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EBSD</title> <meta name="description" content="Search results for: in-situ EBSD"> <meta name="keywords" content="in-situ EBSD"> <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="in-situ EBSD"> <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> 68</div> </div> </div> </div> <h1 class="mt-3 mb-3 text-center" style="font-size:1.6rem;">Search results for: in-situ EBSD</h1> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">68</span> In-situ Observations Using SEM-EBSD for Bending Deformation in Single-Crystal Materials</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Yuko%20Matayoshi">Yuko Matayoshi</a>, <a href="https://publications.waset.org/abstracts/search?q=Takashi%20Sakai"> Takashi Sakai</a>, <a href="https://publications.waset.org/abstracts/search?q=Yin-Gjum%20Jin"> Yin-Gjum Jin</a>, <a href="https://publications.waset.org/abstracts/search?q=Jun-ichi%20Koyama"> Jun-ichi Koyama</a> </p> <p class="card-text"><strong>Abstract:</strong></p> To elucidate the material characteristics of single crystals of pure aluminum and copper, the respective relations between crystallographic orientations and micro structures were examined, along with bending and mechanical properties. The texture distribution was also analysed. Bending tests were performed in a SEM apparatus while its behaviors were observed. Some analytical results related to crystal direction maps, inverse pole figures, and textures were obtained from electron back scatter diffraction (EBSD) analyses. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=pure%20aluminum" title="pure aluminum">pure aluminum</a>, <a href="https://publications.waset.org/abstracts/search?q=pure%20copper" title=" pure copper"> pure copper</a>, <a href="https://publications.waset.org/abstracts/search?q=single%20crystal" title=" single crystal"> single crystal</a>, <a href="https://publications.waset.org/abstracts/search?q=bending" title=" bending"> bending</a>, <a href="https://publications.waset.org/abstracts/search?q=SEM-EBSD%20analysis" title=" SEM-EBSD analysis"> SEM-EBSD analysis</a>, <a href="https://publications.waset.org/abstracts/search?q=texture" title=" texture"> texture</a>, <a href="https://publications.waset.org/abstracts/search?q=microstructure" title=" microstructure"> microstructure</a> </p> <a href="https://publications.waset.org/abstracts/16499/in-situ-observations-using-sem-ebsd-for-bending-deformation-in-single-crystal-materials" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/16499.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">368</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> SEM-EBSD Observation for Microtubes by Using Dieless Drawing Process</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Takashi%20Sakai">Takashi Sakai</a>, <a href="https://publications.waset.org/abstracts/search?q=Itaru%20Kumisawa"> Itaru Kumisawa</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Because die drawing requires insertion of a die, a plug, or a mandrel, higher precision and efficiency are demanded for drawing equipment for a tube having smaller diameter. Manufacturing of such tubes is also accompanied by problems such as cracking and fracture. We specifically examine dieless drawing, which is less affected by these drawing-related difficulties. This deformation process is governed by a similar principle to that of reduction in diameter when pulling a heated glass tube. We conducted dieless drawing of SUS304 stainless steel microtubes under various conditions with three factor parameters of heating temperature, area reduction, and drawing speed. We used SEM-EBSD to observe the processing condition effects on microstructural elements. As the result of this study, crystallographic orientation of microtube is clear by using SEM-EBSD analysis. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=microtube" title="microtube">microtube</a>, <a href="https://publications.waset.org/abstracts/search?q=dieless%20drawing" title=" dieless drawing"> dieless drawing</a>, <a href="https://publications.waset.org/abstracts/search?q=IPF%20%28inverse%20pole%20figure%29" title=" IPF (inverse pole figure)"> IPF (inverse pole figure)</a>, <a href="https://publications.waset.org/abstracts/search?q=GOS%20%28grain%20orientation%20spread%29" title=" GOS (grain orientation spread)"> GOS (grain orientation spread)</a>, <a href="https://publications.waset.org/abstracts/search?q=crystallographic%20analysis" title=" crystallographic analysis"> crystallographic analysis</a> </p> <a href="https://publications.waset.org/abstracts/74385/sem-ebsd-observation-for-microtubes-by-using-dieless-drawing-process" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/74385.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">248</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> Texture Observation of Bending by XRD and EBSD Method</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Takashi%20Sakai">Takashi Sakai</a>, <a href="https://publications.waset.org/abstracts/search?q=Yuri%20Shimomura"> Yuri Shimomura</a> </p> <p class="card-text"><strong>Abstract:</strong></p> The crystal orientation is a factor that affects the microscopic material properties. Crystal orientation determines the anisotropy of the polycrystalline material. And it is closely related to the mechanical properties of the material. In this paper, for pure copper polycrystalline material, two different methods; X-Ray Diffraction (XRD) and Electron Backscatter Diffraction (EBSD); and the crystal orientation were analyzed. In the latter method, it is possible that the X-ray beam diameter is thicker as compared to the former, to measure the crystal orientation macroscopically relatively. By measurement of the above, we investigated the change in crystal orientation and internal tissues of pure copper. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=bending" title="bending">bending</a>, <a href="https://publications.waset.org/abstracts/search?q=electron%20backscatter%20diffraction" title=" electron backscatter diffraction"> electron backscatter diffraction</a>, <a href="https://publications.waset.org/abstracts/search?q=X-ray%20diffraction" title=" X-ray diffraction"> X-ray diffraction</a>, <a href="https://publications.waset.org/abstracts/search?q=microstructure" title=" microstructure"> microstructure</a>, <a href="https://publications.waset.org/abstracts/search?q=IPF%20map" title=" IPF map"> IPF map</a>, <a href="https://publications.waset.org/abstracts/search?q=orientation%20distribution%20function" title=" orientation distribution function"> orientation distribution function</a> </p> <a href="https://publications.waset.org/abstracts/74539/texture-observation-of-bending-by-xrd-and-ebsd-method" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/74539.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">330</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> Characterizing Surface Machining-Induced Local Deformation Using Electron Backscatter Diffraction</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Wenqian%20Zhang">Wenqian Zhang</a>, <a href="https://publications.waset.org/abstracts/search?q=Xuelin%20Wang"> Xuelin Wang</a>, <a href="https://publications.waset.org/abstracts/search?q=Yujin%20Hu"> Yujin Hu</a>, <a href="https://publications.waset.org/abstracts/search?q=Siyang%20Wang"> Siyang Wang</a> </p> <p class="card-text"><strong>Abstract:</strong></p> The subsurface layer of a component plays a significant role in its service performance. Any surface mechanical process during fabrication can introduce a deformed layer near the surface, which can be related to the microstructure alteration and strain hardening, and affects the mechanical properties and corrosion resistance of the material. However, there exists a great difficulty in determining the subsurface deformation induced by surface machining. In this study, electron backscatter diffraction (EBSD) was used to study the deformed layer of surface milled 316 stainless steel. The microstructure change was displayed by the EBSD maps and characterized by misorientation variation. The results revealed that the surface milling resulted in heavily nonuniform deformations in the subsurface layer and even in individual grains. The direction of the predominant grain deformation was about 30-60 deg to the machined surface. Moreover, a local deformation rate (LDR) was proposed to quantitatively evaluate the local deformation degree. Both of the average and maximum LDRs were utilized to characterize the deformation trend along the depth direction. It was revealed that the LDR had a strong correlation with the development of grain and sub-grain boundaries. In this work, a scan step size of 1.2 μm was chosen for the EBSD measurement. A LDR higher than 18 deg/μm indicated a newly developed grain boundary, while a LDR ranged from 2.4 to 18 deg/μm implied the generation of a sub-grain boundary. And a lower LDR than 2.4 deg/μm could only introduce a slighter deformation and no sub-grain boundary was produced. According to the LDR analysis with the evolution of grain or sub grain boundaries, the deformed layer could be classified into four zones: grain broken layer, seriously deformed layer, slightly deformed layer and non-deformed layer. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=surface%20machining" title="surface machining">surface machining</a>, <a href="https://publications.waset.org/abstracts/search?q=EBSD" title=" EBSD"> EBSD</a>, <a href="https://publications.waset.org/abstracts/search?q=subsurface%20layer" title=" subsurface layer"> subsurface layer</a>, <a href="https://publications.waset.org/abstracts/search?q=local%20deformation" title=" local deformation"> local deformation</a> </p> <a href="https://publications.waset.org/abstracts/65094/characterizing-surface-machining-induced-local-deformation-using-electron-backscatter-diffraction" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/65094.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">331</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> An EBSD Investigation of Ti-6Al-4Nb Alloy Processed by Plan Strain Compression Test </h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Anna%20Jastrzebska">Anna Jastrzebska</a>, <a href="https://publications.waset.org/abstracts/search?q=K.%20S.%20Suresh"> K. S. Suresh</a>, <a href="https://publications.waset.org/abstracts/search?q=T.%20Kitashima"> T. Kitashima</a>, <a href="https://publications.waset.org/abstracts/search?q=Y.%20Yamabe-Mitarai"> Y. Yamabe-Mitarai</a>, <a href="https://publications.waset.org/abstracts/search?q=Z.%20Pakiela"> Z. Pakiela </a> </p> <p class="card-text"><strong>Abstract:</strong></p> Near α titanium alloys are important materials for aerospace applications, especially in high temperature applications such as jet engine. Mechanical properties of Ti alloys strongly depends on their processing route, then it is very important to understand micro-structure change by different processing. In our previous study, Nb was found to improve oxidation resistance of Ti alloys. In this study, micro-structure evolution of Ti-6Al-4Nb (wt %) alloy was investigated after plain strain compression test in hot working temperatures in the α and β phase region. High-resolution EBSD was successfully used for precise phase and texture characterization of this alloy. 1.1 kg of Ti-6Al-4Nb ingot was prepared using cold crucible levitation melting. The ingot was subsequently homogenized in 1050 deg.C for 1h followed by cooling in the air. Plate like specimens measuring 10×20×50 mm3 were cut from an ingot by electrical discharge machining (EDM). The plain strain compression test using an anvil with 10 x 35 mm in size was performed with 3 different strain rates: 0.1s-1, 1s-1and 10s-1 in 700 deg.C and 1050 deg.C to obtain 75% of deformation. The micro-structure was investigated by scanning electron microscopy (SEM) equipped with electron backscatter diffraction (EBSD) detector. The α/β phase ratio and phase morphology as well as the crystallographic texture, subgrain size, misorientation angles and misorientation gradients corresponding to each phase were determined over the middle and the edge of sample areas. The deformation mechanism in each working temperature was discussed. The evolution of texture changes with strain rate was investigated. The micro-structure obtained by plain strain compression test was heterogeneous with a wide range of grain sizes. This is because deformation and dynamic recrystallization occurred during deformation at temperature in the α and β phase. It was strongly influenced by strain rate. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=EBSD" title="EBSD">EBSD</a>, <a href="https://publications.waset.org/abstracts/search?q=plain%20strain%20compression%20test" title=" plain strain compression test"> plain strain compression test</a>, <a href="https://publications.waset.org/abstracts/search?q=Ti%20alloys" title=" Ti alloys"> Ti alloys</a> </p> <a href="https://publications.waset.org/abstracts/21431/an-ebsd-investigation-of-ti-6al-4nb-alloy-processed-by-plan-strain-compression-test" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/21431.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">380</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> Interface Analysis of Annealed Al/Cu Cladded Sheet</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Joon%20Ho%20Kim">Joon Ho 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> Effect of aging treatment on microstructural aspects of interfacial layers of the Cu/Al clad sheet produced by Differential Speed Rolling (DSR) process were studied by Electron Back Scattered Diffraction (EBSD). Clad sheet of Al/Cu has been fabricated by using DSR, which caused severe shear deformation between Al and Cu plate to easily bond to each other. Rolling was carried out at 100°C with speed ratio of 2, in which the total thickness reduction was 45%. Interface layers of clad sheet were analyzed by EBSD after subsequent annealing at 400°C for 30 to 120 min. With increasing annealing time, thickness of interface layer and fraction of high angle grain boundary were increased and average grain size was decreased. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=aluminium%2Fcopper%20clad%20sheet" title="aluminium/copper clad sheet">aluminium/copper clad sheet</a>, <a href="https://publications.waset.org/abstracts/search?q=differential%20speed%20rolling" title=" differential speed rolling"> differential speed rolling</a>, <a href="https://publications.waset.org/abstracts/search?q=interface%20layer" title=" interface layer"> interface layer</a>, <a href="https://publications.waset.org/abstracts/search?q=microstructure" title=" microstructure"> microstructure</a>, <a href="https://publications.waset.org/abstracts/search?q=annealing" title=" annealing"> annealing</a>, <a href="https://publications.waset.org/abstracts/search?q=electron%20back%20scattered%20diffraction" title=" electron back scattered diffraction"> electron back scattered diffraction</a> </p> <a href="https://publications.waset.org/abstracts/7126/interface-analysis-of-annealed-alcu-cladded-sheet" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/7126.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">366</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> Microscopic Analysis of Bulk, High-Tc Superconductors by Transmission Kikuchi Diffraction</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Anjela%20Koblischka-Veneva">Anjela Koblischka-Veneva</a>, <a href="https://publications.waset.org/abstracts/search?q=Michael%20R.%20Koblischka"> Michael R. Koblischka</a> </p> <p class="card-text"><strong>Abstract:</strong></p> In this contribution, the Transmission-Kikuchi Diffraction (TKD, or sometimes called t-EBSD) is applied to bulk, melt-grown YBa₂Cu₃O₇ (YBCO) superconductors prepared by the MTMG (melt-textured melt-grown) technique and the infiltration growth (IG) technique. TEM slices required for the analysis were prepared by means of Focused Ion-Beam (FIB) milling using mechanically polished sample surfaces, which enable a proper selection of the interesting regions for investigations. The required optical transparency was reached by an additional polishing step of the resulting surfaces using FIB-Ga-ion and Ar-ion milling. The improved spatial resolution of TKD enabled the investigation of the tiny YBa₂Cu₃O₅ (Y-211) particles having a diameter of about 50-100 nm embedded within the YBCO matrix and of other added secondary phase particles. With the TKD technique, the microstructural properties of the YBCO matrix are studied in detail. It is observed that the matrix shows the effects of stress/strain, depending on the size and distribution of the embedded particles, which are important for providing additional flux pinning centers in such superconducting bulk samples. Using the Kernel Average Misorientation (KAM) maps, the strain induced in the superconducting matrix around the particles, which increases the flux pinning effectivity, can be clearly revealed. This type of analysis of the EBSD/TKD data is, therefore, also important for other material systems, where nanoparticles are embedded in a matrix. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=transmission%20Kikuchi%20diffraction" title="transmission Kikuchi diffraction">transmission Kikuchi diffraction</a>, <a href="https://publications.waset.org/abstracts/search?q=EBSD" title=" EBSD"> EBSD</a>, <a href="https://publications.waset.org/abstracts/search?q=TKD" title=" TKD"> TKD</a>, <a href="https://publications.waset.org/abstracts/search?q=embedded%20particles" title=" embedded particles"> embedded particles</a>, <a href="https://publications.waset.org/abstracts/search?q=superconductors%20YBa%E2%82%82Cu%E2%82%83O%E2%82%87" title=" superconductors YBa₂Cu₃O₇"> superconductors YBa₂Cu₃O₇</a> </p> <a href="https://publications.waset.org/abstracts/123869/microscopic-analysis-of-bulk-high-tc-superconductors-by-transmission-kikuchi-diffraction" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/123869.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">135</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> Bake Hardening Behavior of Ultrafine Grained and Nano-Grained AA6061 Aluminum Alloy </h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Hamid%20Alihosseini">Hamid Alihosseini</a>, <a href="https://publications.waset.org/abstracts/search?q=Kamran%20Dehghani"> Kamran Dehghani</a> </p> <p class="card-text"><strong>Abstract:</strong></p> In this study, the effects of grain size of AA6061 aluminum on the bake hardening have been investigated. The grains of sample sheets refined by applying 4, 8, and 12 passes of ECAP and their microstructures and mechanical properties were investigated. EBSD and TEM studies of the sheets showed grain refinement, and the EBSD micrograph of the alloy ECAPed for 12 passes showed nano-grained (NG) ∼95nm in size. Then, the bake hardenability of processed sheet was compared by pre-straining to 6% followed by baking at 200°C for 20 min. The results show that in case of baking at 200°C, there was an increase about 108%, 93%, and 72% in the bake hardening for 12, 8, and 4 passes, respectively. The maximum in bake hardenability (120 MPa) and final yield stress (583 MPa) were pertaining to the ultra-fine grain specimen pre-strained 6% followed by baking at 200◦C. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=bake%20hardening" title="bake hardening">bake hardening</a>, <a href="https://publications.waset.org/abstracts/search?q=ultrafine%20grain" title=" ultrafine grain"> ultrafine grain</a>, <a href="https://publications.waset.org/abstracts/search?q=nano%20grain" title=" nano grain"> nano grain</a>, <a href="https://publications.waset.org/abstracts/search?q=AA6061%20aluminum" title=" AA6061 aluminum"> AA6061 aluminum</a>, <a href="https://publications.waset.org/abstracts/search?q=" title=" "> </a> </p> <a href="https://publications.waset.org/abstracts/33963/bake-hardening-behavior-of-ultrafine-grained-and-nano-grained-aa6061-aluminum-alloy" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/33963.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">60</span> Growth Patterns of Pyrite Crystals Studied by Electron Back Scatter Diffraction (EBSD)</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Kirsten%20Techmer">Kirsten Techmer</a>, <a href="https://publications.waset.org/abstracts/search?q=Jan-Erik%20Rybak"> Jan-Erik Rybak</a>, <a href="https://publications.waset.org/abstracts/search?q=Simon%20Rudolph"> Simon Rudolph</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Natural formed pyrites (FeS2) are frequent sulfides in sedimentary and metamorphic rocks. Growth textures of idiomorphic pyrite assemblages reflect the conditions during their formation in the geologic sequence, furtheron the local texture analyses of the growth patterns of pyrite assemblages by EBSD reveal the possibility to resolve the growth conditions during the formation of pyrite at the micron scale. The spatial resolution of local texture measurements in the Scanning Electron Microscope used can be in the nanomete scale. Orientation contrasts resulting from domains of smaller misorientations within larger pyrite crystals can be resolved as well. The electron optical studies have been carried out in a Field-Emission Scanning Electron Microscope (FEI Quanta 200) equipped with a CCD camera to study the orientation contrasts along the surfaces of pyrite. Idiomorphic cubic single crystals of pyrite, polycrystalline assemblages of pyrite, spherically grown spheres of pyrite as well as pyrite-bearing ammonites have been studied by EBSD in the Scanning Electron Microscope. Samples were chosen to show no or minor secondary deformation and an idiomorphic 3D crystal habit, so the local textures of pyrite result mainly from growth and minor from deformation. The samples studied derived from Navajun (Spain), Chalchidiki (Greece), Thüringen (Germany) and Unterkliem (Austria). Chemical analyses by EDAX show pyrite with minor inhomogeneities e.g., single crystals of galena and chalcopyrite along the grain boundaries of larger pyrite crystals. Intergrowth between marcasite and pyrite can be detected in one sample. Pyrite may form intense growth twinning lamellae on {011}. Twinning, e.g., contact twinning is abundant within the crystals studied and the individual twinning lamellaes can be resolved by EBSD. The ammonites studied show a replacement of the shale by newly formed pyrite resulting in an intense intergrowth of calcite and pyrite. EBSD measurements indicate a polycrystalline microfabric of both minerals, still reflecting primary surface structures of the ammonites e.g, the Septen. Discs of pyrite (“pyrite dollar”) as well as pyrite framboids show growth patterns comprising a typical microfabric. EBSD studies reveal an equigranular matrix in the inner part of the discs of pyrite and a fiber growth with larger misorientations in the outer regions between the individual segments. This typical microfabric derived from a formation of pyrite crystals starting at a higher nucleation rate and followed by directional crystal growth. EBSD studies show, that the growth texture of pyrite in the samples studied reveals a correlation between nucleation rate and following growth rate of the pyrites, thus leading to the characteristic crystal habits. Preferential directional growth at lower nucleation rates may lead to the formation of 3D framboids of pyrite. Crystallographic misorientations between the individual fibers are similar. In ammonites studied, primary anisotropies of the substrates like e.g., ammonitic sutures, influence the nucleation, crystal growth and habit of the newly formed pyrites along the surfaces. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=Electron%20Back%20Scatter%20Diffraction%20%28EBSD%29" title="Electron Back Scatter Diffraction (EBSD)">Electron Back Scatter Diffraction (EBSD)</a>, <a href="https://publications.waset.org/abstracts/search?q=growth%20pattern" title=" growth pattern"> growth pattern</a>, <a href="https://publications.waset.org/abstracts/search?q=Fe-sulfides%20%28pyrite%29" title=" Fe-sulfides (pyrite)"> Fe-sulfides (pyrite)</a>, <a href="https://publications.waset.org/abstracts/search?q=texture%20analyses" title=" texture analyses"> texture analyses</a> </p> <a href="https://publications.waset.org/abstracts/56526/growth-patterns-of-pyrite-crystals-studied-by-electron-back-scatter-diffraction-ebsd" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/56526.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">292</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> Residual Stress Around Embedded Particles in Bulk YBa2Cu3Oy Samples</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Anjela%20Koblischka-Veneva">Anjela Koblischka-Veneva</a>, <a href="https://publications.waset.org/abstracts/search?q=Michael%20R.%20Koblischka"> Michael R. Koblischka</a> </p> <p class="card-text"><strong>Abstract:</strong></p> To increase the flux pinning performance of bulk YBa2Cu3O7-δ (YBCO or Y-123) superconductors, it is common to employ secondary phase particles, either Y2BaCuO5 (Y-211) particles created during the growth of the samples or additionally added (nano)particles of various types, embedded in the superconducting Y-123 matrix. As the crystallographic parameters of all the particles indicate a misfit to Y-123, there will be residual strain within the Y-123 matrix around such particles. With a dedicated analysis of electron backscatter diffraction (EBSD) data obtained on various bulk, Y-123 superconductor samples, the strain distribution around such embedded secondary phase particles can be revealed. The results obtained are presented in form of Kernel Average Misorientation (KAM) mappings. Around large Y-211 particles, the strain can be so large that YBCO subgrains are formed. Therefore, it is essential to properly control the particle size as well as their distribution within the bulk sample to obtain the best performance. The impact of the strain distribution on the flux pinning properties is discussed. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=Bulk%20superconductors" title="Bulk superconductors">Bulk superconductors</a>, <a href="https://publications.waset.org/abstracts/search?q=EBSD" title=" EBSD"> EBSD</a>, <a href="https://publications.waset.org/abstracts/search?q=Strain" title=" Strain"> Strain</a>, <a href="https://publications.waset.org/abstracts/search?q=YBa2Cu3Oy" title=" YBa2Cu3Oy"> YBa2Cu3Oy</a> </p> <a href="https://publications.waset.org/abstracts/122638/residual-stress-around-embedded-particles-in-bulk-yba2cu3oy-samples" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/122638.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">150</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> Use of Simultaneous Electron Backscatter Diffraction and Energy Dispersive X-Ray Spectroscopy Techniques to Characterize High-Temperature Oxides Formed on Nickel-Based Superalloys Exposed to Super-Critical Water Environment</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Mohsen%20Sanayei">Mohsen Sanayei</a>, <a href="https://publications.waset.org/abstracts/search?q=Jerzy%20Szpunar"> Jerzy Szpunar</a>, <a href="https://publications.waset.org/abstracts/search?q=Sami%20Penttil%C3%A4"> Sami Penttilä</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Exposure of Nickel-based superalloys to high temperature and harsh environment such as Super-Critical Water (SCW) environment leads to the formation of oxide scales composed of multiple and complex phases that are difficult to differentiate with conventional analysis techniques. In this study, we used simultaneous Electron Backscatter Diffraction (EBSD) and Energy Dispersive X-ray Spectroscopy (EDS) to analyze the complex oxide scales formed on several Nickel-based Superalloys exposed to high temperature SCW. Multi-layered structures of Iron, Nickel, Chromium and Molybdenum oxides and spinels were clearly identified using the simultaneous EBSD-EDS analysis technique. Furthermore, the orientation relationship between the oxide scales and the substrate has been investigated. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=electron%20backscatter%20diffraction" title="electron backscatter diffraction">electron backscatter diffraction</a>, <a href="https://publications.waset.org/abstracts/search?q=energy%20dispersive%20x-ray%20spectroscopy" title=" energy dispersive x-ray spectroscopy"> energy dispersive x-ray spectroscopy</a>, <a href="https://publications.waset.org/abstracts/search?q=superalloy" title=" superalloy"> superalloy</a>, <a href="https://publications.waset.org/abstracts/search?q=super-critical%20water" title=" super-critical water"> super-critical water</a> </p> <a href="https://publications.waset.org/abstracts/70076/use-of-simultaneous-electron-backscatter-diffraction-and-energy-dispersive-x-ray-spectroscopy-techniques-to-characterize-high-temperature-oxides-formed-on-nickel-based-superalloys-exposed-to-super-critical-water-environment" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/70076.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">316</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> In Situ Analysis of the Effect of Twinning on Deformation and Cracking of Magnesium Alloy</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Chaoqun%20Zhao">Chaoqun Zhao</a>, <a href="https://publications.waset.org/abstracts/search?q=Gang%20Fang"> Gang Fang</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Twinning is an important deformation mechanism of magnesium alloys, but there is no consensus on the relationship between twinning and ductility. To comprehensively understand the effect of twinning on plastic deformation and cracking, the in situ tensile tests of a magnesium alloy sample along its extrusion direction were conducted, accompanied by the observations using scanning electron microscopy (SEM) and electron backscattered diffraction (EBSD). The misorientation angles around specific axes and trace analysis of grains were used to identify the active twinning systems. The results show that the area fraction of tension twins increases with the increasing strain, resulting in the c-axes of most grains rotating from the normal direction to the transverse direction, and the intensity of (0002) pole is weakened. Based on the analysis of kernel average misorientation (KAM) and SEM maps, it is found that the appearance of tension twins accommodates plastic deformation. However, the stress concentration caused by the intersection of tension twinning with the second phase can lead to crack initiation, and the crack propagates along the direction perpendicular to the tension twinning. For contraction twinning, it plays a role in plastic relaxation and improving strain compatibility during deformation, and is not a necessary potential mechanism of crack nucleation. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=magnesium%20alloy" title="magnesium alloy">magnesium alloy</a>, <a href="https://publications.waset.org/abstracts/search?q=cracking" title=" cracking"> cracking</a>, <a href="https://publications.waset.org/abstracts/search?q=in-situ%20EBSD" title=" in-situ EBSD"> in-situ EBSD</a>, <a href="https://publications.waset.org/abstracts/search?q=twinning" title=" twinning"> twinning</a> </p> <a href="https://publications.waset.org/abstracts/190893/in-situ-analysis-of-the-effect-of-twinning-on-deformation-and-cracking-of-magnesium-alloy" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/190893.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">26</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> High-Temperature Behavior of Boiler Steel by Friction Stir Processing</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Supreet%20Singh">Supreet Singh</a>, <a href="https://publications.waset.org/abstracts/search?q=Manpreet%20Kaur"> Manpreet Kaur</a>, <a href="https://publications.waset.org/abstracts/search?q=Manoj%20Kumar"> Manoj Kumar</a> </p> <p class="card-text"><strong>Abstract:</strong></p> High temperature corrosion is an imperative material degradation method experienced in thermal power plants and other energy generation sectors. Metallic materials such as ferritic steels have special properties such as easy fabrication and machinibilty, low cost, but a serious drawback of these materials is the worsening in properties initiating from the interaction with the environments. The metallic materials do not endure higher temperatures for extensive period of time because of their poor corrosion resistance. Friction Stir Processing (FSP), has emerged as the potent surface modification means and control of microstructure in thermo mechanically heat affecting zones of various metal alloys. In the current research work, FSP was done on the boiler tube of SA 210 Grade A1 material which is regularly used by thermal power plants. The strengthening of SA210 Grade A1 boiler steel through microstructural refinement by Friction Stir Processing (FSP) and analyze the effect of the same on high temperature corrosion behavior. The high temperature corrosion performance of the unprocessed and the FSPed specimens were evaluated in the laboratory using molten salt environment of Na₂SO₄-82%Fe₂(SO₄). The unprocessed and FSPed low carbon steel Gr A1 evaluation was done in terms of microstructure, corrosion resistance, mechanical properties like hardness- tensile. The in-depth characterization was done by EBSD, SEM/EDS and X-ray mapping analyses with an aim to propose the mechanism behind high temperature corrosion behavior of the FSPed steel. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=boiler%20steel" title="boiler steel">boiler steel</a>, <a href="https://publications.waset.org/abstracts/search?q=characterization" title=" characterization"> characterization</a>, <a href="https://publications.waset.org/abstracts/search?q=corrosion" title=" corrosion"> corrosion</a>, <a href="https://publications.waset.org/abstracts/search?q=EBSD%2FSEM%2FEDS%2FXRD" title=" EBSD/SEM/EDS/XRD"> EBSD/SEM/EDS/XRD</a>, <a href="https://publications.waset.org/abstracts/search?q=friction%20stir%20processing" title=" friction stir processing"> friction stir processing</a> </p> <a href="https://publications.waset.org/abstracts/91954/high-temperature-behavior-of-boiler-steel-by-friction-stir-processing" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/91954.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">237</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> Microscopic Analysis of Bulk, High-TC Superconductors by Transmission Kikuchi Diffraction</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Anjela%20Koblischka-Veneva">Anjela Koblischka-Veneva</a>, <a href="https://publications.waset.org/abstracts/search?q=Michael%20Koblischka"> Michael Koblischka</a> </p> <p class="card-text"><strong>Abstract:</strong></p> In this contribution, the transmission-Kikuchi diffrac-tion (TKD, or sometimes called t-EBSD) is applied to bulk, melt-grown YBa2Cu3O7 (YBCO) superconductors prepared by the MTMG (melt-textured melt-grown) technique and the infiltration (IG) growth technique. TEM slices required for the analysis were prepared by means of focused ion-beam (FIB) milling using mechanically polished sample surfaces, which enable a proper selection of the in-teresting regions for investigations. The required optical transparency was reached by an additional polishing step of the resulting surfaces using FIB-Ga-ion and Ar-ion milling. The improved spatial resolution of TKD enabled the investigation of the tiny Y2BaCuO5 (Y-211) particles having a diameter of about 50-100 nm embedded within the YBCO matrix and of other added secondary phase particles. With the TKD technique, the microstructural properties of the YBCO matrix are studied in detail. It is observed that the matrix shows effects of stress/strain, depending on the size and distribution of the embedded particles, which are important for providing additional flux pinning centers in such superconducting bulk samples. Using the Kernel average misorientation (KAM) maps, the strain induced in the superconducting matrix around the particles, which increases the flux pinning effectivity, can be clearly revealed. This type of analysis of the EBSD/TKD data is, therefore, also important for other material systems, where nanoparticles are embedded in a matrix. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=electron%20backscatter%20Diffraction" title="electron backscatter Diffraction">electron backscatter Diffraction</a>, <a href="https://publications.waset.org/abstracts/search?q=transmission%20Kikuchi%20diffraction" title=" transmission Kikuchi diffraction"> transmission Kikuchi diffraction</a>, <a href="https://publications.waset.org/abstracts/search?q=SEM" title=" SEM"> SEM</a>, <a href="https://publications.waset.org/abstracts/search?q=YBCO" title=" YBCO"> YBCO</a>, <a href="https://publications.waset.org/abstracts/search?q=microstructure" title=" microstructure"> microstructure</a>, <a href="https://publications.waset.org/abstracts/search?q=nanoparticles" title=" nanoparticles"> nanoparticles</a> </p> <a href="https://publications.waset.org/abstracts/126917/microscopic-analysis-of-bulk-high-tc-superconductors-by-transmission-kikuchi-diffraction" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/126917.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">128</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> Pre-Transformation Phase Reconstruction for Deformation-Induced Transformation in AISI 304 Austenitic Stainless Steel</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Manendra%20Singh%20Parihar">Manendra Singh Parihar</a>, <a href="https://publications.waset.org/abstracts/search?q=Sandip%20Ghosh%20Chowdhury"> Sandip Ghosh Chowdhury</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Austenitic stainless steels are widely used and give a good combination of properties. When this steel is plastically deformed, a phase transformation of the metastable Face Centred Cubic Austenite to the stable Body Centred Cubic (α’) or to the Hexagonal close packed (ԑ) martensite may occur, leading to the enhancement in the mechanical properties like strength. The work was based on variant selection and corresponding texture analysis for the strain induced martensitic transformation during deformation of the parent austenite FCC phase to form the product HCP and the BCC martensite phases separately, obeying their respective orientation relationships. The automated method for reconstruction of the parent phase orientation using the EBSD data of the product phase orientation is done using the MATLAB and TSL-OIM software. The method of triplets was used which involves the formation of a triplet of neighboring product grains having a common variant and linking them using a misorientation-based criterion. This led to the proper reconstruction of the pre-transformation phase orientation data and thus to its microstructure and texture. The computational speed of current method is better compared to the previously used methods of reconstruction. The reconstruction of austenite from ԑ and α’ martensite was carried out for multiple samples and their IPF images, pole figures, inverse pole figures and ODFs were compared. Similar type of results was observed for all samples. The comparison gives the idea for estimating the correct sequence of the transformation i.e. γ → ε → α’ or γ → α’, during deformation of AISI 304 austenitic stainless steel. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=variant%20selection" title="variant selection">variant selection</a>, <a href="https://publications.waset.org/abstracts/search?q=reconstruction" title=" reconstruction"> reconstruction</a>, <a href="https://publications.waset.org/abstracts/search?q=EBSD" title=" EBSD"> EBSD</a>, <a href="https://publications.waset.org/abstracts/search?q=austenitic%20stainless%20steel" title=" austenitic stainless steel"> austenitic stainless steel</a>, <a href="https://publications.waset.org/abstracts/search?q=martensitic%20transformation" title=" martensitic transformation"> martensitic transformation</a> </p> <a href="https://publications.waset.org/abstracts/28354/pre-transformation-phase-reconstruction-for-deformation-induced-transformation-in-aisi-304-austenitic-stainless-steel" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/28354.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">497</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> Variant Selection and Pre-transformation Phase Reconstruction for Deformation-Induced Transformation in AISI 304 Austenitic Stainless Steel</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Manendra%20Singh%20Parihar">Manendra Singh Parihar</a>, <a href="https://publications.waset.org/abstracts/search?q=Sandip%20Ghosh%20Chowdhury"> Sandip Ghosh Chowdhury</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Austenitic stainless steels are widely used and give a good combination of properties. When this steel is plastically deformed, a phase transformation of the metastable Face Centred Cubic Austenite to the stable Body Centred Cubic (α’) or to the Hexagonal close packed (ԑ) martensite may occur, leading to the enhancement in the mechanical properties like strength. The work was based on variant selection and corresponding texture analysis for the strain induced martensitic transformation during deformation of the parent austenite FCC phase to form the product HCP and the BCC martensite phases separately, obeying their respective orientation relationships. The automated method for reconstruction of the parent phase orientation using the EBSD data of the product phase orientation is done using the MATLAB and TSL-OIM software. The method of triplets was used which involves the formation of a triplet of neighboring product grains having a common variant and linking them using a misorientation-based criterion. This led to the proper reconstruction of the pre-transformation phase orientation data and thus to its micro structure and texture. The computational speed of current method is better compared to the previously used methods of reconstruction. The reconstruction of austenite from ԑ and α’ martensite was carried out for multiple samples and their IPF images, pole figures, inverse pole figures and ODFs were compared. Similar type of results was observed for all samples. The comparison gives the idea for estimating the correct sequence of the transformation i.e. γ → ε → α’ or γ → α’, during deformation of AISI 304 austenitic stainless steel. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=variant%20selection" title="variant selection">variant selection</a>, <a href="https://publications.waset.org/abstracts/search?q=reconstruction" title=" reconstruction"> reconstruction</a>, <a href="https://publications.waset.org/abstracts/search?q=EBSD" title=" EBSD"> EBSD</a>, <a href="https://publications.waset.org/abstracts/search?q=austenitic%20stainless%20steel" title=" austenitic stainless steel"> austenitic stainless steel</a>, <a href="https://publications.waset.org/abstracts/search?q=martensitic%20transformation" title=" martensitic transformation"> martensitic transformation</a> </p> <a href="https://publications.waset.org/abstracts/24633/variant-selection-and-pre-transformation-phase-reconstruction-for-deformation-induced-transformation-in-aisi-304-austenitic-stainless-steel" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/24633.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">489</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> Effect of Strains and Temperature on the Twinning Behavior of High Purity Titanium Compressed by Split Hopkinson Pressure Bar</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Ping%20Zhou">Ping Zhou</a>, <a href="https://publications.waset.org/abstracts/search?q=Dawu%20Xiao"> Dawu Xiao</a>, <a href="https://publications.waset.org/abstracts/search?q=Chunli%20Jiang"> Chunli Jiang</a>, <a href="https://publications.waset.org/abstracts/search?q=Ge%20Sang"> Ge Sang</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Deformation twinning plays an important role in the mechanical properties of Ti which has high specific strength and excellent corrosion resistance ability. To investigate the twinning behavior of Ti under high strain rate compression, the split Hopkinson pressure bar (SHPB) was adopted to deform samples to different strains at room temperature. In addition, twinning behaviors under varied temperatures of 373K, 573K and 873K were also investigated. The cylindrical-shaped samples with purity 99.995% were annealed at 1073K for 1 hour in vacuum before compression. All the deformation twins were identified by electron backscatter diffraction (EBSD) techniques. The mechanical behavior showed three-stage work hardening in stress-strain curves for samples deformed at temperature 573K and 873K, while only two stages were observed for those deformed at room temperature. For samples compressed at room temperature, the predominant twin types are {10-12}<10-11> (E1), {11-21}<11-26> (E2) and {11-21}<11-23> (C1). The secondary and tertiary twinning was observed inside some E1, E2 and C1 twins. Most of the twin boundaries of E2 acted as the nucleate sites of E1. The densities of twins increase remarkably with increment of strains. For samples compressed at relatively higher temperatures, the migration of twin boundaries of E1, E2 and C1 was observed. All the twin lamellas shorten with temperature, and nearly disappeared at 873K except some remaining E1 twins. Polygonizations of grain boundaries were observed above 573K. The microstructure intended to have a texture with c-axes parallel to compression direction with temperature increment. Factors affecting the dynamic recovery and re-crystallization were discussed. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=deformation%20twins" title="deformation twins">deformation twins</a>, <a href="https://publications.waset.org/abstracts/search?q=EBSD" title=" EBSD"> EBSD</a>, <a href="https://publications.waset.org/abstracts/search?q=mechanical%20behavior" title=" mechanical behavior"> mechanical behavior</a>, <a href="https://publications.waset.org/abstracts/search?q=high%20strain%20rate" title=" high strain rate"> high strain rate</a>, <a href="https://publications.waset.org/abstracts/search?q=titanium" title=" titanium"> titanium</a> </p> <a href="https://publications.waset.org/abstracts/67586/effect-of-strains-and-temperature-on-the-twinning-behavior-of-high-purity-titanium-compressed-by-split-hopkinson-pressure-bar" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/67586.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">51</span> Effect of Cryogenic Pre-stretching on the Room Temperature Tensile Behavior of AZ61 Magnesium Alloy and Dominant Grain Growth Mechanisms During Subsequent Annealing</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Umer%20Masood%20Chaudry">Umer Masood Chaudry</a>, <a href="https://publications.waset.org/abstracts/search?q=Hafiz%20Muhammad%20Rehan%20Tariq"> Hafiz Muhammad Rehan Tariq</a>, <a href="https://publications.waset.org/abstracts/search?q=Chung-soo%20Kim"> Chung-soo Kim</a>, <a href="https://publications.waset.org/abstracts/search?q=Tea-sung%20Jun"> Tea-sung Jun</a> </p> <p class="card-text"><strong>Abstract:</strong></p> This study explored the influence of pre-stretching temperature on the microstructural characteristics and deformation behavior of AZ61 magnesium alloy and its implications on grain growth during subsequent annealing. AZ61 alloy was stretched to 5% plastic strain along rolling (RD) and transverse direction (TD) at room (RT) and cryogenic temperature (-150 oC, CT) followed by annealing at 320 oC for 1 h to investigate the twinning and dislocation evolution and its consequent effect on the flow stress, plastic strain and strain hardening rate. Compared to RT-stretched samples, significant improvement in yield stress, strain hardening rate and moderate reduction in elongation to failure were witnessed for CT-stretched samples along RD and TD. The subsequent EBSD analysis revealed the increased fraction of fine {10-12} twins and nucleation of multiple {10-12} twin variants caused by higher local stress concentration at the grain boundaries in CT-stretched samples as manifested by the kernel average misorientation. This higher twin fraction and twin-twin interaction imposed the strengthening by restricting the mean free path of dislocations, leading to higher flow stress and strain hardening rate. During annealing of the RT/CT-stretched samples, the residual strain energy and twin boundaries were decreased due to static recovery, leading to a coarse-grained twin-free microstructure. Strain induced boundary migration (SBIM) was found to be the predominant mechanism governing the grain growth during annealing via movement of high angle grain boundaries. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=magnesium" title="magnesium">magnesium</a>, <a href="https://publications.waset.org/abstracts/search?q=twinning" title=" twinning"> twinning</a>, <a href="https://publications.waset.org/abstracts/search?q=twinning%20variant%20selection" title=" twinning variant selection"> twinning variant selection</a>, <a href="https://publications.waset.org/abstracts/search?q=EBSD" title=" EBSD"> EBSD</a>, <a href="https://publications.waset.org/abstracts/search?q=cryogenic%20deformation" title=" cryogenic deformation"> cryogenic deformation</a> </p> <a href="https://publications.waset.org/abstracts/172106/effect-of-cryogenic-pre-stretching-on-the-room-temperature-tensile-behavior-of-az61-magnesium-alloy-and-dominant-grain-growth-mechanisms-during-subsequent-annealing" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/172106.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">67</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> Effect of Crystallographic Characteristics on Toughness of Coarse Grain Heat Affected Zone for Different Heat Inputs</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Trishita%20Ray">Trishita Ray</a>, <a href="https://publications.waset.org/abstracts/search?q=Ashok%20Perka"> Ashok Perka</a>, <a href="https://publications.waset.org/abstracts/search?q=Arnab%20Karani"> Arnab Karani</a>, <a href="https://publications.waset.org/abstracts/search?q=M.%20Shome"> M. Shome</a>, <a href="https://publications.waset.org/abstracts/search?q=Saurabh%20Kundu"> Saurabh Kundu</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Line pipe steels are used for long distance transportation of crude oil and gas under extreme environmental conditions. Welding is necessary to lay large scale pipelines. Coarse Grain Heat Affected Zone (CGHAZ) of a welded joint exhibits worst toughness because of excessive grain growth and brittle microstructures like bainite and martensite, leading to early failure. Therefore, it is necessary to investigate microstructures and properties of the CGHAZ for different welding heat inputs. In the present study, CGHAZ for two heat inputs of 10 kJ/cm and 50 kJ/cm were simulated in Gleeble 3800, and the microstructures were investigated in detail by means of Scanning Electron Microscopy (SEM) and Electron Backscattered Diffraction (EBSD). Charpy Impact Tests were also done to evaluate the impact properties. High heat input was characterized with very low toughness and massive prior austenite grains. With the crystallographic information from EBSD, the area of a single prior austenite grain was traced out for both the welding conditions. Analysis of the prior austenite grains showed the formation of high angle boundaries between the crystallographic packets. Effect of these packet boundaries on secondary cleavage crack propagation was discussed. It was observed that in the low heat input condition, formation of finer packets with a criss-cross morphology inside prior austenite grains was effective in crack arrest whereas, in the high heat input condition, formation of larger packets with higher volume of low angle boundaries failed to resist crack propagation resulting in a brittle fracture. Thus, the characteristics in a crystallographic packet and impact properties are related and should be controlled to obtain optimum properties. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=coarse%20grain%20heat%20affected%20zone" title="coarse grain heat affected zone">coarse grain heat affected zone</a>, <a href="https://publications.waset.org/abstracts/search?q=crystallographic%20packet" title=" crystallographic packet"> crystallographic packet</a>, <a href="https://publications.waset.org/abstracts/search?q=toughness" title=" toughness"> toughness</a>, <a href="https://publications.waset.org/abstracts/search?q=line%20pipe%20steel" title=" line pipe steel"> line pipe steel</a> </p> <a href="https://publications.waset.org/abstracts/72858/effect-of-crystallographic-characteristics-on-toughness-of-coarse-grain-heat-affected-zone-for-different-heat-inputs" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/72858.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">245</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> Grain Structure Evolution during Friction-Stir Welding of 6061-T6 Aluminum Alloy</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Aleksandr%20Kalinenko">Aleksandr Kalinenko</a>, <a href="https://publications.waset.org/abstracts/search?q=Igor%20Vysotskiy"> Igor Vysotskiy</a>, <a href="https://publications.waset.org/abstracts/search?q=Sergey%20Malopheyev"> Sergey Malopheyev</a>, <a href="https://publications.waset.org/abstracts/search?q=Sergey%20Mironov"> Sergey Mironov</a>, <a href="https://publications.waset.org/abstracts/search?q=Rustam%20Kaibyshev"> Rustam Kaibyshev</a> </p> <p class="card-text"><strong>Abstract:</strong></p> From a thermo-mechanical standpoint, friction-stir welding (FSW) represents a unique combination of very large strains, high temperature and relatively high strain rate. The material behavior under such extreme deformation conditions is not studied well and thus, the microstructural examinations of the friction-stir welded materials represent an essential academic interest. Moreover, a clear understanding of the microstructural mechanisms operating during FSW should improve our understanding of the microstructure-properties relationship in the FSWed materials and thus enables us to optimize their service characteristics. Despite extensive research in this field, the microstructural behavior of some important structural materials remains not completely clear. In order to contribute to this important work, the present study was undertaken to examine the grain structure evolution during the FSW of 6061-T6 aluminum alloy. To provide an in-depth insight into this process, the electron backscatter diffraction (EBSD) technique was employed for this purpose. Microstructural observations were conducted by using an FEI Quanta 450 Nova field-emission-gun scanning electron microscope equipped with TSL OIMTM software. A suitable surface finish for EBSD was obtained by electro-polishing in a solution of 25% nitric acid in methanol. A 15° criterion was employed to differentiate low-angle boundaries (LABs) from high-angle boundaries (HABs). In the entire range of the studied FSW regimes, the grain structure evolved in the stir zone was found to be dominated by nearly-equiaxed grains with a relatively high fraction of low-angle boundaries and the moderate-strength B/-B {112}<110> simple-shear texture. In all cases, the grain-structure development was found to be dictated by an extensive formation of deformation-induced boundaries, their gradual transformation to the high-angle grain boundaries. Accordingly, the grain subdivision was concluded to the key microstructural mechanism. Remarkably, a gradual suppression of this mechanism has been observed at relatively high welding temperatures. This surprising result has been attributed to the reduction of dislocation density due to the annihilation phenomena. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=electron%20backscatter%20diffraction" title="electron backscatter diffraction">electron backscatter diffraction</a>, <a href="https://publications.waset.org/abstracts/search?q=friction-stir%20welding" title=" friction-stir welding"> friction-stir welding</a>, <a href="https://publications.waset.org/abstracts/search?q=heat-treatable%20aluminum%20alloys" title=" heat-treatable aluminum alloys"> heat-treatable aluminum alloys</a>, <a href="https://publications.waset.org/abstracts/search?q=microstructure" title=" microstructure"> microstructure</a> </p> <a href="https://publications.waset.org/abstracts/130602/grain-structure-evolution-during-friction-stir-welding-of-6061-t6-aluminum-alloy" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/130602.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">236</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">48</span> The Role of Nickel on the High-Temperature Corrosion of Modell Alloys (Stainless Steels) before and after Breakaway Corrosion at 600°C: A Microstructural Investigation</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Imran%20Hanif">Imran Hanif</a>, <a href="https://publications.waset.org/abstracts/search?q=Amanda%20Persdotter"> Amanda Persdotter</a>, <a href="https://publications.waset.org/abstracts/search?q=Sedigheh%20Bigdeli"> Sedigheh Bigdeli</a>, <a href="https://publications.waset.org/abstracts/search?q=Jesper%20Liske"> Jesper Liske</a>, <a href="https://publications.waset.org/abstracts/search?q=Torbjorn%20Jonsson"> Torbjorn Jonsson</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Renewable fuels such as biomass/waste for power production is an attractive alternative to fossil fuels in order to achieve a CO₂ -neutral power generation. However, the combustion results in the release of corrosive species. This puts high demands on the corrosion resistance of the alloys used in the boiler. Stainless steels containing nickel and/or nickel containing coatings are regarded as suitable corrosion resistance material especially in the superheater regions. However, the corrosive environment in the boiler caused by the presence of water vapour and reactive alkali very rapidly breaks down the primary protection, i.e., the Cr-rich oxide scale formed on stainless steels. The lifetime of the components, therefore, relies on the properties of the oxide scale formed after breakaway, i.e., the secondary protection. The aim of the current study is to investigate the role of varying nickel content (0–82%) on the high-temperature corrosion of model alloys with 18% Cr (Fe in balance) in the laboratory mimicking industrial conditions at 600°C. The influence of nickel is investigated on both the primary protection and especially the secondary protection, i.e., the scale formed after breakaway, during the oxidation/corrosion process in the dry O₂ (primary protection) and more aggressive environment such as H₂O, K₂CO₃ and KCl (secondary protection). All investigated alloys experience a very rapid loss of the primary protection, i.e., the Cr-rich (Cr, Fe)₂O₃, and the formation of secondary protection in the aggressive environments. The microstructural investigation showed that secondary protection of all alloys has a very similar microstructure in all more aggressive environments consisting of an outward growing iron oxide and inward growing spinel-oxide (Fe, Cr, Ni)₃O₄. The oxidation kinetics revealed that it is possible to influence the protectiveness of the scale formed after breakaway (secondary protection) through the amount of nickel in the alloy. The difference in oxidation kinetics of the secondary protection is linked to the microstructure and chemical composition of the complex spinel-oxide. The detailed microstructural investigations were carried out using the extensive analytical techniques such as electron back scattered diffraction (EBSD), energy dispersive X-rays spectroscopy (EDS) via the scanning and transmission electron microscopy techniques and results are compared with the thermodynamic calculations using the Thermo-Calc software. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=breakaway%20corrosion" title="breakaway corrosion">breakaway corrosion</a>, <a href="https://publications.waset.org/abstracts/search?q=EBSD" title=" EBSD"> EBSD</a>, <a href="https://publications.waset.org/abstracts/search?q=high-temperature%20oxidation" title=" high-temperature oxidation"> high-temperature oxidation</a>, <a href="https://publications.waset.org/abstracts/search?q=SEM" title=" SEM"> SEM</a>, <a href="https://publications.waset.org/abstracts/search?q=TEM" title=" TEM"> TEM</a> </p> <a href="https://publications.waset.org/abstracts/106753/the-role-of-nickel-on-the-high-temperature-corrosion-of-modell-alloys-stainless-steels-before-and-after-breakaway-corrosion-at-600c-a-microstructural-investigation" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/106753.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">141</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">47</span> A New Correlation between SPT and CPT for Various Soils</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Fauzi%20Jarushi">Fauzi Jarushi</a>, <a href="https://publications.waset.org/abstracts/search?q=Sinan%20Mohsin%20AlKaabi"> Sinan Mohsin AlKaabi</a> </p> <p class="card-text"><strong>Abstract:</strong></p> The Standard Penetration Test (SPT) is the most common insitu test for soil investigations. On the other hand, the Cone Penetration Test (CPT) is considered one of the best investigation tools. Due to the fast and accurate results that can be obtained it complaints the SPT in many applications like field explorations, design parameters, and quality control assessments. Many soil index and engineering properties have been correlated to both of SPT and CPT. Various foundation design methods were developed based on the outcome of these tests. Therefore it is vital to correlate these tests to each other so that either one of the tests can be used in the absence of the other, especially for preliminary evaluation and design purposes. The primary purpose of this study was to investigate the relationships between the SPT and CPT for different types of soil in Florida. Data for this research were collected from number of projects sponsored by the Florida Department of Transportation (FDOT), six sites served as the subject of SPT-CPT correlations. The correlations were established between the cone resistance (qc) and the SPT blows (i.e., N) for various soils. A positive linear relationship was found between fs and N for various soils. In general, qc versus N showed higher correlation coefficients than fs versus N. qc/N ratios were developed for different soil types and compared to literature values, the results of this research revealed higher ratios than literature values. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=in%20situ%20tests" title="in situ tests">in situ tests</a>, <a href="https://publications.waset.org/abstracts/search?q=correlation" title=" correlation"> correlation</a>, <a href="https://publications.waset.org/abstracts/search?q=SPT" title=" SPT"> SPT</a>, <a href="https://publications.waset.org/abstracts/search?q=CPT" title=" CPT"> CPT</a> </p> <a href="https://publications.waset.org/abstracts/23108/a-new-correlation-between-spt-and-cpt-for-various-soils" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/23108.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">397</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">46</span> Experimental Analysis of the Origins of the Anisotropy Behavior in the 2017 AA Aluminum Alloy</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=May%20Abdelghani">May Abdelghani</a> </p> <p class="card-text"><strong>Abstract:</strong></p> The present work is devoted to the study of the microstructural anisotropy in mechanical cyclic behavior of the 2017AA aluminum alloy which is widely used in the aerospace industry. The main purpose of the study is to investigate the microstructural origins of this anisotropy already confirmed in our previous work in 2017AA aluminum alloy. To do this, we have used the microstructural analysis resources such as Scanning Electron Microscope (SEM) to see the differences between breaks from different directions of cyclic loading. Another resource of investigation was used in this study is that the EBSD method, which allows us to obtain a mapping of the crystallographic texture of our material. According to the obtained results in the microscopic analysis, we are able to identify the origins of the anisotropic behavior at the macroscopic scale. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=fatigue%20damage" title="fatigue damage">fatigue damage</a>, <a href="https://publications.waset.org/abstracts/search?q=cyclic%20behavior" title=" cyclic behavior"> cyclic behavior</a>, <a href="https://publications.waset.org/abstracts/search?q=anisotropy" title=" anisotropy"> anisotropy</a>, <a href="https://publications.waset.org/abstracts/search?q=microstructural%20analysis" title=" microstructural analysis"> microstructural analysis</a> </p> <a href="https://publications.waset.org/abstracts/20127/experimental-analysis-of-the-origins-of-the-anisotropy-behavior-in-the-2017-aa-aluminum-alloy" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/20127.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">411</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">45</span> Undercooling of Refractory High-Entropy Alloy</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Liang%20Hu">Liang Hu</a> </p> <p class="card-text"><strong>Abstract:</strong></p> The innovation of refractory high-entropy alloy (RHEA) formed from refractory metals W, Ta, Mo, Nb, Hf, V, and Zr was firstly implemented in 2010 to obtain better strength at high temperature than conventional HEAs based on Al, Co, Cr, Cu, Fe and Ni. Due to the refractory characteristic and high chemical activity at elevated temperature, electrostatic levitation technique has been utilized to fulfill the rapid solidification of RHEA. Several RHEAs consisting W, Ta, Mo, Nb, Zr have been selected to perform the undercooling and rapid solidification by ESL. They are substantially undercooled by up to 0.2TL. The evolution of as-solidified microstructure and component redistribution with undercooling have been investigated by SEM, EBSD, and EPMA analysis. According to the EPMA results of composing elements at different undercooling levels, the chemical distribution relevant to undercooling was also analyzed. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=chemical%20distribution" title="chemical distribution">chemical distribution</a>, <a href="https://publications.waset.org/abstracts/search?q=high-entropy%20alloy" title=" high-entropy alloy"> high-entropy alloy</a>, <a href="https://publications.waset.org/abstracts/search?q=rapid%20solidification" title=" rapid solidification"> rapid solidification</a>, <a href="https://publications.waset.org/abstracts/search?q=undercooling" title=" undercooling"> undercooling</a> </p> <a href="https://publications.waset.org/abstracts/127404/undercooling-of-refractory-high-entropy-alloy" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/127404.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">128</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">44</span> Texture and Twinning in Selective Laser Melting Ti-6Al-4V Alloys</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=N.%20Kazantseva">N. Kazantseva</a>, <a href="https://publications.waset.org/abstracts/search?q=P.%20Krakhmalev"> P. Krakhmalev</a>, <a href="https://publications.waset.org/abstracts/search?q=I.%20Yadroitsev"> I. Yadroitsev</a>, <a href="https://publications.waset.org/abstracts/search?q=A.%20Fefelov"> A. Fefelov</a>, <a href="https://publications.waset.org/abstracts/search?q=N.%20Vinogradova"> N. Vinogradova</a>, <a href="https://publications.waset.org/abstracts/search?q=I.%20Ezhov"> I. Ezhov</a>, <a href="https://publications.waset.org/abstracts/search?q=T.%20Kurennykh"> T. Kurennykh</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Martensitic texture-phase transition in Selective Laser Melting (SLM) Ti-6Al-4V (ELI) alloys was found. Electron Backscatter Diffraction (EBSD) analysis showed the initial cubic beta < 100 > (001) BCC texture. Such kind of texture is observed in BCC metals with flat rolling texture when axis is in the direction of rolling and the texture plane coincides with the plane of rolling. It was found that the texture of the parent BCC beta-phase determined the texture of low-temperature HCP alpha-phase limited the choice of its orientation variants. The {10-12} < -1011 > twinning system in titanium alloys after SLM was determined. Analysis of the oxygen contamination in SLM alloys was done. Comparison of the obtained results with the conventional titanium alloys is also provided. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=additive%20technology" title="additive technology">additive technology</a>, <a href="https://publications.waset.org/abstracts/search?q=texture" title=" texture"> texture</a>, <a href="https://publications.waset.org/abstracts/search?q=twins" title=" twins"> twins</a>, <a href="https://publications.waset.org/abstracts/search?q=Ti-6Al-4V" title=" Ti-6Al-4V"> Ti-6Al-4V</a>, <a href="https://publications.waset.org/abstracts/search?q=oxygen%20content" title=" oxygen content"> oxygen content</a> </p> <a href="https://publications.waset.org/abstracts/63604/texture-and-twinning-in-selective-laser-melting-ti-6al-4v-alloys" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/63604.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">637</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">43</span> Phase Stability and Grain Growth Kinetics of Oxide Dispersed CoCrFeMnNi</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Prangya%20P.%20Sahoo">Prangya P. Sahoo</a>, <a href="https://publications.waset.org/abstracts/search?q=B.%20S.%20Murty"> B. S. Murty</a> </p> <p class="card-text"><strong>Abstract:</strong></p> The present study deals with phase evolution of oxide dispersed CoCrFeMnNi high entropy alloy as a function of amount of added Y2O3 during mechanical alloying and analysis of grain growth kinetics of CoCrFeMnNi high entropy alloy without and with oxide dispersion. Mechanical alloying of CoCrFeMnNi resulted in a single FCC phase. However, evolution of chromium carbide was observed after heat treatment between 1073 and 1473 K. Comparison of grain growth time exponents and activation energy barrier is also reported. Micro structural investigations, using electron microscopy and EBSD techniques, were carried out to confirm the enhanced grain growth resistance which is attributed to the presence oxide dispersoids. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=grain%20growth%20kinetics" title="grain growth kinetics">grain growth kinetics</a>, <a href="https://publications.waset.org/abstracts/search?q=mechanical%20alloying" title=" mechanical alloying"> mechanical alloying</a>, <a href="https://publications.waset.org/abstracts/search?q=oxide%20dispersion" title=" oxide dispersion"> oxide dispersion</a>, <a href="https://publications.waset.org/abstracts/search?q=phase%20evolution" title=" phase evolution"> phase evolution</a> </p> <a href="https://publications.waset.org/abstracts/58015/phase-stability-and-grain-growth-kinetics-of-oxide-dispersed-cocrfemnni" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/58015.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">429</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">42</span> Direct In-Situ Ring Opening Polymerization of E-caprolactone to Produce Biodegradable PCL/Montmorillonite Nanocomposites</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Amine%20Harrane">Amine Harrane</a>, <a href="https://publications.waset.org/abstracts/search?q=Mahmoud%20Belalia"> Mahmoud Belalia</a> </p> <p class="card-text"><strong>Abstract:</strong></p> During the last decade, polymer layered silicate nanocomposites have received increasing attention from scientists and industrial researchers because they generally exhibit greatly improved mechanical, thermal, barrier and flame-retardant properties at low clay content in comparison with unfilled polymers or more conventional micro composites. Poly(ε-caprolactone) (PCL)-layered silicate nanocomposites have the advantage of adding biocompatibility and biodegradability to the traditional properties of nanocomposites. They can be prepared by in situ ring-opening polymerization of ε-caprolactone using a conventional initiator to induce polymerization in the presence of an organophilic clay, such as organomodified montmorillonite. Messersmith and Giannelis used montmorillonite exchanged with protonated 12-amino dodecanoic acid and Cr3+ exchanged fluorohectorite, a synthetic mica type of silicate. Sn-based catalysts such as tin (II) octoate and dibutyltin (IV) dimethoxide have been reported to efficiently promote the polymerization of ε-caprolactone in the presence of organomodified clays. In this work, we have used an alternative method to prepare PCL/montmorillonite nanocomposites. The cationic polymerization of ε-caprolactone was initiated directly by Maghnite-TOA, organomodified montmorillonite clay, to produce nanocomposites (Scheme 1). Resulted from nanocomposites were characterized by X-ray diffraction (XRD), transmission electron microscopy (TEM), force atomic microscopy (AFM) and thermogravimetry. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=polycaprolactone" title="polycaprolactone">polycaprolactone</a>, <a href="https://publications.waset.org/abstracts/search?q=polycaprolactone%2Fclay%20nanocomposites" title=" polycaprolactone/clay nanocomposites"> polycaprolactone/clay nanocomposites</a>, <a href="https://publications.waset.org/abstracts/search?q=biodegradables%20nanocomposites" title=" biodegradables nanocomposites"> biodegradables nanocomposites</a>, <a href="https://publications.waset.org/abstracts/search?q=Maghnite" title=" Maghnite"> Maghnite</a>, <a href="https://publications.waset.org/abstracts/search?q=Insitu%20polymeriation" title=" Insitu polymeriation"> Insitu polymeriation</a> </p> <a href="https://publications.waset.org/abstracts/163797/direct-in-situ-ring-opening-polymerization-of-e-caprolactone-to-produce-biodegradable-pclmontmorillonite-nanocomposites" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/163797.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">78</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">41</span> A Study of the Weld Properties of Inconel 625 Based on Nb Content</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=JongWon%20Han">JongWon Han</a>, <a href="https://publications.waset.org/abstracts/search?q=NoHoon%20Kim"> NoHoon Kim</a>, <a href="https://publications.waset.org/abstracts/search?q=HyoIk%20Ahn"> HyoIk Ahn</a>, <a href="https://publications.waset.org/abstracts/search?q=HaeWoo%20Lee"> HaeWoo Lee</a> </p> <p class="card-text"><strong>Abstract:</strong></p> In this study, shielded metal arc welding was performed as a function of Nb content at 2.24 wt%, 3.25 wt%, and 4.26 wt%. The microstructure was observed using scanning electron microscopy/energy dispersive X-ray spectroscopy (SEM/EDS) and showed the development of a columnar dendrite structure in the specimen having the least Nb content. From the hardness test, the hardness value was confirmed to reduce with decreasing Nb content. From electron backscatter diffraction (EBSD) analysis, the largest grain size was found in the specimen with Nb content of 2.24 wt%. The potentiodynamic polarization test was carried out to determine the pitting corrosion resistance; there was no significant difference in the pitting corrosion resistance with increasing Nb content. To evaluate the degree of sensitization to intergranular corrosion, the Double Loop Electrochemical Potentiodynamic Reactivation(DL-EPR test) was conducted. A similar degree of sensitization was found in two specimens except with a Nb content of 2.24 wt%, while a relatively high degree of sensitization was found in the specimen with a Nb content of 2.24 wt%. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=inconel%20625" title="inconel 625">inconel 625</a>, <a href="https://publications.waset.org/abstracts/search?q=Nb%20content" title=" Nb content"> Nb content</a>, <a href="https://publications.waset.org/abstracts/search?q=potentiodynamic%20test" title=" potentiodynamic test"> potentiodynamic test</a>, <a href="https://publications.waset.org/abstracts/search?q=DL-EPR%20test" title=" DL-EPR test"> DL-EPR test</a> </p> <a href="https://publications.waset.org/abstracts/85849/a-study-of-the-weld-properties-of-inconel-625-based-on-nb-content" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/85849.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">308</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">40</span> The Role of Deformation Strain and Annealing Temperature on Grain Boundary Engineering and Texture Evolution of Haynes 230</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Mohsen%20Sanayei">Mohsen Sanayei</a>, <a href="https://publications.waset.org/abstracts/search?q=Jerzy%20Szpunar"> Jerzy Szpunar</a> </p> <p class="card-text"><strong>Abstract:</strong></p> The present study investigates the effects of deformation strain and annealing temperature on the formation of twin boundaries, deformation and recrystallization texture evolution and grain boundary networks and connectivity. The resulting microstructures were characterized using Electron Backscatter Diffraction (EBSD) and X-Ray Diffraction (XRD) both immediately following small amount of deformation and after short time annealing at high temperature to correlate the micro and macro texture evolution of these alloys. Furthermore, this study showed that the process of grain boundary engineering, consisting cycles of deformation and annealing, is found to substantially reduce the mass and size of random boundaries and increase the proportion of low Coincidence Site Lattice (CSL) grain boundaries. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=coincidence%20site%20lattice" title="coincidence site lattice">coincidence site lattice</a>, <a href="https://publications.waset.org/abstracts/search?q=grain%20boundary%20engineering" title=" grain boundary engineering"> grain boundary engineering</a>, <a href="https://publications.waset.org/abstracts/search?q=electron%20backscatter%20diffraction" title=" electron backscatter diffraction"> electron backscatter diffraction</a>, <a href="https://publications.waset.org/abstracts/search?q=texture" title=" texture"> texture</a>, <a href="https://publications.waset.org/abstracts/search?q=x-ray%20diffraction" title=" x-ray diffraction"> x-ray diffraction</a> </p> <a href="https://publications.waset.org/abstracts/70079/the-role-of-deformation-strain-and-annealing-temperature-on-grain-boundary-engineering-and-texture-evolution-of-haynes-230" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/70079.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">311</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">39</span> Recrystallization Microstructure Studies of Cold-Rolled Ta0.5Nb0.5Hf0.5ZrTi1.5 Non-Equiatomic Refractory High Entropy Alloy</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Veeresham%20Mokali">Veeresham Mokali</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Recrystallization microstructure and grain growth studies of Ta₀.₅Nb₀.₅Hf₀.₅ZrTi₁.₅ refractory high entropy alloy have been explored in the present work. The as-cast Ta₀.₅Nb₀.₅Hf₀.₅ZrTi₁.₅ alloy was cold-rolled to 90% in several passes at room temperature and further subjected to annealing treatment for recrystallization at 800°C, 1000°C, 1250°C, and 1400°C temperatures for one hour. However, the characterization of heavily cold-rolled and annealed condition specimens was done using scanning electron microscopy (SEM-EBSD). The cold-rolled specimens showed the development of an inhomogeneous microstructure. Upon annealing, recrystallized microstructures were achieved; in addition to that, the coarsening of microstructure with raising annealing temperature noticed in the range of 800°C – 1400°C annealed temperatures. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=refractory%20high%20entropy%20alloys" title="refractory high entropy alloys">refractory high entropy alloys</a>, <a href="https://publications.waset.org/abstracts/search?q=cold-rolling" title=" cold-rolling"> cold-rolling</a>, <a href="https://publications.waset.org/abstracts/search?q=recrystallization" title=" recrystallization"> recrystallization</a>, <a href="https://publications.waset.org/abstracts/search?q=microstructure" title=" microstructure"> microstructure</a> </p> <a href="https://publications.waset.org/abstracts/138947/recrystallization-microstructure-studies-of-cold-rolled-ta05nb05hf05zrti15-non-equiatomic-refractory-high-entropy-alloy" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/138947.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">202</span> </span> </div> </div> <ul class="pagination"> <li class="page-item disabled"><span class="page-link">&lsaquo;</span></li> <li class="page-item active"><span class="page-link">1</span></li> <li class="page-item"><a class="page-link" href="https://publications.waset.org/abstracts/search?q=in-situ%20EBSD&page=2">2</a></li> <li class="page-item"><a class="page-link" href="https://publications.waset.org/abstracts/search?q=in-situ%20EBSD&page=3">3</a></li> <li class="page-item"><a class="page-link" href="https://publications.waset.org/abstracts/search?q=in-situ%20EBSD&page=2" rel="next">&rsaquo;</a></li> </ul> </div> </main> <footer> <div id="infolinks" class="pt-3 pb-2"> <div class="container"> <div style="background-color:#f5f5f5;" 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