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precipitates</title> <meta name="description" content="Search results for: precipitates"> <meta name="keywords" content="precipitates"> <meta name="viewport" content="width=device-width, initial-scale=1, minimum-scale=1, maximum-scale=1, user-scalable=no"> <meta charset="utf-8"> <link href="https://cdn.waset.org/favicon.ico" type="image/x-icon" rel="shortcut icon"> <link href="https://cdn.waset.org/static/plugins/bootstrap-4.2.1/css/bootstrap.min.css" rel="stylesheet"> <link href="https://cdn.waset.org/static/plugins/fontawesome/css/all.min.css" rel="stylesheet"> <link href="https://cdn.waset.org/static/css/site.css?v=150220211555" rel="stylesheet"> </head> <body> <header> <div class="container"> <nav class="navbar navbar-expand-lg navbar-light"> <a class="navbar-brand" href="https://waset.org"> <img src="https://cdn.waset.org/static/images/wasetc.png" alt="Open Science Research Excellence" title="Open Science Research Excellence" /> </a> <button class="d-block d-lg-none navbar-toggler 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id="custom-search-input"> <div class="input-group"> <i class="fas fa-search"></i> <input type="text" class="search-query" name="q" placeholder="Author, Title, Abstract, Keywords" value="precipitates"> <input type="submit" class="btn_search" value="Search"> </div> </div> </form> </div> </div> <div class="row mt-3"> <div class="col-sm-3"> <div class="card"> <div class="card-body"><strong>Commenced</strong> in January 2007</div> </div> </div> <div class="col-sm-3"> <div class="card"> <div class="card-body"><strong>Frequency:</strong> Monthly</div> </div> </div> <div class="col-sm-3"> <div class="card"> <div class="card-body"><strong>Edition:</strong> International</div> </div> </div> <div class="col-sm-3"> <div class="card"> <div class="card-body"><strong>Paper Count:</strong> 78</div> </div> </div> </div> <h1 class="mt-3 mb-3 text-center" style="font-size:1.6rem;">Search results for: precipitates</h1> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">78</span> Isolation, Preparation and Biological Properties of Soybean-Flaxseed Protein Co-Precipitates</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Muhammad%20H.%20Alu%E2%80%99datt">Muhammad H. Alu’datt</a>, <a href="https://publications.waset.org/abstracts/search?q=Inteaz%20Alli"> Inteaz Alli</a> </p> <p class="card-text"><strong>Abstract:</strong></p> This study was conducted to prepare and evaluate the biological properties of protein co-precipitates from flaxseed and soybean. Protein was prepared by NaOH extraction through the mixing of soybean flour (Sf) and flaxseed flour (Ff) or mixtures of soybean extract (Se) and flaxseed extract (Fe). The protein co-precipitates were precipitated by isoelectric (IEP) and isoelectric-heating (IEPH) co-precipitation techniques. Effects of extraction and co-precipitation techniques on co-precipitate yield were investigated. Native-PAGE, SDS-PAGE were used to study the molecular characterization. Content and antioxidant activity of extracted free and bound phenolic compounds were evaluated for protein co-precipitates. Removal of free and bound phenolic compounds from protein co-precipitates showed little effects on the electrophoretic behavior of the proteins or the protein subunits of protein co-precipitates. Results showed that he highest protein contents and yield were obtained in for Sf-Ff/IEP co-precipitate with values of 53.28 and 25.58% respectively as compared to protein isolates and other co-precipitates. Results revealed that the Sf-Ff/IEP showed a higher content of bound phenolic compounds (53.49% from total phenolic content) as compared to free phenolic compounds (46.51% from total phenolic content). Antioxidant activities of extracted bound phenolic compounds with and without heat treatment from Sf-Ff/IEHP were higher as compared to free phenolic compounds extracted from other protein co-precipitates (29.68 and 22.84%, respectively). <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=antioxidant" title="antioxidant">antioxidant</a>, <a href="https://publications.waset.org/abstracts/search?q=phenol" title=" phenol"> phenol</a>, <a href="https://publications.waset.org/abstracts/search?q=protein%20co-precipitate" title=" protein co-precipitate"> protein co-precipitate</a>, <a href="https://publications.waset.org/abstracts/search?q=yield" title=" yield"> yield</a> </p> <a href="https://publications.waset.org/abstracts/47994/isolation-preparation-and-biological-properties-of-soybean-flaxseed-protein-co-precipitates" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/47994.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">239</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">77</span> Effect of Aging on Hardness and Corrosion Resistance of WE43 Magnesium Alloy</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Ziya%20Esen">Ziya Esen</a>, <a href="https://publications.waset.org/abstracts/search?q=%C3%96zg%C3%BCr%20Duygulu"> Özgür Duygulu</a>, <a href="https://publications.waset.org/abstracts/search?q=Nazl%C4%B1%20S.%20B%C3%BCy%C3%BCkatak"> Nazlı S. Büyükatak</a> </p> <p class="card-text"><strong>Abstract:</strong></p> This study investigates the effects of aging heat treatment on corrosion resistance and mechanical properties of WE43 Magnesium alloy. The heat treatment of alloys was conducted by solutionizing at 525oC for 16 h, followed by aging at 190, 210 and 230oC for up to 48 h. The type and the size of precipitates formed upon aging have influenced both the mechanical properties and corrosion behavior of the alloy. Solutionized alloy displayed the worst corrosion resistance in simulated body fluid, while peak hardness and the best corrosion resistance were observed in the alloy aged at 210oC for 24 h as a result of β’ precipitate formation. Longer aging duration at 210oC decreased the corrosion rate due to the coarsening of the precipitates and formation of precipitate-free zones. The increased corrosion resistance of the peak aged samples was attributed to the slowing down effect of the Mg(OH)₂/MgO corrosion layer by the pinning effect of β’-precipitates. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=WE43%20magnesium%20alloy" title="WE43 magnesium alloy">WE43 magnesium alloy</a>, <a href="https://publications.waset.org/abstracts/search?q=simulated%20body%20fluid" title=" simulated body fluid"> simulated body fluid</a>, <a href="https://publications.waset.org/abstracts/search?q=corrosion" title=" corrosion"> corrosion</a>, <a href="https://publications.waset.org/abstracts/search?q=mechanical%20properties" title=" mechanical properties"> mechanical properties</a> </p> <a href="https://publications.waset.org/abstracts/186918/effect-of-aging-on-hardness-and-corrosion-resistance-of-we43-magnesium-alloy" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/186918.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">5</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">76</span> Comparison of the Hydration Products of Commercial and Experimental Calcium Silicate Cement: The Preliminary Observational Study</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Seok%20Woo%20Chang">Seok Woo Chang</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Aim: The objective of this study was to compare and evaluate the hydration products of commercial and experimental calcium silicate cement. Materials and Methods: The commercial calcium silicate cement (ProRoot MTA, Dentsply) and experimental calcium silicate cement (n=10) were mixed with distilled water (water/powder ratio = 20 w/w) and stirred at room temperature for 10 hours. These mixtures were dispersed on wafer and dried for 12 hours at room temperature. Thereafter, the dried specimens were examined with Scanning Electron Microscope (SEM). Electron Dispersive Spectrometry (EDS) was also carried out. Results: The commercial calcium silicate cement (ProRoot MTA) and experimental calcium silicate cement both showed precipitation of rod-like and globule-like crystals. Based on EDS analysis, these precipitates were supposed to be calcium hydroxide or calcium silicate hydrates. The degree of formation of these precipitates was higher in commercial MTA. Conclusions: Based on the results, both commercial and experimental calcium silicate cement had ability to produce calcium hydroxide or calcium silicate hydrate precipitates. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=calcium%20silicate%20cement" title="calcium silicate cement">calcium silicate cement</a>, <a href="https://publications.waset.org/abstracts/search?q=ProRoot%20MTA" title=" ProRoot MTA"> ProRoot MTA</a>, <a href="https://publications.waset.org/abstracts/search?q=precipitation" title=" precipitation"> precipitation</a>, <a href="https://publications.waset.org/abstracts/search?q=calcium%20hydroxide" title=" calcium hydroxide"> calcium hydroxide</a>, <a href="https://publications.waset.org/abstracts/search?q=calcium%20silicate%20hydrate" title=" calcium silicate hydrate"> calcium silicate hydrate</a> </p> <a href="https://publications.waset.org/abstracts/8741/comparison-of-the-hydration-products-of-commercial-and-experimental-calcium-silicate-cement-the-preliminary-observational-study" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/8741.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">265</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">75</span> Corrosion Response of Friction Stir Processed Mg-Zn-Zr-RE Alloy</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Vasanth%20C.%20Shunmugasamy">Vasanth C. Shunmugasamy</a>, <a href="https://publications.waset.org/abstracts/search?q=Bilal%20Mansoor"> Bilal Mansoor</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Magnesium alloys are increasingly being considered for structural systems across different industrial sectors, including precision components of biomedical devices, owing to their high specific strength, stiffness and biodegradability. However, Mg alloys exhibit a high corrosion rate that restricts their application as a biomaterial. For safe use as biomaterial, it is essential to control their corrosion rates. Mg alloy corrosion is influenced by several factors, such as grain size, precipitates and texture. In Mg alloys, microgalvanic coupling between the α-Mg matrix and secondary precipitates can exist, which results in an increased corrosion rate. The present research addresses this challenge by engineering the microstructure of a biodegradable Mg–Zn–RE–Zr alloy by friction stir processing (FSP), a severe plastic deformation process. The FSP-processed Mg alloys showed improved corrosion resistance and mechanical properties. FSPed Mg alloy showed refined grains, a strong basal texture and broken and uniformly distributed secondary precipitates in the stir zone. Mg, alloy base material, exposed to In vitro corrosion medium showed micro galvanic coupling between precipitate and matrix, resulting in the unstable passive layer. However, FS processed alloy showed uniform corrosion owing to stable surface film formation. The stable surface film is attributed to refined grains, preferred texture and distribution of precipitates. The research results show promising potential for Mg alloy to be developed as a biomaterial. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=biomaterials" title="biomaterials">biomaterials</a>, <a href="https://publications.waset.org/abstracts/search?q=severe%20plastic%20deformation" title=" severe plastic deformation"> severe plastic deformation</a>, <a href="https://publications.waset.org/abstracts/search?q=magnesium%20alloys" title=" magnesium alloys"> magnesium alloys</a>, <a href="https://publications.waset.org/abstracts/search?q=corrosion" title=" corrosion"> corrosion</a> </p> <a href="https://publications.waset.org/abstracts/186884/corrosion-response-of-friction-stir-processed-mg-zn-zr-re-alloy" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/186884.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">43</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">74</span> Advanced Electron Microscopy Study of Fission Products in a TRISO Coated Particle Neutron Irradiated to 3.6 X 1021 N/cm² Fast Fluence at 1040 ⁰C</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Haiming%20Wen">Haiming Wen</a>, <a href="https://publications.waset.org/abstracts/search?q=Isabella%20J.%20Van%20Rooyen"> Isabella J. Van Rooyen</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Tristructural isotropic (TRISO)-coated fuel particles are designed as nuclear fuel for high-temperature gas reactors. TRISO coating consists of layers of carbon buffer, inner pyrolytic carbon (IPyC), SiC, and outer pyrolytic carbon. The TRISO coating, especially the SiC layer, acts as a containment system for fission products produced in the kernel. However, release of certain metallic fission products across intact TRISO coatings has been observed for decades. Despite numerous studies, mechanisms by which fission products migrate across the coating layers remain poorly understood. In this study, scanning transmission electron microscopy (STEM), energy dispersive X-ray spectroscopy (EDS), high-resolution transmission electron microscopy (HRTEM) and electron energy loss spectroscopy (EELS) were used to examine the distribution, composition and structure of fission products in a TRISO coated particle neutron irradiated to 3.6 x 1021 n/cm² fast fluence at 1040 ⁰C. Precession electron diffraction was used to investigate characters of grain boundaries where specific fission product precipitates are located. The retention fraction of 110mAg in the investigated TRISO particle was estimated to be 0.19. A high density of nanoscale fission product precipitates was observed in the SiC layer close to the SiC-IPyC interface, most of which are rich in Pd, while Ag was not identified. Some Pd-rich precipitates contain U. Precipitates tend to have complex structure and composition. Although a precipitate appears to have uniform contrast in STEM, EDS indicated that there may be composition variations throughout the precipitate, and HRTEM suggested that the precipitate may have several parts different in crystal structure or orientation. Attempts were made to measure charge states of precipitates using EELS and study their possible effect on precipitate transport. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=TRISO%20particle" title="TRISO particle">TRISO particle</a>, <a href="https://publications.waset.org/abstracts/search?q=fission%20product" title=" fission product"> fission product</a>, <a href="https://publications.waset.org/abstracts/search?q=nuclear%20fuel" title=" nuclear fuel"> nuclear fuel</a>, <a href="https://publications.waset.org/abstracts/search?q=electron%20microscopy" title=" electron microscopy"> electron microscopy</a>, <a href="https://publications.waset.org/abstracts/search?q=neutron%20irradiation" title=" neutron irradiation "> neutron irradiation </a> </p> <a href="https://publications.waset.org/abstracts/63680/advanced-electron-microscopy-study-of-fission-products-in-a-triso-coated-particle-neutron-irradiated-to-36-x-1021-ncm2-fast-fluence-at-1040-c" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/63680.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">265</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">73</span> Effect of Thermal Aging on Low Cycle Fatigue of Alloy 690</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Kushal%20Gowda%20Jayaram">Kushal Gowda Jayaram</a>, <a href="https://publications.waset.org/abstracts/search?q=Joseph%20Huret"> Joseph Huret</a>, <a href="https://publications.waset.org/abstracts/search?q=Jonathan%20Quibel"> Jonathan Quibel</a>, <a href="https://publications.waset.org/abstracts/search?q=Walter-John%20Chitty"> Walter-John Chitty</a>, <a href="https://publications.waset.org/abstracts/search?q=Gilbert%20Henaff"> Gilbert Henaff</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Thermal aging is one of the concerns for the long-term operation of nuclear power plants. Indeed, components in the primary circuit undergo thermal aging while exposed to the chemically active environment of Pressurized Water Reactors (PWRs) over time. Among the materials used in the reactor components, Alloy 690 can be found in some critical components for nuclear safety. Despite its importance, research on the effect of thermal aging on the microstructural changes and low cycle fatigue (LCF) behavior of Alloy 690 remains limited. This study aims to assess the impact of thermal aging on the fatigue life of Alloy 690. The as-received sample underwent aging at 420°C for 4000 hours, representing the equivalent aging of 60 years in reactor working conditions. First, the characterization of the area and density of intergranular and intragranular precipitates was performed to understand the microstructural changes in the aged specimen. Then, low cycle fatigue tests were conducted on the as received and aged samples at varying strain amplitudes. To investigate the influence of thermal aging on the fatigue behavior of Alloy 690, fracture surfaces were analyzed to estimate fatigue crack growth rates based on striation spacing measurements. Additionally, the axially cut fractured samples have undergone analysis using Electron Backscatter Diffraction (EBSD) to understand the effect of aging on strain localization near the crack path. Results indicate that while the characterization of the area and density of intergranular precipitates in the aged specimen (for 2000 hours, approximately 30 years) showed no significant changes, there was a slight increase in the area and density of intragranular precipitates under the same conditions. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=alloy%20690" title="alloy 690">alloy 690</a>, <a href="https://publications.waset.org/abstracts/search?q=thermal%20aging" title=" thermal aging"> thermal aging</a>, <a href="https://publications.waset.org/abstracts/search?q=low%20cycle%20fatigue" title=" low cycle fatigue"> low cycle fatigue</a>, <a href="https://publications.waset.org/abstracts/search?q=precipitates" title=" precipitates"> precipitates</a> </p> <a href="https://publications.waset.org/abstracts/185273/effect-of-thermal-aging-on-low-cycle-fatigue-of-alloy-690" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/185273.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">40</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">72</span> The Study of Aluminum Effects Layer Austenite Twins Adjacent to K-Carbide Plates in the Cellular Structure of a Mn-Al Alloy Steel</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Wu%20Wei-Ting">Wu Wei-Ting</a>, <a href="https://publications.waset.org/abstracts/search?q=Liu%20Po-Yen"> Liu Po-Yen</a>, <a href="https://publications.waset.org/abstracts/search?q=Chang%20Chin-Tzu"> Chang Chin-Tzu</a>, <a href="https://publications.waset.org/abstracts/search?q=Cheng%20Wei-Chun"> Cheng Wei-Chun</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Three types of low-temperature phase transformations in an Fe-12.5 Mn-6.53 Al-1.28 C (wt %) alloy have been studied. The steel underwent solution heat treatment at 1100℃ and isothermal holding at low temperatures. γ’ phase appears in the austenite matrix in the air-cooled steel. Coherent ultra-fine particles of γ’ phase precipitated uniformly in the austenite matrix after the air-cooling process. These ultra-fine particles were very small and only could be detected by TEM through dark-field images. After short periods of isothermal holding at low temperatures these particles of γ’ phase grew and could be easily detected by TEM. A pro-eutectoid reaction happened after isothermal holding at temperatures below 875 ℃. Proeutectoid κ-carbide and ferrite appear in the austenite matrix as grain boundary precipitates and cellular precipitates. The cellular precipitates are composed of lamellar κ-carbide and austenite. The lamellar κ-carbide grains are always accompanied by layers of austenite twins. The presence of twin layers adhering to the κ-carbide plates might be attributed to the lower activation energy for the precipitation of κ-carbide plates in the austenite. The final form of phase transformation is the eutectoid reaction for the decomposition of supersaturated austenite into stable κ-carbide and ferrite phases at temperatures below 700℃. The ferrite and κ-carbide are in the form of pearlite lamellae. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=austenite" title="austenite">austenite</a>, <a href="https://publications.waset.org/abstracts/search?q=austenite%20twin%20layers" title=" austenite twin layers"> austenite twin layers</a>, <a href="https://publications.waset.org/abstracts/search?q=%CE%BA-carbide" title=" κ-carbide"> κ-carbide</a>, <a href="https://publications.waset.org/abstracts/search?q=twins" title=" twins"> twins</a> </p> <a href="https://publications.waset.org/abstracts/72110/the-study-of-aluminum-effects-layer-austenite-twins-adjacent-to-k-carbide-plates-in-the-cellular-structure-of-a-mn-al-alloy-steel" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/72110.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">227</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">71</span> Effects of Hydrogen-Ion Irritation on the Microstructure and Hardness of Fe-0.2wt.%V Alloy</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Jing%20Zhang">Jing Zhang</a>, <a href="https://publications.waset.org/abstracts/search?q=Yongqin%20Chang"> Yongqin Chang</a>, <a href="https://publications.waset.org/abstracts/search?q=Yongwei%20Wang"> Yongwei Wang</a>, <a href="https://publications.waset.org/abstracts/search?q=Xiaolin%20Li"> Xiaolin Li</a>, <a href="https://publications.waset.org/abstracts/search?q=Shaoning%20Jiang"> Shaoning Jiang</a>, <a href="https://publications.waset.org/abstracts/search?q=Farong%20Wan"> Farong Wan</a>, <a href="https://publications.waset.org/abstracts/search?q=Yi%20Long"> Yi Long</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Microstructural and hardening changes of Fe-0.2wt.%V alloy and pure Fe irradiated with 100 keV hydrogen ions at room temperature were investigated. It was found that dislocation density varies dramatically after irradiation, ranging from dislocation free to dense areas with tangled and complex dislocation configuration. As the irradiated Fe-0.2wt.%V samples were annealed at 773 K, the irradiation-induced dislocation loops disappear, while many small precipitates with enriched C distribute in the matrix. Some large precipitates with enriched V were also observed. The hardness of Fe-0.2wt.%V alloy and pure Fe increases after irradiation, which ascribes to the formation of dislocation loops in the irradiated specimens. Compared with pure Fe, the size of the irradiation-introduced dislocation loops in Fe-0.2wt.%V alloy decreases and the density increases, the change of the hardness also decreases. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=irradiation" title="irradiation">irradiation</a>, <a href="https://publications.waset.org/abstracts/search?q=Fe-0.2wt.%25V%20alloy" title=" Fe-0.2wt.%V alloy"> Fe-0.2wt.%V alloy</a>, <a href="https://publications.waset.org/abstracts/search?q=microstructures" title=" microstructures"> microstructures</a>, <a href="https://publications.waset.org/abstracts/search?q=hardness" title=" hardness"> hardness</a> </p> <a href="https://publications.waset.org/abstracts/30363/effects-of-hydrogen-ion-irritation-on-the-microstructure-and-hardness-of-fe-02wtv-alloy" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/30363.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">386</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">70</span> Improvement of Mechanical Properties and Corrosion Resistance of AA7056 Aluminum Alloys by the Non-isothermal Aging Process</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Tse-An%20Pan">Tse-An Pan</a>, <a href="https://publications.waset.org/abstracts/search?q=Sheng-Long%20Lee"> Sheng-Long Lee</a> </p> <p class="card-text"><strong>Abstract:</strong></p> The effect of non-isothermal aging on the mechanical properties and corrosion resistance of Al-9Zn-2.3Mg-1.9Cu (AA7056) alloys was investigated. The results revealed that thick materials were limited to retrogression and re-aging treatment (RRA). It could not reach the retrogression temperature in the RRA treatment. Compared with the RRA treatment, the non-isothermal aging (NIA) treatment produced discontinuous precipitates at grain boundaries, while the intragranular precipitates were fine and dense. The strength was similar to that of the RRA treatment; the corrosion resistance of the alloy was significantly improved by NIA aging. NIA treatment was less affected by the thickness of the alloy. The difference between the actual temperature and the setting temperature of the alloy is minimal during the aging process. The combination of properties could overcome the fact that RRA treatment cannot handle thick materials. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=Al-Zn-Mg-Cu%20alloy" title="Al-Zn-Mg-Cu alloy">Al-Zn-Mg-Cu alloy</a>, <a href="https://publications.waset.org/abstracts/search?q=corrosion" title=" corrosion"> corrosion</a>, <a href="https://publications.waset.org/abstracts/search?q=retrogression" title=" retrogression"> retrogression</a>, <a href="https://publications.waset.org/abstracts/search?q=re-aging" title=" re-aging"> re-aging</a>, <a href="https://publications.waset.org/abstracts/search?q=non-isothermal%20aging" title=" non-isothermal aging"> non-isothermal aging</a> </p> <a href="https://publications.waset.org/abstracts/162230/improvement-of-mechanical-properties-and-corrosion-resistance-of-aa7056-aluminum-alloys-by-the-non-isothermal-aging-process" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/162230.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">181</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">69</span> Effect of Transition Metal Addition on Aging Behavior of Invar Alloy</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Young%20Sik%20Kim">Young Sik Kim</a>, <a href="https://publications.waset.org/abstracts/search?q=Tae%20Kwon%20Ha"> Tae Kwon Ha</a> </p> <p class="card-text"><strong>Abstract:</strong></p> High strength Fe-36Ni-base Invar alloys containing Al contents up to 0.3 weight per cent were cast into ingots and thermodynamic equilibrium during solidification has been investigated in this study. From the thermodynamic simulation using Thermo-Calc®, it has been revealed that equilibrium phases which can be formed are two kinds of MC-type precipitates, MoC, and M2C carbides. The mu phase was also expected to form by addition of aluminum. Microstructure observation revealed the coarse precipitates in the as-cast ingots, which was non-equilibrium phase and could be resolved by the successive heat treatment. With increasing Al contents up to 0.3 wt.%, tensile strength of Invar alloy increased as 1400MPa after cold rolling and thermal expansion coefficient increased significantly. Cold rolling appeared to dramatically decrease thermal expansion coefficient. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=Invar%20alloy" title="Invar alloy">Invar alloy</a>, <a href="https://publications.waset.org/abstracts/search?q=transition%20metals" title=" transition metals"> transition metals</a>, <a href="https://publications.waset.org/abstracts/search?q=phase%20equilibrium" title=" phase equilibrium"> phase equilibrium</a>, <a href="https://publications.waset.org/abstracts/search?q=aging%20behavior" title=" aging behavior"> aging behavior</a>, <a href="https://publications.waset.org/abstracts/search?q=microstructure" title=" microstructure"> microstructure</a>, <a href="https://publications.waset.org/abstracts/search?q=hardness" title=" hardness"> hardness</a> </p> <a href="https://publications.waset.org/abstracts/26118/effect-of-transition-metal-addition-on-aging-behavior-of-invar-alloy" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/26118.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">532</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">68</span> Thermo-Mechanical Processing Scheme to Obtain Micro-Duplex Structure Favoring Superplasticity in an As-Cast and Homogenized Medium Alloyed Nickel Base Superalloy</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=K.%20Sahithya">K. Sahithya</a>, <a href="https://publications.waset.org/abstracts/search?q=I.%20Balasundar"> I. Balasundar</a>, <a href="https://publications.waset.org/abstracts/search?q=Pritapant"> Pritapant</a>, <a href="https://publications.waset.org/abstracts/search?q=T.%20Raghua"> T. Raghua</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Ni-based superalloy with a nominal composition Ni-14% Cr-11% Co-5.8% Mo-2.4% Ti-2.4% Nb-2.8% Al-0.26 % Fe-0.032% Si-0.069% C (all in wt %) is used as turbine discs in a variety of aero engines. Like any other superalloy, the primary processing of the as-cast superalloy poses a major challenge due to its complex alloy chemistry. The challenge was circumvented by characterizing the different phases present in the material, optimizing the homogenization treatment, identifying a suitable thermomechanical processing window using dynamic materials modeling. The as-cast material was subjected to homogenization at 1200°C for a soaking period of 8 hours and quenched using different media. Water quenching (WQ) after homogenization resulted in very fine spherical γꞌ precipitates of sizes 30-50 nm, whereas furnace cooling (FC) after homogenization resulted in bimodal distribution of precipitates (primary gamma prime of size 300nm and secondary gamma prime of size 5-10 nm). MC type primary carbides that are stable till the melting point of the material were found in both WQ and FC samples. Deformation behaviour of both the materials below (1000-1100°C) and above gamma prime solvus (1100-1175°C) was evaluated by subjecting the material to series of compression tests at different constant true strain rates (0.0001/sec-1/sec). An in-detail examination of the precipitate dislocation interaction mechanisms carried out using TEM revealed precipitate shearing and Orowan looping as the mechanisms governing deformation in WQ and FC, respectively. Incoherent/semi coherent gamma prime precipitates in the case of FC material facilitates better workability of the material, whereas the coherent precipitates in WQ material contributed to higher resistance to deformation of the material. Both the materials exhibited discontinuous dynamic recrystallization (DDRX) above gamma prime solvus temperature. The recrystallization kinetics was slower in the case of WQ material. Very fine grain boundary carbides ( ≤ 300 nm) retarded the recrystallisation kinetics in WQ. Coarse carbides (1-5 µm) facilitate particle stimulated nucleation in FC material. The FC material was cogged (primary hot working) 1120˚C, 0.03/sec resulting in significant grain refinement, i.e., from 3000 μm to 100 μm. The primary processed material was subjected to intensive thermomechanical deformation subsequently by reducing the temperature by 50˚C in each processing step with intermittent heterogenization treatment at selected temperatures aimed at simultaneous coarsening of the gamma prime precipitates and refinement of the gamma matrix grains. The heterogeneous annealing treatment carried out, resulted in gamma grains of 10 μm and gamma prime precipitates of 1-2 μm. Further thermo mechanical processing of the material was carried out at 1025˚C to increase the homogeneity of the obtained micro-duplex structure. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=superalloys" title="superalloys">superalloys</a>, <a href="https://publications.waset.org/abstracts/search?q=dynamic%20material%20modeling" title=" dynamic material modeling"> dynamic material modeling</a>, <a href="https://publications.waset.org/abstracts/search?q=nickel%20alloys" title=" nickel alloys"> nickel alloys</a>, <a href="https://publications.waset.org/abstracts/search?q=dynamic%20recrystallization" title=" dynamic recrystallization"> dynamic recrystallization</a>, <a href="https://publications.waset.org/abstracts/search?q=superplasticity" title=" superplasticity"> superplasticity</a> </p> <a href="https://publications.waset.org/abstracts/121172/thermo-mechanical-processing-scheme-to-obtain-micro-duplex-structure-favoring-superplasticity-in-an-as-cast-and-homogenized-medium-alloyed-nickel-base-superalloy" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/121172.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">121</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">67</span> Effect of Al Addition on Microstructure and Physical Properties of Fe-36Ni Invar Alloy</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Seok%20Hong%20Min">Seok Hong Min</a>, <a href="https://publications.waset.org/abstracts/search?q=Tae%20Kwon%20Ha"> Tae Kwon Ha</a> </p> <p class="card-text"><strong>Abstract:</strong></p> High strength Fe-36Ni-base Invar alloys containing Al contents up to 0.3 weight percent were cast into ingots and thermodynamic equilibrium during solidification has been investigated in this study. From the thermodynamic simulation using Thermo-Calc®, it has been revealed that equilibrium phases which can be formed are two kinds of MC-type precipitates, MoC, and M2C carbides. The mu phase was also expected to form by addition of aluminum. Microstructure observation revealed the coarse precipitates in the as-cast ingots, which was non-equilibrium phase and could be resolved by the successive heat treatment. With increasing Al contents up to 0.3 wt.%, tensile strength of Invar alloy increased as 1400MPa after cold rolling and thermal expansion coefficient increased significantly. Cold rolling appeared to dramatically decrease thermal expansion coefficient. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=invar%20alloy" title="invar alloy">invar alloy</a>, <a href="https://publications.waset.org/abstracts/search?q=aluminum" title=" aluminum"> aluminum</a>, <a href="https://publications.waset.org/abstracts/search?q=phase%20equilibrium" title=" phase equilibrium"> phase equilibrium</a>, <a href="https://publications.waset.org/abstracts/search?q=thermal%20expansion%20coefficient" title=" thermal expansion coefficient"> thermal expansion coefficient</a>, <a href="https://publications.waset.org/abstracts/search?q=microstructure" title=" microstructure"> microstructure</a>, <a href="https://publications.waset.org/abstracts/search?q=tensile%20properties" title=" tensile properties"> tensile properties</a> </p> <a href="https://publications.waset.org/abstracts/9726/effect-of-al-addition-on-microstructure-and-physical-properties-of-fe-36ni-invar-alloy" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/9726.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">371</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">66</span> Microstructure Dependent Fatigue Crack Growth in Aluminum Alloy</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=M.%20S.%20Nandana">M. S. Nandana</a>, <a href="https://publications.waset.org/abstracts/search?q=K.%20Udaya%20Bhat"> K. Udaya Bhat</a>, <a href="https://publications.waset.org/abstracts/search?q=C.%20M.%20Manjunatha"> C. M. Manjunatha</a> </p> <p class="card-text"><strong>Abstract:</strong></p> In this study aluminum alloy 7010 was subjected to three different ageing treatments i.e., peak ageing (T6), over-ageing (T7451) and retrogression and re ageing (RRA) to study the influence of precipitate microstructure on the fatigue crack growth rate behavior. The microstructural modification was studied by using transmission electron microscope (TEM) to examine the change in the size and morphology of precipitates in the matrix and on the grain boundaries. The standard compact tension (CT) specimens were fabricated and tested under constant amplitude fatigue crack growth tests to evaluate the influence of heat treatment on the fatigue crack growth rate properties. The tests were performed in a computer-controlled servo-hydraulic test machine applying a load ratio, R = 0.1 at a loading frequency of 10 Hz as per ASTM E647. The fatigue crack growth was measured by adopting compliance technique using a CMOD gauge attached to the CT specimen. The average size of the matrix precipitates were found to be of 16-20 nm in T7451, 5-6 nm in RRA and 2-3 nm in T6 conditions respectively. The grain boundary precipitate which was continuous in T6, was disintegrated in RRA and T7451 condition. The PFZ width was lower in RRA compared to T7451 condition. The crack growth rate was higher in T7451 and lowest in RRA treated alloy. The RRA treated alloy also exhibits an increase in threshold stress intensity factor range (∆Kₜₕ). The ∆Kₜₕ measured was 11.1, 10.3 and 5.7 MPam¹/² in RRA, T6 and T7451 alloys respectively. The fatigue crack growth rate in RRA treated alloy was nearly 2-3 times lower than that in T6 and was one order lower than that observed in T7451 condition. The surface roughness of RRA treated alloy was more pronounced when compared to the other conditions. The reduction in fatigue crack growth rate in RRA alloy was majorly due to the increase in roughness and partially due to increase in spacing between the matrix precipitates. The reduction in crack growth rate and increase in threshold stress intensity range is expected to benefit the damage tolerant capability of aircraft structural components under service loads. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=damage%20tolerance" title="damage tolerance">damage tolerance</a>, <a href="https://publications.waset.org/abstracts/search?q=fatigue" title=" fatigue"> fatigue</a>, <a href="https://publications.waset.org/abstracts/search?q=heat%20treatment" title=" heat treatment"> heat treatment</a>, <a href="https://publications.waset.org/abstracts/search?q=PFZ" title=" PFZ"> PFZ</a>, <a href="https://publications.waset.org/abstracts/search?q=RRA" title=" RRA"> RRA</a> </p> <a href="https://publications.waset.org/abstracts/100680/microstructure-dependent-fatigue-crack-growth-in-aluminum-alloy" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/100680.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">153</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">65</span> Effect of Prior Heat Treatment on the Microstructure Evolution and Creep Resistance of ZK60 Mg Alloy Under Tensile Creep Loading Along Normal Direction</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Sijia%20Hu">Sijia Hu</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Tensile creep tests were performed along the normal direction on the as-solutioned (AS) and as-aged (AA) samples of a commercial ZK60 alloy in this work. The results showed that the AA sample obtained a stronger 0.2% proof stress but a poorer creep resistance in comparison to the AS sample. It was revealed that the creep deformation in the AS sample was attributed to basal slip and twinning, while the creep behavior of the AA sample was controlled by basal slip, pyramidal <c+a> slip and twinning. Besides, the reasons for the poorer creep resistance of the AA sample were unveiled. Pyramidal dislocations towards various moving directions were found to accelerate the creep deformation, and basal dislocations kinking at twin boundaries were found to induce heavy stress concentration. Furthermore, massive dynamic precipitates, including beta 1 prime and beta 2 prime types, were formed in the AS sample during the creep exposure, contributing to the superior creep resistance. But in the AA sample, plentiful beta 1 prime and beta 2 prime phases generated during the prior peak-aging treatment dissolved into the matrix fast and only beta 1 prime re-precipitated during the creep process. With the decreased area fractions of precipitates, the age-hardening effect slacked off and failed to enhance the creep resistance. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=Mg%20alloy" title="Mg alloy">Mg alloy</a>, <a href="https://publications.waset.org/abstracts/search?q=creep" title=" creep"> creep</a>, <a href="https://publications.waset.org/abstracts/search?q=precipitation" title=" precipitation"> precipitation</a>, <a href="https://publications.waset.org/abstracts/search?q=microstructure" title=" microstructure"> microstructure</a> </p> <a href="https://publications.waset.org/abstracts/186519/effect-of-prior-heat-treatment-on-the-microstructure-evolution-and-creep-resistance-of-zk60-mg-alloy-under-tensile-creep-loading-along-normal-direction" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/186519.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">38</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">64</span> Effect of Annealing Temperature on Microstructural Evolution of Nanoindented Cu/Si Thin Films</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Woei-Shyan%20Lee">Woei-Shyan Lee</a>, <a href="https://publications.waset.org/abstracts/search?q=Yu-Liang%20Chuang"> Yu-Liang Chuang</a> </p> <p class="card-text"><strong>Abstract:</strong></p> The nano-mechanical properties of as-deposited Cu/Si thin films indented to a depth of 2000 nm are investigated using a nanoindentation technique. The nanoindented specimens are annealed at a temperature of either 160 °C or 210°C, respectively. The microstructures of the as-deposited and annealed samples are then examined via transmission electron microscopy (TEM). The results show that both the loading and the unloading regions of the load-displacement curve are smooth and continuous, which suggests that no debonding or cracking occurs during nanoindentation. In addition, the hardness and Young’s modulus of the Cu/Si thin films are found to vary with the nanoindentation depth, and have maximum values of 2.8 GPa and 143 GPa, respectively, at the maximum indentation depth of 2000 nm. The TEM observations show that the region of the Cu/Si film beneath the indenter undergoes a phase transformation during the indentation process. In the case of the as-deposited specimens, the indentation pressure induces a completely amorphous phase within the indentation zone. For the specimens annealed at a temperature of 160°C, the amorphous nature of the microstructure within the indented zone is maintained. However, for the specimens annealed at a higher temperature of 210°C, the indentation affected zone consists of a mixture of amorphous phase and nanocrystalline phase. Copper silicide (η-Cu3Si) precipitates are observed in all of the annealed specimens. The density of the η-Cu3Si precipitates is found to increase with an increasing annealing temperature. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=nanoindentation" title="nanoindentation">nanoindentation</a>, <a href="https://publications.waset.org/abstracts/search?q=Cu%2FSi%20thin%20films" title=" Cu/Si thin films"> Cu/Si thin films</a>, <a href="https://publications.waset.org/abstracts/search?q=microstructural%20evolution" title=" microstructural evolution"> microstructural evolution</a>, <a href="https://publications.waset.org/abstracts/search?q=annealing%20temperature" title=" annealing temperature"> annealing temperature</a> </p> <a href="https://publications.waset.org/abstracts/46615/effect-of-annealing-temperature-on-microstructural-evolution-of-nanoindented-cusi-thin-films" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/46615.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">391</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">63</span> Grain Growth Behavior of High Carbon Microalloyed Steels Containing Very Low Amounts of Niobium</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Huseyin%20Zengin">Huseyin Zengin</a>, <a href="https://publications.waset.org/abstracts/search?q=Muhammet%20Emre%20Turan"> Muhammet Emre Turan</a>, <a href="https://publications.waset.org/abstracts/search?q=Yunus%20Turen"> Yunus Turen</a>, <a href="https://publications.waset.org/abstracts/search?q=Hayrettin%20Ahlatci"> Hayrettin Ahlatci</a>, <a href="https://publications.waset.org/abstracts/search?q=Yavuz%20Sun"> Yavuz Sun</a> </p> <p class="card-text"><strong>Abstract:</strong></p> This study aimed for understanding the effects of dilute Nb additions on the austenite microstructure of microalloyed steels at five different reheating temperatures from 950 °C to 1300 °C. Four microalloyed high-carbon steels having 0.8 %wt C were examined in which three of them had varying Nb concentrations from 0.005 wt% to 0.02 wt% and one of them had no Nb concentration. The quantitative metallographic techniques were used to measure the average prior austenite grain size in order to compare the grain growth pinning effects of Nb precipitates as a function of reheating temperature. Due to the higher stability of the precipitates with increasing Nb concentrations, the grain coarsening temperature that resulted in inefficient grain growth impediment and a bimodal grain distribution in the microstructure, showed an increase with increasing Nb concentration. The respective grain coarsening temperatures (T_GC) in an ascending order for the steels having 0.005 wt% Nb, 0.01 wt% Nb and 0.02 wt% Nb were 950 °C, 1050 °C and 1150 °C. According to these observed grain coarsening temperatures, an approximation was made considering the complete dissolution temperature (T_DISS) of second phase particles as T_GC=T_DISS-300. On the other hand, the plain carbon steel did not show abnormal grain growth behaviour due to the absence of second phase particles. It was also observed that the higher the Nb concentration, the smaller the average prior austenite grain size although the small increments in Nb concenration did not change the average grain size considerably. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=microalloyed%20steels" title="microalloyed steels">microalloyed steels</a>, <a href="https://publications.waset.org/abstracts/search?q=prior%20austenite%20grains" title=" prior austenite grains"> prior austenite grains</a>, <a href="https://publications.waset.org/abstracts/search?q=second%20phase%20particles" title=" second phase particles"> second phase particles</a>, <a href="https://publications.waset.org/abstracts/search?q=grain%20coarsening%20temperature" title=" grain coarsening temperature"> grain coarsening temperature</a> </p> <a href="https://publications.waset.org/abstracts/50132/grain-growth-behavior-of-high-carbon-microalloyed-steels-containing-very-low-amounts-of-niobium" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/50132.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">265</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">62</span> Effect of Carbide Precipitates in Tool Steel on Material Transfer: A Molecular Dynamics Study</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Ahmed%20Tamer%20AlMotasem">Ahmed Tamer AlMotasem</a>, <a href="https://publications.waset.org/abstracts/search?q=Jens%20Bergstr%C3%B6m"> Jens Bergström</a>, <a href="https://publications.waset.org/abstracts/search?q=Anders%20G%C3%A5%C3%A5rd"> Anders Gåård</a>, <a href="https://publications.waset.org/abstracts/search?q=Pavel%20Krakhmalev"> Pavel Krakhmalev</a>, <a href="https://publications.waset.org/abstracts/search?q=Thijs%20Jan%20Holleboom"> Thijs Jan Holleboom</a> </p> <p class="card-text"><strong>Abstract:</strong></p> In sheet metal forming processes, accumulation and transfer of sheet material to tool surfaces, often referred to as galling, is the major cause of tool failure. Initiation of galling is assumed to occur due to local adhesive wear between two surfaces. Therefore, reducing adhesion between the tool and the work sheet has a great potential to improve the tool materials galling resistance. Experimental observations and theoretical studies show that the presence of primary micro-sized carbides and/or nitrides in alloyed steels may significantly improve galling resistance. Generally, decreased adhesion between the ceramic precipitates and the sheet material counter-surface are attributed as main reason to the latter observations. On the other hand, adhesion processes occur at an atomic scale and, hence, fundamental understanding of galling can be obtained via atomic scale simulations. In the present study, molecular dynamics simulations are used, with utilizing second nearest neighbor embedded atom method potential to investigate the influence of nano-sized cementite precipitates embedded in tool atoms. The main aim of the simulations is to gain new fundamental knowledge on galling initiation mechanisms. Two tool/work piece configurations, iron/iron and iron-cementite/iron, are studied under dry sliding conditions. We find that the average frictional force decreases whereas the normal force increases for the iron-cementite/iron system, in comparison to the iron/iron configuration. Moreover, the average friction coefficient between the tool/work-piece decreases by about 10 % for the iron-cementite/iron case. The increase of the normal force in the case of iron-cementite/iron system may be attributed to the high stiffness of cementite compared to bcc iron. In order to qualitatively explain the effect of cementite on adhesion, the adhesion force between self-mated iron/iron and cementite/iron surfaces has been determined and we found that iron/cementite surface exhibits lower adhesive force than that of iron-iron surface. The variation of adhesion force with temperature was investigated up to 600 K and we found that the adhesive force, generally, decreases with increasing temperature. Structural analyses show that plastic deformation is the main deformation mechanism of the work-piece, accompanied with dislocations generation. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=adhesion" title="adhesion">adhesion</a>, <a href="https://publications.waset.org/abstracts/search?q=cementite" title=" cementite"> cementite</a>, <a href="https://publications.waset.org/abstracts/search?q=galling" title=" galling"> galling</a>, <a href="https://publications.waset.org/abstracts/search?q=molecular%20dynamics" title=" molecular dynamics"> molecular dynamics</a> </p> <a href="https://publications.waset.org/abstracts/37180/effect-of-carbide-precipitates-in-tool-steel-on-material-transfer-a-molecular-dynamics-study" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/37180.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">301</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">61</span> Microstructural Interactions of Ag and Sc Alloying Additions during Casting and Artificial Ageing to a T6 Temper in a A356 Aluminium Alloy</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Dimitrios%20Bakavos">Dimitrios Bakavos</a>, <a href="https://publications.waset.org/abstracts/search?q=Dimitrios%20Tsivoulas"> Dimitrios Tsivoulas</a>, <a href="https://publications.waset.org/abstracts/search?q=Chaowalit%20Limmaneevichitr"> Chaowalit Limmaneevichitr</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Aluminium cast alloys, of the Al-Si system, are widely used for shape castings. Their microstructures can be further improved on one hand, by alloying modification and on the other, by optimised artificial ageing. In this project four hypoeutectic Al-alloys, the A356, A356+ Ag, A356+Sc, and A356+Ag+Sc have been studied. The interactions of Ag and Sc during solidification and artificial ageing at 170°C to a T6 temper have been investigated in details. The evolution of the eutectic microstructure is studied by thermal analysis and interrupted solidification. The ageing kinetics of the alloys has been identified by hardness measurements. The precipitate phases, number density, and chemical composition has been analysed by means of transmission electron microscopy (TEM) and EDS analysis. Furthermore, the SHT effect onto the Si eutectic particles for the four alloys has been investigated by means of optical microscopy, image analysis, and the UTS strength has been compared with the UTS of the alloys after casting. The results suggest that the Ag additions, significantly enhance the ageing kinetics of the A356 alloy. The formation of β” precipitates were kinetically accelerated and an increase of 8% and 5% in peak hardness strength has been observed compared to the base A356 and A356-Sc alloy. The EDS analysis demonstrates that Ag is present on the β” precipitate composition. After prolonged ageing 100 hours at 170°C, the A356-Ag exhibits 17% higher hardness strength compared to the other three alloys. During solidification, Sc additions change the macroscopic eutectic growth mode to the propagation of a defined eutectic front from the mold walls opposite to the heat flux direction. In contrast, Ag has no significance effect on the solidification mode revealing a macroscopic eutectic growth similar to A356 base alloy. However, the mechanical strength of the as cast A356-Ag, A356-Sc, and A356+Ag+Sc additions has increased by 5, 30, and 35 MPa, respectively. The outcome is a tribute to the refining of the eutectic Si that takes place which it is strong in the A356-Sc alloy and more profound when silver and scandium has been combined. Moreover after SHT the Al alloy with the highest mechanical strength, is the one with Ag additions, in contrast to the as-cast condition where the Sc and Sc+Ag alloy was the strongest. The increase of strength is mainly attributed to the dissolution of grain boundary precipitates the increase of the solute content into the matrix, the spherodisation, and coarsening of the eutectic Si. Therefore, we could safely conclude for an A356 hypoeutectic alloy additions of: Ag exhibits a refining effect on the Si eutectic which is improved when is combined with Sc. In addition Ag enhance, the ageing kinetics increases the hardness and retains its strength at prolonged artificial ageing in a Al-7Si 0.3Mg hypoeutectic alloy. Finally the addition of Sc is beneficial due to the refinement of the α-Al grain and modification-refinement of the eutectic Si increasing the strength of the as-cast product. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=ageing" title="ageing">ageing</a>, <a href="https://publications.waset.org/abstracts/search?q=casting" title=" casting"> casting</a>, <a href="https://publications.waset.org/abstracts/search?q=mechanical%20strength" title=" mechanical strength"> mechanical strength</a>, <a href="https://publications.waset.org/abstracts/search?q=precipitates" title=" precipitates"> precipitates</a> </p> <a href="https://publications.waset.org/abstracts/34561/microstructural-interactions-of-ag-and-sc-alloying-additions-during-casting-and-artificial-ageing-to-a-t6-temper-in-a-a356-aluminium-alloy" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/34561.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">498</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">60</span> Precipitation Kinetics of Al-7%Mg Alloy Studied by DSC and XRD</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=M.%20Fatmi">M. Fatmi</a>, <a href="https://publications.waset.org/abstracts/search?q=T.%20Chihi"> T. Chihi</a>, <a href="https://publications.waset.org/abstracts/search?q=M.%20A.%20Ghebouli"> M. A. Ghebouli</a>, <a href="https://publications.waset.org/abstracts/search?q=B.%20Ghebouli"> B. Ghebouli </a> </p> <p class="card-text"><strong>Abstract:</strong></p> This work presents the experimental results of the differential scanning calorimetry (DSC), hardness measurements (Hv) and XRD analysis, for order to investigate the kinetics of precipitation phenomena in Al-7%wt. Mg alloy. In the XRD and DSC curves indicates the formation of the intermediate precipitation of β-(Al3Mg2) phase respectively. The activation energies associated with the processes have been determined according to the three models proposed by Kissinger, Ozawa, and Boswell. Consequently, the nucleation mechanism of the precipitates can be explained. These phases are conﬁrmed by XRD analysis. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=discontinuous%20precipitation" title="discontinuous precipitation">discontinuous precipitation</a>, <a href="https://publications.waset.org/abstracts/search?q=hardening" title=" hardening"> hardening</a>, <a href="https://publications.waset.org/abstracts/search?q=Al%E2%80%93Mg%20alloys" title=" Al–Mg alloys"> Al–Mg alloys</a>, <a href="https://publications.waset.org/abstracts/search?q=mechanical%20and%20mechatronics%20engineering" title=" mechanical and mechatronics engineering"> mechanical and mechatronics engineering</a> </p> <a href="https://publications.waset.org/abstracts/13735/precipitation-kinetics-of-al-7mg-alloy-studied-by-dsc-and-xrd" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/13735.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">412</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">59</span> Effect of Thermal Treatment on Mechanical Properties of Reduced Activation Ferritic/Martensitic Eurofer Steel Grade</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Athina%20Puype">Athina Puype</a>, <a href="https://publications.waset.org/abstracts/search?q=Lorenzo%20Malerba"> Lorenzo Malerba</a>, <a href="https://publications.waset.org/abstracts/search?q=Nico%20De%20Wispelaere"> Nico De Wispelaere</a>, <a href="https://publications.waset.org/abstracts/search?q=Roumen%20Petrov"> Roumen Petrov</a>, <a href="https://publications.waset.org/abstracts/search?q=Jilt%20Sietsma"> Jilt Sietsma</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Reduced activation ferritic/martensitic (RAFM) steels like EUROFER97 are primary candidate structural materials for first wall application in the future demonstration (DEMO) fusion reactor. Existing steels of this type obtain their functional properties by a two-stage heat treatment, which consists of an annealing stage at 980°C for thirty minutes followed by quenching and an additional tempering stage at 750°C for two hours. This thermal quench and temper (Q&T) treatment creates a microstructure of tempered martensite with, as main precipitates, M23C6 carbides, with M = Fe, Cr and carbonitrides of MX type, e.g. TaC and VN. The resulting microstructure determines the mechanical properties of the steel. The ductility is largely determined by the tempered martensite matrix, while the resistance to mechanical degradation, determined by the spatial and size distribution of precipitates and the martensite crystals, plays a key role in the high temperature properties of the steel. Unfortunately, the high temperature response of EUROFER97 is currently insufficient for long term use in fusion reactors, due to instability of the matrix phase and coarsening of the precipitates at prolonged high temperature exposure. The objective of this study is to induce grain refinement by appropriate modifications of the processing route in order to increase the high temperature strength of a lab-cast EUROFER RAFM steel grade. The goal of the work is to obtain improved mechanical behavior at elevated temperatures with respect to conventionally heat treated EUROFER97. A dilatometric study was conducted to study the effect of the annealing temperature on the mechanical properties after a Q&T treatment. The microstructural features were investigated with scanning electron microscopy (SEM), electron back-scattered diffraction (EBSD) and transmission electron microscopy (TEM). Additionally, hardness measurements, tensile tests at elevated temperatures and Charpy V-notch impact testing of KLST-type MCVN specimens were performed to study the mechanical properties of the furnace-heated lab-cast EUROFER RAFM steel grade. A significant prior austenite grain (PAG) refinement was obtained by lowering the annealing temperature of the conventionally used Q&T treatment for EUROFER97. The reduction of the PAG results in finer martensitic constituents upon quenching, which offers more nucleation sites for carbide and carbonitride formation upon tempering. The ductile-to-brittle transition temperature (DBTT) was found to decrease with decreasing martensitic block size. Additionally, an increased resistance against high temperature degradation was accomplished in the fine grained martensitic materials with smallest precipitates obtained by tailoring the annealing temperature of the Q&T treatment. It is concluded that the microstructural refinement has a pronounced effect on the DBTT without significant loss of strength and ductility. Further investigation into the optimization of the processing route is recommended to improve the mechanical behavior of RAFM steels at elevated temperatures. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=ductile-to-brittle%20transition%20temperature%20%28DBTT%29" title="ductile-to-brittle transition temperature (DBTT)">ductile-to-brittle transition temperature (DBTT)</a>, <a href="https://publications.waset.org/abstracts/search?q=EUROFER" title=" EUROFER"> EUROFER</a>, <a href="https://publications.waset.org/abstracts/search?q=reduced%20activation%20ferritic%2Fmartensitic%20%28RAFM%29%20steels" title=" reduced activation ferritic/martensitic (RAFM) steels"> reduced activation ferritic/martensitic (RAFM) steels</a>, <a href="https://publications.waset.org/abstracts/search?q=thermal%20treatments" title=" thermal treatments"> thermal treatments</a> </p> <a href="https://publications.waset.org/abstracts/59346/effect-of-thermal-treatment-on-mechanical-properties-of-reduced-activation-ferriticmartensitic-eurofer-steel-grade" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/59346.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">299</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">58</span> Role of Fracturing, Brecciation and Calcite Veining in Fluids Flow and Permeability Enhancement in Low-Porosity Rock Masses: Case Study of Boulaaba Aptian Dolostones, Kasserine, Central Tunisia</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Mohamed%20Khali%20Zidi">Mohamed Khali Zidi</a>, <a href="https://publications.waset.org/abstracts/search?q=Mohsen%20Henchiri"> Mohsen Henchiri</a>, <a href="https://publications.waset.org/abstracts/search?q=Walid%20Ben%20Ahmed"> Walid Ben Ahmed</a> </p> <p class="card-text"><strong>Abstract:</strong></p> In the context of a hypogene hydrothermal travertine system, including low-porosity brittle bedrock and rock-mass permeability in Aptian dolostone of Boulaaba, Kasserine is enhanced through faulting and fracturing. This permeability enhancement related to the deformation modes along faults and fractures is likely to be in competition with permeability reduction when microcracks, fractures, and faults all become infilled with breccias and low-permeability hydrothermal precipitates. So that, fault continual or intermittent reactivation is probably necessary for them to keep their potential as structural high-permeability conduits. Dilational normal faults in strong mechanical stratigraphy associated with fault segments with dip changes are sites for porosity and permeability in groundwater infiltration and flow, hydrocarbon reservoirs, and also may be important sources of mineralization. The brecciation mechanism through dilational faulting and gravitational collapse originates according to hosting lithologies chaotic clast-supported breccia in strong lithologies such as sandstones, limestones, and dolostones, and matrix-supported cataclastic in weaker lithologies such as marls and shales. Breccias contribute to controlling fluid flow when the porosity is sealed either by low-permeability hydrothermal precipitates or by fine matrix materials. All these mechanisms of fault-related rock-mass permeability enhancement and reduction can be observed and analyzed in the region of Sidi Boulaaba, Kasserine, central Tunisia, where dilational normal faulting occurs in mechanical strong dolostone layering alternating with more weak marl and shale lithologies, has originated a variety of fault voids (fluid conduits) breccias (chaotic, crackle and mosaic breccias) and carbonate cement. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=travertine" title="travertine">travertine</a>, <a href="https://publications.waset.org/abstracts/search?q=Aptian%20dolostone" title=" Aptian dolostone"> Aptian dolostone</a>, <a href="https://publications.waset.org/abstracts/search?q=Boulaaba" title=" Boulaaba"> Boulaaba</a>, <a href="https://publications.waset.org/abstracts/search?q=fracturing" title=" fracturing"> fracturing</a> </p> <a href="https://publications.waset.org/abstracts/182430/role-of-fracturing-brecciation-and-calcite-veining-in-fluids-flow-and-permeability-enhancement-in-low-porosity-rock-masses-case-study-of-boulaaba-aptian-dolostones-kasserine-central-tunisia" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/182430.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">65</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">57</span> Recrystallization Behavior and Microstructural Evolution of Nickel Base Superalloy AD730 Billet during Hot Forging at Subsolvus Temperatures</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Marcos%20Perez">Marcos Perez</a>, <a href="https://publications.waset.org/abstracts/search?q=Christian%20Dumont"> Christian Dumont</a>, <a href="https://publications.waset.org/abstracts/search?q=Olivier%20Nodin"> Olivier Nodin</a>, <a href="https://publications.waset.org/abstracts/search?q=Sebastien%20Nouveau"> Sebastien Nouveau</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Nickel superalloys are used to manufacture high-temperature rotary engine parts such as high-pressure disks in gas turbine engines. High strength at high operating temperatures is required due to the levels of stress and heat the disk must withstand. Therefore it is necessary parts made from materials that can maintain mechanical strength at high temperatures whilst remain comparatively low in cost. A manufacturing process referred to as the triple melt process has made the production of cast and wrought (C&W) nickel superalloys possible. This means that the balance of cost and performance at high temperature may be optimized. AD730TM is a newly developed Ni-based superalloy for turbine disk applications, with reported superior service properties around 700°C when compared to Inconel 718 and several other alloys. The cast ingot is converted into billet during either cogging process or open die forging. The semi-finished billet is then further processed into its final geometry by forging, heat treating, and machining. Conventional ingot-to-billet conversion is an expensive and complex operation, requiring a significant amount of steps to break up the coarse as-cast structure and interdendritic regions. Due to the size of conventional ingots, it is difficult to achieve a uniformly high level of strain for recrystallization, resulting in non-recrystallized regions that retain large unrecrystallized grains. Non-uniform grain distributions will also affect the ultrasonic inspectability response, which is used to find defects in the final component. The main aim is to analyze the recrystallization behavior and microstructural evolution of AD730 at subsolvus temperatures from a semi-finished product (billet) under conditions representative of both cogging and hot forging operations. Special attention to the presence of large unrecrystallized grains was paid. Double truncated cones (DTCs) were hot forged at subsolvus temperatures in hydraulic press, followed by air cooling. SEM and EBSD analysis were conducted in the as-received (billet) and the as-forged conditions. AD730 from billet alloy presents a complex microstructure characterized by a mixture of several constituents. Large unrecrystallized grains present a substructure characterized by large misorientation gradients with the formation of medium to high angle boundaries in their interior, especially close to the grain boundaries, denoting inhomogeneous strain distribution. A fine distribution of intragranular precipitates was found in their interior, playing a key role on strain distribution and subsequent recrystallization behaviour during hot forging. Continuous dynamic recrystallization (CDRX) mechanism was found to be operating in the large unrecrystallized grains, promoting the formation intragranular DRX grains and the gradual recrystallization of these grains. Evidences that hetero-epitaxial recrystallization mechanism is operating in AD730 billet material were found. Coherent γ-shells around primary γ’ precipitates were found. However, no significant contribution to the overall recrystallization during hot forging was found. By contrast, strain presents the strongest effect on the microstructural evolution of AD730, increasing the recrystallization fraction and refining the structure. Regions with low level of deformation (ε ≤ 0.6) were translated into large fractions of unrecrystallized structures (strain accumulation). The presence of undissolved secondary γ’ precipitates (pinning effect), prior to hot forging operations, could explain these results. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=AD730%20alloy" title="AD730 alloy">AD730 alloy</a>, <a href="https://publications.waset.org/abstracts/search?q=continuous%20dynamic%20recrystallization" title=" continuous dynamic recrystallization"> continuous dynamic recrystallization</a>, <a href="https://publications.waset.org/abstracts/search?q=hot%20forging" title=" hot forging"> hot forging</a>, <a href="https://publications.waset.org/abstracts/search?q=%CE%B3%E2%80%99%20precipitates" title=" γ’ precipitates"> γ’ precipitates</a> </p> <a href="https://publications.waset.org/abstracts/98142/recrystallization-behavior-and-microstructural-evolution-of-nickel-base-superalloy-ad730-billet-during-hot-forging-at-subsolvus-temperatures" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/98142.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">199</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">56</span> Influence of Thermal Ageing on Microstructural Features and Mechanical Properties of Reduced Activation Ferritic/Martensitic Grades </h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Athina%20Puype">Athina Puype</a>, <a href="https://publications.waset.org/abstracts/search?q=Lorenzo%20Malerba"> Lorenzo Malerba</a>, <a href="https://publications.waset.org/abstracts/search?q=Nico%20De%20Wispelaere"> Nico De Wispelaere</a>, <a href="https://publications.waset.org/abstracts/search?q=Roumen%20Petrov"> Roumen Petrov</a>, <a href="https://publications.waset.org/abstracts/search?q=Jilt%20Sietsma"> Jilt Sietsma</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Reduced Activation Ferritic/Martensitic (FM) steels like EUROFER are of interest for first wall application in the future demonstration (DEMO) fusion reactor. Depending on the final design codes for the DEMO reactor, the first wall material will have to function in low-temperature mode or high-temperature mode, i.e. around 250-300°C of above 550°C respectively. However, the use of RAFM steels is limited up to a temperature of about 550°C. For the low-temperature application, the material suffers from irradiation embrittlement, due to a shift of ductile-to-brittle transition temperature (DBTT) towards higher temperatures upon irradiation. The high-temperature response of the material is equally insufficient for long-term use in fusion reactors, due to the instability of the matrix phase and coarsening of the precipitates at prolonged high-temperature exposure. The objective of this study is to investigate the influence of thermal ageing for 1000 hrs and 4000 hrs on microstructural features and mechanical properties of lab-cast EUROFER. Additionally, the ageing behavior of the lab-cast EUROFER is compared with the ageing behavior of standard EUROFER97-2 and T91. The microstructural features were investigated with light optical microscopy (LOM), electron back-scattered diffraction (EBSD) and transmission electron microscopy (TEM). Additionally, hardness measurements, tensile tests at elevated temperatures and Charpy V-notch impact testing of KLST-type MCVN specimens were performed to study the microstructural features and mechanical properties of four different F/M grades, i.e. T91, EUROFER97-2 and two lab-casted EUROFER grades. After ageing for 1000 hrs, the microstructures exhibit similar martensitic block sizes independent on the grain size before ageing. With respect to the initial coarser microstructures, the aged microstructures displayed a dislocation structure which is partially fragmented by polygonization. On the other hand, the initial finer microstructures tend to be more stable up to 1000hrs resulting in similar grain sizes for the four different steels. Increasing the ageing time to 4000 hrs, resulted in an increase of lath thickness and coarsening of M23C6 precipitates leading to a deterioration of tensile properties. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=ageing%20experiments" title="ageing experiments">ageing experiments</a>, <a href="https://publications.waset.org/abstracts/search?q=EUROFER" title=" EUROFER"> EUROFER</a>, <a href="https://publications.waset.org/abstracts/search?q=ferritic%2Fmartensitic%20steels" title=" ferritic/martensitic steels"> ferritic/martensitic steels</a>, <a href="https://publications.waset.org/abstracts/search?q=mechanical%20properties" title=" mechanical properties"> mechanical properties</a>, <a href="https://publications.waset.org/abstracts/search?q=microstructure" title=" microstructure"> microstructure</a>, <a href="https://publications.waset.org/abstracts/search?q=T91" title=" T91"> T91</a> </p> <a href="https://publications.waset.org/abstracts/65950/influence-of-thermal-ageing-on-microstructural-features-and-mechanical-properties-of-reduced-activation-ferriticmartensitic-grades" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/65950.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">261</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">55</span> Stabilizing Additively Manufactured Superalloys at High Temperatures</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Keivan%20Davami">Keivan Davami</a>, <a href="https://publications.waset.org/abstracts/search?q=Michael%20Munther"> Michael Munther</a>, <a href="https://publications.waset.org/abstracts/search?q=Lloyd%20Hackel"> Lloyd Hackel</a> </p> <p class="card-text"><strong>Abstract:</strong></p> The control of properties and material behavior by implementing thermal-mechanical processes is based on mechanical deformation and annealing according to a precise schedule that will produce a unique and stable combination of grain structure, dislocation substructure, texture, and dispersion of precipitated phases. The authors recently developed a thermal-mechanical technique to stabilize the microstructure of additively manufactured nickel-based superalloys even after exposure to high temperatures. However, the mechanism(s) that controls this stability is still under investigation. Laser peening (LP), also called laser shock peening (LSP), is a shock based (50 ns duration) post-processing technique used for extending performance levels and improving service life of critical components by developing deep levels of plastic deformation, thereby generating high density of dislocations and inducing compressive residual stresses in the surface and deep subsurface of components. These compressive residual stresses are usually accompanied with an increase in hardness and enhance the material’s resistance to surface-related failures such as creep, fatigue, contact damage, and stress corrosion cracking. While the LP process enhances the life span and durability of the material, the induced compressive residual stresses relax at high temperatures (>0.5Tm, where Tm is the absolute melting temperature), limiting the applicability of the technology. At temperatures above 0.5Tm, the compressive residual stresses relax, and yield strength begins to drop dramatically. The principal reason is the increasing rate of solid-state diffusion, which affects both the dislocations and the microstructural barriers. Dislocation configurations commonly recover by mechanisms such as climbing and recombining rapidly at high temperatures. Furthermore, precipitates coarsen, and grains grow; virtually all of the available microstructural barriers become ineffective.Our results indicate that by using “cyclic” treatments with sequential LP and annealing steps, the compressive stresses survive, and the microstructure is stable after exposure to temperatures exceeding 0.5Tm for a long period of time. When the laser peening process is combined with annealing, dislocations formed as a result of LPand precipitates formed during annealing have a complex interaction that provides further stability at high temperatures. From a scientific point of view, this research lays the groundwork for studying a variety of physical, materials science, and mechanical engineering concepts. This research could lead to metals operating at higher sustained temperatures enabling improved system efficiencies. The strengthening of metals by a variety of means (alloying, work hardening, and other processes) has been of interest for a wide range of applications. However, the mechanistic understanding of the often complex processes of interactionsbetween dislocations with solute atoms and with precipitates during plastic deformation have largely remained scattered in the literature. In this research, the elucidation of the actual mechanisms involved in the novel cyclic LP/annealing processes as a scientific pursuit is investigated through parallel studies of dislocation theory and the implementation of advanced experimental tools. The results of this research help with the validation of a novel laser processing technique for high temperature applications. This will greatly expand the applications of the laser peening technology originally devised only for temperatures lower than half of the melting temperature. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=laser%20shock%20peening" title="laser shock peening">laser shock peening</a>, <a href="https://publications.waset.org/abstracts/search?q=mechanical%20properties" title=" mechanical properties"> mechanical properties</a>, <a href="https://publications.waset.org/abstracts/search?q=indentation" title=" indentation"> indentation</a>, <a href="https://publications.waset.org/abstracts/search?q=high%20temperature%20stability" title=" high temperature stability"> high temperature stability</a> </p> <a href="https://publications.waset.org/abstracts/144656/stabilizing-additively-manufactured-superalloys-at-high-temperatures" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/144656.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">149</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">54</span> Efficiency of Different Types of Addition onto the Hydration Kinetics of Portland Cement</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Marine%20Regnier">Marine Regnier</a>, <a href="https://publications.waset.org/abstracts/search?q=Pascal%20Bost"> Pascal Bost</a>, <a href="https://publications.waset.org/abstracts/search?q=Matthieu%20Horgnies"> Matthieu Horgnies</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Some of the problems to be solved for the concrete industry are linked to the use of low-reactivity cement, the hardening of concrete under cold-weather and the manufacture of pre-casted concrete without costly heating step. The development of these applications needs to accelerate the hydration kinetics, in order to decrease the setting time and to obtain significant compressive strengths as soon as possible. The mechanisms enhancing the hydration kinetics of alite or Portland cement (e.g. the creation of nucleation sites) were already studied in literature (e.g. by using distinct additions such as titanium dioxide nanoparticles, calcium carbonate fillers, water-soluble polymers, C-S-H, etc.). However, the goal of this study was to establish a clear ranking of the efficiency of several types of additions by using a robust and reproducible methodology based on isothermal calorimetry (performed at 20°C). The cement was a CEM I 52.5N PM-ES (Blaine fineness of 455 m²/kg). To ensure the reproducibility of the experiments and avoid any decrease of the reactivity before use, the cement was stored in waterproof and sealed bags to avoid any contact with moisture and carbon dioxide. The experiments were performed on Portland cement pastes by using a water-to-cement ratio of 0.45, and incorporating different compounds (industrially available or laboratory-synthesized) that were selected according to their main composition and their specific surface area (SSA, calculated using the Brunauer-Emmett-Teller (BET) model and nitrogen adsorption isotherms performed at 77K). The intrinsic effects of (i) dry powders (e.g. fumed silica, activated charcoal, nano-precipitates of calcium carbonate, afwillite germs, nanoparticles of iron and iron oxides , etc.), and (ii) aqueous solutions (e.g. containing calcium chloride, hydrated Portland cement or Master X-SEED 100, etc.) were investigated. The influence of the amount of addition, calculated relatively to the dry extract of each addition compared to cement (and by conserving the same water-to-cement ratio) was also studied. The results demonstrated that the X-SEED®, the hydrated calcium nitrate, the calcium chloride (and, at a minor level, a solution of hydrated Portland cement) were able to accelerate the hydration kinetics of Portland cement, even at low concentration (e.g. 1%wt. of dry extract compared to cement). By using higher rates of additions, the fumed silica, the precipitated calcium carbonate and the titanium dioxide can also accelerate the hydration. In the case of the nano-precipitates of calcium carbonate, a correlation was established between the SSA and the accelerating effect. On the contrary, the nanoparticles of iron or iron oxides, the activated charcoal and the dried crystallised hydrates did not show any accelerating effect. Future experiments will be scheduled to establish the ranking of these additions, in terms of accelerating effect, by using low-reactivity cements and other water to cement ratios. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=acceleration" title="acceleration">acceleration</a>, <a href="https://publications.waset.org/abstracts/search?q=hydration%20kinetics" title=" hydration kinetics"> hydration kinetics</a>, <a href="https://publications.waset.org/abstracts/search?q=isothermal%20calorimetry" title=" isothermal calorimetry"> isothermal calorimetry</a>, <a href="https://publications.waset.org/abstracts/search?q=Portland%20cement" title=" Portland cement"> Portland cement</a> </p> <a href="https://publications.waset.org/abstracts/43797/efficiency-of-different-types-of-addition-onto-the-hydration-kinetics-of-portland-cement" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/43797.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">256</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">53</span> Precipitation and Age Hardening in Al-Mg-Si-(Cu) Alloys for Automotive Body Sheet</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Tahar%20Abid">Tahar Abid</a>, <a href="https://publications.waset.org/abstracts/search?q=Haoues%20Ghouss"> Haoues Ghouss</a>, <a href="https://publications.waset.org/abstracts/search?q=Abdelhamid%20Boubertakh"> Abdelhamid Boubertakh</a> </p> <p class="card-text"><strong>Abstract:</strong></p> This present work is focused on the hardening precipitation in two AlMgSi(Cu) automotive body sheets. The effect of pre-aging, aging treatment and 0.10 wt % copper addition on the hardening response was investigated using scanning calorimetry (DSC), transmission electron microscopy (TEM), and Vickers microhardness measurements (Hv). The results reveal the apparition of α-AlFeSi, α-AlFe(Mn)Si type precipitates frequently present and witch remain stable at high temperature in Al-Mg-Si alloys. Indeed, the hardening response in both sheets is certainly due to the predominance of very fine typical phases β' and β'' as rods and needles developed during aging with and without pre-aging. The effect of pre ageing just after homogenization and quenching is to correct the undesirable effect of aging at ambient temperature by making faster alloy hardening during artificial aging.The addition of 0.10 wt % copper has allowed to refine and to enhance the precipitation hardening after quenching. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=AlMgSi%20alloys" title="AlMgSi alloys">AlMgSi alloys</a>, <a href="https://publications.waset.org/abstracts/search?q=precipitation" title=" precipitation"> precipitation</a>, <a href="https://publications.waset.org/abstracts/search?q=hardening" title=" hardening"> hardening</a>, <a href="https://publications.waset.org/abstracts/search?q=activation%20energy" title=" activation energy"> activation energy</a> </p> <a href="https://publications.waset.org/abstracts/166964/precipitation-and-age-hardening-in-al-mg-si-cu-alloys-for-automotive-body-sheet" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/166964.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">89</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">52</span> Electrocoagulation of Ni(OH)2/NiOOH for the Removal of Boron Using Nickel Foam as Sacrificial Anode </h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Yu-Jen%20Shih">Yu-Jen Shih</a>, <a href="https://publications.waset.org/abstracts/search?q=Yao-Hui%20Hunag"> Yao-Hui Hunag</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Electrocoagulation (EC) using metallic nickel foam as anode and cathode for the removal of boron from solution was studied. The electrolytic parameters included pH, current density, and initial boron concentration for optimizing the EC process. Experimental results showed that removal efficiency was increased by elevating pH from 4.0 to 8.0, and then decreased at higher pH. The electrolytic efficacy was not affected by current density. In respect of energy consumption, 1.25 mA/cm2 of current density was acceptable for an effective EC of boron, while increasing boric acid from 10 to 100 ppm-B did not impair removal efficiency too much. Cyclic voltammetry indicated that the oxide film, Ni(OH)2 and NiOOH, at specific overpotentials would result in less weight loss of anode than that predicted by the Faraday’s law. The optimal conditions under which 99.2% of boron was removed and less than 1 ppm-B remained in the electrolyte would be pH 8, four pairs of electrodes, and 1.25 mA/cm2 in 120 min as treating wastewaters containing 10 ppm-B. XRD and SEM characterization suggested that the granular crystallites of hydroxide precipitates was composed of theophrastite. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=borohydrides" title="borohydrides">borohydrides</a>, <a href="https://publications.waset.org/abstracts/search?q=hydrogen%20generation" title=" hydrogen generation"> hydrogen generation</a>, <a href="https://publications.waset.org/abstracts/search?q=NiOOH" title=" NiOOH"> NiOOH</a>, <a href="https://publications.waset.org/abstracts/search?q=electrocoagulation" title=" electrocoagulation"> electrocoagulation</a>, <a href="https://publications.waset.org/abstracts/search?q=cyclic%20voltammetry" title=" cyclic voltammetry"> cyclic voltammetry</a>, <a href="https://publications.waset.org/abstracts/search?q=boron%20removal" title=" boron removal"> boron removal</a> </p> <a href="https://publications.waset.org/abstracts/45835/electrocoagulation-of-nioh2niooh-for-the-removal-of-boron-using-nickel-foam-as-sacrificial-anode" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/45835.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">260</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">51</span> Mechanical and Tribological Characterization of Squeeze Cast Al 6061 Alloy Reinforced with SiC and Al₂O₃ Particulates</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Gurcan%20A.%20B.">Gurcan A. B.</a>, <a href="https://publications.waset.org/abstracts/search?q=Baker%20T.%20N."> Baker T. N.</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Due to economic and environmental requirements, it is becoming increasingly important to reduce vehicle weight. The first approach consisted in using light materials with high thermal conductivity, such as aluminium alloys. This choice allowed significant mass reduction and lower temperature but required recourse to ventilated discs. Among aluminium alloys, Al 6xxx series alloys enjoy the highest strength-to-weight ratio and, therefore, have found wide applications in the automobile and aerospace industries. However, these alloys lose their high strength rapidly when they are exposed to elevated temperatures. This rapid decline in the strength is directly related to the coarsening of very fine precipitates which are then not as effective in obstructing the dislocations. The incorporation of micro-scale and nano-scale particulates in aluminium systems can greatly enhance their mechanical characteristics. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=mechanical%20and%20tribological%20behaviour" title="mechanical and tribological behaviour">mechanical and tribological behaviour</a>, <a href="https://publications.waset.org/abstracts/search?q=scanning%20electron%20microscope" title=" scanning electron microscope"> scanning electron microscope</a>, <a href="https://publications.waset.org/abstracts/search?q=optical%20test" title=" optical test"> optical test</a>, <a href="https://publications.waset.org/abstracts/search?q=mechanical%20properties%20test" title=" mechanical properties test"> mechanical properties test</a>, <a href="https://publications.waset.org/abstracts/search?q=experimental%20test" title=" experimental test"> experimental test</a> </p> <a href="https://publications.waset.org/abstracts/185439/mechanical-and-tribological-characterization-of-squeeze-cast-al-6061-alloy-reinforced-with-sic-and-al2o3-particulates" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/185439.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">55</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">50</span> Acid Mine Drainage Remediation Using Silane and Phosphate Coatings</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=M.%20Chiliza">M. Chiliza</a>, <a href="https://publications.waset.org/abstracts/search?q=H.%20P.%20Mbukwane"> H. P. Mbukwane</a>, <a href="https://publications.waset.org/abstracts/search?q=P%20Masita"> P Masita</a>, <a href="https://publications.waset.org/abstracts/search?q=H.%20Rutto"> H. Rutto</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Acid mine drainage (AMD) one of the main pollutants of water in many countries that have mining activities. AMD results from the oxidation of pyrite and other metal sulfides. When these metals gets exposed to moisture and oxygen, leaching takes place releasing sulphate and Iron. Acid drainage is often noted by 'yellow boy,' an orange-yellow substance that occurs when the pH of acidic mine-influenced water raises above pH 3, so that the previously dissolved iron precipitates out. The possibility of using environmentally friendly silane and phosphate based coatings on pyrite to remediate acid mine drainage and prevention at source was investigated. The results showed that both coatings reduced chemical oxidation of pyrite based on Fe and sulphate release. Furthermore, it was found that silane based coating performs better when coating synthesis take place in a basic hydrolysis than in an acidic state. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=acid%20mine%20drainage" title="acid mine drainage">acid mine drainage</a>, <a href="https://publications.waset.org/abstracts/search?q=pyrite" title=" pyrite"> pyrite</a>, <a href="https://publications.waset.org/abstracts/search?q=silane" title=" silane"> silane</a>, <a href="https://publications.waset.org/abstracts/search?q=phosphate" title=" phosphate"> phosphate</a> </p> <a href="https://publications.waset.org/abstracts/59866/acid-mine-drainage-remediation-using-silane-and-phosphate-coatings" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/59866.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">342</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">49</span> Hard Water Softening by Chronoamperometry and Impedancemetry</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Samira%20Ghizellaoui">Samira Ghizellaoui</a>, <a href="https://publications.waset.org/abstracts/search?q=Manel%20Boumagoura"> Manel Boumagoura</a>, <a href="https://publications.waset.org/abstracts/search?q=Rayane%20Menzri"> Rayane Menzri</a> </p> <p class="card-text"><strong>Abstract:</strong></p> The ground water Hamma rich in calcium and bicarbonate likely to deposit the tartar and subsequently lead to the obstruction of the pipes and the seizing of the stopping devices in addition to the financial losses resulting there from. It is therefore necessary to optimise an antiscaling treatment in order to avoid the risk of formation of tartar deposits in the various installations and to protect the equipment in contact with this water. MgCl2 is the chemical inhibitor which was tested. To optimise the effective concentration of this product, we used two electrochemical methods (chronoamperometry and impedancemetry) to identify the best method for optimizing antiscaling treatment. IR, RX, Raman spectroscopy and SEM indicate that the raw waters of Hamma give precipitates in the form of calcite (the most stable form), with the presence of a small amount of magnesian calcite and aragonite. In the presence of the inhibitor (MgCl2), calcium carbonate changes morphology to other forms that do not exist in the deposit obtained from the raw water (vaterite and calcium carbonate monohydrate). <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=calcium%20carbonate" title="calcium carbonate">calcium carbonate</a>, <a href="https://publications.waset.org/abstracts/search?q=MgCl2" title=" MgCl2"> MgCl2</a>, <a href="https://publications.waset.org/abstracts/search?q=chronoamperometry" title=" chronoamperometry"> chronoamperometry</a>, <a href="https://publications.waset.org/abstracts/search?q=Impedancemetry" title=" Impedancemetry"> Impedancemetry</a> </p> <a href="https://publications.waset.org/abstracts/167707/hard-water-softening-by-chronoamperometry-and-impedancemetry" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/167707.pdf" target="_blank" class="btn btn-primary 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