. http://dx.doi.org/10.1117/12.543662.

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7

D'Anna, Emilia, Gilberto Leggieri, Armando Luches, Maurizio Martino, Alessio Perrone, Guiseppe Majni, Paolo Mengucci, and Ion N. Mihailescu. "Laser reactive ablation deposition of titanium nitride and titanium carbide films." In Optics for Productivity in Manufacturing, edited by Rolf-Juergen Ahlers, Peter Hoffmann, Hermann Lindl, and Ruediger Rothe. SPIE, 1994. http://dx.doi.org/10.1117/12.193108.

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8

Paisley, M. J., Z. Sitar, C. H. Carter, and R. F. Davis. "Growth Of Gallium Nitride On Silicon Carbide By Molecular Beam Epitaxy." In 1988 Los Angeles Symposium--O-E/LASE '88, edited by Carl A. Kukkonen. SPIE, 1988. http://dx.doi.org/10.1117/12.943932.

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9

Treu, M., E. Vecino, M. Pippan, O. Haberlen, G. Curatola, G. Deboy, M. Kutschak, and U. Kirchner. "The role of silicon, silicon carbide and gallium nitride in power electronics." In 2012 IEEE International Electron Devices Meeting (IEDM). IEEE, 2012. http://dx.doi.org/10.1109/iedm.2012.6478995.

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Liu, Yuncong, Yanan Wang, Xu-Qian Zheng, Qiang Lin, and Philip X. L. Feng. "Nanomechanical and Optomechanical Coupling in Silicon Carbide / Hexagonal Boron Nitride Hybrid Resonator." In 2021 21st International Conference on Solid-State Sensors, Actuators and Microsystems (Transducers). IEEE, 2021. http://dx.doi.org/10.1109/transducers50396.2021.9495564.

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Reports on the topic "Carbide and nitride precipitation"

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Jan W. Nowok, John P. Hurley, and John P. Kay. SiAlON COATINGS OF SILICON NITRIDE AND SILICON CARBIDE. Office of Scientific and Technical Information (OSTI), June 2000. http://dx.doi.org/10.2172/824976.

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Sundberg, G. J. Analytical and Experimental Evaluation of Joining Silicon Carbide to Silicon Carbide and Silicon Nitride to Silicon Nitride for Advanced Heat Engine Applications Phase II. Office of Scientific and Technical Information (OSTI), January 1994. http://dx.doi.org/10.2172/814549.

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Perry, Scott S., and Stephen V. Didziuliz. The Surface Chemistry and Tribology of Carbide and Nitride Hard Coatings. Fort Belvoir, VA: Defense Technical Information Center, August 2000. http://dx.doi.org/10.21236/ada383271.

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Buss, R. J. Rf-plasma synthesis of nanosize silicon carbide and nitride. Final report. Office of Scientific and Technical Information (OSTI), February 1997. http://dx.doi.org/10.2172/453776.

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Cross, M. T. Aluminum nitride-silicon carbide whisker composites: Processing, properties, and microstructural stability. Office of Scientific and Technical Information (OSTI), January 1990. http://dx.doi.org/10.2172/6381576.

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Kingon, A. I., R. F. Davis, and A. K. Singh. Integrated Synthesis and Post Processing of Silicon Carbide and Aluminum Nitride. Fort Belvoir, VA: Defense Technical Information Center, December 1990. http://dx.doi.org/10.21236/ada230810.

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Sundberg, G. J., A. M. Vartabedian, J. A. Wade, and C. S. White. Analytical and experimental evaluation of joining silicon carbide to silicon carbide and silicon nitride to silicon nitride for advanced heat engine applications Phase 2. Final report. Office of Scientific and Technical Information (OSTI), October 1994. http://dx.doi.org/10.2172/28303.

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Perry, Scott S. Temperature Dependent Studies of the Tribological Properties of Carbide and Nitride Hard Coatings. Fort Belvoir, VA: Defense Technical Information Center, September 2000. http://dx.doi.org/10.21236/ada383260.

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Willis, C. F. A study of chromium carbide precipitation at interphase boundaries in stainless steel welds. Office of Scientific and Technical Information (OSTI), April 1990. http://dx.doi.org/10.2172/6552861.

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Perry, Scott S. Spectroscopic Studies of Perfluorinated Lubricants and Additive Interfacial Reactivity at Metal Carbide and Nitride Surfaces. Fort Belvoir, VA: Defense Technical Information Center, September 2000. http://dx.doi.org/10.21236/ada383270.

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