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Relevant bibliographies by topics / Secondary recrystallisation

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Academic literature on the topic 'Secondary recrystallisation'

Author: Grafiati

Published: 4 June 2021

Last updated: 7 February 2022

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Journal articles on the topic "Secondary recrystallisation"

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Miodownik, M. A., A. J. Wilkinson, and J. W. Martin. "On the secondary recrystallisation of MA754." Acta Materialia 46, no. 8 (May 1998): 2809–21. http://dx.doi.org/10.1016/s1359-6454(97)00460-6.

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Duggan, B. J., M. Z. Quadir, and Richard Penelle. "An Examination of Cluster Nucleation of Goss Oriented Grains Formed during Secondary Recrystallisation in an Fe-3.2% Si Electrical Steel." Materials Science Forum 558-559 (October 2007): 723–28. http://dx.doi.org/10.4028/www.scientific.net/msf.558-559.723.

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The idea that a single subgrain is sufficient to produce a single recrystallised grain is the simplest explanation for the recrystallisation process. Likewise, a single Goss oriented grain arising from the primary recrystallisation process is the simplest unit which can give rise to a secondary Goss oriented grain. More complicated cluster models, for example subgrain coalescence is also considered feasible for primary recrystallisation, clusters of Goss oriented grains might be another mechanism for forming Goss oriented secondary grains. This paper examines the cluster theory using material which is produced by the ARMCO process which requires two stages of rolling. In order to achieve this aim it is necessary to destroy the connectivity between individual Goss oriented grains by using thin foils derived from sheet which gives a strong Goss texture on conventional annealing. The foils were sectioned from the subsurface which had a strong η fibre after primary recrystallisation, and ranged in thickness from 18μm (the average grain size after primary recrystallisation) up to 80μm, which is the approximate thickness of the η textured layer. The central layer, which had the classical {111}<hkl> primary recrystallised texture, was similarly processed, but this did not produce secondary recrystallisation. The experiment followed the secondary recrystallisation process in the same area using sequential annealing in a vacuum furnace by a combination of EBSD and Channelling contrast microscopy. The data does not support the high energy boundary hypothesis nor the CSL explanation. But it is clear that connectivity is important, because when this is destroyed by the thin foil two dimensional morphology, as it is in the thinnest foil, secondary recrystallisation does not occur.

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Gladman, T. "Second phase particle distribution and secondary recrystallisation." Scripta Metallurgica et Materialia 27, no. 11 (December 1992): 1569–73. http://dx.doi.org/10.1016/0956-716x(92)90146-6.

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Homma, Hotaka, and Bevis Hutchinson. "Orientation dependence of secondary recrystallisation in silicon–iron." Acta Materialia 51, no. 13 (August 2003): 3795–805. http://dx.doi.org/10.1016/s1359-6454(03)00193-9.

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Reyes Barragan, Jose Luis, Roberto Ademar Rodriguez Diaz, Maria Luisa Ojeda Martinez, Silvia Gaona Jimenez, and Julio Alberto Juarez Islas. "Effect of Isothermal Treatment on Microstructure and Mechanical Properties of Cold-Deformed IF Steel." Advances in Materials Science and Engineering 2019 (March 12, 2019): 1–13. http://dx.doi.org/10.1155/2019/8674323.

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In this study, we investigated the recrystallisation kinetics of Ti-stabilised interstitial-free (IF) steel manufactured by the Mexican steel industry through the route of electric arc furnace with vacuum degassing, secondary refining, and subsequent continuous casting. The IF steel was hot-rolled at 950°C and then cold-rolled until deformation of 94% was attained, followed by recrystallisation at different times at a constant temperature of 780°C. In addition, the mechanical properties of the IF steel were assessed as a function of recrystallisation time. The results obtained from the mechanical property tests were presented in the form of plots of microhardness, yield strength, ultimate tensile stress, and deformation percent as functions of the recrystallised fraction with an indirect dependence on recrystallisation time. A graphical model of the recrystallisation behaviour showed the evolution of the microstructure, including phase transformations, hardness, and the mechanical properties determined from the tensile tests. In view of subsequent recovery and recrystallisation, stored energy analysis derived from the strain induced by deformation was presented. Furthermore, we determined the precipitates formed in the different processing stages of IF steel.

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Zaefferer, Stefan. "Application of Orientation Microscopy in SEM and TEM for the Study of Texture Formation during Recrystallisation Processes." Materials Science Forum 495-497 (September 2005): 3–12. http://dx.doi.org/10.4028/www.scientific.net/msf.495-497.3.

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Orientation microscopy in TEM and SEM is a particularly well suited tool to study recrystallisation processes because these are always associated with orientation and microstructure changes. The present work discusses the possibilities and limits of the TEM and SEM based techniques and illustrates their use by means of 3 different examples. The examples include studies on nucleation mechanisms of primary recrystallisation where the techniques meet their limits in spatial resolution. The problem of in-situ observations of annealing processes is discussed and it is shown how recrystallisation simulation techniques based on experimental data may be used. Furthermore the new technique of 3-dimensional EBSD in a focused-ion-beam (FIB) SEM is presented with one example. Finally, the statistical analysis of very large orientation data sets is discussed by an example of secondary recrystallisation in electrical steels.

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Hutchinson, W. Bevis. "Origin of Goss Texture during Secondary Recrystallisation in Silicon-Steel." Materials Science Forum 715-716 (April 2012): 73–80. http://dx.doi.org/10.4028/www.scientific.net/msf.715-716.73.

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Primary recrystallised sheets of 3% silicon steel from two different industrial processing routes have been examined after laboratory annealing to initiate secondary recrystallisation. Metallography included etching to reveal individual dislocations and sub-boundaries as well as EBSD in scanning electron microscopy. Residual low angle boundaries are not normally observed inside the secondary grains. The growth of secondaries appears to occur in a jerky manner, associated with local intrusions into the primary matrix that destabilise the interface. The frequency of occurrence of special low energy grain boundaries such as 9 and 5 is believed to dictate the selectivity of the Goss orientation in both types of steel sheet.

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Evens, P. J., J. W. Martin, and E. A. Little. "Secondary recrystallisation of MA 957 oxide dispersion strengthened ferritic superalloy." Materials Science and Technology 8, no. 6 (June 1992): 531–36. http://dx.doi.org/10.1179/mst.1992.8.6.531.

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Baganis, Antonis, Marianthi Bouzouni, and Spyros Papaefthymiou. "Phase Field Simulation of AA6XXX Aluminium Alloys Heat Treatment." Metals 11, no. 2 (February 1, 2021): 241. http://dx.doi.org/10.3390/met11020241.

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Heat treatment has a significant impact on the microstructure and the mechanical properties of Al-Mg-Si alloys. The present study presents a first Phase-Field modelling approach on the recrystallisation and grain growth mechanism during annealing. It focuses on the precipitate fraction, radius, and Mg-Si concentration in the matrix phase, which are used as input data for the calculation of the yield strength and hardness at the end of different ageing treatments. Annealing and artificial ageing simulations have been conducted on the MultiPhase-Field based MICRESS@ software, while the ThermoCalc@ software has been used to construct the pseudo-binary Al-Mg phase-diagrams and the atomic-mobility databases of MgxSiy precipitates. Recrystallisation simulation estimates the recrystallisation kinetics, the grain growth, and the interface mobility with the presence/absence of secondary particles, selecting as annealing temperature 400 °C and a microstructure previously subjected to cold rolling. The pinning force of secondary particles decelerates the overall recrystallisation time, causing a slight decrease in the final grain radius due to the reduction of interface mobility. The ageing simulation examines different ageing temperatures (180 and 200 °C) for two distinct ternary systems (Al-0.9Mg-0.6Si/Al-1.0Mg-1.1Si wt.%) considering the interface energy and the chemical free energy as the driving force for precipitation. The combination of Phase-Field and the Deschamps–Brechet model predicted the under-ageing condition for the 180 °C ageing treatment and the peak-ageing condition for the 200 °C ageing treatment.

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Bao, Siqian, Bingbing Liu, Gang Zhao, Huan Xiao, Yaowen Xu, Gengwei Yang, and Shanshan Ke. "Secondary recrystallisation behaviours of grain-orientated silicon steel produced by TSCR process." Ironmaking & Steelmaking 45, no. 10 (December 24, 2017): 924–28. http://dx.doi.org/10.1080/03019233.2017.1412385.

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Dissertations / Theses on the topic "Secondary recrystallisation"

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Miodownik, Mark A. "Fundamentals of grain growth phenomena in ODS alloys." Thesis, University of Oxford, 1996. http://ethos.bl.uk/OrderDetails.do?uin=uk.bl.ethos.318817.

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Paluch, Krzysztof J., L. Tajber, M. I. Amaro, O. I. Corrigan, and A. M. Healy. "Impact of process variables on the micromeritic and physicochemical properties of spray-dried microparticles, part II: physicochemical characterisation of spray-dried materials." 2012. http://hdl.handle.net/10454/14361.

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Yes
Objectives In this work we investigated the residual organic solvent content and physicochemical properties of spray-dried chlorothiazide sodium (CTZNa) and potassium (CTZK) salts. Methods The powders were characterised by thermal, X-ray diffraction, infrared and dynamic vapour sorption (DVS) analyses. Solvent levels were investigated by Karl–Fischer titration and gas chromatography. Key findings Spray-drying from water, methanol (MeOH) and mixes of MeOH and butyl acetate (BA) resulted in amorphous microparticles. The glass transition temperatures of CTZNa and CTZK were ∼192 and ∼159°C, respectively. These materials retained their amorphous nature when stored at 25°C in dry conditions for at least 6 months with no chemical decomposition observed. DVS determined the critical relative humidity of recrystallisation of CTZNa and CTZK to be 57% RH and 58% RH, respectively. The inlet temperature dependant oxidation of MeOH to formaldehyde was observed; the formaldehyde was seen to deposit within the amorphous matrix of spray-dried product. Spray-drying in the open blowing mode coupled with secondary drying resulted in a three-fold reduction in residual BA (below pharmacopoeial permitted daily exposure limit) compared to spray-drying in the closed mode. Conclusions Experiments showed that recirculation of recovered drying gas increases the risk of deposition of residual solvents in the spray-dried product.
The Irish Research Council for Science and Engineering Technology (IRCSET), the Solid State Pharmaceutical Cluster (SSPC), supported by Science Foundation Ireland under grant number (07/SRC/B1158) and the Irish Drug Delivery Research Network, a Strategic Research Cluster grant (07/SRC/B1154) under the National Development Plan co-funded by EU Structural Funds and Science Foundation Ireland.

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Book chapters on the topic "Secondary recrystallisation"

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Homma, Hotaka, K. Murakami, T. Tamaki, Naoya Shibata, Takahisa Yamamoto, and Yuichi Ikuhara. "Effects of Grain Boundary Characters for Secondary Recrystallisation in Grain Oriented Silicon Steel." In Materials Science Forum, 633–40. Stafa: Trans Tech Publications Ltd., 2007. http://dx.doi.org/10.4028/0-87849-443-x.633.

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Duggan, B. J., M. Z. Quadir, and Richard Penelle. "An Examination of Cluster Nucleation of Goss Oriented Grains Formed during Secondary Recrystallisation in an Fe-3.2% Si Electrical Steel." In Materials Science Forum, 723–28. Stafa: Trans Tech Publications Ltd., 2007. http://dx.doi.org/10.4028/0-87849-443-x.723.

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Conference papers on the topic "Secondary recrystallisation"

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Dent, A. H., A. J. Horlock, S. J. Harris, and D. G. Mccartney. "Microstructure and Corrosion Behaviour of HVOF Sprayed Nickel-Based Amorphous/Nanocrystalline Alloys." In ITSC 1998, edited by Christian Coddet. ASM International, 1998. http://dx.doi.org/10.31399/asm.cp.itsc1998p0665.

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Abstract The corrosion characteristics of two bespoke Ni-Cr-Mo-B alloy powders sprayed by the high velocity oxy-fuel (HVOF) process have been studied using potentiodynamic and potentiostatic corrosion analysis in 0.5M H2SO4. The deposits have also been microstructurally characterised using X-ray diffraction (XRD), scanning electron microscopy (utilising both secondary electron (SE) and backscattered electron (BE) modes), and transmission electron microscopy (TEM). Results from the microstructural examination of the two alloys have revealed a predominantly amorphous/nanocrystalline (fcc) matrix containing submicron boride precipitates as well as regions of martensitically transformed laths. Apparent recrystallisation of the amorphous matrix has also been observed in the form of cellular crystals with an fcc structure. The oxide stringers observed at splat boundaries were found to be columnar grained α-Cr2O3, though regions of the spinel oxide NiCr2O4 with a globular morphology were also observed. The coatings of the two alloys exhibited comparable resistance to corrosion in 0.5M H2SO4, as revealed by potentiodynamic tests. They both had rest potentials approximately equal to -300mV(SCE) and passive region current densities of around 1mAcm-2. Microstructural examination of samples tested potentiostatically revealed the prevalence of degradation at splat boundaries, especially those where significant oxidation of the deposit had occurred.

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Boegelein, Thomas, Ashwin Rao, Andrew R. Jones, and Gordon J. Tatlock. "Selective Laser Melting of Oxide Dispersion Strengthened Steels." In ASME 2011 Pressure Vessels and Piping Conference. ASMEDC, 2011. http://dx.doi.org/10.1115/pvp2011-57892.

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Oxide Dispersion Strengthened (ODS) alloys are a long established class of materials manufactured using powder metallurgy techniques. These alloys can offer exceptional high temperature strength and resistance to radiation damage, thus are envisioned to be used in a number of future nuclear and fossil energy power applications. However, due to the manufacturing steps involved, the overall cost to build components with these materials can be high. This paper presents work conducted to assess the feasibility of applying Selective Laser Melting (SLM) techniques to either coat or direct build on substrates with Fe-based Oxide Dispersion Strengthened (ODS) alloys. SLM is a rapid prototyping technique which can be used to manufacture near net-shape solid components from layered metallic powder beds. Two different geometries were of interest in this study — a simple button configuration with a nickel-base superalloy (IN939) substrate and a more complex hexagonal shaped wall with a mild steel substrate. Powders of PM2000 (a FeCrAl based ODS alloy) were deposited in both cases. Heat treatments were subsequently conducted on these structures to investigate effects of temperature on the bond characteristics and secondary recrystallisation. Electron microscopy examination revealed significant amounts of diffusion between the nickel and the ODS powders which enhances the bond strength. The studies have revealed the existence of a strong bond between the substrate and the interface even after prolonged exposure at elevated temperatures.

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