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287 results for “alloy”
Dataset: The effect of a keyhole defect on strain localisation in an additive manufactured titanium alloy
<p><strong>This is the dataset used in the following publication: </strong></p> <div> <div> <div> <p>S. Cao, R. Thomas, A.D. Smith, P. Zhang, L. Meng, H. Liu, J. Guo, J. Donoghue, D. Lunt, The effect of a keyhole defect on strain localisation in an additive manufactured titanium alloy, Journal of Materials Research and Technology, https://doi.org/10.1016/j.jmrt.2024.11.237</p> </div> </div> </div> <p><strong>Contained in this dataset are:</strong></p> <p>A Jupyter notebook which uses the open-source DefDAP Python package (https://github.com/MechMicroMan/DefDAP) to open enclosed HRDIC and EBSD data for two regions in an SLM Ti64 sample, one around a keyhole defect and one ~1mm away in the bulk.</p> <p>Please use the 'master' version of DefDAP: <a href="https://github.com/MechMicroMan/DefDAP/tree/51074e158b0131c69358ddf7eee319e41cf582ca">https://github.com/MechMicroMan/DefDAP/</a></p> <p><strong>Publication abstract:</strong></p> <p>The influence of a keyhole defect on local deformation behaviour in additive manufactured Ti-6Al-4V was investigated by comparing it to a representative bulk region without a defect. High resolution digital image correlation (HRDIC) was used to measure the differences in strain localisation at the microstructural length-scale. A nanoscale speckle pattern was used to allow small changes in strain to be detected and resolved within a single individual lamella and at pre-existing crack locations around the defect. Strain localisation was observed around the defect and formed well below the macroscopic yield stress. In contrast, minimal deformation was found in the bulk at this stress level. Following further deformation into the plastic regime, the strain localisation around the keyhole became more heterogenous with a distinct strain field. A large amount of strain localisation and <c+a> slip was observed either side of the defect normal to the loading direction compared to relatively little in the regions close to the defect in line with the loading direction. This HRDIC observation was consistent with finite element analysis of the expected strain fields around the defect both below and above the yield point. Furthermore, micro-cracks were observed in αp/αp and αp/βt interfaces in both regions with the more pronounced strain fields around the defect leading to an increased number of long micro-cracks than in the bulk. The formation mechanisms of micro-cracks have been discussed, emphasising the role of localised strain caused by the defect.</p> <p> </p>
Imaging luminescence thermometry to 750 °C for the heat treatment of common engineering alloys and comparison with thermal imaging
<p>Data presented in the IJOT paper: Imaging luminescence thermometry to 750 °C for the heat treatment of common engineering alloys and comparison with thermal imaging</p>
Dataset for "Studying GPI zones in Al-Zn-Mg alloys by 4D-STEM"
<p>This dataset contains the data used in the publication titled "Studying GPI zones in Al-Zn-Mg alloys by 4D-STEM" currently in review in Materials Characterization.</p> <p>The data in this dataset are:</p> <ul> <li>Raw SPED data</li> <li>All structural models used in the density functional theory (DFT) calculations</li> </ul> <p>The raw SPED data are given as .mib- and .hdr files and can be opened using e.g. the Python package HyperSpy. The jupyter notebook used to analyse the data is available from <a href="https://doi.org/10.5281/zenodo.5518852">10.5281/zenodo.5518852</a>. A total of five SPED datasets were used in the analysis and are included in the .zip-file.</p> <p>The DFT calculations are given in the OUTCAR files. OUTCAR1 contains all the information about the initial relaxation. OUTCAR2 contains all the information about the final relaxations steps at a higher accuracy than OUTCAR1. OUTCAR3 contains all the information about the accurate energy calculations. </p> <p> </p>
Permittivity of AuAg alloys along with calculations and measurements of the alloyed Fano-resonant structures
<p>Here I present the data corresponding to the manuscript "Low temperature annealing method for fabricating alloy nanostructures and metasurfaces: Unlocking a novel degree of freedom" (arXiv:2105.02461). In this work, I have provided a technique of alloying AuAg at low temperature. Here I present the measured ellipsometric data of the AuAg alloys alloyed at low temperatures and measurements of the single structure AuAg alloyed 4-rod Fano-resonance nanostructures. I have also provided the calculations of the Fano-resonant structures using the permittivity of the Rioux model as well as well as the permittivity obtained from the Rioux model. Each .zip file is associated with a Readme file explaining everything in greater details.</p>
Dataset for paper entitled 'Microstructure transition gradients in titanium dissimilar alloy (Ti-5Al-5V-5Mo-3Cr/Ti-6Al-4V) tailored wire-arc additively manufactured components'
<p>Dataset for paper entitled 'Microstructure transition gradients in titanium dissimilar alloy (Ti-5Al-5V-5Mo-3Cr/Ti-6Al-4V) tailored wire-arc additively manufactured components'. doi: <a href="https://doi.org/10.1016/j.matchar.2021.111577">https://doi.org/10.1016/j.matchar.2021.111577</a></p>
Cast Al-Si-Mg alloy APT data
<p>Data from publication. Will be opened when publication is online (hopefully 2022).</p> <p>Atom probe tomography data.</p>
Electron backscatter diffraction data and backscatter electron images from a cold-rolled and recovered Al-Mn alloy
<p>Three electron backscatter diffraction (EBSD) data sets and three sets of backscatter electron (BSE) images from the same region of interest in a cold-rolled and recovered Al-Mn alloy.</p> <p>The data forms part of the supplementary material to the paper H W Ånes, A T J van Helvoort, K Marthinsen "Correlated subgrain and particle analysis of a recovered Al-Mn alloy by directly combining EBSD and backscatter electron imaging" (2022), published in Materials Characterization.</p> <p>The data was acquired in order to study the effect of particles on recovery and recrystallization in the Al-Mn alloy. The particles detected in the BSE images were inserted in the EBSD map after the EBSD map had been corrected for distortions by image registration using the BSE images.</p> <p>See the GitHub repository https://github.com/hakonanes/correlated-grains-particles-workflow for Jupyter notebooks and (MATLAB) MTEX scripts used to analyze the data.</p>
Modelling dynamic precipitation in pre-aged aluminium alloys
<p>Calculation of precipitation kinetics under deformation</p> <p>This repository contains the data plotted in https://doi.org/10.1016/j.actamat.2022.118036 as well as the code used to generate them.</p> <p>The code can be run reading the instructions contained in README.txt</p>
Data of "Ductile fracture of high entropy alloys: from the design of an experimental campaign to the development of a micromechanics-based modeling framework"
<p>Data related to the publication (we would be grateful if you could cite the paper in the case in which you are using the data):</p> <p>title = "Ductile fracture of high entropy alloys: from the design of an experimental campaign to the development of a micromechanics-based modeling framework",<br> journal = "Engineering Fracture Mechanics",<br> year = "2022",<br> volume = "275",<br> pages = "108844 ",<br> doi = "https://doi.org/10.1016/j.engfracmech.2022.108844",<br> author = "Antoine Hilhorst, Julien Leclerc, Thomas Pardoen, Pascal J. Jacques, Ludovic Noels, Van-Dung Nguyen"</p> <p>New version following review.</p> <p> </p> <p> </p>
Data for "Structure, short-range order, and phase stability of the Al$_x$CrFeCoNi high-entropy alloy: Insights from a perturbative, DFT-based analysis"
<p>Data associated with "Structure, short-range order, and phase stability of the AlxCrFeCoNi high-entropy alloy: Insights from a perturbative, DFT-based analysis", published in npj Comput. Mater. <strong>10</strong>, 271 (2024).</p>
High temperature properties incuding creep, creep crack growth rate and thermal fatigue linked with chemical composition of alloys derived from 1.4848 refractory stainless steels
<p>The following set of data results from cast alloys modifying chemical composition taking as reference 1.4848 alloy and getting sound samples that have been tested to calculate creep, creep crack growth rate and thermal fatigue data. </p>
DFT-based Monte Carlo Trajectories for Surface Segregation of Disordered FCC AuCuPd Alloys
<p>A zip file containing 600 subfolders named as "mc_run_$idx"". Each subfolder contains an "analysis.json" and "run_state.json" containing an analysis of the surface segregation output and describing the simulation (the composition of the bulk slab, whether the simulation encountered any errors, etc). Optionally also includes a "job.out" with job logs.</p>
DFT-based Monte Carlo Trajectories for Surface Segregation of Disordered FCC AgAuCu Alloys
<p>A zip file containing 600 subfolders named as "mc_run_$idx". Each subfolder contains an "analysis.json" and "run_state.json" containing an analysis of the surface segregation output and describing the simulation (the composition of the bulk slab, whether the simulation encountered any errors, etc). Optionally also includes a "job.out" with job logs.</p>
Datased for a publication: "Harmonizing Microstructures and Enhancing Mechanical Resilience: Novel Powder Metallurgy Approach for Zn-Mg Alloys"
<p>These data are published as a part of the paper: Harmonizing Microstructures and Enhancing Mechanical Resilience: Novel Powder Metallurgy Approach for Zn-Mg Alloys. The structure and organization of the data are outlined in the readme file. </p> <p> </p> <p><strong>Dataset versions:</strong></p> <p><strong>V1:</strong> Original version of the data.</p>
Effect of a laser heat treatment on the thickness distribution of AZ31B Mg Alloy Truncated Cone obtained via Superplastic Forming
<p><span>Thickness distribution of a Mg alloy (AZ31B) truncated cone obtained by means of the superplastic forming process (SPF) starting both from the alloy in the As Received condition and after a localised laser heat treatment, using different initial blank diameters and radii of the laser trajectory </span></p>
Role of laser wobbling welding parameters in dissimilar welding of aluminum and copper alloys: general preliminary process window.
<p>This database explores a wide range of process parameters concerning laser welding of aluminum and copper 0.3 mm thick foils in lap configuration. In particular, this application involves wobbling technique as a dynamic beam shaping for enhancing the formation of a correct interface width in this kind of welding. Given different values of laser power, wobbling tangential speed and wobbling diameter, the results are expressed in terms of weld bead width at the face of the weld bead, weld bead width at the interface between the two sheets and bead penetration depth in the lower sheet. Some trials gave an excessive penetration so that the specimen was cut in two separate parts after the process. This specific type of dissimilar welding is useful for enhancing "hybrid" characteristics of components, where a trade-off between mechanical and electrical or thermal characteristics is needed.</p>
Segmented primary phases of Al-alloy EN AW-2618A in the T61 state using synchrotron computed tomography
<p><span>This video shows the primary phases of the aluminum alloy EN AW-2618A in the T61 state measured by synchrotron computed tomography. </span></p> <p><span>Further information is provided in the file content.pdf. </span></p>
High Temperature Compression Studies of Ti64 and Ti407 Alloys using Dilatometer
Ti64 and Ti407 alloys were compressed at temperatures 700C, 850C and 950C and strain rates 10-2, 10-1 and 1 s-1 to 50% height reduction using TA Instruments DIL805 Compression Dilatometer. The cylindrical samples measured 5 mm diameter and 10 mm length. The Ti64 alloy was machined from the top of an as-received forged Airbus testpiece with a bimodal microstructure. The Ti407 alloy was machined from the edge of a forged TIMET testpiece with a lamellar microstructure. Al2O3 platens were used throughout all tests to minimise temperature differences between the end and centre of the samples, except at 700C in Ti64 which used Si3N4 platens due to the higher material yield strength. Temperature was controlled using an S-Type thermocouple welded to the centre of the samples, along with another two thermocouples welded to the end and between the end and centre of samples to monitor temperature differences. Mo disks were attached to the ends of the samples to further reduce temperature differences at the ends of the samples, along with graphite lubricant to reduce friction. The alloys were deformed in an inert He gas atmosphere.
Data bundle for "The role of beta-titanium ligaments in the deformation of dual phase titanium alloys"
<p>Data bundle for "The role of ¥â-titanium ligaments in the deformation of dual phase titanium alloys"</p> <p>Tea-Sung Jun1,2, Xavier Maeder3, Ayan Bhowmik1,a, Gaylord Guillonneau3,4, Johann Michler3, Finn Giuliani1, T. Ben Britton1*<br> 1 Department of Materials, Royal School of Mines, Imperial College London, London SW7 2AZ, UK<br> 2 Department of Mechanical Engineering, Incheon National University, Incheon 22012, Republic of Korea<br> 3 EMPA, Swiss Federal Laboratories for Materials Science and Technology, Laboratory for Mechanics of Materials and Nanostructures, Feuerwerkerstrasse 39, CH-3602 Thun, Switzerland<br> 4 Universite de Lyon, Ecole Centrale de Lyon, LTDS UMR CNRS 5513, 36 Avenue Guy de Collongue, 69134 Ecully Cedex, France<br> a now at Rolls-Royce@NTU Corporate Lab, Nanyang Technological University, Singapore</p> <p>For more information please contact: b.britton@imperial.ac.uk (Ben Britton)</p> <p>---</p> <p>This data bundle contains 1 file and 5 subfolders:</p> <p>Figures - all the images that were included in the paper<br> Subfolder for Figure 4 - raw data for load vs. displacement<br> Subfolder for Figure 7(A) - raw data for engineering stress vs. engineering strain <br> Subfolder for Figure 7(B) - cross court data and images of beta vertical micropillar <br> Subfolder for Figure 7(C) - cross court data and images of beta inclined micropillar<br> Subfolder for Figure 10 - raw data for stress relaxation vs. time</p>
EDX Electron Tomography Dataset on AlSiYb-Alloy
<p>Sample: Al-5 wt.% Si alloy with 50 ppm Na and 6100 ppm Yb, FIB prepared</p> <p>Microscope: FEI Titan<sup>3 </sup>60-300, Cs-corrected, FEI Super-X Detector</p> <p>Fischione 2020 Advanced Tomography Holder</p> <p>300 kV, STEM Nanoprobe, Convergence angle: 10 mrad, Camera length: 46 mm, Magnification: 160 kx</p> <p>Tilt angle: -74° to 78°, 4° linear tilt step</p> <p>Pixel Size: 0.760305 nm, Image Size: 276*296, Pixel time: 2ms</p> <p>HAADF Data: Fischione HAADF Detector (~116-177 mrad)</p> <p>EDX Data: Maps extracted with GMS 3, Kramers Background fit, Al-K, Si-K and Yb-L maps</p>
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