Relevant bibliographies by topics / Precipitate dissolution

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  1. Journal articles
  2. Dissertations / Theses
  3. Book chapters
  4. Conference papers
  5. Reports

Academic literature on the topic 'Precipitate dissolution'

Author: Grafiati
Published: 4 June 2021
Last updated: 19 February 2022

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Journal articles on the topic "Precipitate dissolution"

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Solis-Bravo, Gregorio, Matthew Merwin, and C. Isaac Garcia. "Impact of Precipitate Morphology on the Dissolution and Grain-Coarsening Behavior of a Ti-Nb Microalloyed Linepipe Steel." Metals 10, no. 1 (January 4, 2020): 89. http://dx.doi.org/10.3390/met10010089.

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The relationship between precipitate morphology and dissolution on grain coarsening behavior was studied in two Ti-Nb microalloyed Linepipe (LP) Steels. The developed understanding highlights the importance of the complex relationship between precipitate constitutive make-up, dissolution mechanism and grain boundary (GB) pinning force. Equilibrium-based empirical solubility products were used to calculate precipitate volume fractions and compared to experimental measurements. Scanning Electron Microscopy (SEM), Electron Backscatter Diffraction (EBSD) and Electron Probe Micro-Analysis (EPMA) were conducted on bulk samples. Transmission Electron Microscopy (TEM)-based techniques were used on C-replica extractions and thin-foils. A retardation in the grain-coarsening temperature compared to the predicted coarsening temperature based on equilibrium calculations was noticed. In addition, a consistent NbC epitaxial formation over pre-existing TiN was observed. The resulting reduction in total precipitate/matrix interface area and the low energy of the TiN/NbC interface are pointed to as responsible mechanisms for the retardation in the kinetics of precipitates’ dissolution. This dissolution retardation mechanism suggests that a lower Nb content might be effective in controlling the grain coarsening behavior of austenite.
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Mineta, S., Shigenobu Namba, Takashi Yoneda, Kyosuke Ueda, and Takayuki Narushima. "Changes in Microstructure of Biomedical Co-Cr-Mo-C Alloys with Solution Treating and Aging." Advanced Materials Research 89-91 (January 2010): 377–82. http://dx.doi.org/10.4028/www.scientific.net/amr.89-91.377.

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Microstructural changes occurring in biomedical Co-Cr-Mo alloys with three carbon levels due to solution treatment and aging were investigated. Ingots of Co-Cr-Mo alloys with three different carbon levels were prepared by vacuum furnace melting; their chemical composition was Co-28Cr-6Mo-xC (x = 0.12, 0.25 and 0.35 mass%). Precipitates were electrolytically extracted from as-cast and heat-treated alloys. An M23C6 type carbide and a phase were detected as precipitates in as-cast Co-28Cr-6Mo-0.12C alloy, and an M23C6 type carbide and an  phase (M6C-M12C type carbide) were detected in as-cast Co-28Cr-6Mo-0.25C and Co-28Cr-6Mo-0.35C alloys. Only the M23C6 type carbide was detected during solution treatment. Complete precipitate dissolution occurred in all the three alloys after solution treatment. The holding time required for complete precipitate dissolution increased with increasing carbon content and decreasing solution treatment temperature. Complete precipitate dissolution occurred in the Co-Cr-Mo-C alloys solution treated at 1523 K for 43.2 ks; they were then subjected to aging from 873 to 1473 K for a heating time up to 44.1 ks after complete precipitate dissolution in solution treatment at 1523 K for 43.2 ks. The M23C6 type carbide with a grain size of 0.1–3 m was observed after aging. A time-temperature-precipitation diagram of the M23C6 type carbide formed in the Co-28Cr-6Mo-0.25C alloy was plotted.
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Mineta, Shingo, Alfirano, Shigenobu Namba, Takashi Yoneda, Kyosuke Ueda, and Takayuki Narushima. "Phase and Morphology of Carbides in ASTM F75 Co-Cr-Mo-C Alloys Formed at 1473 to 1623 K." Materials Science Forum 654-656 (June 2010): 2176–79. http://dx.doi.org/10.4028/www.scientific.net/msf.654-656.2176.

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The phase and morphology of precipitates in heat-treated Co-28Cr-6Mo-xC (x = 0.12, 0.15, 0.25, and 0.35mass%) alloys were investigated. The as-cast alloys were solution-treated in the temperature range of 1473 to 1623 K for 0 to 43.2 ks. Complete precipitate dissolution was observed in all four alloys, each of which had different carbon contents. The holding time for complete dissolution was greater for alloys with greater carbon content. The curve representing the boundary between the complete- and incomplete-dissolution conditions for each alloy is C shaped. Under the incomplete precipitate dissolution conditions of the Co-28Cr-6Mo-0.25C alloy, an M23C6 type carbide and a π-phase (M2T3X type carbide with β-Mn structure) were observed at 1548 to 1623 K, and starlike precipitates with a stripe pattern and with a dense appearance were both observed; the former comprised the M23C6 type carbide + γ-phase, and the latter was the π-phase. In contrast, only a blocky-dense M23C6 type carbide was observed at 1473 to 1523 K.
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Chemezova, K. S., and N. M. Khlynova. "FORMATION OF ANODE ARSENATE FILM ON SILVER ELECTRODE." IZVESTIYA VYSSHIKH UCHEBNYKH ZAVEDENIY KHIMIYA KHIMICHESKAYA TEKHNOLOGIYA 59, no. 1 (June 7, 2018): 63. http://dx.doi.org/10.6060/tcct.20165901.5174.

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The single current peak is registrated on voltammograms of electro dissolution of precipitates forming on silver electrode into solutions containing arsenate ions. The precipitate amount is proportional to a concentration of arsenate ions in a solution. This amount can be used for ions determination. Optimal conditions for electro deposition and electro dissolution are recommended.
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Liu, Yong, Dongyu Fang, Bin Zhu, Yilin Wang, Shiqi Li, and Yisheng Zhang. "Modeling of Isothermal Dissolution of Precipitates in a 6061 Aluminum Alloy Sheet during Solution Heat Treatment." Metals 11, no. 8 (August 3, 2021): 1234. http://dx.doi.org/10.3390/met11081234.

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During the solution heat treatment (SHT) process of aluminum alloys, precipitates dissolve into the matrix. To predict the dissolution time, modeling of isothermal dissolution of precipitates in 6061 aluminum alloy during SHT was conducted. A precipitate dissolution model was established, and the flowchart of the modeling was designed as well. Then the explicit finite-difference method was employed to solve the dissolution model, and the mobile nodes method was used to deal with the moving interface. The simulation was based on real precipitates in 6061, and SHT experiments were conducted to validate the numerical model. The simulation results showed that the isothermal dissolution time of precipitates in 6061-T6 aluminum alloy at 560 °C is 11.6856 s. The dissolution time in the simulation was close to the experimental results, with an error of 16.7%, indicating that the modeling in this study was fairly reasonable and accurate. The error was caused by many factors, and the model should be improved.
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Ueki, Kosuke, Motoka Kasamatsu, Kyosuke Ueda, Yuichiro Koizumi, Daixiu Wei, Akihiko Chiba, and Takayuki Narushima. "Precipitation during γ-ε Phase Transformation in Biomedical Co-Cr-Mo Alloys Fabricated by Electron Beam Melting." Metals 10, no. 1 (January 2, 2020): 71. http://dx.doi.org/10.3390/met10010071.

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We studied the precipitates that were induced during γ-ε phase transformation in biomedical Co-28Cr-6Mo (mass%) alloys that were fabricated by electron beam melting with carbon contents of 0.184 and 0.018 mass%. In the high-C as-built alloy, M23X6-type, π-phase (M3T2X-type), and η-phase (M6X-M12X-type) precipitates were observed (M and T: metallic elements, X: C and/or N). σ-phase (Co(Cr,Mo)), π-phase, and Co3Mo2Si-type precipitates were observed in the low-C as-built alloy. This is the first report that shows the presence and chemical composition of this precipitate, as the Co3Mo2Si-type precipitate has not been detected in biomedical Co-Cr-Mo alloys before. After aging in the ε-phase stability region, the high-C and low-C alloys both contained a single ε-phase matrix, and the amount of π-phase precipitates increased. Conversely, the amount of π-phase precipitates in both alloys decreased when a reverse transformation treatment was applied in the γ-phase stability region after aging. In the low-C alloy, the amount of Co3Mo2Si-type precipitates increased after reverse transformation treatment. These results indicate that the dissolution of π-phase precipitates and the formation of Co3Mo2Si-type precipitates during reverse transformation promote the formation of fine γ-phase grains at the precipitate/ε-phase matrix interface, because the formation and dissolution of these precipitates affect the γ-phase stability of the matrix.
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Katsman, A., Anton Gorny, D. Shepelev, and Menachem Bamberger. "Evolution of Precipitate Depleted Zones in Mg-Based Alloys Strengthened by Precipitation Hardening." Defect and Diffusion Forum 289-292 (April 2009): 153–59. http://dx.doi.org/10.4028/www.scientific.net/ddf.289-292.153.

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Extensive research work has been devoted to Mg-based alloys strengthened by precipitation hardening. Increasing the aging time leads to the appearance of zones depleted of precipitates near grain boundaries. The formation of precipitate depleted zones (PDZ's) is explained by near-grain boundary (NGB) coarsening. The evolution of PDZ's was considered on the basis of the model taking into account diffusional fluxes between adjacent precipitates. The set of equations was solved numerically by using a fourth-order Runge-Kutta method for different initial sizes of precipitates and densities of precipitate layers near grain boundaries. The dissolution of precipitates in the NGB-zones is initially provided by diffusion from them to large precipitates at the grain boundary, and then also by diffusion from these decreased precipitates to the larger precipitates at the outer border of the PDZ. As a result, the outer borders of the depleted zones are adjoined by bands of enlarged precipitates forming a PDZ "crust". Being a diffusion controlled process, the depleted zones are widened with temperature and aging time. Experimental investigation of PDZ evolution was conducted by SEM and TEM on Mg-Zn-Sn-alloys aged at different temperatures for different times. Comparison of the calculated results with experimental data allowed the evaluation of the model parameters and physical parameters of the system (diffusion coefficients and interface energy of the precipitated phases).
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Danielsen, Hilmar Kjartansson. "Atomic Resolution Microscopy of Nitrides in Steel." Materials Science Forum 783-786 (May 2014): 1617–22. http://dx.doi.org/10.4028/www.scientific.net/msf.783-786.1617.

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MN and CrMN type nitride precipitates in 12%Cr steels have been investigated using atomic resolution microscopy. The MN type nitrides were observed to transform into CrMN both by composition and crystallography as Cr diffuses from the matrix into the MN precipitates. Thus a change from one precipitate type to another does not necessarily involve nucleation of the new precipitate type followed by dissolution of the old precipitates. By studying the interface between these nitrides and the matrix, it could be observed that the MN and CrMN type precipitates had a few nanometers thick amorphous layer between the crystalline nitride and ferrite matrix. Usually precipitates are described as having (semi) coherent or incoherent interfaces, but in this case it is more energetically favourable to create an amorphous layer instead of the incoherent interface.
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Narushima, T., Alfirano, S. Mineta, Shigenobu Namba, Takashi Yoneda, and Kyosuke Ueda. "Precipitates in Biomedical Co-Cr-Mo-C-Si-Mn Alloys." Advanced Materials Research 277 (July 2011): 51–58. http://dx.doi.org/10.4028/www.scientific.net/amr.277.51.

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The phase and dissolution behavior of precipitates in biomedical ASTM F75 Co-Cr-Mo-C-Si-Mn alloys were investigated. Alloys of five different compositions, Co-28Cr-6Mo-0.25C-1Si, Co-28Cr-6Mo-0.25C-1Mn, Co-28Cr-6Mo-0.25C-1Si-1Mn, Co-28Cr-6Mo-0.15C-1Si, and Co-28Cr-6Mo-0.35C-1Si, were heat-treated from 1448 to 1548 K. The precipitates observed in the as-cast and heat-treated alloys were carbides (M23C6type, h-phase, and p-phase) and an intermetallic compound (c-phase). The main precipitates observed after heat treatment at high temperatures such as 1548 K were p-phase and M23C6type carbide. At these high temperatures, two types of starlike precipitates—dense and stripe-patterned—were observed. The starlike-dense precipitate was the p-phase, and the starlike precipitate with a stripe pattern was identified as the M23C6type carbide and metallic fcc g-phase. In the alloys heat-treated at 1448 to 1498 K, blocky-dense M23C6type carbide was primarily observed. c-phase was detected in the Co-28Cr-6Mo-0.15C-1Si alloy under as-cast condition and after heat treatment at 1448–1523 K for a short holding time. The addition of Si seemed to increase the holding time for complete precipitate dissolution because of the effects of Si on the promotion of p-phase formation at high temperatures and the increased carbon activity in the metallic matrix.
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Sharma, Chaitanya, and Vikas Upadhyay. "Investigating the Effect of Friction Stir Welding on Microstructure and Corrosion Behaviour of Al-Zn-Mg Alloy." Materials Science Forum 969 (August 2019): 517–23. http://dx.doi.org/10.4028/www.scientific.net/msf.969.517.

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In this work, Friction Stir Welding (FSW) of alloy 7039 was carried out in T4 temper and resulting microstructure and corrosion behaviour of developed weld were studied. FSW transformed the starting microstructure of base metal and formed stirred zone (SZ) and heat affected zone (HAZ) with varying microstructure and precipitate morphology. The observed zones in welded joints exhibited decreased protection to corrosion resistance than base metal. Dissolution of secondary precipitates in SZ and occurrence of precipitate free zones (PFZs) in HAZ enhanced susceptibility to corrosion of HAZ and weld nugget zone (WNZ) than base metal.
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Dissertations / Theses on the topic "Precipitate dissolution"

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Susanto, Benny Laurensius Materials Science &amp Engineering Faculty of Science UNSW. "Kinetics of carbide dissolution in chromium + molybdenum steels during oxidation." Awarded by:University of New South Wales. Materials Science and Engineering, 2004. http://handle.unsw.edu.au/1959.4/19385.

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Iron-based alloys containing 15% chromium, 2-3% molybdenum and 0.02-1.7% carbon, consisting of M23C6 and M6C carbides in an austenitic matrix were oxidised at 8500C to study their oxidation resistance and a precipitate-free zone formation. Alloy design was carried out using a thermodynamic software Thermo-Calc. Carbides in these alloys were expected to dissolve during oxidation, releasing chromium required for the protective oxide formation. Decarburisation of the matrix was expected to trigger the carbide dissolution, and form a precipitate-free zone. Transformation of the austenitic into ferritic matrix in the precipitate-free zone was expected be essential for providing a fast chromium supply to the oxide/alloy interface. Upon exposure to pure oxygen, most of the alloys oxidised non-protectively due to the fast oxidation attack and low chromium content in the matrix, while carbide dissolution was too slow. The alloys were then pre-oxidised in H2+10%H2O to grow a purely chromia scale. In this low oxygen partial pressure environment, carbides in the alloy's sub-surface dissolved and formed a ferritic precipitate-free zone. The precipitate dissolution model developed by previous investigators was then tested and proven to be valid in this iron-based alloy system. The endurance of the pre-formed chromia scale with its underlying precipitate-free zone was then tested in pure oxygen environment. All of the alloys that had successfully developed a ferritic precipitate-free zone in the pre-oxidation stage, survived the subsequent oxidation in pure oxygen up until 3 weeks observation. Although x-ray diffraction found some minor iron oxides, the oxide consisted of mainly Cr2O3. Since iron activity had increased and iron oxides had become stable after the pure oxygen gas was introduced, the growth of the precipitate-free zone had to compete with the rate at which it was consumed by oxidation. It was concluded that the transformation from austenite to ferrite at the subsurface region of the alloy could be achieved provided that the volume fraction of the carbides did not exceed 0.2. Evidence indicated that the chromia scale grew by chromium provided by the dissolving carbides. Pre-oxidation led to a promising use of the alloys at atmospheric oxygen pressure.
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Hammons, Joshua Aaron. "A study of precipitated films formed during electrochemically driven dissolution processes." Thesis, University of Birmingham, 2012. http://etheses.bham.ac.uk//id/eprint/3165/.

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Precipitated surface films form when metal cations are produced faster than they can move away from the dissolving interface. This build up of cations results in supersaturation conditions, which cause a solid to precipitate. The precipitated solid affects ion transport and thus the dissolution kinetics, which ultimately control the two systems studied here. X-ray diffraction, small angle X-ray scattering and fast radiography were chosen to study the metal/solution interface in-situ, using synchrotron radiation. The AC electrograining system is a widely used industrial process whereby an alternating current is applied to aluminium plates to form a pitted surface. During this process, an Al(OH)3 surface gel (smut) forms within seconds whilst electrograining continues for several minutes in its presence. Although smut formation has been investigated previously, how the smut affects metal dissolution is currently unknown and is the primary goal of this project. The second system is a nickel “artificial pit,” which is commonly used to simulate pit propagation. In this system, a salt film is precipitated by imposing a large overpotential whilst restricting transport through a 1-D pit. Interfacial phenomena that occur during salt film formation are investigated towards an understanding of how the salt film forms.
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Baron, Dirk. "Iron-chromate precipitates in CR(VI)-contaminated soils : identification, solubility, and solid solution/aqueous solution reactions." Full text open access at:, 1996. http://content.ohsu.edu/u?/etd,217.

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Smart, Heather. "A study of directionally solidified Rene 80 subjected to short-term overtemperature." 2017. http://hdl.handle.net/1993/32170.

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Effects of short-term overtemperature on Rene 80 DS were studied using Gleeble thermo-mechanical simulation apparatus. Volume fraction of gamma prime to gamma matrix was quantified and used to assess the effects of time, temperature and stress. Volume fraction was found to decrease with increasing temperature and time. Dissolution was found to occur through both solid and liquid state dissolution. Application of tensile stress was found to influence dissolution behaviour of gamma prime.
May 2017
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Book chapters on the topic "Precipitate dissolution"

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Klein, Gerhard. "Fixed-Bed Ion Exchange with Formation or Dissolution of Precipitate." In Ion Exchange: Science and Technology, 199–226. Dordrecht: Springer Netherlands, 1986. http://dx.doi.org/10.1007/978-94-009-4376-6_7.

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Wollenberger, H., S. Matsumura, S. Müller, and C. Abromeit. "Radiation-Induced Disordering and Dissolution of LRO Precipitates in Disordered Matrix." In Stability of Materials, 687–92. Boston, MA: Springer US, 1996. http://dx.doi.org/10.1007/978-1-4613-0385-5_54.

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Conforto, Egle, Stephane Cohendoz, Patrick Girault, Cyril Berziou, and Xavier Feaugas. "Hydride Precipitates in Zirconium Alloys: Evolution of Dissolution and Precipitation Temperatures During Thermal Cycling Correlated to Microstructure Features." In TMS 2017 146th Annual Meeting & Exhibition Supplemental Proceedings, 771–82. Cham: Springer International Publishing, 2017. http://dx.doi.org/10.1007/978-3-319-51493-2_74.

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Haworth, C. W. "Precipitate Dissolution." In Encyclopedia of Materials: Science and Technology, 7818–20. Elsevier, 2001. http://dx.doi.org/10.1016/b0-08-043152-6/01405-4.

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Skoko, Željko, and Stanko Popović. "Microstructure of Al-Cu, Al-Zn, Al-Ag-Zn, and Al-Zn-Mg Alloys." In Encyclopedia of Aluminum and Its Alloys. Boca Raton: CRC Press, 2019. http://dx.doi.org/10.1201/9781351045636-140000172.

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The precipitation phenomena and their connection with the microstructure of several Al alloys (Al-Cu, Al-Zn, Al-Ag-Zn, Al-Zn-Mg) are described with respect to the concentration and applied thermal treatment. The alloys were rapidly quenched or slowly cooled from a temperature higher than the solid solution temperature to room temperature. Both quenched-aged and slowly cooled alloys were heated from room temperature to the solid solution state and cooled back to room temperature, and their microstructure and precipitation phenomena were followed in situ by X-ray powder diffraction, e.g., anisotropy of thermal expansion, phase transitions, thermal hysteresis in phase transitions, change of precipitate shape, partial or complete dissolution of precipitates in the matrix, and formation of solid solution. It has been shown that the microstructure strongly depends on the previous thermal history of the alloys.
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Jolivet, Jean-Pierre. "Conclusion." In Metal Oxide Nanostructures Chemistry. Oxford University Press, 2019. http://dx.doi.org/10.1093/oso/9780190928117.003.0012.

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Metal oxide nanostructures are of major interest in technology. It is therefore es­sential to have a full understanding of the phenomena involved in the aqueous synthesis of nanoparticles, so that their properties can be adjusted to a desired application. Understanding these phenomena is also important in other fields, for instance, in geology and environmental sciences, enabling us to explain the presence and formation of a given mineral. The precipitation of metal oxy(hydroxi)des is a complex phenomenon initiated by hydroxylation of the cations in solution and resulting from condensation of the hydroxylated species. Therefore, the acidity of the cations is the main charac­teristic of their reactivity. Three main parameters are essential in predicting and rationalizing the behavior of metal cations in water: the formal charge (the oxida­tion degree), size, and electronegativity, which determine the degree of polariza­tion of the oxygenated ligands. One may thus define five classes of cations: . . . The too weakly polarizing cations that form only aquocomplexes unable to condense and to precipitate; for instance, the alkaline cations M+, The cations that condense by olation and form polycations and hydroxides, typically, the divalent cations and also Al3+. The cations that condense by olation and oxolation and form oxyhydroxides and oxides (such as Cr3+, Fe3+, and Mn3+). The cations that condense essentially by oxolation and form oxides that are more or less hydrated (Ti4+, Mn4+, V5+). The cations that form anionic oxocomplexes and exhibit no trend toward condensation, typically, MnVII. . . . This series thus includes cations of increasing polarizing power, that is cations of increasing oxidation degree and electronegativity. Precipitation usually generates nanosized particles. In a system that is not con­tinuously fed, in which a limited amount of matter is available in the reactor, the nucleation step is always sudden and easy enough, allowing lower supersaturation and creating nuclei that have stopped growing because of the too low concentra­tion in soluble precursor. That does not, however, exclude an intense dynamics of dissolution–crystallization because of the evolution of the criticality of the particle size during the decrease in supersaturation.
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"Hydride Precipitates in Zirconium Alloys: Formation, Dissolution, Stability After Temperature Cycling and Crystallographic Relationships." In International Hydrogen Conference (IHC 2016): Materials Performance in Hydrogen Environments, 548–56. ASME Press, 2017. http://dx.doi.org/10.1115/1.861387_ch62.

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Anil Kumar, V., S. Arjun, R. K. Gupta, and P. V. Venkitakrishnan. "Retrogression and Re-aging Heat Treatment: AA7XXX Aluminum Alloys." In Encyclopedia of Aluminum and Its Alloys. Boca Raton: CRC Press, 2019. http://dx.doi.org/10.1201/9781351045636-140000213.

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Retrogression and re-aging (RRA) treatment was introduced to increase the stress corrosion cracking (SCC) resistance while retaining the strength attainable in T6 (peak aged) temper. Retrogression is a short-term heat treatment at an elevated temperature wherein a partial dissolution of metastable precipitates occurs, which are responsible for the hardening. During the next step, the material is re-aged in the regime of typical age hardening parameters to restore the strength with improved ductility. Response of RRA treatment has been reported on AA7XXX series Aluminum alloys such as AA7075, AA7050, AA7150, AA7049, and AA7010. Studies have been done on the effect of RRA on microstructure, mechanical properties such as tensile and hardness, corrosion, exfoliation corrosion, and SCC resistance by various researchers. The key characteristic of RRA is retrogression, which makes the re-precipitation in the matrix and coarsening of grain boundary precipitates such as MgZn2, η′. The retrogression treatment however requires high temperature and a short time, which limits the industrial application of RRA, especially in the heat treatment of the components with large cross section, due to the inherent thermal conductivity limitations. Hence, further work needs to be done in this area to apply this specialized heat treatment for industrial applications. This article brings out a comprehension of the changes in microstructure, tensile properties, and corrosion resistance of the various commonly used AA7XXX Aluminum alloys in structural applications with RRA heat treatment. The future scope of the work in RRA heat treatment is also discussed in this article.
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Conference papers on the topic "Precipitate dissolution"

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Hieslmair, H., A. A. Istratov, C. Flink, and E. R. Weber. "Fe/Cu precipitation and precipitate dissolution in silicon." In National center for photovoltaics (NCPV) 15th program review meeting. AIP, 1999. http://dx.doi.org/10.1063/1.57914.

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Looney, Erin E., Hannu S. Laine, Mallory A. Jensen, Amanda Youssef, Vincenzo LaSalvia, Paul Stradins, and Tonio Buonassisi. "Tabula Rasa: Oxygen precipitate dissolution though rapid high temperature processing in silicon." In 2017 IEEE 44th Photovoltaic Specialists Conference (PVSC). IEEE, 2017. http://dx.doi.org/10.1109/pvsc.2017.8366688.

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Wiskel, J. B., X. Li, J. Lu, D. G. Ivey, and H. Henein. "The Application of Quantitative X-Ray Diffraction (Rietveld Refinement) in Characterizing the Microstructure and Precipitates in Microalloyed Steels." In 2010 8th International Pipeline Conference. ASMEDC, 2010. http://dx.doi.org/10.1115/ipc2010-31033.

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Quantitative X-ray diffraction (the Rietveld Method) was used to quantify both the crystallite size (diffracting length) and precipitate size in several grades of microalloyed steels. The crystallite size calculated from diffraction profiles obtained from the rolling faces of X80 and X100 was found to decrease with decreasing coiling temperature. Quantitative X-ray diffraction analysis was also conducted on precipitate residues extracted (by matrix dissolution) from a Grade 100 microalloyed steel. A mean precipitate size of 4.8 nm was calculated for the fine (Nb, Mo, Ti, V) carbides observed in this steel. This value compares favourably with precipitate size measured using TEM and SANS analysis.
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Lundin, Carl D., and Cong-Yue P. Qiao. "Microstructural Investigation of the Weld HAZ in a Modified 800H Alloy." In ASME 1993 International Gas Turbine and Aeroengine Congress and Exposition. American Society of Mechanical Engineers, 1993. http://dx.doi.org/10.1115/93-gt-202.

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Detailed metallographic investigations of Gleeble simulated HAZ samples in modified 800H were performed. Precipitate dissolution, grain growth, HAZ liquation and the hardness degradation behavior in modified 800H were also addressed. Results of this study agree with previous HAZ hot cracking and softening behavior evaluations.
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Sopori, Bhushan, Srinivas Devayajanam, Prakash Basnyat, Teh Tan, Ajay Upadhyaya, Ajeet Rohatgi, and Han Xu. "Notice of Removal Dissolution of oxygen precipitate nuclei in N-type CZ Si wafers to improve their material quality: Experimental results." In 2017 IEEE 44th Photovoltaic Specialists Conference (PVSC). IEEE, 2017. http://dx.doi.org/10.1109/pvsc.2017.8366188.

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Cryderman, Robert, Dalton Garrett, and Zachary Schlittenhart. "Effects of Rapid Induction Heating on Transformations in 0.6% C Steels." In HT2019. ASM International, 2019. http://dx.doi.org/10.31399/asm.cp.ht2019p0106.

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Abstract Rapid induction hardening of martensitic steel can attain the very high strength levels needed for light-weighting components subjected to high operating stresses. Specimens of martensitic 0.6% C steels were heat treated using a dilatometer to investigate the effects of heating rates of 5 to 500 °C/s to temperatures of 850 to 1050 °C on the transformation to austenite and subsequent transformation to martensite during quenching. Selected specimens were quenched after partial transformation to austenite to assess the initial cementite precipitate size formed in ferrite during heating. Other specimens were isothermally held at the austenitizing temperature to assess cementite dissolution rates. Higher heating rates increased the Ac1 and Ac3 temperatures, and lowered the Ms temperature. Alloy content and prior microstructure also influenced the transformation temperatures.
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7

Zhao, Yanping, Jianming Gong, and Yong Jiang. "The Effect of Carbon Diffusion on Creep Behaviours for a Dissimilar Joint Between P91 and 12Cr1MoV Steels." In ASME 2016 Pressure Vessels and Piping Conference. American Society of Mechanical Engineers, 2016. http://dx.doi.org/10.1115/pvp2016-63108.

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Dissimilar joints have been widely used in many applications, especially for steam piping in the superheater and reheater of power plants. However, these dissimilar metal welds tend to fail less than half of their design life, and carbon diffusion is the main cause of the premature failure. Dissimilar joints operated at high temperature or after post-weld heat treatment (PWHT) exhibit carbon-enriched zone (CEZ) in the high alloy part and carbon-depleted zone (CDZ) in the low alloy part, causing by the chemical potential gradients across the weld interface. The carbides dissolute in the low alloy part while precipitate in the high alloy part. At the same time, a consequent of strength gradients are generated between the CEZ and CDE. The CDZ results in a loss of creep strength due to the carbides dissolution while an increase of strength due to the carbides precipitation. In this work, welding consumable of GTR-2CM was used to join P91 and 12Cr1MoV metals together. The stable phases and carbon activities of these metals are calculated by THERMO-CALC software. Carbon diffusion between P91/GTR-2CM/12Cr1MoV dissimilar joint after aging at 550 °C for varying time are predicted by employing dispersed multiphase model in DICTRA software. Volume fractions of carbides varying with distance from both sides of the weld interfaces were also investigated, showing that the formation of CDZs and CEZs is related to the dissolution and precipitation of M23C6 and M7C3 carbides. The dissolution and coarsening of M7C3 and M23C6 particles in the CDZ and CEZ were also modelled by DICTRA software. The creep properties of base metals, weld metal and the dissimilar joint were investigated at 550 °C. The stress dependence of minimum creep rate and rupture life obeyed the Norton’s power law, and the stress exponents can be used to identify the creep mechanism. Monkman-Grant (MG) relations were also used to study the creep rupture data. The simulation results of carbon diffusion can be used to study the creep properties of CDZ and CEZ for the P91/GTR-2CM/12Cr1MoV dissimilar joint. The threshold stress concept can be incorporated into the analysis of creep power law. The magnitudes of threshold stress within CEZ and CDZ can be calculated according to the volume fraction and average diameter of carbides from carbon diffusion.
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8

Poole, W. J., M. Militzer, F. Fazeli, M. Maalekian, C. Penniston, and D. Taylor. "Microstructure Evolution in the HAZ of Girth Welds in Linepipe Steels for the Arctic." In 2010 8th International Pipeline Conference. ASMEDC, 2010. http://dx.doi.org/10.1115/ipc2010-31155.

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A critical aspect of building pipelines to transport natural gas will be development of suitable high strength steels and new economic welding procedures, e.g. dual torch welding, without compromising the pipeline’s structural integrity during its in-service performance. The objective of this project is to predict the microstructure and mechanical properties of the weld heat affected zone (HAZ) of an X80 linepipe steel as a function of its temperature-time history. The approach taken involves a combination of experimental techniques and advanced modelling approaches. On the experimental side, dual-torch weld trials for assessment of spatial and temporal variations of temperature in the HAZ were conducted. To simulate and investigate the microstructure evolutions in the HAZ, i.e. precipitate dissolution, austenite formation, grain growth and decompositions, Gleeble thermo-mechanical simulations were performed. These simulations include rapid heating and cooling tests at rates of up to 1000 °C/s. Notably, real-time monitoring of austenite grain growth was possible by using a novel laser ultrasonic technique. Further, bulk samples were produced using the Gleeble adopting the experimentally determined temperature time history. These bulk specimens were subsequently subjected to tensile and fracture resistance tests. A concise overview of these novel experimental activities, highlighting new insights, is presented and challenges associated with the measurements are discussed.
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9

Romualdi, Nicolas, Matthias Militzer, Warren Poole, Laurie Collins, and Robert Lazor. "Austenite Grain Size Model for the Coarse Grain Heat Affected Zone in Line Pipe Steels." In 2020 13th International Pipeline Conference. American Society of Mechanical Engineers, 2020. http://dx.doi.org/10.1115/ipc2020-9687.

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Abstract Pipelines are the safest and most cost-effective method of oil and gas transportation to storage and processing facilities. Large diameter welded pipes fabricated by submerged arc welding (SAW) are the preferred product in many cases for pipeline construction. Furthermore, pipelines are constructed by welding segments of pipe, typically by single or dual torch Gas Metal Arc Welding (GMAW). During welding, both during pipe fabrication and girth welding, the Heat Affected Zone (HAZ) experiences rapid thermal cycles with peak temperatures up to the melting temperature of the base metal. Controlling the microstructure evolution in the HAZ during welding of line pipe steels is critical to ensure that these products meet the Charpy impact testing and CTOD requirements imposed by clients and specifications. In particular, the Coarse Grain Heat Affected Zone (CGHAZ) is of concern. Here, austenite grain growth occurs readily due to the combination of high temperature and precipitate dissolution. Controlling the CGHAZ austenite grain size is critical to obtain final microstructures with acceptable impact properties. In this study, austenite grain growth has been measured and modeled for thermal conditions relevant for the CGHAZ in 27 steels, including industrial as well as laboratory steels with systematic variations of alloying element content. Austenite grain size was measured using a Laser Ultrasonics for Metallurgy (LUMet) sensor attached to a Gleeble 3500 Thermomechanical Simulator, which enables high-throughput in-situ monitoring of austenite grain growth. A classical grain growth model has been developed based on a standard test. The grain growth kinetics are described by combining curvature driven grain growth with pinning due to TiN precipitates. A phenomenological relationship has been developed for the grain boundary mobility that decreases with C, Nb and Mo alloying which is consistent with their expected grain boundary segregation. The pinning parameter is rationalized in terms of volume fraction and size of TiN particles. The proposed model has been validated for CGHAZ heat treatment cycles including an industrial welding trial. The results of this study provide a model to predict the austenite grain size in the CGHAZ as a function of steel chemistries and heat treatment paths, i.e. welding parameters. Austenite grain size maps have been constructed as a function of peak local temperature and line pipe steel chemistry. The model can be used both for steel chemistry design and for optimizing welding of steels with known chemical composition to minimize the CGHAZ austenite grain size both during pipe fabrication and girth welding.
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10

Lu, Junfang, Douglas Ivey, and Hani Henein. "Quantification of Nano-Sized Precipitates in Microalloyed Steels by Matrix Dissolution." In 2006 International Pipeline Conference. ASMEDC, 2006. http://dx.doi.org/10.1115/ipc2006-10600.

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Microalloyed steels possess good strength, toughness and excellent weldability, all of which are necessary attributes for oil and gas pipelines in northern climates. These properties are attributed in part to the presence of nano-sized Nb/Ti carbide precipitates. In order to understand the strengthening mechanisms and to optimize the strengthening effects, it is necessary to quantify the size distribution, volume fraction and chemical speciation of these precipitates. However, characterization techniques suitable for quantifying fine precipitates are limited. A matrix dissolution method has been developed to extract the nano-sized precipitates from microalloyed steels. The results from Grade 100 microalloyed steel are presented in this paper.
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Reports on the topic "Precipitate dissolution"

1

Tan, T. Y., and N. Li. Precipitate Dissolution and Gettering under Vacancy Injection in Silicon: Final Subcontract Report, 21 March 2006 - 15 January 2008. Office of Scientific and Technical Information (OSTI), September 2008. http://dx.doi.org/10.2172/939277.

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2

Tan, T. Y. Modeling Metallic Precipitate Dissolution in Silicon Under Point Defect Injection: Final Subcontract Report, 20 January 2004--19 January 2005. Office of Scientific and Technical Information (OSTI), May 2005. http://dx.doi.org/10.2172/15016265.

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3

Estill, J., J. Farmer, S. Gordon, K. King, L. Logotetta, and D. Silberman. Distribution of soluble and precipitated iron and chromium products generated by anodic dissolution of 316L stainless steel and alloy C-22: final report. Office of Scientific and Technical Information (OSTI), August 1999. http://dx.doi.org/10.2172/10450.

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